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超好的环氧树脂复合材料英文文献

超好的环氧树脂复合材料英文文献

/Journal of Reinforced Plastics and Composites/content/30/19/1621The online version of this article can be found at:DOI: 10.1177/07316844114268102011 30: 1621 originally published online 7 November 2011Journal of Reinforced Plastics and Composites N. Venkateshwaran, A. ElayaPerumal and M. S. JagatheeshwaranEffect of fiber length and fiber content on mechanical properties of banana fiber/epoxy compositePublished by: can be found at:Journal of Reinforced Plastics and Composites Additional services and information for/cgi/alerts Email Alerts:/subscriptions Subscriptions: /journalsReprints.nav Reprints:/journalsPermissions.nav Permissions:/content/30/19/1621.refs.html Citations:What is This?- Nov 7, 2011OnlineFirst Version of Record- Dec 16, 2011Version of Record >>ArticleEffect of fiber length and fiber contenton mechanical properties of banana fiber/epoxy compositeN.Venkateshwaran,A.ElayaPerumal and M.S.JagatheeshwaranAbstractThe main factors that influence the properties of composite are fiber length and content.Hence the prediction of optimum fiber length and content becomes important,so that composite can be prepared with best mechanical prop-erties.Experiments are carried out as per ASTM standards to find the mechanical properties namely,tensile strength and modulus,flexural strength and modulus,and impact strength.In addition to mechanical properties,water absorption capacity of the composite is also studied.Further,fractured surface of the specimen are subjected to morphological study using scanning electron microscope.The investigation revealed the suitability of banana fiber as an effective reinforce-ment in epoxy matrix.Keywordspolymer composites,banana fiber,mechanical properties,scanning electron microscopeIntroductionNowadays,polymers are used everywhere in the day-to-day life.Plastics found its way when the need for low weight high strength material became important for various applications.The research in thefield of poly-mer and polymer-based components has gained wide-spread recognition owing to its property;however,its bio-degradability is still a matter of concern.Further, glassfiber reinforced polymers(GFRP)have become appealing substitutes for aluminum,concrete,and steel due to its high strength-to-weight ratio,ease of handling,and for being corrosion-free.Moreover, they can also be engineered to get the desired proper-ties.1Since large-scale production and fabrication of glassfiber causes environmental problems and also health hazards,a suitable alternate which is environ-mental friendly is the need of the hour.Naturalfibers that are low cost,lightweight and environmental friendly provide an excellent alternative to glassfiber. Joshi et al.2reviewed the life cycle assessment of natural fiber and glassfiber composite and found that natural fibers are environmentally superior to glassfiber,and also reduces the polymer content as reinforcement. Schmidt and Beyer,Wotzel et al.,and Corbiere et al.carried out some important works using the natural fibers as reinforcement in polymer matrix for use in automobile parts.Schmit and Beyer3have replaced the glassfiber polypropylene(PP)with hemp-PP com-posite for auto-insulation application.Wotzel et al.4 have used hemp-epoxy to replace glassfiber acryloni-trile butadien–styrene(ABS)for usage in auto-side panel.Similarly,Corbiere et al.5replaced glassfiber PP with Curaua PP for transporting pallet.All these studies revealed that the naturalfiber based polymer composite has successfully replaced the glassfiber. Pothan et al.6studied the effect offiber length and con-tent on the mechanical properties of the short banana/ polyester composite.Study shows that30–40mmfiber length and40%fiber loading provides better mechan-ical properties.Idicula et al.7investigated the mechan-ical performance of banana/sisal hybrid composite and Department of Mechanical Engineering,Anna University,Chennai,India.Corresponding author:N.Venkateshwaran,Department of Mechanical Engineering,Anna University,Chennai,IndiaEmail:venkatcad@Journal of Reinforced Plasticsand Composites30(19)1621–1627!The Author(s)2011Reprints and permissions:/journalsPermissions.navDOI:10.1177/0731684411426810the positive hybrid effect for tensile strength was found to be in the ratio of4:1(banana:sisal). Further,the tensile strength of the composite is better when bananafiber is used as skin and sisal as core material.Visco-elastic property of the banana/ sisal(1:1ratio)hybrid composite was studied by Idicula et al.8The study shows that sisal/polyester composite has maximum damping behavior and high-est impact strength as compared to banana/polyester and hybrid composite.Sapuan et al.9prepared the composite by reinforcing woven bananafibers with epoxy matrix.Tensile test result showed that the woven kind of reinforcement has better strength and the same was confirmed using Anova technique also. Venkateshwaran and ElayaPerumal10reviewed the various work in thefield of bananafiber reinforced with polymer matrix composite with reference to phys-ical properties,structure,and application. Venkateshwaran et al.11studied the effect of hybridi-zation on mechanical and water absorption properties. Investigation revealed that the addition of sisal in bananafiber composite upto50%increases the mechanical properties.Sapuan et al.12designed and fabricated the household telephone stand using woven banana fabric and epoxy as resin.Zainudin et al.13studied the thermal stability of banana pseudo-stem(BPS)filled unplastisized polyvinyl chlo-ride(UPVC)composites using thermo-gravimetric analysis.The study revealed that the incorporation of bananafiller decreases the thermal stability of the composite.Zainudin et al.14investigated the effect of bananafiller content in the UPVC matrix.The inser-tion offiller increases the modulus of the composite and not the tensile andflexural strength.Zainudin et al.15studied the effect of temperature on storage modulus and damping behavior of bananafiber rein-forced with UPVC.Uma Devi et al.16studied the mechanical properties of pineapple leaffiber rein-forced with polyester composite.Study found that optimum mechanical properties are achieved at 30mmfiber length and30%fiber content.Dabade et al.17investigated the effect offiber length and weight ratio on tensile properties of sun hemp and palmyra/polyester composite.The optimumfiber length and weight ratio were30mm and around 55%,respectively.From the above literatures,it is evident that the fiber length and content are the important factors that affect properties of the composite.Hence in this work,the effect offiber length and weight percentage on the mechanical and water absorption properties of the bananafiber epoxy composite is investigated. Further,the fractured surface of the composite are subjected to fractography study to evaluate the frac-ture mechanism.ExperimentalFabrication of compositeA molding box made of well-seasoned teak wood of dimensions300Â300Â3mm3is used to make a com-posite specimen.The top,bottom surfaces of the mold and the walls are coated with remover and kept for drying.Fibers of different length(5,10,15,and 20mm)and weight percentage(8,12,16,and20)are used along with Epoxy(LY556)and Hardener (HY951)for the preparation of composite.Testing standardsThe tensile strength of the composite was determined using Tinnus Olsen Universal Testing Machine (UTM)as per ASTM D638standard.The test speed was maintained at5mm/min.In this case,five specimens were tested with variedfiber length andfiber weight ratio.The average value of tensile load at breaking point was calculated.Theflexural strength was determined using the above-mentioned UTM as per ASTM D790procedure.The test speed was maintained between1.3and1.5mm/min. In this case,five samples were tested and the average flexural strength was reported.The impact strength of the composite specimen was determined using an Izod impact tester according to ASTM D256 Standards.In this case,five specimens were tested to obtain the average value.Figures1to5show the effect offiber length and weight content on ten-sile,flexural,and impact properties.Water absorp-tion behavior of banana/epoxy composites in water at room temperature was studied as per ASTM D570to study the kinetics of water absorption. The samples were taken out periodically andFigure1.Effect of fiber length and weight percentage on tensile strength.1622Journal of Reinforced Plastics and Composites30(19)weighed immediately,after wiping out the water from the surface of the sample and using a precise 4-digit balance to find out the content of water absorbed.All the samples were dried in an oven until constant weight was reached before immersing again in the water.The percentage of moisture absorption was plotted against time (hours)and are shown in Figures 6–13.Scanning electron microscopeThe fractured surfaces of the specimens were exam-ined directly by scanning electron microscope Hitachi-S3400N.The fractured portions of the sam-ples were cut and gold coated over the surface uni-formly for examination.The accelerating voltage used in this work was 10kV.Figures 14to 17show the fractured surface characteristics of the compositespecimen.Figure 6.Effect of moisture on fiber content;Fiber length –5mm.Figure 3.Effect of fiber length and weight percentage on flexural strength.Figure 2.Effect of fiber length and weight percentage on tensilemodulus.Figure 4.Effect of fiber length and weight percentage on flexuralmodulus.Figure 5.Effect of fiber length and weight percentage on impact strength.Venkateshwaran et al.1623Figure 12.Effect of moisture on fiber length;Fiber wt%–16.Figure 7.Effect of moisture on fiber content;Fiber length –10mm.Figure 11.Effect of moisture on fiber length;Fiber wt%–12.Figure 10.Effect of moisture on fiber length;Fiber wt%–8.Figure 8.Effect of moisture on fiber content;Fiber length –15mm.Figure 9.Effect of moisture on fiber content;Fiber length –20mm.1624Journal of Reinforced Plastics and Composites 30(19)Results and discussion Mechanical propertiesFor the tensile test,composite specimens are made of fibers of different length (5,10,15,and 20mm)and weight ratio (8,12,16,and 20)were used to calculate the tensile strength.Figures 1and 2show the effect of fiber length and weight ratios on tensile strength and modulus of the composite,respectively.Figure 1shows that the increase in fiber length and weight ratio increases the tensile strength and modulus upto 15mm fiber length and 12%weight ratio.Further increases cause the properties to decrease because of lower fiber–matrix adhesion and the quantity of fiber content being more than matrix.From Figures 1and 2,the maximum tensile strength and modulus oftheFigure 14.SEM micrograph of tensile fracturedspecimen.Figure 15.SEM micrograph of fractured specimen under flexuralload.Figure 16.SEM micrograph of fractured specimen under impactload.Figure 17.Micrograph of poorinterface.Figure 13.Effect of moisture on fiber length;Fiber wt%–20.Venkateshwaran et al.1625composite are16.39MPa and0.652GPa,respectively for thefiber length of5mm and12%weight ratio. Flexural strength and modulus for differentfiber lengths(5,10,15,and20mm)and weight ratios(8, 12,16,and20)are shown in Figures3and4,respec-tively.It was found that the maximumflexural strength and modulus are57.53MPa and8.92GPa,respectively for thefiber length of15mm andfiber weight of16%.The results of the pendulum impact test are shown in Figure 5.As thefiber weight and length increases impact strength also increases upto16%fiber weight ratio and then begin to decrease.The maximum impact strength of 2.25J/m was found for thefiber length 20mm and16%fiber weight.Although the variousfiber lengths and weight per-centage provides the maximum mechanical properties, from Figures10,12,and14it can be concluded that the optimumfiber length andfiber weight percentage is 15mm and16%respectively as the properties variation with15mm and16%are negligible when compared to the maximum mechanical properties provided by differ-entfiber lengths and weight percentage indicated as above.The mechanical properties provided above are better than coir18and palmyra.19Water absorption studyThe effects offiber length and content on the water absorption study are shown in Figures6–13.Figures 6to9show the effect offiber content on the water absorption property of the banana/epoxy composite. It shows that as thefiber content increases the moisture uptake of the composite also increases.This is due to the affinity of the bananafiber towards the moisture. The maximum moisture absorption for the composite is around5%for all length and weight percentage of composite.Figures10to13show the effect offiber length on the water uptake capability of composite.It indicates that the variation of length(5,10,15,and 20mm)does not have much impact as compared with thefiber content.The moisture absorption percentage of bananafiber/epoxy composite seems to be lesser than hempfiber20andflaxfiber21composite. Fractography studyMicrographs of fractured tensile,flexural,and impact specimens are shown in Figures14–17.Figure14shows the micrograph of fractured surface of specimen under tensile load.It clearly indicates that the failure is due to fiber pull out phenomenon.Figure15shows the frac-tured surface of the specimen under bending load. Micrograph also shows the bending offibers due to the application of load.Figure16shows the failure of the composite under impact load.Further,it also shows the striation occurring on the matrix surface and the presence of hole due tofiber pull out.Figure17shows the micrograph of20mmfiber length and20%fiber weight composite specimen.It clearly indicates that the clustering offibers result in poor interface with matrix,and in turn decreases the mechanical properties of the composite.ConclusionBased on thefindings of this investigation the following conclusions can be drawn:.The optimumfiber length and weight ratio are 15mm and16%,respectively for bananafiber/ epoxy composite..Moisture absorption percentage of banana/epoxy composite for all length and weight percentage is around5..Also,the moisture uptake capability of the compos-ite is greatly influenced byfiber content than length. .SEM image shows that increasing thefiber content above16%results in poor interface betweenfiber and matrix.References1.Houston N and Acosta F.Environmental effect of glassfiber reinforced polymers.In:Proceedings of2007Earth Quake Engineering Symposium for Young Researcher, Seattle,Washington,2007.2.Joshi SV,Drzal LT,Mohanty AK and Arora S.Are nat-ural fiber composites environmentally superior to glass fiber reinforced posite Part A2004;35: 371–376.3.Schmidt WP and Beyer HM.Life cycle study on a naturalfiber reinforced component.In:SAE Technical Paper 982195.SAE Total Life-Cycle Conference,1–3 December,1998,Graz,Austria.4.Wotzel K,Wirth R and Flake R.Life cycle studies onhemp fiber reinforced components and ABS for automo-tive parts.Die Angewandte Makromolekulare Chemie1999;272:121–127.5.Corbiere-Nicollier T,Laban BG and Lundquist.Lifecycleassessment of bio-fibers replacing glass fibers as reinforce-ment in plastics.Resour Conserv Recycl2001;33:267–287.6.Pothan LA,Thomas S and Neelakantan NR.Shortbanana fiber reinforced polyester composites:mechanical, failure and aging characteristics.J Reinf Plast Compos 1997;16:744–765.7.Idicula M,Neelakantan NR and Oommen Z.A study ofthe mechanical properties of randomly oriented short banana and sisal hybrid fibre reinforced polyester compos-ites.J Appl Polym Sci2005;96:1699–1709.1626Journal of Reinforced Plastics and Composites30(19)8.Idicula M,Malhotra SK,Joseph K and Thomas S.Dynamic mechanical analysis of randomly oriented short banana/sisal hybrid fibre reinforced polyester pos Sci Technol2005;65:1077–1085.9.Sapuan SM,Leenie A,Harimi M and Beng YK.Mechanical property analysis of woven banana/epoxy composite.Mater Design2006;27:689–693.10.Venkateshwaran N and ElayaPerumal A.Banana fiberreinforced polymer composite-a review.J Reinf Plast Compos2010;29:2387–2396.11.Venkateshwaran N,ElayaPerumal A,Alavudeen A andThiruchitrambalam M.Mechanical and water absorption behavior of banana/sisal reinforced hybrid composites.Mater Design2011;32:4017–4021.12.Sapuan SM and Maleque MA.Design and fabrication ofnatural woven fabric reinforced epoxy composite for household telephone stand.Mater Design2005;26: 65–71.13.Zainudin ES,Sapuan SM,Abdan K and MohamadMTM.Thermal degradation of banana pseudo-stem fibre reinforced unplastisized polyvinyl chloride compos-ites.Mater Design2009;30:557–562.14.Zainudin ES,Sapuan SM,Abdan K and MohamadMTM.The mechanical performance of banana pseudo-stem reinforced unplastisized polyvinyl chloride compos-ites.Polym Plast Technol Eng2009;48:97–101.15.Zainudin ES,Sapuan SM,Abdan K and MohamadMTM.Dynamic mechanical behaviour of bananapseudo-stem filled unplasticized polyvinyl chloride com-posites.Polym Polym Compos2009;17:55–62.16.Uma Devi L,Bhagawan SS and Sabu Thomas.Mechanical properties of pineapple leaf fiber-reinforced polyester composites.J Appl Polym Sci1997;64: 1739–1748.17.Dabade BM,Ramachandra Reddy G,Rajesham S andUdaya kiran C.Effect of fiber length and fiber weight ratio on tensile properties of sun hemp and palmyra fiber reinforced polyester composites.J Reinf Plast Compos 2006;25:1733–1738.18.Harish S,Peter Michael D,Bensely A,Mohan Lal D andRajadurai A.Mechanical property evaluation of natural fiber coir composite.Mater Characterisation2009;60: 44–49.19.Velmurugan R and Manikandan V.Mechanical proper-ties of palmyra/glass fiber hybrid posite Part-A2009;38:2216–2226.20.Dhakal HN,Zhang ZY and Richardson MOW.Effect ofwater absorption on the mechanical properties of hemp fibre reinforced unsaturated polyester composites.Compos Sci Technol2007;67:1674–1683.21.Alix S,Philippe E,Bessadok A,Lebrun V,Morvan V andMarais S.Effect of chemical treatments on water sorption and mechanical properties of flax fibres.Bioresour Technol2009;100:4742–4749.Venkateshwaran et al.1627。

毕业设计外文参考资料及译文

毕业设计外文参考资料及译文

Fundamental information, including the effects of porosity, water-to-cement ratio, cement paste characteristic, volume fraction of coarse aggregates, size of coarse aggregates on pervious concrete strength, had been studied [3, 9−12]. However, for the reason that the porosity played a key role in the functional and structural performances of pervious concretes [13 − 14], there was still a need to understand more about the mechanical responses of pervious concretes proportioned for desired levels of porosities. Although it was possible to have widely different pore structure features for a given porosity, or similar pore structure features for varied porosities in pervious concrete, it was imperative to focus on the mechanical responses of pervious concrete at different designed porosities. However, compared with the related research on conventional concrete, very limited study had been conducted on the fracture and fatigue behaviors of pervious concrete, which were especially important for pavement concrete subjected to heavy traffic and to severe seasonal temperature change. The presented work outlined the raw materials and mixing proportions to produce high-strength supplementary cementitious material (SCM) modified pervious concrete (SPC) and polymer-intensified pervious concrete (PPC) at different porosities within the range of 15%−25%. Then, the mechanical properties of pervious concrete, including the compressive and flexural strengths, fracture energy, as well as fatigue property, were investigated in details.

复合材料与工程专业专业英语

复合材料与工程专业专业英语

复合材料与工程专业专业英语复合材料原理中文英文复合材料composite material基体matrix增强体reinforcement纤维fiber颗粒particle晶须whisker纳米管nanotube石墨烯graphene复合效应composite effect复合理论composite theory增强机制reinforcement mechanism界面interface界面层interphase界面粘结强度interfacial bond strength界面物理化学interfacial physical chemistry聚合物基复合材料polymer matrix composite (PMC)金属基复合材料metal matrix composite (MMC)陶瓷基复合材料ceramic matrix composite (CMC)碳-碳复合材料carbon-carbon composite (C-C)遗态复合材料biomimetic composite分级结构复合材料hierarchical composite剪切增稠柔性复合材料shear thickening fluid composite (STFC)连续缠绕工艺filament winding process拉挤工艺pultrusion process注射成型工艺injection molding process压缩成型工艺compression molding process热压工艺hot pressing process热等静压工艺hot isostatic pressing process (HIP)化学气相沉积法chemical vapor deposition (CVD)物理气相沉积法physical vapor deposition (PVD)液相浸渗法liquid phase infiltration (LPI)气相浸渗法gas phase infiltration (GPI)反应浸渗法reaction infiltration (RI)自蔓延高温合成法self-propagating high-temperature synthesis (SHS)电泳沉积法electrophoretic deposition (EPD)溶胶-凝胶法sol-gel method复合材料工艺中文英文复合材料工艺学composite material processing science复合材料加工技术composite material processing technology复合材料成型方法composite material forming method复合材料固化方法composite material curing method复合材料后处理方法composite material post-processing method复合材料接头技术composite material joint technology复合材料修复技术composite material repair technology复合材料表面处理技术composite material surface treatment technology复合材料工艺参数composite material process parameters复合材料工艺性能composite material process performance复合材料工艺缺陷composite material process defects复合材料工艺模拟composite material process simulation复合材料工艺优化composite material process optimization手糊法hand lay-up method喷射成型法spray-up method真空吸附法vacuum bagging method自动糊层机法automatic tape laying method (ATL)自动纤维放置法automated fiber placement method (AFP)树脂传输成型法resin transfer molding method (RTM)树脂膜层叠加成型法resin film infusion method (RFI)真空辅助树脂传输成型法vacuum assisted resin transfer molding method (VARTM)真空辅助树脂注射成型法vacuum assisted resin injection molding method (VARI)树脂浸渍拉挤成型法resin impregnation pultrusion method树脂浸渍缠绕成型法resin impregnation winding method树脂浸渍编织成型法resin impregnation weaving method预浸料成型法prepreg molding method预浸料自动糊层机法prepreg automatic tape laying method预浸料自动纤维放置法prepreg automated fiber placement method预浸料真空吸附法prepreg vacuum bagging method预浸料热压成型法prepreg hot pressing method预浸料热等静压成型法prepreg hot isostatic pressing method预浸料自动模具线成型法prepreg automatic mold line method (AML)模塑复合材料成型法molded compound molding method压缩模塑复合材料成型法compression molded compound molding method注射模塑复合材料成型法injection molded compound molding method转移模塑复合材料成型法transfer molded compound molding method挤出模塑复合材料成型法extrusion molded compound molding method热解复合材料制备方法pyrolysis composite preparation method复合材料结构设计中文英文复合材料结构设计composite material structural design复合材料结构分析composite material structural analysis复合材料结构优化composite material structural optimization复合材料结构可靠性composite material structural reliability复合材料结构失效模式composite material structural failure mode复合材料结构失效准则composite material structural failure criterion复合材料结构强度composite material structural strength复合材料结构刚度composite material structural stiffness复合材料结构稳定性composite material structural stability复合材料结构疲劳性能composite material structural fatigue performance 复合材料结构断裂韧性composite material structural fracture toughness 复合材料结构损伤容限composite material structural damage tolerance复合材料层合板composite material laminate复合材料夹层板composite material sandwich panel复合材料桁架composite material truss复合材料梁composite material beam复合材料板壳composite material plate-shell复合材料管壳composite material tube-shell复合材料网格壳composite material grid-shell复合材料蜂窝板composite material honeycomb panel纤维方向角fiber orientation angle层厚比thickness ratio层间剪切模量interlaminar shear modulus层间剪切强度interlaminar shear strength层间正应力强度因子interlaminar normal stress intensity factor层间剪应力强度因子interlaminar shear stress intensity factor层间断裂韧度interlaminar fracture toughness层间脱层interlaminar delamination层间裂纹扩展速率interlaminar crack propagation rate层间裂纹扩展阻力曲线interlaminar crack resistance curve (R-curve)层内应力分布intralaminar stress distribution层内应变分布intralaminar strain distribution层内失效模式intralaminar failure mode层内失效准则intralaminar failure criterion复合材料力学中文英文复合材料力学composite material mechanics复合材料弹性理论composite material elasticity theory复合材料弹塑性理论composite material elasto-plasticity theory复合材料粘弹性理论composite material viscoelasticity theory复合材料热弹性理论composite material thermoelasticity theory复合材料非线性力学composite material nonlinear mechanics复合材料动力学composite material dynamics复合材料疲劳力学composite material fatigue mechanics复合材料断裂力学composite material fracture mechanics复合材料损伤力学composite material damage mechanics复合材料微观力学composite material micromechanics复合材料宏观力学composite material macromechanics复合材料多尺度力学composite material multiscale mechanics复合材料本构关系composite material constitutive relation复合材料本构方程composite material constitutive equation复合材料本构模型composite material constitutive model复合材料本构参数composite material constitutive parameter复合材料本构参数识别方法composite material constitutive parameter identification method纤维增强复合材料单元细胞模型fiber reinforced composite unit cell model纤维增强复合材料等效模量计算方法fiber reinforced composite equivalent modulus calculation method纤维增强复合材料等效泊松比计算方法fiber reinforced composite equivalent poisson ratio calculation method纤维增强复合材料等效热膨胀系数计算方法fiber reinforced composite equivalent thermal expansion coefficient calculation method纤维增强复合材料等效热导率计算方法fiber reinforced composite equivalent thermal conductivity calculation method 纤维增强复合材料等效电导率计算方法fiber reinforced composite equivalent electrical conductivity calculation method 纤维增强复合材料等效介电常数计算方法fiber reinforced composite equivalent dielectric constant calculation method 颗粒增强复合材料单元细胞模型particle reinforced composite unit cell model颗粒增强复合材料等效模量计算方法particle reinforced composite equivalent modulus calculation method颗粒增强复合材料等效泊松比计算方法particle reinforced composite equivalent poisson ratio calculation method颗粒增强复合材料等效热膨胀系数计算方法particle reinforced composite equivalent thermal expansion coefficient calculation method颗粒增强复合材料等效热导率计算方法particle reinforced composite equivalent thermal conductivity calculation method 颗粒增强复合材料等效电导率计算方法particle reinforced composite equivalent electrical conductivity calculation method 颗粒增强复合材料等效介电常数计算方法particle reinforced composite equivalent dielectric constant calculation method 晶须增强复合材料单元细胞模型whisker reinforced composite unit cell model晶须增强复合材料等效模量计算方法whisker reinforced composite equivalent modulus calculation method晶须增强复合材料等效泊松比计算方法whisker reinforced composite equivalent poisson ratio calculation method晶须增强复合材料等效热膨胀系数计算方法whisker reinforced composite equivalent thermal expansion coefficient calculation method晶须增强复合材料等效热导率计算方法whisker reinforced composite equivalent thermal conductivity calculation method 晶须增强复合材料等效电导率计算方法whisker reinforced composite equivalent electrical conductivity calculation method晶须增强复合材料等效介电常数计算方法whisker reinforced composite equivalent dielectric constant calculation method 纳米复合材料中文英文纳米复合材料nanocomposite material纳米粒子nanoparticle纳米纤维nanofiber纳米管nanotube纳米线nanowire纳米带nanoribbon纳米棒nanorod纳米片nanosheet纳米球nanosphere纳米星nanostar纳米花nanoflower纳米棘轮nanoratchet纳米泡沫nanofoam纳米多孔材料nanoporous material纳米气凝胶nanoaerogel纳米海绵nanosponge纳米网格nanogrid纳米蜂窝结构nanohoneycomb structure纳米层状结构nanolayered structure纳米纤维素复合材料nanocellulose composite material石墨烯复合材料graphene composite material二维纳米材料复合材料two-dimensional nanomaterial composite material量子点复合材料quantum dot composite material全息纳米复合材料holographic nanocomposite material超分子纳米复合材料supramolecular nanocomposite material生物医用复合材料中文英文生物医用复合材料biomedical composite material生物相容性biocompatibility生物降解性biodegradability生物吸收性bioabsorbability生物活性bioactivity生物力学性能biomechanical performance生物功能化biofunctionalization药物缓释drug delivery组织工程tissue engineering骨组织工程bone tissue engineering软骨组织工程cartilage tissue engineering皮肤组织工程skin tissue engineering神经组织工程nerve tissue engineering血管组织工程vascular tissue engineering心脏组织工程cardiac tissue engineering肝脏组织工程liver tissue engineering肾脏组织工程kidney tissue engineering胰腺组织工程pancreas tissue engineering肺组织工程lung tissue engineering骨水泥复合材料bone cement composite material骨替代材料复合材料bone substitute material composite material 骨修复板复合材料bone fixation plate composite material骨钉复合材料bone screw composite material骨髓钉复合材料bone nail composite material骨髓钉复合材料bone nail composite material人工关节复合材料artificial joint composite material人工韧带复合材料artificial ligament composite material人工心脏瓣膜复合材料artificial heart valve composite material人工血管复合材料artificial blood vessel composite material 人工角膜复合材料artificial cornea composite material人工耳蜗复合材料artificial cochlea composite material人工牙齿复合材料artificial tooth composite material人工皮肤复合材料artificial skin composite material人工肝脏复合材料artificial liver composite material复合材料测试与评价中文英文复合材料测试与评价composite material testing and evaluation复合材料测试方法composite material testing method复合材料测试标准composite material testing standard复合材料测试仪器composite material testing instrument复合材料测试数据composite material testing data复合材料测试结果composite material testing result复合材料测试分析composite material testing analysis复合材料评价方法composite material evaluation method复合材料评价指标composite material evaluation index复合材料评价模型composite material evaluation model复合材料评价系统composite material evaluation system复合材料评价报告composite material evaluation report静态力学性能测试static mechanical performance test动态力学性能测试dynamic mechanical performance test疲劳性能测试fatigue performance test断裂性能测试fracture performance test热性能测试thermal performance test电性能测试electrical performance test光学性能测试optical performance test磁学性能测试magnetic performance test磁学性能测试magnetic performance test损伤性能测试damage performance test环境适应性能测试environmental adaptability performance test 耐腐蚀性能测试corrosion resistance performance test耐磨性能测试wear resistance performance test耐老化性能测试aging resistance performance test耐辐射性能测试radiation resistance performance test耐火性能测试fire resistance performance test耐水性能测试water resistance performance test耐化学品性能测试chemical resistance performance test。

复合材料与工程专业设计外文文献翻译本科本科毕业论文

复合材料与工程专业设计外文文献翻译本科本科毕业论文

毕业设计外文资料翻译题目POLISHING OF CERAMIC TILES抛光瓷砖学院材料科学与工程专业复合材料与工程班级复材0802学生学号20080103114指导教师二〇一二年三月二十八日MATERIALS AND MANUFACTURING PROCESSES, 17(3), 401–413 (2002) POLISHING OF CERAMIC TILESC. Y. Wang,* X. Wei, and H. YuanInstitute of Manufacturing Technology, Guangdong University ofTechnology,Guangzhou 510090, P.R. ChinaABSTRACTGrinding and polishing are important steps in the production of decorative vitreous ceramic tiles. Different combinations of finishing wheels and polishing wheels are tested to optimize their selection. The results show that the surface glossiness depends not only on the surface quality before machining, but also on the characteristics of the ceramic tiles as well as the performance of grinding and polishing wheels. The performance of the polishing wheel is the key for a good final surface quality. The surface glossiness after finishing must be above 208 in order to get higher polishing quality because finishing will limit the maximum surface glossiness by polishing. The optimized combination of grinding and polishing wheels for all the steps will achieve shorter machining times and better surface quality. No obvious relationships are found between the hardness of ceramic tiles and surface quality or the wear of grinding wheels; therefore, the hardness of the ceramic tile cannot be used for evaluating its machinability.Key Words: Ceramic tiles; Grinding wheel; Polishing wheelINTRODUCTIONCeramic tiles are the common decoration material for floors and walls of hotel, office, and family buildings. Nowadays, polished vitreous ceramic tiles are more popular as decoration material than general vitreous ceramic tiles as they can *Corresponding author. E-mail: cywang@401Copyright q 2002 by Marcel Dekker, Inc. have a beautiful gloss on different colors. Grinding and polishing of ceramic tiles play an important role in the surface quality, cost, and productivity of ceramic tiles manufactured for decoration. The grinding and polishing of ceramic tiles are carried out in one pass through polishing production line with many different grinding wheels or by multi passes on a polishing machine, where different grinding wheels are used.Most factories utilize the grinding methods similar to those used for stone machining although the machining of stone is different from that of ceramic tiles. Vitreous ceramic tiles are thin, usually 5–8mm in thickness, and are a sintered material,which possess high hardness, wear resistance, and brittleness. In general, the sintering process causes surface deformation in the tiles. In themachining process, the ceramic tiles are unfixed and put on tables. These characteristics will cause easy breakage and lower surface quality if grinding wheel or grinding parameters are unsuitable. To meet the needs of ceramic tiles machining, the machinery, grinding parameters (pressure, feed speed, etc.), and grinding wheels (type and mesh size of abrasive, bond, structure of grinding wheel, etc.) must be optimized. Previous works have been reported in the field of grinding ceramic and stone[1 –4]. Only a few reports have mentioned ceramic tile machining[5 –8], where the grinding mechanism of ceramic tiles by scratching and grinding was studied. It was pointed out that the grinding mechanism of ceramic tiles is similar to that of other brittle materials. For vitreous ceramic tiles, removing the plastic deformation grooves, craters (pores), and cracks are of major concern, which depends on the micro-structure of the ceramic tile, the choice of grinding wheel and processing parameters, etc. The residual cracks generated during sintering and rough grinding processes, as well as thermal impact cracks caused by the transformation of quartz crystalline phases are the main reasons of tile breakage during processing. Surface roughness Ra and glossiness are different measurements of the surface quality. It is suggested that the surface roughness can be used to control the surface quality of rough grinding and semi-finish grinding processes, and the surface glossiness to assess the quality of finishing and polishing processes. The characteristics of thegrinding wheels, abrasive mesh size for the different machining steps, machining time, pressure, feed, and removing traces of grinding wheels will affect the processing of ceramic tiles[9].In this paper, based on the study of grinding mechanisms of ceramic tiles, the manufacturing of grinding wheels is discussed. The actions and optimization of grinding and polishing wheels for each step are studied in particular for manualpolishing machines.GRINDING AND POLISHING WHEELS FOR CERAMIC TILEMACHININGT he mac hi ni ng of cer ami c t i l e s i s a vol ume-pr oduc t i on pr oc e s s t ha t uses significant numbers of grinding wheels. The grinding and polishing wheels forceramic tile machining are different from those for metals or structural ceramics. In this part, some results about grinding and polishing wheels are introduced for better understanding of the processing of ceramic tiles.Grinding and Polishing WheelsCeramic tiles machining in a manual-polishing machine can be divided into four steps—each using different grinding wheels. Grinding wheels are marked as 2#, 3#, and 4# grinding wheels, and 0# polishing wheel; in practice, 2# and 3# grinding wheels are used for flattening uneven surfaces. Basic requirements of rough grinding wheels are long life, high removal rate, and lower price. For 2# and 3# gr inding wheel s, Si C a brasi ve s wi th me s h #180 (#320)a r e bonde d by m a g n e s i u m o x yc h l o r i d e c e m e n t(M O C)t o g e t h e r w i t h s o m e p o r o u s f i l l s, waterproof additive, etc. The MOC is used as a bond because of its low price, simple manufacturing process, and proper performance.T he 4# grinding wheel will refine the surface to show the brightness of ceramic tile. The GC#600 abrasives and some special polishingmaterials, etc., are bonded by MOC. In order to increase the performance such as elasticity, etc., of the grinding wheel, the bakelite is always added. The 4# grinding wheels must be able to rapidly eliminate all cutting grooves and increase the surface glossiness of the ceramic tiles. The 0# polishing wheel is used for obtaining final surface glossiness, whichis made of fine Al2O3 abrasives and fill. It is bonded by unsaturated resin. The polishing wheels must be able to increase surface glossiness quickly and make the glossy ceramic tile surface permanent.Manufacturing of Magnesium Oxychloride Cement Grinding WheelsAfter the abrasives, the fills and the bond MOC are mixed and poured into the models for grinding wheels, where the chemical reaction of MOC will solidify the shape of the grinding wheels. The reaction will stop after 30 days but the hardness of grinding wheel is essentially constant after 15 days. During the initial 15-day period, the grinding wheels must be maintained at a suitable humidity and temperature.For MOC grinding wheels, the structure of grinding wheel, the quality of abrasives, and the composition of fill will affe ct their grinding ability. All the factors related to the chemical reaction of MOC, such as the mole ratio of MgO/MgCl2, the specific gravity of MgCl2, the temperature and humidity to care the cement will also affect the performance of the MOC grinding wheels.Mole Ratio of MgO/MgCl2When MOC is used as the bond for the grinding wheels, hydration reaction takes place between active MgO and MgCl2, which generates a hard XMg e OH T2·Y e MgCl2T·ZH2O phase. Through proper control of the mole ratio of MgO/MgCl2, a reaction product with stable performance is formed. The bond is composed of 5Mg e OH T2·e MgCl2T·8H2O and 3Mg e OH T2·e MgCl2T·8H2O: As the former is more stable, optimization of the mole ratio of MgO/MgCl2 to produce more 5Mg e OH T2·e MgCl2T·8H2O is required. In general, the ideal range for the mole ratio of MgO/MgCl2 is 4–6. When the contents of the active MgO and MgCl2 are known, the quantified MgO and MgCl2 can be calculated.Active MgOThe content of active MgO must be controlled carefully so that hydration reaction can be successfully completed with more 5Mg e OH T2·e MgCl2T·8H2O: If the content of active MgO is too high, the hydration reaction time will be too short with a large reaction heat, which increases too quickly. The concentrations of the thermal stress can cause generation of cracks in the grinding wheel. On thecontrary, if the content of active MgO is too low, the reaction does not go to completion and the strength of the grinding wheel is decreased.Fills and AdditivesThe fills and additives play an important role in grinding wheels. Some porous fills must be added to 2# and 3# grinding wheels in order to improve the capacity to contain the grinding chips, and hold sufficient cutting grit. Waterproof additives such as sulfates can ensure the strength of grinding wheels in processing under water condition. Some fills are very effective in increasing the surface quality of ceramic tile, but the principle is not clear.Manufacturing of Polishing WheelsFine Al2O3 and some soft polishing materials, such as Fe2O3, Cr2O3, etc., are mixed together with fills. Unsaturated resin is used to bond these powders, where a chemical reaction takes place between the resin and the hardener by means of an activator. The performance of polishing wheels depends on the properties of resin and the composition of the polishing wheel. In order to contain the fine chips, which are generated by micro-cutting, some cheap soluble salt can be fed into the coolant. On the surface of the polishing wheel, the salt will leave uniform pores, which not only increase the capacity to contain chips and self-sharpening of the polishing wheel, but also improves the contact situation between polishing wheel and ceramic tiles.Experimental ProcedureTests were carried out in a special manual grinding machine for ceramictiles. Two grinding wheels were fixed in the grinding disc that was equipped to the grinding machine. The diameter of grinding disc was 255 mm. The rotating speed of the grinding disc was 580 rpm. The grinding and polishing wheels are isosceles trapezoid with surface area 31.5 cm2 (the upper edge: 2 cm, base edge: 5 cm, height: 9 cm). The pressure was adjusted by means of the load on the handle for different grinding procedures. A zigzag path was used as the moving trace for the grinding disc. To maintain flatness and edge of the ceramic tiles, at least one third of the tile must be under the grinding disc. During the grinding process, sufficient water was poured to both cool and wash the grinding wheels and the tiles. Four kinds of vitreous ceramic tiles were examined, as shown in Table 1.Two different sizes of ceramic A, A400 (size: 400 £400 £5mm3T and A500(size: 500 £500 £5mm3T were tested to understand the effect of the tile size. Forceramic tile B or C, the size was 500 £500 £5mm3: The phase composition of thetiles was determined by x-ray diffraction technique. Surface reflection glossiness and surface roughness of the ceramic tiles and the wear of grinding wheels were measured.The grinding and polishing wheels were made in-house. The 2# grindingwheels with abrasives of mesh #150 and 3# grinding wheels with mesh #320 were used during rough grinding. Using the ceramic tiles with different surface toughness ground by the 2# grinding wheel for 180 sec, the action of the 3# grinding wheels were tested. The ceramic tile was marked as A500-1 (or B500-1, C500-1, A400-1) with higher initial surface toughness or A500-2 (or B500-2, C500-2, A400-2) with lower initial surface toughness.Two kinds of finishing wheels, 4#A and 4#B were made with the same structure, abrasivity, and process, but different composition of fills and additives. Only in 4#B, a few Al2O3, barium sulfate, and magnesium stearate were added for higher surface glossiness. The composition of the polishing wheels 0#A and 0#B were different as well. In 0#B, a few white alundum (average diameter 1mm), barium sulfate, and chrome oxide were used as polishing additives, specially. After ground by 4#A (or 4#B) grinding wheel, the ceramic tiles were polished with 0#A (or 0#B). The processing combinations with 4# grinding wheels and 0#RESULTS AND DISCUSSIONSEffects of 2# and 3# Grinding WheelsSurface QualityIn rough grinding with a 2# grinding wheel, the surface roughness for all the tiles asymptotically decreases as the grinding time increases, see Fig. 1. The initial asymptote point of this curve represents the optimized rough grinding time, as continued grinding essentially has no effect on the surface roughness. In these tests, the surface roughness curves decrease with grindingtime and become smooth at ,120 sec. The final surface quality for different kinds of ceramic tiles is slightly different. In terms of the initial size of the tile, the surface roughness of ceramic tile A400 e £400 £5mm3T is lower than that of A500 e500 £500 £5mm3T: The surface roughness ofc e r a m i c t i l e B500r a p id l y d r o p s a s t he g r i n d i n g t i m e i n c r e a s e s.Thus, it is easier to remove surface material from the hardest of thethree kinds of the ceramic tiles (Table 1). However, as the final surface roughness of ceramic tile A500 is the same as that of ceramic tile C500, the hardness of theceramic tile does not have a direct relationship with the final surface quality.In the 3# grinding wheel step, all craters and cracks on the surface of ceramic tiles caused by the 2# grinding wheel must be removed. If residual cracks and craters exist, it will be impossible to get a high surface quality in the next step. The surface roughness obtained by the 2# grinding wheel willalso affect the surfaceFigure 1. Surface roughness of several ceramic tiles as a function of grinding time for 2# grindingwheel.quality of next grinding step by the 3# grinding wheel. In Fig. 2, the actions of the 3# grinding wheels are given using the ceramic tiles with different initial R a, which were ground by the 2# grinding wheel for 180 sec. The curves of surface vs. grinding time rapidly decrease in 60 sec. Asymptotic behavior essentially becomes constant after 60 sec. In general, the larger the initial surface roughness, the worse the final surface roughness. For example, for ceramic tile B500-1, the initial R a was 1.53mm, the finial R a was 0.59mm after being ground by the 3# grinding wheel. When the initial R a was 2.06mm for ceramic tile B500-2, the finial R a was 0.67mm. In Ref. [8], we studied the relations between abrasive mesh size and evaluation indices of surface quality, such as surface roughness and surface glossiness. In rough grinding, the ground surface of ceramic tile shows fracture craters. These craters scatter the light, so that the surface glossiness values are almost constant at a low level. It is difficult to improve the surface glossiness after these steps. Figure 3 shows the slow increase in surface glossiness with time by means of the 3# grinding wheel. It can be seen that the glossiness of ceramic tile B500-1 is the highest. The surface glossiness of ceramic tile A400-1 is better than that of A500-1 because the effective grinding times per unit area for former is longer than for latter. These trends are similar to those for surface r o u g h n e s s i nFig. 2.Wear of Grinding WheelsThe wear of grinding wheels is one of the factors controlling the machining cost. As shown in Fig.4, the wear of grinding wheels is proportional to grindingFigure 2. Surface roughness of several ceramic tiles as a function of grinding time for 3# grindingwheel.Figure 3. Surface glossiness of several ceramic tiles as a function of grinding time by 3# grindingwheel.time for both the grinding wheels and the three types of ceramic tiles. The wear rate of the 3# grinding wheel is larger than the 2# grinding wheel. It implies that the wear resistance of the 3# grinding wheel is not as good as 2# for constant grinding time of 180 sec. When the slope of thecurve is smaller, life of thegrinding wheels will be longer. Comparison of the ceramic tiles hardness (Table 1) with the wear resistance behavior in Fig. 4 does not reveal a strong dependency. Therefore, the hardness of the ceramic tile cannot be used to distinguish the machinability. The difference ofFigure 4. Wear of grinding wheels of several ceramic tiles as a function of grinding time for 2# and3# grinding wheels.initial surface roughness of ceramic tile will affect the wear of grinding wheel. In Fig. 4, the wear of the 3# grinding wheel for ceramic tile B500-1 is smaller than that for ceramic tile B500-2. The initial surface roughness of the latter is higher than that of the former so that additional grinding time is required to remove the deeper residual craters on the surface. Improvement of the initial surface roughness can be the principal method for obtaining better grinding quality and grinding wheel life during rough grinding.Effects of 4# Grinding Wheels and 0# Polishing WheelsSurface QualityThe combination and the performance of 4# grinding and 0# polishingwheels show different results for each ceramic tile. The grinding quality vs. grinding (polishing) time curves are presented in Fig. 5, where all the ceramic tiles were previously ground by 2# and 3# grinding wheels to the same surface quality.The surface glossiness is used to assess surface quality because the surface roughness is nearly constant as finishing or polishing time increases[8]. In this test, the ceramic tile A400 were fast ground by 4#A and 4#B grinding wheels [Fig. 5(a)]. The surface glossiness increased rapidly during the initial 90 sec and then slowly increased. The surface glossiness by grinding wheel 4#B is higher than by 4#A. Afterwards, polishing was done by four different combinations of finishing wheel and polishing wheel. By means of polishing wheels 0#A and 0#B, we processed the surface finished by 4#A grinding wheel (described as 4#A–0#A and 4#A–0#B in Fig. 5), and the surfacef i n i s h e d b y4#Bg r i n d i n g wh e e l (described as 4#B–0#A and 4#B–0#B in Fig. 5). The curves of surface glossiness vs. polishing timeshow parabolic behavior. After 60 sec of polishing, the surface glossiness reaches to ,508, then slowly increases. The polishing wheel 0#B gives a better surface quality than 0#A.In Fig. 5(a), the maximum surface glossiness of ceramic tile A400 is about ,75 by 4#B–0#B.The relation between initial surface glossiness and the final surface quality is not strong. The effect of pre-polishing surface glossiness can be observed by 0#B polishing wheel as polishing ceramictile A500 [Fig. 5(b)]. The maximum surface glossiness that can be achieved is 748 in 240 sec by4#A–0#B or 4#B–0#B. This value is lower than that of ceramic tile A400 [Fig. 5(a)].The final surface glossiness by 4#A grinding wheel is highly different from that by 4#B grinding wheel for ceramic tile B500, as shown in Fig. 5(c), but the final polishing roughness is the same when 0#A polishing wheel is used. The better performance of 0#B polishing wheel is shown because the surface glossiness canincrease from 17 to 228 in 30 sec. The maximum surface glossiness is 658 by 4#B–0#B. Thecurves of polishing time vs. surface glossiness in Fig. 5(d) present the same results as polishing of ceramic tile B500 [Fig. 5(c)]. With 0#A polishingFigure 5. Surface glossiness for ceramic tiles (a) A400, (b) A500, (c) B500, and (d) C500 as afunction of grinding (polishing) time for 4# grinding wheels and 0# polishing wheels.wheel, the action of pre-polishing surface glossiness is significant. The best value of surface glossiness in 240 sec is 708 by 4#B–0#B as polishing ceramic tile C500. The results discussed earlier describe that the surface glossiness by 0# polishing wheel will depend not only on the pre-polishing surface glossiness formed by 4# grinding wheel, but also on the characteristics of the ceramic tiles and the performance of 0# polishing wheel. The differences of initial surface glossiness and final surface glossiness are larger for 4#A and 4#B. If the prepolishing surfaceroughness is lower, the final surface glossiness will be higher.Figure 5. Continued.The polishing time taken to achieve the maximum surface glossiness will be also shorter. The initial surface quality will limit the maximum value of polishing surface glossiness that can be obtained. To reach a final surface glossiness of above 608, the minimum pre-polishing surface glossiness must be above 208.The performance of the polishing wheel is the key to good surface quality. The polishing ability of the polishing wheels depends on the properties of the ceramic tiles as well. Even if the same grinding and polishing wheels are used, on all four ceramic tiles, the maximum surface glossiness values of ceramic tiles are different. The ceramic tile A500 shows the best surface glossiness, and ceramictile B500 shows the worst, although it is easier to roughly grind ceramic tile B500. The peak valueof the surface glossiness is also limited by the properties ofWear of Grinding and Polishing WheelsThe life of 4# grinding wheels and 0# polishing wheels (Fig. 6) are longer than those of the rough grinding wheels (Fig. 4). For finer grinding (Fig. 6), it is impossible to distinguish the relation between grinding wheels and ceramic tiles. Polishing wheels have longer life because they produce more plastic deformation than removal.SUMMARY OF RESULTS(1) The performance of grinding and polishing wheels will affect its life and the surface quality of ceramic tiles.(2) In ceramic tile machining, the surface quality gained in the previous step will limit the final surface quality in the next step. The surface glossiness of pre-polishing must be higher than 208 inorder to get the highest polishing quality. The optimization of the combination of grinding wheels and polishing wheels for all the steps will shorten machining time and improve surface quality. Optimization must be determined for each ceramics tiles.Figure 6. Wear of grinding wheels 4# and polishing wheels 0# for several ceramic tiles as afunction of grinding time.(3) The effect of hardness of ceramic tiles is not direct, thus the hardness of ceramic tiles cannot be used for evaluating the machinability ofACKNOWLEDGMENTThe authors thank Nature Science Foundation of Guangdong Province and Science Foundation of Guangdong High Education for their financial support.REFERENCES1. Wang, C.Y.; Liu, P.D.; Chen, P.Y. Grinding Mechanism of Marble. AbrasivesGrinding 1987, 2 (38), 6–10, (in Chinese).2. Inasaki, I. Grinding of Hard and Brittle Materials. Annals of the CIRP 1987, 36 (2),463–471.3. Zhang, B.; Howes, D. Material Removal Mechanisms in Grinding Ceramics. Annalsof the CIRP 1994, 45 (1), 263–266.4. Malkin, S.; Hwang, T.W. Grinding Mechanism for Ceramics. Annals of the CIRP1996, 46 (2), 569–580.5. Black, I. Laser Cutting Decorative Glass, Ceramic Tile. Am. Ceram. Soc. Bull. 1998,77 (9), 53–57.6. Black, I.; Livingstone, S.A.J.; Chua, K.L. A Laser Beam Machining (LBM) Database for the Cutting of Ceramic Tile. J. Mater. Process. Technol. 1998, 84 (1–3), 47–55.7. Jiang, D.F. Mirror Surface Polishing of Ceramic Tile. New Building Mater. 1994, 20(11), 27–30, (in Chinese).8. Ma, J.F. Analysis on Man-Made Floor Brick and Manufacture of Grinding SegmentUsed for Floor Brick. Diamond Abrasive Eng. 1996, 6 (95), 35–46, (in Chinese). 9. Wang, C.Y.; Wei, X.; Yuan, H. Grinding Mechanism of Vitreous Ceramic Tile. Chin.J. Mech. Eng. 1998, 9 (8), 9–11, 46 (in Chinese).材料与制造工艺17(3), 401–413 (2002)抛光瓷砖王CY,* 魏X, 袁H制造技术研究所,广东工业大学科技,广州510090,中国P.R.摘要研磨和抛光,是装饰玻璃陶瓷砖的生产中的重要步骤。

4性复合材料论文 中英文翻译

4性复合材料论文 中英文翻译

Availableonline atwww.sciencedirect.c omJournal of the EuropeanCeramic Society 28(2008) 803–810Recoverability of composite materialsChen,Kuan-ZongFung∗Center for Micro/N ano Science and T echnology, Department ofMaterials Science and Engine ering, National Cheng K ungUniversity, 1 Ta-Hsueh Road, Tainan 701, T aiwan, ROCReceived 25 November 2006; received in revised form 27July 2007; accepted 5 August 20071.I n t r o d u c t i o nDirect restorative composites experience considerable mechanical challenge during function, especially those indicated for posterior restorations. Thus, in order to withstand the mechanical stress generated by the biting forces, these composites contain a high percentage of inorganic reinforcing filler.A huge variation in the size, shape and constitution of filler particles can be observed in the different commercial resin composites, even for those of the same category or from the same manufacturer. Improvements in filler technology for composites increased the variety of options available and even classifications of such materials have been suggested based on the morphology of the filler particles.Studies have shown the influence of the size and shape of the filler particles on the mechanical properties of dental composites. These particle characteristicsdetermine what Braem et al. called “maximum particle packing fraction”, which is the ratio of true particle volume to the apparent volume occupied by the particles in the composite. According to the authors, important mechanical properties, such as Young's modulus, depend upon this ratio. Also, the presence of small spherical particles has been related to a high percentage of filler in the commercial composites, improving the mechanical properties.Nanotechnology has become a reality in different areas of engineering with the development, through physical and chemical methods, of materials and functional structures containing particles within a size interval of 0.1–100 nm. It is also one of the most noticeable advances in composite filler technology, involving the incorporation of silica fillers of nanometer size. Nanofillers are found in microfill and some hybrid composites that can be considered predecessors of the ne wer nanoparticulate composites. A study evaluating the mechanical properties of experimental composites with or without nanofillers was carried out by Musanje and Ferracane, who observed a positive effect of the presence of nanofiller particles, expressed by an improvement in flexural strength, surface hardness (H) and fracture toughness (K c).Nanoparticulate composites bring the perspective of creating another category of universal resin composite that joins the optical properties and the polishability required for anterior restorations with the mechanical properties demanded for posterior restorations. However, relatively little information about these new materials is available in the dental literature.Strength (σ) is an important property for a restorative material. It is dependent upon the material's microstructure, composition, testing method, environment and failure mechanisms. Strength values are valuable when representing information about the flaw population with potential to cause the failure of a restoration or prosthesis, and thus, must be interpreted within a context that involves the analysis of failure and structural reliability, rather than an isolated result. The presence of structural defects with potential to become critical defects, such as microcracks, grains or internal voids depend upon the volume of the material structure.Measurement of the strength of composites is often performed through flexural tests. The test indicated by the International Standards Organization to evaluate the strength of polymer-based restorative materials is the 3-point bending test (3PBT). This test employs bar-shaped specimens that bend under compressive loading equally distant from the lower supports, promoting tensile stresses in the lower surfaces that are more likely related to the fracture initiation (Fig. 1A). The test configuration tends to confine the area submitted to the stress between the supporting rollers and the loading rollers. The so-called 4-point bending test (4PBT) uses the same bar-shaped specimens, but a different configuration for load appliance based on two load cylinders over the upper surface of the specimens (Fig. 1B) that tend to expose a higher flaw containing area of the material to the stress when compared to the 3PBT. Therefore, it is expected that higher strengths are measured with the three-point bending test.Fig. 13-point (A) and 4-point (B) bending tests.Statistical parameters are commonly applied to data from mechanical strength tests to determine the level of structural reliability of the materials. The Weibull modulus (m), or shape parameter, describes the variation in the distribution of strength values from different materials and also establishes a direct relationship with the size and distribution of the defects present in a specific volume of material. In this sense, high Weibull modulus indicates a smaller error range, and potentially greater clinical reliability. In addition, the Weibull analysis can offer more clinically relevant parameters, such as the 5% failure probability (σ0.05).Data obtained from the flexural tests were submitted to Student's t-test for differences between composites in each flexural test and for the flexural test methods with the same composite (= 0.05). Weibull statistics were also carried out in ordersto obtain the shape (m) and scale (σ0) parameters of both composites.3. ResultsThere was no significant difference between the two composites evaluated, either for the 3PBT (p = 0.307) or the 4PBT (p = 0.275). However, a significantly higher flexural strength with the 3PBT was observed for both, the microhybrid (p = 0.004) and the nanofill composites (p = 0.005), in comparison with the 4PBT, confirming the hypothesis of the study4. DiscussionFiller morphology and size are always factors of concern when mechanical properties and fracture behavior of composite resins are evaluated, because they affect the filler volume fraction. In the present study, the flexural strength was not affected by the differences of three orders of magnitude in average filler size between the two composites (p = 0.307). This is in accordance with other studies that showed no significant difference in flexural strength bet ween Filtek Supreme™ (nanofill) and some microhybrid composites and. According to Mitra et al. a high filler loading was obtained in Filtek Supreme™ due to the wide particle distribution and the spherical shape of the filler particles, equaling physical and mechanical properties of microhybrid composites, including the flexural strength. The filler content of this composite is composed of 20 nm non-aggregated silica particles and nanoclusters of 75 nm agglomerated particles that are reported to reach a 0.6–1.4 μm size range that, in turn, corresponds to the average size of the filler particles of Filtek Z250™. In addition, both composites contain spherical-shaped particles that have been associated with reduced stress concentration as compared with the sharp edges present in irregular-shaped filler particles. These factors in association with the similar filler packing between the composites might have produced their similar mechanical behavior.The Weibull statistics is considered to be an acceptable approach in engineering to evaluate the reliability of a material or component. It provides a way of accessing the dependability of the material, disclosing the probability of failure at any selected level of stress. As a measure of the variability of strength in a material and its dependence on crack size distribution, a higher m, even in association with slightly lower mean fracture strength, is often preferable to a lower m associated with a higher mean fracture strength. A high m could also be useful as an indicator of a more favorable test design to evaluate and compare the strength of materials.The overall Weibull modulus results confirmed the variability of strength of both composites with the different tests, expressed by means of the standard deviation a nd the coefficient of variability. A significantly higher m was shown for the microhybrid composite when tested by 3PBT. No significant difference, however, was found between the tests for the nanofill composite. Similar results were found by Jin et al. when testing the flexural strength of ceramics. The authors concluded that it is difficult to determine, based on the Weibull modulus, the most suitable test design for different materials.Weibull statistics have been developed and used since the 1950s in the engineering community to determine equivalent strengths that have been measured by different test configurations. Weibull size scaling is routinely used to predict strength for a 3PBT when strength is measured by a 4PBT, or vice-versa. This is done by m eans of calculating “effective volumes” or “effective areas” that are under stress, and is fairly straightforward for the configurations of this study. Calculation of Weibull size scaling is done with the following formula: σ3/σ4 = (A4/A3)1/m, where σ3 and σ4 are the stresses measured under 3- and 4-point configurations, A3 and A4 are the effective areas of the associated configurations, and m is the Weibull modulus. The effective area for 3PBT is (S/4)[(m + 2)/(m + 1)2] and for 4PBT is (S/12)[(m + 2)(m + 3)/(m + 1)2], where S is the total specimen surface within the load span and is the same for both configurations, for the span lengths and specimen sizes are the same. Calculations predicted a 15% higher strength for the 3-pointconfiguration in comparison to the 4-point configuration for either material. This is slightly higher than the measured results (about 10%), but within experimental error.The fracture behavior of the composites was also expressed by σ0 and σ0.05. Both parameters indicated a lower stress for fracture of the composites when submitted to the 4PBT. This might be explained by the fact that a higher volume (53.4%) is exposed to the stress in the 4PBT comparing to the 3PBT (40%). The macroscopic observation of the composite specimens fractured by 4PBT disclosed fractures occurring in different places along the tensile surface over distances between the upper loading rollers, confirming also the wider volume of material involved in this test. In contrast and as expected, the specimens submitted to 3PBT fractured on the tensile surface midway between the two supports. According to Zeng et al. the 3PBT submits only a very small area to the maximum tensile stress, underestimating the flaws located far from the loading rollers and tending to induce a fracture initiation site. In this sense, although the 4PBT presented lower strength values for both composites, it may represent a more reliable approach as a measure of flexural strength of composites than the 3PBT. In addition, it may provide a more realistic and …safe‟ lower boundary for the resulting strength.The analysis of the fractured surface using fractographic principles is a well-established analytic tool to determine the failure behavior of brittle materials. It is based on the principle that the history of the fracture process is encoded on the fractured surface of the material. According to Le May and Begnall, “investigations of structural failure by brittle fracture should take into account, at least, two separate aspects: (1) the point from which the fracture developed is relevant in order to determine whether the fracture initiated from a manufacturing effect, whether it experienced a prior fatigue or stress corrosion that originated the crack that led to failure; (2) it should indicate that, for whatever the defect present, the load applied was enough for unstable fracture to occur”.Characteristically, brittle materials, such as composites, present a population of flaws of different sizes, geometries and orientations. Fracture occurs when the load exceeds a critical value for the propagation of the largest and most favorably orientedflaw. These flaws are induced by intrinsic imperfections in the structure of the material, by processing or by mechanical grinding and polishing, and might potentially reduce the strength of the material.The defects that led to the fracture initiation were identified as non-homogeneous distributions of organic and inorganic phases, inclusions, cracks and voids. Both, the manufacturing of the materials and the handling procedure might generate these defects. In the present study, defects similar presenting a smooth darker area of matrix, were strongly associated with the initiation of fracture.Surface flaws were identified as the fracture initiation site for 86.6–96.6% of the specimens, independent of the group. The low area exposed to the maximum tensile stress in the bending test makes fractures more likely to develop from the surface. In this sense, bending specimens are considerably sensitive to surface or edge damage during grinding or polishing. Internal critical defects were rare and always associated with moderate to high fracture strength. The internal irregular defects, are more stress inducing than internal spherical-shaped pores, requiring a lower load to propagate the fracture.The polymerization method employed, that was common to both tests, also might have affected the fracture behavior of the composites. According to Le May and Begnall, fracture initiation and propagation depend on the total local stress, which includes the externally applied load and the residual stress of the specimen. This is of major importance, because the production of 25 mm long bar-shaped specimens requires an overlapped light activation procedure when using an 11 mm diameter light guide, resulting in areas of the specimen that are exposed to twice the light and. Attempting to avoid the effect of the inhomogeneous polymerization of the specimens some authors have suggested the use of oven-LCUs.Natural and restored teeth are subjected to cyclic loading during normal masticatory function. Therefore, the wear process and failure due to fatigue stress are phenomena of relevance from the clinical standpoint and should instigate future work.5. ConclusionHigher flexural strength was produced by the 3-point bending test than by the 4-point bending test, independent of the composite evaluated. The flexural strength and the fracture behavior of both composites were similar, despite the difference of the average filler size of the composites tested, probably due to the microstructural arrangement of the nanofillers in clusters that approximate the average size of the filler of the microhybrid composite and due to the similar filler volume in both composites.AcknowledgmentThis work is financially supported by the Council of Agri- culture, Executive Y uan, Taiwan; Grant 96AS-10.1.1-AD-U1.References1. Etsell, T. H. and Flengas, S. N., Electrical properties of solid oxide elec- trolytes. Chem. Rev., 1970, 70, 339–376.2. Ishihara, T., Matsuda, H. and Takita, Y., Doped LaGaO3 perovskite type oxide as a new oxide ionic conductor. J. Am.Chem. Soc., 1994, 116,3801–3803.3. Huang, P. and Petric, A., Superior oxygen ion conductivity of lanthanu m gallate doped with strontium and magnesium. J.Electrochem. Soc., 1996,143, 1644–1648.4. Chen, T. Y. and Fu ng, K. Z., C omparison of dissolu tion behavior and ionic conduction between Sr and/or Mg dopedLaGaO3 and La Al O3. J. Power Sources, 2004, 132, 1–10.5. Stevenson, J. W., Armstrong, T. R., McC ready, D. E., Pederson, L. R. and W eber, W. J., Processing and electrical propertiesof alkaline earth-doped lanthanu m gallate. J. Electrochem. S oc., 1997, 144, 3613–3620.6. Huang, K., Tichy, R. S. and Goodenough, J. B., Superior perovskite oxide-ion conductor; strontium- andmagnesium-d oped La Ga O3. I: Phase relationships and electrical properties. J. Am. Chem. Soc., 1998, 81, 2565–2575.7. Huang, K., Feng, M. and Goodenough, J. B., W et chemical synthesis of Sr- and Mg-d oped La Ga O3, a perovskite-typeoxide-ion conductor. J. Am. Chem. Soc., 1996, 79, 1100–1104.8. Huang, K. and Goodenough, J. B., Wet chemical synthesis of Sr- and Mg- doped La Ga O3, a perovskit e-typ e oxide-ioncond ucto r. J. Solid S tate C hem.,1998, 136, 274–283.9. Simpson II, R. E., Habeger, C., R abinovich, A. and Adair, J. H., Enzyme- catalyzed inorganic precipitation of aluminumbasic sulfate. J. Am. Ceram. Soc., 1998, 81, 1377–1379.10. Tas, A. C., Majewski, P. J. and Aldinger, F., Chemical preparation of pure and strontium- and/or magnesiu m-dopedlanthanum gallate powder. J. Am. C eram. Soc., 2000, 83, 2954–2960.11. Cong, L., He, T., Ji, Y., Guan, P., Huang, Y. and Su, W., Syn- thesis andcharacterization of IT-electrolyte with perovskite structu re La0.8 Sr0.2Ga0.85Mg0.15O3−δ by glycine–nitrate combustion method. J.Alloys Compd., 2003, 348, 325–331.12. Djurado, E. and Labeau, M., Second phases in doped lanthanum gallate perovskites. J. Eur. Ceram. Soc., 1998, 18,1397–1404.13. Khanlou, A. A., Tietz, F. and Sto¨v er, D., Material properties ofLa0.8Sr0.2Ga0.9+x Mg x O3−δas a function of Ga content. Solid State Ionic,2000, 135, 543–547.14. Tas, A. C., Majewski, P. J. and Aldinger, F., Preparation of strontiu m- and zinc-do pe d LaGaO3 po wd ers via precipit ation inthe presen c e o f urea and/or enzyme urease. J. Am. Ceram. Soc., 2002, 85, 1414–1420.15. Shaw, W. H. R. and Bordeaux, J. J., The decomposition o f urea in aqueous media. J. Am. C hem. Soc., 1955, 77, 4729–4733.16. Blendell, J. E., B owen, H. K. and Coble, R. L., High purity alumina b y controlled precipitation from aluminum sulfatesolution. Am. Ceram. Soc. Bull., 1984, 63, 797–802.17. Sordelet, D. and Akinc, M., Preparation of spherical, monosized Y2O3precursor particles. J. Colloid Interface Sci., 1988, 122, 47–59.18. Chen,P.L.and Ch en,I.W., Re a ctive c e riu m(IV)oxide po wd ers by the homo- geneous precipitation method. J. Am. Ceram. Soc.,1993, 76, 1577–1583.19. Sordelet, D. J., Akinc, M., Panchula, M. L., Han, Y. and Han, M. H., Synthesis of yttrium alu minu m garnet precursorpowders by homogeneous precipitation. J. Eur. Ceram. Soc., 1994, 14, 123–127.20. Khanlou, A. A., Tietz, F. and Sto¨ver, D., Material properties ofLa0.8Sr0.2Ga0.9+x Mg x O3−δas a function of Ga content. Solid State Ionic,2000, 135, 543–547.21. Gregg, S. J. and Sing, K. S. W., Adsorption, Surface Area and P orosity.Academic Press, 1982, p. 35.22. Gorelov, V. P., B ronin, D. I., Sokolova, J. V., Nafe, H. and Aldinger, F., The effect of doping and processingconditions on properties of La1−x Sr x Ga1−y M g y O3−δ. J. Eur. C eram. Soc., 2001, 21, 2311–2317.。

毕业设计外文资料翻译——翻译译文

毕业设计外文资料翻译——翻译译文

毕业设计外文资料翻译(二)外文出处:Jules Houde 《Sustainable development slowed down by bad construction practices and natural and technological disasters》2、外文资料翻译译文混凝土结构的耐久性即使是工程师认为的最耐久和最合理的混凝土材料,在一定的条件下,混凝土也会由于开裂、钢筋锈蚀、化学侵蚀等一系列不利因素的影响而易受伤害。

近年来报道了各种关于混凝土结构耐久性不合格的例子。

尤其令人震惊的是混凝土的结构过早恶化的迹象越来越多。

每年为了维护混凝土的耐久性,其成本不断增加。

根据最近在国内和国际中的调查揭示,这些成本在八十年代间翻了一番,并将会在九十年代变成三倍。

越来越多的混凝土结构耐久性不合格的案例使从事混凝土行业的商家措手不及。

混凝土结构不仅代表了社会的巨大投资,也代表了如果耐久性问题不及时解决可能遇到的成本,更代表着,混凝土作为主要建筑材料,其耐久性问题可能导致的全球不公平竞争以及行业信誉等等问题。

因此,国际混凝土行业受到了强烈要求制定和实施合理的措施以解决当前耐久性问题的双重的挑战,即:找到有效措施来解决现有结构剩余寿命过早恶化的威胁。

纳入新的结构知识、经验和新的研究结果,以便监测结构耐久性,从而确保未来混凝土结构所需的服务性能。

所有参与规划、设计和施工过程的人,应该具有获得对可能恶化的过程和决定性影响参数的最低理解的可能性。

这种基本知识能力是要在正确的时间做出正确的决定,以确保混凝土结构耐久性要求的前提。

加固保护混凝土中的钢筋受到碱性的钝化层(pH值大于12.5)保护而阻止了锈蚀。

这种钝化层阻碍钢溶解。

因此,即使所有其它条件都满足(主要是氧气和水分),钢筋受到锈蚀也都是不可能的。

混凝土的碳化作用或是氯离子的活动可以降低局部面积或更大面积的pH值。

当加固层的pH值低于9或是氯化物含量超过一个临界值时,钝化层和防腐保护层就会失效,钢筋受腐蚀是可能的。

欧洲先进的土木工程复合材料外文资料翻译学士学位论文

欧洲先进的土木工程复合材料外文资料翻译学士学位论文

毕业设计外文资料翻译题目欧洲先进的土木工程复合材料学院土木建筑学院 _____________专业土木工程 ________________班级土木1110 _______________学生_______ x xx ________________学号20110622132 ____________________指导教师_______ xxx _________________二O—五年三月九日Structural Engineering In ternatio nal ,1999,9.pp.267-273.ISSN 1016-8664欧洲先进的土木工程复合材料Chris J. Burg oyne 博士剑桥大学,剑桥,英国摘要:复合材料在欧洲被认为用于结构许多年了。

用于结构的材料都具有低蠕变的特点,这些结构被期望能够承受显著永久荷载。

较高刚度的纤维,即碳、芳族聚酰胺、玻璃和聚酯等材料在大多数的应用中被使用。

不幸的是,高强度是以高成本为代价的,人们在试图寻找钢材的一对一替代品的过程中在材料成本的基础上犯了错误。

成功的应用都使用其他合适的材料,其中最重要的是重量轻和顺向易于处理。

预应力玻璃纤维棒1978 年,一个预应力系统(称为Polystal[2])用玻璃纤维并掺入树脂形成圆棒。

进行了大量的研究确定系统的性能,包括量化的应力破坏现象。

锚具是用树脂包裹成束并挤压入钢管中形成的。

这种钢管提供约束限制和可用于机械紧固。

许多桥都用这种刚结束建造:在杜塞尔多夫,一个简单的人行桥是两跨连续结构,内部筋。

二者被认为具有相当数量的未受力筋被设计为部分预应力。

这些例子紧随其后的是柏林的体外预应力筋还有德国和奥地利的一些地方。

尽管该系统技术成功还没有被认为是商业成功,但是这种钢筋已经停产。

预应力芳纶棒在20世纪80年代早期的研究开始于荷兰使用芳族聚酰胺纤维预应力挤压成型的形式,无论平条或圆棒全都命名为Arapree [3]。

复合材料与工程英语介绍范文

复合材料与工程英语介绍范文

复合材料与工程英语介绍范文英文回答:Composite Materials in Engineering: A Comprehensive Overview.Introduction.Composite materials, often referred to as advanced materials, are gaining significant prominence in various engineering applications due to their unique combination of properties. These materials comprise two or more distinct phases or constituents, typically a reinforcing phase and a matrix phase. The reinforcing phase provides strength and stiffness, while the matrix phase holds the reinforcement together and transfers loads.Types and Properties.Composite materials encompass a wide range ofcombinations, with the most common types being fiber-reinforced composites, laminated composites, and polymer-matrix composites (PMCs). Fiber-reinforced composites, such as carbon fiber reinforced polymers (CFRPs), offer exceptional strength-to-weight ratios, stiffness, and thermal stability. Laminated composites, like fiberglass composites, combine multiple layers of material with different orientations, providing tailored mechanical and thermal properties. PMCs, such as glass-reinforced plastics (GRPs), exhibit high strength and durability, along with ease of fabrication.Applications.The versatility of composite materials has led to their adoption in numerous engineering sectors. In the aerospace industry, composites are prized for their lightweight and high strength-to-weight ratios, enabling the construction of lighter and more fuel-efficient aircraft. In the automotive industry, composites find applications in body panels, chassis components, and interior trims, offering improved strength, weight reduction, and corrosionresistance. In the construction industry, composites are used for structural elements such as beams, columns, and panels, providing superior strength, durability, andweather resistance.Advantages.Composite materials offer several advantages over traditional materials. Their high strength-to-weight ratio makes them lightweight and strong, allowing for efficient load-bearing applications. They possess excellent corrosion resistance, reducing the need for protective coatings and enhancing durability in harsh environments. Additionally, composites exhibit tailored mechanical and thermal properties, allowing engineers to optimize them forspecific applications.Challenges.Despite their numerous advantages, composite materials also face some challenges. One challenge lies in their cost, as they are typically more expensive to produce thantraditional materials. Another challenge is the difficultyin fabrication, as the manufacturing processes for composites require specialized equipment and expertise. Furthermore, the repair of composite structures can be complex and costly, necessitating advanced techniques and skilled technicians.Future Outlook.Composite materials continue to attract significant research and development efforts, driven by the demand for advanced and lightweight materials with tailored properties. Advancements in manufacturing technologies, such asadditive manufacturing and automated layup, are expected to reduce production costs and streamline fabrication. Additionally, the development of novel composite materials, including bio-based and self-healing composites, holds promise for sustainable and innovative applications.中文回答:复合材料在工程中的应用,全面综述。

复合材料英文文献

复合材料英文文献

复合材料英文文献Composite materials are engineered to combine the best properties of different materials, creating a new material that is stronger, lighter, and more durable than its individual components.These innovative materials are widely used in various industries, from aerospace where they reduce weight and increase fuel efficiency, to construction where they enhance structural integrity and longevity.The versatility of composite materials lies in their ability to be tailored to specific applications. By varying the composition and arrangement of the constituent materials, engineers can optimize the material for strength, stiffness, or resistance to environmental factors.Recent advancements in nanotechnology have further expanded the capabilities of composites. The incorporation of nanomaterials into composite structures can significantly improve their mechanical and thermal properties.One of the key challenges in composite material research is the development of effective recycling strategies. As these materials become more prevalent, finding sustainable ways to reuse or recycle them will be crucial to minimize environmental impact.Educational institutions and industries alike are investing in research to explore new composite material applications. This includes everything from improving sports equipment to developing next-generation energy storage systems.In conclusion, composite materials represent asignificant leap forward in material science. Their unique properties and potential for customization make them indispensable in a wide range of applications, driving innovation and enhancing performance across multiple sectors.。

材料科学与工程专业英语第10章翻译

材料科学与工程专业英语第10章翻译

The word "ceramic" is derived from the Greek keramos, which means "potter's clay" or "pottery." Its origin is a Sanskrit term meaning "to burn." So the early Greeks used "keramous" when describing products obtained by heating clay-containing materials. The term has long included all products made from fired clay, for example, bricks, fireclay refractories, sanitaryware, and tableware.“陶瓷”这个词是来自希腊keramos,这意味着“陶土”或“陶”。

它的起源是梵文术语,意思是“燃烧”。

因此,早期的希腊人用“keramous”描述加热含粘土的物料获得的产品。

这个词早已包括所有陶土制成的产品,例如,砖,粘土质耐火材料,卫生洁具,餐具。

In 1822, refractory silica were first made. Although they contained no clay, the traditional ceramic process of shaping, drying, and firing was used to make them. So the term" ceramic," while retaining its original sense of a product made from clay, began to include other products made by the same manufacturing process. The field of ceramics (broader than the materials themselves) can be defined as the art and science of making and using solid articles that contain as their essential component a ceramic. This definition covers the purification of raw materials, the study and production of the chemical compounds concerned, their formation into components, and the study of structure, composition, and properties.1822年,耐火材料二氧化硅被首次提出。

复合材料注塑成型中英文对照外文翻译文献

复合材料注塑成型中英文对照外文翻译文献

复合材料注塑成型中英文对照外文翻译文献(文档含英文原文和中文翻译)An experimental study of the water-assisted injection molding ofglass fiber filled poly-butylene-terephthalate(PBT) compositesAbstract:The purpose of this report was to experimentally study the water-assisted injection molding process of poly-butylene-terephthalate(PBT) composites. Experiments were carried out on an 80-ton injection-molding machine equipped with a lab scale water injection system,which included a water pump, a pressure accumulator, a water injection pin, a water tank equipped with a temperature regulator,and a control circuit. The materials included virgin PBT and a 15% glass fiber filled PBT composite, and a plate cavity with a rib across center was used. Various processing variables were examined in terms of their influence on the length of water penetration in molded parts, and mechanical property tests were performed on these parts. X-ray diffraction (XRD) was also used to identify the material andstructural parameters. Finally, a comparison was made between water-assisted and gas-assisted injection molded parts. It was found that the melt fill pressure, melt temperature, and short shot size were the dominant parameters affecting water penetration behavior.Material at the mold-side exhibited a higher degree of crystallinity than that at the water-side. Parts molded by gas also showed a higher degree of crystallinity than those molded by water. Furthermore, the glass fibers near the surface of molded parts were found to be oriented mostly in the flow direction, but oriented substantially more perpendicular to the flow direction with increasing distance from the skin surface.Keywords: Water assisted injection molding; Glass fiber reinforced poly-butylene-terephthalate (PBT) composites; Processing parameters; B. Mechanical properties; Crystallinity; A. Polymer matrix composites;1. IntroductionWater-assisted injection molding technology [1] has proved itself a breakthrough in the manufacture of plastic parts due to its light weight, faster cycle time, and relatively lower resin cost per part. In the water-assisted injection molding process, the mold cavity is partially filled with the polymer melt followed by the injection of water into the core of the polymer melt. A schematic diagram of the water-assisted injection molding process is illustrated in Fig. 1.Water-assisted injection molding can produce parts incorporating both thick and thin sections with less shrink-age and warpage and with a better surface finish, but with a shorter cycle time. The water-assisted injection molding process can also enable greater freedom of design, material savings, weight reduction, and cost savings in terms of tooling and press capacity requirements [2–4]. Typical applications include rods and tubes, and large sheet-like structural parts with a built-in water channel network. On the other hand, despite the advantages associated with the process,the molding window and process control are more critical and difficult since additional processing parameters are involved. Water may also corrode the steel mold, and some materials including thermoplastic composites are difficult to mold successfully. The removal of water after molding is also a challenge for this novel technology. Table 1 lists the advantages and limitations of water-assisted injection molding technology.Fig. 1. Schematic diagram of water-assisted injection molding process.Water assisted injection molding has advantages over its better known competitor process, gas assisted injection molding [5], because it incorporates a shorter cycle time to successfully mold a part due to the higher cooling capacity of water during the molding process. The incompressibility,low cost, and ease of recycling the water makes it an ideal medium for the process. Since water does not dissolve and diffuse into the polymer melts during the molding process, the internal foaming phenomenon [6] that usually occurs in gas-assisted injection molded parts can be eliminated.In addition, water assisted injection molding provides a better capability of molding larger parts with a small residual wall thickness. Table 2 lists a comparison of water and gas assisted injection molding.With increasing demands for materials with improved performance, which may be characterized by the criteria of lower weight, higher strength, and a faster and cheaper production cycle time, the engineering of plastics is a process that cannot be ignored. These plastics include thermoplastic and thermoset polymers. In general, thermoplastic polymers have an advantage over thermoset polymers in popular materials in structural applications.Poly-butylene-terephthalate (PBT) is one of the most frequently used engineering thermoplastic materials, whichis formed by polymerizing 1.4 butylene glycol and DMT together. Fiber-reinforced composite materials have been adapted to improve the mechanical properties of neat plastic materials. Today, short glass fiber reinforced PBT is widely used in electronic, communication and automobile applications. Therefore, the investigation of the processing of fiber-reinforced PBT is becoming increasingly important[7–10].This report was made to experimentally study the waterassisted injection molding process of poly-butylene-terephthalate (PBT) materials. Experiments were carried out on an 80-ton injection-molding machine equipped with a lab scale water injection system, which included a water pump, a pressure accumulator, a water injection pin, a water tank equipped with a temperature regulator, and a control circuit. The materials included a virgin PBT and a 15% glass fiber filled PBT composite, and a plate cavity with a rib across center was used. Various processing variables were examined in terms of their influence on the length of water penetration in molded parts, which included melt temperature, mold temperature, melt filling speed, short-shot size, water pressure, water temperature,water hold and water injection delay time. Mechanical property tests were also performed on these molded parts,and XRD was used to identify the material and structural parameters. Finally, a comparison was made betweenwater-assisted and gas-assisted injection molded parts.Table 12. Experimental procedure2.1. MaterialsThe materials used included a virgin PBT (Grade 1111FB, Nan-Ya Plastic, Taiwan) and a 15% glass fiber filled PBT composite (Grade 1210G3, Nan-Ya Plastic, Taiwan).Table 3 lists the characteristics of the composite materials.2.2. Water injection unitA lab scale water injection unit, which included a water pump, a pressure accumulator, a water injection pin, a water tank equipped with a temperature regulator, and a control circuit, was used for all experiments [3]. An orifice-type water injection pin with two orifices (0.3 mm in diameter) on the sides was used to mold the parts. During the experiments, the control circuit of the water injection unit received a signal from the molding machine and controlled the time and pressure of the injected water. Before injection into the mold cavity, the water was stored in a tank with a temperature regulator for 30 min to sustain an isothermal water temperature.2.3. Molding machine and moldsWater-assisted injection molding experiments were conducted on an 80-ton conventional injection-molding machine with a highest injection rate of 109 cm3/s. A plate cavity with a trapezoidal water channel across the center was used in this study. Fig. 2 shows the dimensions ofthe cavity. The temperature of the mold was regulated by a water-circulating mold temperature control unit. Various processing variables were examined in terms of their influence on the length of water penetration in water channels of molded parts: melt temperature, mold temperature, meltfill pressure, water temperature and pressure, water injection delay time and hold time, and short shot size of the polymer melt. Table 4 lists these processing variables as well as the values used in the experiments.2.4. Gas injection unitIn order to make a comparison of water and gas-assisted injection molded parts, a commercially available gas injection unit (Gas Injection PPC-1000) was used for the gas assisted injection molding experiments. Details of the gas injection unit setup can be found in the Refs. [11–15].The processing conditions used for gas-assisted injection molding were the same as that of water-assisted injection molding (terms in bold in Table 4), with the exception of gas temperature which was set at 25 C.2.5. XRDIn order to analyze the crystal structure within the water-assisted injection-molded parts, wide-angle X-ray diffraction (XRD) with 2D detector analyses in transmission mode were performed with Cu Ka radiation at 40 kV and 40 mA. More specifically, the measurements were performed on the mold-side andwater-side layers of the water-assisted injection-molded parts, with the 2h angle ranging from 7 to 40 . The samples required for these analyses were taken from the center portion of these molded parts. To obtain the desired thickness for the XRD samples, the excess was removed by polishing theTable 3samples on a rotating wheel on a rotating wheel, first with wet silicon carbide papers, then with 300-grade silicon carbide paper, followed by 600- and 1200-grade paper fora better surface smoothness.2.6. Mechanical propertiesTensile strength and bending strength were measured on a tensile tester. Tensile tests were performed on specimens obtained from the water-assisted injection molded parts (see Fig. 3) to evaluate the effect of water temperature on the tensile properties. The dimensions of specimens forthe experiments were 30 mm · 10 mm · 1 mm. Tensile tests were performed in a LLOYD tensiometer according to the ASTM D638M test. A 2.5 kN load cell was used and the crosshead speed was 50 mm/min.Bending tests were also performed at room temperature on water-assisted injection molded parts. The bending specimens were obtained with a die cutter from parts (Fig. 3) subjected to various water temperatures.The dimensions of the specimens were 20 mm · 10 mm · 1 mm. Bending tests were performed in a micro tensile tester according to the ASTM D256 test. A 200 N load cell was used and the crosshead speed was 50 mm/min.2.7. Microscopic observationThe fiber orientation in molded specimens was observed under a scanning electron microscope (Jeol Model 5410).Specimens for observation were cut from parts molded by water-assisted injection molding across the thickness (Fig. 3). They were observed on the cross-section perpendicular to the flow direction. All specimen surfaces were gold sputtered before observation.3. Results and discussionAll experiments were conducted on an 80-ton conventional injection-moldingmachine, with a highest injection rate of 109 cm3/s. A plate cavity with a trapezoidal water channel across the center was used for all experimentsTable 4Fig. 3. Schematically, the positioning of the samples cut from the molded parts for tensile and bending tests and microscopic observations.3.1. Fingerings in molded partsAll molded parts exhibited the water fingering phenomenon at the channel to plate transition areas. In addition,molded glass fiber filled composites showed more severe water fingerings than those of non-filled materials, as shown photographically in Fig. 4. Fingerings usually form when a less dense, less viscous fluid penetrates a denser,more viscous fluid immiscible with it. Consider a sharp two phase interface or zone where density and viscosity change rapidly. The pressure force (P2 P1) on the displaced fluid as a result of a virtual displacement dx of the interface can be described by [16], where U is the characteristic velocity and K is the permeability.If the net pressure force is positive, then any small displacement will be amplified and lead to an instabilityand part fingerings. For the displacement of a dense, viscous fluid (the polymer melt) by a lighter, less viscous one (water), we can have Dl = l1 l2 > 0, and U > 0 [16].In this case, instability and the relevant fingering result when a more viscousfluid is displaced by a less viscous one, since the less viscous fluid has the greater mobility.The results in this study suggest that glass fiber filled composites exhibit a higher tendency for part fingerings. This might be due to the fact that the viscosity difference Dl between water and the filled composites is larger than the difference between water and the non-filled materials. Waterassisted injection molded composites thus exhibit more severe part fingerings.Fig. 4. Photograph of water-assisted injection molded PBT composite part.3.2. Effects of processing parameters on water penetrationVarious processing variables were studied in terms of their influence on the water penetration behavior. Table 4 lists these processing variables as well as the values used in the experiments. To mold the parts, one central processing condition was chosen as a reference (bold term in TableBy changing one of the parameters in each test, we were able to better understand the effect of each parameter on the water penetration behavior of water assisted injection molded composites. After molding, the length of water penetration was measured. Figs. 5–10 show the effects of these processing parameters on the length of water penetration in molded parts, including melt fill pressure, melt temperature, mold temperature, short shot size, water temperature, and water pressure.The experimental results in this study suggest that water penetrates further in virgin PBT than in glass fiber filled PBT composites. This is due to the fact that with the reinforcing glass fibers the composite materials have less volumetric shrinkage during the cooling process. Therefore,they mold parts with a shorter water penetration length.The length of water penetration decreases with the melt fill pressure (Fig. 5). This can be explained by the fact that increasing the melt fill pressure increases the flow resistance inside the mold cavity. It is then more difficult for the water to penetrate into the core of the materials. The length of water penetration decreases accordingly [3].The melt temperature was also found to reduce the water penetration in molded PBT composite parts (Fig. 6). This might be due to the fact that increasing the melt temperature decreases viscosity of the polymer melt.A lower viscosity of the materials helps the water to packthe water channel and increase its void area, instead of penetrating further into theparts [4]. The hollow core ratio at the beginning of the water channel increases and the length of water penetration may thus decrease.Increasing the mold temperature decreases somewhat the length of water penetration in molded parts (Fig. 7).This is due to the fact that increasing the mold temperature decreases the cooling rate as well as the viscosity of the materials. The water then packs the channel and increases its void area near the beginning of the water channel,instead of penetrating further into the parts [3]. Molded parts thus have a shorter water penetration length.Increasing the short shot size decreases the length of water penetration (Fig. 8). In water-assisted injection molding, the mold cavity is partially filled with the polymer melt followed by the injection of water into the core of the polymer melt [4]. Increasing the short shot size of the polymer melt will therefore decrease the length of water penetration in molded parts.For the processing parameters used in the experiments,increasing the water temperature (Fig. 9) or the water pressure(Fig. 10) increases the length of water penetration in molded parts. Increasing the water temperature decreases the cooling rate of the materials and keeps the polymer melt hot for a longer time; the viscosity of the materials decreases accordingly. This will help the water penetratefurther into the core of the parts [3]. Increasing the water pressure also helps the water penetrate into the materials.The length of water penetration thus increases.Finally, the deflection of molded parts, subjected to various processing parameters, was also measured by a profilemeter.The maximum measured deflection is considered as the part warpage. The result in Fig. 11 suggests that the part warpage decreases with the length of water penetration.This is due to the fact that the longer the water penetration,the more the water pressure can pack the polymeric materials against the mold wall. The shrinkage as well as the relevant part warpage decreases accordingly.Fig. 5. Effects of melt fill pressure on the length of water penetration in molded parts.Fig. 6. Effects of melt temperature on the length of water penetration in molded parts.Fig. 9. Effects of water temperature on the length of water penetration in moldedparts.Fig. 7. Effects of mold temperature on the length of water penetration in molded parts.Fig. 8. Effects of short shot size on the length of water penetration inmolded parts.Fig. 10. Effects of water pressure on the length of water penetration inmolded parts.3.3. Crystallinity of molded partsPBT is a semi-crystalline thermoplastic polyester with a high crystallization rate. In the water-assisted injection molding process, crystallization occurs under non-isothermal conditions in which the cooling rate varies with cooling time. Here the effects of various processing parameters(including melt temperature, mold temperature, and water temperature) on the level of crystallinity in molded parts were studied. Measurements were conducted ona wideangle X-ray diffraction (XRD) with 2D detector analyses(as described in Section 2). The measured results in Fig. 12 showed that all materials at the mold-side lay erexhibited a higher degree of crystallinity than those at the water-side layer. The result indicates that the water has a better cooling capacity than the mold during the cooling process. This matches our earlier finding [17] by measuring the in-mold temperature distribution. In addition, the experimental result in Fig. 12c also suggests that the crystallinity of the molded materials generally increases with the water temperature. This is due to the fact that increasing the water temperature decreases the cooling rate of the materials during the cooling process. Molded parts thus exhibited a higher level of crystallinity.On the other hand, to make a comparison of the crysallinity of parts molded by gas and water, gas-assisted injection molding experiments were carried out on the same injection molding machine as that used with water, but equipped with a high-pressure nitrogen gas injection unit [11–15]. The measured results in Fig. 13 suggests that gas-assisted injection molded parts have a higher degree of crystallinity than water-assisted injection mold parts.This is due to the fact that water has a higher cooling capacity and cools down the parts faster than gas. Parts molded by water thus exhibited a lower level of crystallinity than those molded by gas.Fig. 11. Measured warpage of molded parts decreases with the length of waterpenetration.3.4. Mechanical propertiesTensile tests were performed on specimens obtained from the water-assisted injection molded parts to examine the effect of water temperature on the tensile properties.Fig. 14 showed the measured decrease subjected to various water temperatures. As can be observed, both yield strength and the elongational strain at break of water assisted molded PBT materials decrease with the water temperature. On the other hand, bending tests were also performed at room temperature on water-assisted injection molded parts. The measured result in Fig. 15 suggests that the bending strength of molded parts decreases with the water temperature.Increasing the water temperature generally decreases the cooling rate and molds parts with higher level of crystallin-content of free volume and therefore an increasing level of stiffness. However, the experimental results here suggest that the quantitative contribution of crystallinity to PBT’s mechanical properties is negligible, while there is a more important quantitative increase of tensile and bending strength for the PBT materials.The mechanical properties of molded materials are dependent on both the amount and the type of crystalline regions developed during processing.The fact that the ductility of PBT decreases with the degree of crystallinity may indicate that a more crystalline and stiffer PBT developed at a lower cooling rate during processing and did not exhibit higher stress values in tensile tests because of a lack of ductility, and therefore did not behave as strong as expected from their stiffness [18]. Nevertheless,more detailed experiments will be needed for the future works to investigate the morphological parameters of water-assisted injection molded parts and their correlation with the parts’ mechanical properties.3.5. Fiber orientation in molded partsSmall specimens were cut out from the middle of molded parts in order to observe their fiber orientation. The position of the specimen for the fiber orientation observation is as shown in Fig. 3. All specimen surfaces were polished and gold sputtered before observation. Fig. 16 shows the microstructure of the water-assisted injection molded composite parts. The measured result suggests that the fiber orientation distribution in water-assisted injection molded parts is quite different from that of conventional injection ity. As is usually encountered in semi-crystalline thermoplastics,a higher degree of crystallization means a lower molded parts.In conventional injection molded parts, two regions are usually observed: the thin skin and the core. In the skin region near the wall, all fibers are oriented parallel to the injection molding, water-assisted injection molding technology is different in the way the mold is filled. With a conventional injection molding machine, one cycle is characterized by the phases of filling, packing and cooling.In the water-assisted injection molding process, the mold cavity is partially filled with the polymer melt followed by the injection of water into the core of the polymer melt.The novel filling process influences the orientation of fibers and matrix in a part significantly.From Fig. 16, the fiber orientation in water-assisted injection molded parts can be approximately divided intothree zones. In the zone near the mold-side surface where the shear is more severe during the mold filling, fibers are principally parallel. For the zone near the water-side surface,the shear is smaller and the velocity vector greater.In this case, the fiber tends to be positioned more transversely in the direction of injection. At the core, the fibers tend to be oriented more randomly. Generally speaking,the glass fibers near the mold-side surface of molded parts were found to be oriented mostly in the flow direction, and oriented substantially perpendicular to the flow direction with increasing distance from the mold-side surface.Finally, it should be noted that a quantitative comparison of morphology and fiber orientation [21] in waterassisted molded and conventional injection molded parts will be made by our lab in future works.Fig. 16. Fiber orientation across the thickness of water-assisted injection molded PBTcomposites.4. ConclusionsThis report was made to experimentally study the water-assisted injection molding process of poly-butylene-terephthalate(PBT) composites. The following conclusions can be drawn based on the current study.1. Water-assisted injection molded PBT parts exhibit the fingering phenomenon at the channel to plate transition areas. In addition, glass fiber filled composites exhibit more severe water fingerings than those of non-filled materials.2. The experimental results in this study suggest that the length of water penetration in PBT composite materials increases with water pressure and temperature, and decreases with melt fill pressure, melt temperature, and short shot size.3. Part warpage of molded materials decreases with the length of water penetration.4. The level of crystallinity of molded parts increases with the water temperature. Parts molded by water show a lower level of crystallinity than those molded by gas.5. The glass fibers near the surface of molded PBT composite parts were found to be oriented mostly in the flow direction, and oriented substantially perpendicular to the flow direction with increasing distance from the skin surface.玻璃纤维增强复合材料水辅注塑成型的实验研究摘要:本报告的目的是通过实验研究聚对苯二甲酸丁二醇复合材料水辅注塑的成型工艺。

Interface Shear Tests on FRP Composite Piles毕业翻译

Interface Shear Tests on FRP Composite Piles毕业翻译

1.摘要传统桩材料在严酷环境下使用的相关问题包括混凝土恶化、钢筋腐蚀和蛀虫对木桩的咬蚀。

据估计美国每年花费超过十亿美元在维修和替换滨水区的打桩系统。

如此高的维修和更换成本已经导致一些北美高速公路机构和人员调查使用纤维增强聚合物复合装和钢管桩等玻璃钢桩的可行性。

这些桩,如果被发现是可行的,可以提供优势如提高耐用性和降低寿命周期成本。

然而,复合桩具有相对较短的性能记录,并且很少有容易得到的证据充分的使用玻璃钢复合桩的项目。

、玻璃钢复合材料和钢筋混凝土不同在以下性能非均向性、低刚度、低表面硬度和不同的表面粗糙度。

因此,现有桩设计方法可能不能直接适用于玻璃钢复合材料成桩。

本文的重点主要是在玻璃钢复合桩的表面摩擦特性。

本文总结了沙复合桩界面剪切测试两种类型玻璃钢的结果,测试结果是与那些沙混凝土测试相比较,讨论了界面剪切强度对组合桩轴向应力的影响。

2.介绍传统的桥梁基础桩材料包括钢筋、混凝土和木材。

这些桩材料当被用在恶劣的海洋环境中寿命有限维修成本高。

降解问题包括氯攻击,混凝土钢筋腐蚀以及海虫的咬蚀。

据估计,修理和修理和更换打桩系统成本在美国超过每年10亿美元。

维修和更换成本高导致北美公路机构和研究人员调查了在运输和土木工程结构包括桥梁桩基础中使用复合材料的可行性,纤维增强聚合物(FPR)被认为是有吸引力的对于海洋和其他恶劣环境,因为他们能抵抗降解机制。

1980年以来,许多美国销售商已经开始销售选择桩产品成为“复合桩”。

术语“复合桩”通常是由玻璃钢,回收塑料或混合材料组成。

一些商用复合桩如图1所示。

到目前为止,复合桩使用一直仅限于海洋防撞桩,轻结构承重桩和一些实验测试桩。

组合桩尚未被土木行业广泛接受的原因主要是由于缺乏一个长期跟踪的性能记录。

然而,玻璃复合桩在严酷环境中可能出现的生命周期增长和耐久性提高,呈现出降低成本的大幅潜力。

玻璃钢复合材料与钢筋混凝土有明显的不同,是由于它的非均向性、低刚度、低表面硬度,和不同的表面粗糙度。

一篇关于复合材料非常好的一篇英文文献

一篇关于复合材料非常好的一篇英文文献

Hydrogen-storage materials dispersed into nanoporous substrates studied through incoherent inelastic neutron scatteringD.Colognesi a ,⇑,L.Ulivi a ,M.Zoppi a ,A.J.Ramirez-Cuesta b ,A.Orecchini c ,A.J.Karkamkar d ,M.Fichtner e ,E.Gil Bardajíe ,Z.Zhao-Karger eaConsiglio Nazionale delle Ricerche,Istituto dei Sistemi Complessi,Via Madonna del Piano 10,50019Sesto Fiorentino (FI),Italy bISIS Facility,STFC Rutherford Appleton Laboratory,Harwell Oxford,Didcot OX110QX,United Kingdom cInstitut Laue-Langevin,6Rue Jules Horowitz,38042Grenoble Cedex 9,France dPacific Northwest National Laboratory,P.O.Box 999,Richland,WA 99352,USA eKarlsruhe Institute of Technology,Institute of Nanotechnology,Hermann-von-Helmholtz-Platz 1,76347Eggenstein-Leopoldshafen,Germanya r t i c l e i n f o Article history:Received 26March 2012Received in revised form 18May 2012Accepted 18May 2012Available online 30May 2012Keywords:Hydrogen storage Nanomaterials Lattice dynamicsInelastic neutron scatteringa b s t r a c tIncoherent inelastic neutron scattering measurements on four impregnated/infiltrated composites of hydrides (namely,NaAlH 4,NH 3BH 3,LiBH 4+Mg(BH 4)2,and MgH 2)plus nanoporous scaffolds (active car-bon fibers or silica-based MCM41)have been performed at low temperature.After a careful data analysis,the present experimental results have been compared to the corresponding spectroscopic data of bulk hydrides.Evident signatures induced by infiltration process on the NaAlH 4phonon bands have been detected,showing up as a strong peak broadening and smoothing together with,in some cases,an energy shift.Less pronounced phonon spectrum modifications have been found in MgH 2and NH 3BH 3,mainly concentrated in the low-energy acoustic region.Finally,no relevant effect has been observed for LiBH 4+Mg(BH 4)2.Ó2012Elsevier B.V.All rights reserved.1.IntroductionHydrogen is currently studied as a possible environment-friendly and efficient energy carrier in connection with the future exploitation of alternative and/or renewable energy sources [1].The construction of an effective and reliable storage system is one of the key issues in the use of hydrogen as an energy carrier alternative to liquid and gaseous hydrocarbons [2].In this perspec-tive one can note that various complex ionic hydrides based on Al (alanates),N (amides)and B (boranates)[3–5]exhibit a very high hydrogen content,close or even exceeding the 2015target (i.e.,9wt.%)for hydrogen storage systems set by the US Department of Energy (DOE)[6].Nevertheless,although these materials are in principle highly interesting,they still cannot be used in technical applications,mainly due to the following reasons:(1)The thermodynamic properties of the pure hydride phasesare not appropriate because these materials are often too stable.This fact implies decomposition temperatures higher than 200°C,which are particularly undesirable in automo-tive applications.(2)The hydrogenation/dehydrogenation kinetics of the purehydride phases is too slow for practical purposes.It has been shown in several cases [7]that the transformation processes are dominated by the sluggish material-transport kinetics.(3)The reversibility upon cycling is hampered by the separationof phases appearing during the dehydrogenation of the material.These phases may segregate and grow,leading to a slowdown of the kinetics and the formation of inert frac-tions in the sample which cannot be re-hydrogenated upon cycling.Particles aggregation is also seen as a potential risk causing the formation of a bulk-like hydride.In order to tackle these problems,several strategies have been suggested.A promising approach is based on the well-known fact that the enthalpy of formation of a material is lowered in most cases [8]by increasing its surface energy [9].Thus it is possible to attain hydride destabilization by decreasing the particle size,reaching lower hydrogen-release temperatures.In general,parti-cles having nano-scale sizes are characterized by different thermo-dynamics,enhanced surface interactions,faster kinetics,increased number of defects,modified phase transformations,as well as the occurrence of new and meta-stable phases.Most of the work accomplished so far in order to achieve active hydride nano-particles has made use of the so-called scaffolding0925-8388/$-see front matter Ó2012Elsevier B.V.All rights reserved./10.1016/j.jallcom.2012.05.081Corresponding author.Tel.:+390555226681;fax:+390555226683.E-mail address:daniele.colognesi@fir.it (D.Colognesi).technique.By the word‘‘active’’we mean a material exhibiting appropriate thermodynamic conditions and fast dynamics,but rid of phase separation and other unwanted effects.In this respect, it has been suggested[10]that the incorporation of hydrogen stor-age materials into micro-and meso-porous rigid structures would stabilize nanomaterials and prevent aggregation during cycling. Thus,the hydride would retain the thermodynamic parameters and kinetic behavior associated with the hydrogenation/rehydro-genation of the nanomaterial rather than reverting to the standard bulk material when cycled.Several nanoporous scaffold-confined hydrogen storage materials have been reported so far,and most of them are carbonaceous structures,including active carbonfi-bers[11],carbon aerogels[12],and even C20-and C60-based solids [13].On the other hand,in the ammonia borane case,Gutowska et al.[14]have developed a way to deposit the active material within the channels of mesoporous silica(i.e.,SBA-15).The silica increases the rate of hydrogen release from the NH3BH3by two orders of magnitude compared with the release of hydrogen from the pristine compound.Furthermore,heating the hybrid material above100°C to release the second equivalent of hydrogen(i.e., the second H2molecule)gives rise to very little amount of borazine.Although a number of preparation methods are being devel-oped to disperse hydrogen containing materials into nano-porous matrices(e.g.,melt infiltration,wet impregnation,etc.),the phys-ical properties of such nano-dispersed complex systems have not yet been fully investigated.In particular,there is a lack of under-standing with respect to the influence of the particle size and the nature of the particle interface on hydride binding energies.A de-tailed analysis of the vibrational properties will be an essential contribution to this new and both scientifically and technically interestingfield.Actually,some incoherent inelastic neutron scat-tering(IINS)measurements have been recently performed on so-dium alanate,pristine and infiltrated into activated carbonfiber (namely,in ACF25from Kynol Inc.with most of the pores ranging between0.5and4nm)[15].The neutron spectrum of the pristine material(i.e.,NaAlH4)appears very rich in sharp spectral features caused by the proton vibrational dynamics in the system.On the contrary,the spectrum of the infiltrated material is completely disrupted by the nano-confining action of the matrix,ending up in an almost complete hydride amorphization.In addition,the inter-ionic vibrational modes turn out to be substantially weak-ened,while the intra-ionic ones are strengthened.So it is valuable to know if similar effects are observed after changing:hydroge-nated compound(i.e.,from NaAlH4to MgH2,LiBH4+Mg(BH4)2, and NH3BH3);pore shape(i.e.,from roughly spherical to cylindrical);pore size(i.e.,from dispersed between0.5and 4nm to afixed diameter of4.0nm);substrate(i.e.,from graphitic carbon to silica).This is exactly the objective of the present comparative work.Data related to nanoconfined NaAlH4will be presented again for comparison,but with a completely different aim with respect to Ref.[15]:in the present study the same technique is used to characterize various samples(representative of the main classes of H-containing systems),while in the aforementioned paper two different techniques(i.e.,IINS and Raman)have been applied to the same nanoconfined sodium alanate sample.The paper is organized as follows:the sample synthesis is de-scribed in detail in the next section,followed in Section3by the experimental IINS procedure,while all the data reduction details are reported in Appendix A.In Section4,the present experimental results are thoroughly analyzed,also in connection with previous spectroscopic measurements and,if existing,ab-initio density-functional theory simulations.Finally,the last section contains the conclusions of the present work.2.Sample synthesisEven though the synthesis details have been reported elsewhere(namely in Refs.[14,16–18],respectively,for NH3BH3,NaAlH4,MgH2,and Mg(BH4)2),it is worthwhile to describe in detail what kinds of materials have been investigated by neutron spectroscopy,mainly focusing on the nature and the differences of their respective scaffoldings:(1)sodium aluminum tetrahydride(NaAlH4,from Albemarle Corp.,purity96%)was employed as received,while,prior to use,activated carbonfibers ACF25(from Kynol Inc.)were milled in a planetary ball mill so to obtain afine powder according to the following conditions:10.0g of ACF25con-tained in a silicon nitride vial with six balls of13.0g each rotating at about 550rpm.Six milling cycles30min long were accomplished,each one fol-lowed by a5min pause.Subsequently the ground product was treated under Ar plus H2(i.e.,with5%of H2)atmosphere at600°C overnight,in order to remove moisture and oxygen containing surface groups.ACF25is defined as both a micro-and a mesoporous carbonaceous material,with most of the pores ranging between0.5and4nm and peaked at0.8nm[19].Its surface area,measured via the Brunauer,Emmet,and Teller(BET)method,was1815m2/g,while its free pore volume was estimated to be0.66cm3/g(for pore widths below4nm and after ball milling).A mixtureof NaAlH4(1.85g)and ground ACF25(1.85g)was lightly ball-milled,trans-ferred into an autoclave,and then heated under hydrogen atmosphere(150 barfinal pressure)to190°C(1h soaking time),i.e.,slightly above the melt-ing temperature of NaAlH4.The characteristics of the melt-infiltrated com-posite were completely different from those of pure ACF25:the surface area was reduced to242m2/g and the free pore volume to0.09cm3/g only,indi-cating that the largest portion of NaAlH4was inside the pores and not only on the external part of the carbonfibers.Thus at the end of the synthesis procedure the following melt-infiltrated NaAlH4+ACF25sample were available:NaAlH4:ACF25=1:1by weight,m=2.5g.(2)MCM-41silica was obtained from Mobil Corporation,while ammonia bor-ane was synthesized according to the procedure reported in Ref.[20]and purified by sublimation in vacuum.In order to disperse NH3BH3into the porous substrate,a solution of ammonia borane(m=5.6g,containing iso-topically enriched11B to reduce neutron absorption)in tetrahydrofuran (about100cm3)was slowly added to a sample of MCM-41(11.2g).The solution appeared to havefilled the internal channels of the mesoporous scaffold by capillarity.The impregnated MCM-41was then dried under vac-uum so to produce a sample with an internal coating of ammonia borane (approximately1:2NH3BH3to MCM-41by weight).As for the porous silica presently used,it exhibited a relatively large surface area(700–800m2/g from BET)and a medium-sized primary pore width(diameter:4.0nm), being formed by an ordered hexagonal array of cylindrical channels witha very regular morphology(space group P6mm).For this reason it was easyto calculate the total pore volume,which was in the range0.7–0.8cm3/g. (3–4)The two samples containing MgH2or LiBH4+Mg(BH4)2were obtained mak-ing use of ACF25or IRH33activated carbon,respectively.The latter,pro-duced at the Institut de recherche sur l’hydrogène of Universitédu QuébecàTrois-Rivières(Canada)was prepared by carbon dioxide activation of a car-bonaceous material(namely,coal from coconut shells)and showed a pore distribution from0.5to4.0nm,peaked at2.75nm.The physisorption mea-surement of IRH33revealed a BET surface area of2587m2/g and a micro-pore volume of about1.2cm3/g.IRH33was used after being ground by mortar and pestle so to get afine powder material.Then a eutectic mixture of LiBH4+Mg(BH4)2(m=0.28g,containing isotopically enriched7Li and11B to reduce the sample neutron absorption)was dispersed into0.73g of IRH33by melt infiltration at180°C under30bar-pressure of H2for1h.Thefinal concentration was estimated to be LiBH4+Mg(B-H4)2:IRH33=1:2.6by weight.This composite has been characterized by means of X-ray diffraction and electron microscopic methods.The infil-trated composite did not present any Bragg peaks and also no particles were visible in the transmission electron microscopy(TEM)images.The concen-tration of Mg,B and C have been mapped by energy-dispersive X-ray(EDX) and electron energy loss(EELS)spectra,where the homogeneous distribu-tion of the elements within the map indicates that borohydrides have been homogeneously incorporated within the carbon scaffold.These results are the indication of nanodispersion and/or amorphization of the borohydrides within the carbon scaffold.As for the MgH2sample,a dibutyl magnesium(Bu2Mg)solution was slowly added to pre-treated ACF25at room temperature,and then the mixture was quenched into liquid nitrogen in order to draw up all the precursor into the carbon ter,the solvent was removed under dynamic vacuum at a gradually increasing temperature for5h.This procedure of carbon impregnation/drying was repeated several times so to prevent the excess of Bu2Mg from sticking on the surface of the carbon material:at the end,18cm3of Bu2Mg solution had been added to2.0g of ACF25and dried.Then the composite was hydrogenated by heat-92 D.Colognesi et al./Journal of Alloys and Compounds538(2012)91–99ing up the sample to180°C under60bar of H2,causing the decomposition of Bu2Mg into MgH2and butane.Finally,the prepared composite containing20wt.%of MgH2 was again ground in a mortar under argon atmosphere producing afine powder.3.Experimental neutron scattering proceduresFour distinct neutron scattering experiments have been per-formed,namely:on sodium alanate infiltrated into ACF25(I),on LiBH4+Mg(BH4)2infiltrated into IRH33activated carbon(II),on ammonia borane dispersed into MCM41mesoporous silica(III), andfinally on magnesium hydride dispersed into ACF25(IV).The first and the third IINS measurements have carried out on TOS-CA-II[21]spectrometer,while the remaining two on IN4C spec-trometer[22].For this reason the description of the experimental procedure has been split into two separate parts:Section3.1deal-ing with the TOSCA-II experiments,and Section3.2dealing with the IN4C ones.3.1.Incoherent inelastic neutron scattering on TOSCA-IIThe neutron scattering measurements on samples(I)and(III) were carried out using TOSCA-II inelastic spectrometer of the ISIS pulsed neutron source at Rutherford Appleton Laboratory(Harwell, Didcot,Oxon,UK),according to the scheme reported in Table1.TOS-CA-II is a crystal-analyzer inverse-geometry spectrometer[21], where thefinal neutron energy is selected by two sets of pyrolytic graphite crystals placed in forward scattering(at around42.6°with respect to the incident beam)and in backscattering(at about137.7°with respect to the incident beam).This arrangement sets the nom-inal scattered neutron energy to E1=3.35meV(forward scattering) and to E1=3.32meV(backscattering).Higher-order Bragg reflec-tions arefiltered out by120mm-thick beryllium rods,wrapped in cadmium and cooled down to a temperature lower than30K.The incident neutron energy,E0,on the other hand,spans a broad range allowing to cover an extended energy transfer(E=E0ÀE1)region: 3meV<E<500meV.Because of thefixed geometry of this spec-trometer,the wave-vector transfer,Q,is related to the energy trans-fer through a monotonic function,roughly proportional to the square root of the incoming neutron energy:Q¼Q F;BðE0Þ/E1=20 (where suffixes F or B stand for forward scattering or backscattering, respectively).TOSCA-II has an excellent energy resolution in the accessible energy transfer range(D E/E0=1.5–3%).The sample cell used for the infiltrated sample(I)was an airtight indium-sealed cylinder made of vanadium(75.0mm long, 15.0mm internal diameter,wall0.4mm thick);while for sample (III)-b a standardflat can made of aluminum(47.0Â34.0mm2, 3.0mm-internal gap,wall0.5mm thick)was employed.Finally, for sample(III)-a an airtight copper-sealed cylinder made of stain-less steel(60.0mm long,15.0mm internal diameter,wall2.5mm thick)was preferred in order to perform an in situ thermal treat-ment at the end of the experiment(not dealt with in the present study).Special care was taken to prevent possible hydride wetting and oxidation during the sample loading procedure,performed in an inert-gas glove-box.Before the actual measurements,the empty cells were cooled down to the low temperature value of the exper-iment,and their time-of-flight spectra were recorded up to ade-quate integrated proton current(IPC)values.Then the samples were placed into the cryostat,one after the other,and the real neu-tron scattering measurement started when the sample tempera-ture reached approximately20K.The stability of the temperature conditions during these experiments was not regarded as particu-larly important.So for sample(I)the cryostat was left slowly reach-ing its base temperature T’12K,while for samples(III)the controller was set to T=20K.The obtained average temperature values(together with their stabilities)are reported in Table1.3.2.Incoherent inelastic neutron scattering on IN4CThe neutron scattering measurements of the infiltrated/impreg-nated samples(II)and(IV)were performed using IN4C spectrom-eter located at the Institut Laue-Langevin(Grenoble,France), following the scheme of Table2.IN4C[22]is a so-called hybrid-geometry spectrometer,where a crystal monochromatorfixes the initial neutron energy,and a chopper system determines thefinal neutron energy by time-of-flight analysis.The thermal neutron beam emerging from the reactor isfirst collimated(divergence, 1°)before impinging,with a Bragg angle varying between39°and65°,on the double focusing monochromator[23].In the case of our experiment,the selected values of initial energy were: E0=83.4meV from the(220)Bragg reflection of an array of copper crystals,and E0=149.2meV from the(006)Bragg reflection of an array of pyrolitic graphite(PG)crystals.Two rotating disk choppers are used to minimize background neutrons and gamma rays com-ing from the moderator.The long neutron pulses produced by the disk choppers travel through a collimating diaphragm and a sap-phirefilter is used to suppress contaminations from higher-order monochromator reflections.The beam isfinally reduced to short pulses by a Fermi chopper and hits the sample after passing through another collimating diaphragm.Neutrons scattered by the sample are then collected by3003He tubes covering angles up to120°.In addition,a3He-filled multidetector allows to observe forward scattering down to an angle of about3°.The scattering cells used for both samples(II)and(IV)were air-tight indium-sealed cylinders made of aluminum,(60.0mm long, wall0.5mm thick),but exhibiting two different internal diame-ters:7.5for(II)and15.0for(IV).Special care was taken to prevent possible hydride wetting and oxidation during the sample loading procedure,performed in an inert-gas glove-box.Before the actual measurements,the empty cells were cooled down to the low tem-perature value of the experiment,and their neutron spectra were recorded up to adequate counting time(s)values.Then the men-tioned samples were placed into the cryostat,one after the other, and the real neutron scattering measurement started when the sample temperature reached15K.The obtained temperature val-ues(together with their stabilities)are reported in Table2.For samples(IV)a monochromator change from Cu(220)to PG (006)was performed at the end of the run with E0=83.4meV, without varying the thermodynamic conditions of the sample un-der investigation.4.DiscussionThis section is divided into four subsections:in each of them a detailed comparison between the IINS spectrum of a selected bulk sample and that of the corresponding infiltrated/impregnatedTable1Experimental conditions of the IINS measurements on samples(I)and(III)performed on TOSCA-II,including:temperature T,integrated proton current of the ISIS neutron source IPC,total sample mass M,and proton concentration(molar)c[H].Label Sample T(K)IPC(l A h)M(g)c[H](%)(I)Inf.NaAlH4+ACF2516±21263.8 2.5038.11(III)-a Impr.NH3BH3+MCM4119.91±0.021006.3 1.6354.04 (III)-b Pure MCM4119.8±0.6580.20.990.00D.Colognesi et al./Journal of Alloys and Compounds538(2012)91–9993material will be shown,taking into account,if available,appropri-ate published IINS data and lattice dynamics simulations in order to make the spectral interpretation and assignment easier.It worth noting at this stage that the neutron spectra presented in the fol-lowing(with the exception of that from sample(III))represent the so-called hydrogen-projected density of phonon states[24] (H-DoPS),G H(E),and have been obtained through an appropriate data redaction procedure.All the details this analysis are reported in Appendix A.Subsequently,a comparative evaluation of the re-sults obtained for the all various samples will provided in the fol-lowing,and conclusive,section.4.1.NaAlH4infiltrated into ACF25The IINS result for sample(I),i.e.,NaAlH4infiltrated into ACF25, is shown in Fig.1and directly compared to equivalent spectra from bulk NaAlH4[15,25]and Na3AlH6[25],both measured at low-tem-perature on the same TOSCA-II instrument.In these two references detailed assignment schemes of both bulk sodium alanate com-pounds are also provided,in full agreement with the ab-initio study by Ke and Tanaka[26].For this reason the mentioned band assignments will not be repeated here.Just by inspecting Fig.1,a comparison between bulk NaAlH4and sample(I)looks straightfor-ward:some phonon bands are shifted after the infiltration process, while all the bands are broadened and smoothed,becoming almost structureless.The following observations can be made in detail. Being more accurate,one can note that:(a)the Al–H stretching frequencies(at about217and225meV)slightly increase in the infiltrated sample;(b)the AlH4libration frequencies(43.4–69.4meV)stronglydecrease in the melt-infiltrated sample;(c)the Al–H–Na bending and the H–Al–H scissoring modes(at74.4and111.6meV,respectively)are almost unaffected.In addition,the band broadening can be quantified as an extra full-width-at-half-maximum(FWHM)ranging from18.8meV(lat-tice phonon band),to17.1meV(librational band),to30.3meV (bending band)and,finally,to25.4meV(scissoring band).All these results are considered to be compatible with the typical crys-tal-size effects,where the AlHÀ4tetrahedra located in the external part of an alanate nano-particle are affected by the interaction with the carbon scaffold more strongly than those contained in the core of the particle itself.As for the possible presence of Na3AlH6(or even,but much less likely,of some NaH),nofinal conclusion can be drawn at this stage,even though the presence of a modest quan-tity of Na3AlH6appears to be compatible with our neutron data. The IINS spectrum of Na3AlH6is reported in Fig.1,and NaH has been studied in detail in Ref.[27].While the spectrum of NaH exhibits only two strong optical bands(i.e.,transverse and longitu-dinal)between65meV and120meV,basically overlapping the NaAlH4bending mode region,that of Na3AlH6shows an intense band(namely,Al–H valence modes),ranging between130meV and200meV.This interval is particularly important in our case since it exactly overlaps the extra-intensity found in the IINS spec-trum of samples(I),which is totally absent in bulk NaAlH4.4.2.NH3BH3impregnated into MCM41silicaThe neutron spectrum of NH3BH3impregnated into MCM41sil-ica,once subtracted of the small MCM41component,has been compared to a corresponding measurement,always performed on TOSCA-II[28,29],on a bulk NH3BH3sample(with isotopically enriched11B)kept at T=20K.The two measurements are reported in Fig.2,where in both cases the backscattering and forward scat-tering spectra have been summed together so to increase the counting statistics.Before discussing the actual effect of the silica scaffolding on NH3BH3,it is important to understand the nature of the IINS bands visible in Fig.2.For a complete assignment of the vibrational bands of the low-temperature(i.e.orthorhombic) ammonia borane phase,the readership can consult Refs.[30,31]. In the following we report only a rough scheme of the main spec-tral ranges concerning the fundamental vibrational bands:(1)a low frequency region(19–62meV)which contains the lat-tice phonon modes;(2)a medium-low spectral region(87–112meV)containing theB–N stretching modes;(3)an intermediate region(112–161meV)which contains theBH3deformations;(4)a medium-high spectral region(161–211meV)where theNH3deformations are observed;Table2Experimental conditions of the IINS measurements on samples(II)and(IV)performed on IN4C,including:monochromator type,temperature T,counting time s,total sample mass M,and proton concentration(molar)c[H].For samples(II)-a and(IV)-b,d,bulk hydrides and carbonfibers(both asfine powders)have been mechanically mixed before the IINS measurements.Label Sample Monochrom.T(K)s(h)M(g)c[H](%)(II)-a Inf.LiBH4+Mg(BH4)2+IRH33Cu(220)15.04±0.018.810.9135.92 (II)-b Bulk LiBH4+Mg(BH4)2+IRH33Cu(220)15.04±0.0113.000.9542.79 (II)-c IRH33Cu(220)15.04±0.0120.650.590.00 (IV)-a Impr.MgH2+ACF25Cu(220)15.03±0.019.37 2.5317.00 (IV)-b Bulk MgH2+ACF25Cu(220)15.03±0.017.27 2.4715.55 (IV)-c Impr.MgH2+ACF25PG(006)15.03±0.0111.44 2.5317.00 (IV)-d Bulk MgH2+ACF25PG(006)15.03±0.01 5.01 2.4715.5594 D.Colognesi et al./Journal of Alloys and Compounds538(2012)91–99(5)a high frequency region(273–310meV)containing the B–Hstretching modes;(6)a very high frequency region(384–422meV)containing theN–H stretching modes.However,two points have to be stressed concerning the afore-mentioned assignment obtained through Raman scattering at T=88K.First,IINS on TOSCA-II,due to the well-known Sachs–Tell-er mass tensor effects[32],is not sensitive in this system to bands located at energies higher than180meV,so the H stretching modes are not at all visible in neutron spectra and are not reported in Fig.2.Second,the presence of overtones and combinations in IINS spectra follows very different rules with respect to Raman measurements,so it is also important to consider Ref.[33],where NH3BH3is both simulated and measured by inelastic neutron scat-tering between6and124meV,unfortunately with an energy res-olution not as high as the TOSCA-II one.Nevertheless,the authors of that study were confident enough to rule out the presence of overtones and combinations at least for E<124meV.Going back to ammonia borane impregnated into MCM41silica,one sees that the effect of MCM41on NH3BH3seems indeed very modest as far as proton vibrational dynamics is concerned.However,some real differences in the lattice phonon bands below45meV(i.e.,acoustic or optical)are visible,as expected since the lattice periodicity is partially disrupted by MCM41[34,35].4.3.LiBH4+Mg(BH4)2infiltrated into IRH33carbonThe equimolar solid mixture of lithium borohydride and mag-nesium borohydride is a relatively new system,being proposed by Zhan-Zhao Fan et al.in2010[36],and not much is known about its structure at low temperature,not to mention its lattice and vibrational dynamics.However,from the very recent diffraction studies by Gil Bardajíet al.[37]and Hagemann et al.[38],it seems reasonable to suppose that at the temperature of our IINS measure-ments(i.e.,at about T=15K),Mg(BH4)2appears in its a phase (hexagonal,space group P61)and LiBH4with an orthorhombic structure(space group Pnma,labeled o-LiBH4).For this reason in the rest of the subsection we will pay attention to the dynamic properties of the two separate components,i.e.,o-LiBH4and a-Mg(BH4)2,even though we are well aware that it may be too sim-ple to assume that solid solution properties are simply obtained from a linear combination of those belonging to their components.IINS measurements on bulk o-LiBH4at low temperature(T=5K) have been performed by Hartman et al.[39]making use of a com-pletely isotopic sample(i.e.,7Li and11B)and,subsequently with an improved resolution,by Borgschulte et al.[40]from the same kind of sample at T=15K.From the latter data sets[40,41],employing the procedure sketched in the appendix,we have been able to ex-tract a high resolution estimate of the G H(E)in LiBH4,which has been subsequently altered through a convolution procedure so to match the same energy resolution as that obtained on IN4C.Final results are plotted in Fig.3as EÀ1G H(E).As for pure bulk a-Mg(BH4)2,only IINS data from Ref.[38](apparently taken at low temperature,T’20K)are currently available.However,the experimental conditions(especially those connected to the(Q,E) kinematic path)were not clearly stated in the text,so,unlike in the LiBH4case,no rigorous data treatment has been attempted. The raw experimental spectrum has been just assumed to be approximately proportional to EÀ1G H(E)(after a simple correction for the Bose phonon population factor),neglecting both instrumen-tal background and multiphonon contamination corrections,and has been reported in Fig.3.As a result,one can observe two main facts:(1)LiBH4+Mg(BH4)2infiltrated into IRH33and bulk LiBH4+Mg(BH4)2spectra look very similar in all the spectral range 5meV<E<80meV,even though some small differences are clearly detectable.These are certainly larger than the statistical uncertainty of the experimental data(the statisti-cal error bars in Fig.3are of the same size of the line thick-ness),but are homogeneously spread all over the spectra,so it is likely that they have been originated during the data reduction procedure(e.g.,via background subtraction)and do not have a clear physical meaning.(2)Making use of the o-LiBH4and the a-Mg(BH4)2aforemen-tioned data,it is possible to understand the origin of the two bands in the higher frequency part of the spectra of LiBH4+Mg(BH4)2,namely that placed between43and 61meV(A),and that located between61and78meV(B).The former peak,(A),is mainly connected to LiBH4,even though slightly blue-shifted,and represents the rigid libra-tions of the[BH4]Àgroup in this compound[39].The latterD.Colognesi et al./Journal of Alloys and Compounds538(2012)91–9995。

复合材料与工程英语介绍范文

复合材料与工程英语介绍范文

复合材料与工程英语介绍范文In the realm of advanced materials, composites stand as a testament to human ingenuity, blending the strengths of various materials to create a new class of substances that are stronger, lighter, and more versatile than their individual components. The field of composite materials and engineering is a dynamic and rapidly evolving sector that is revolutionizing industries from aerospace to automotive, from sports equipment to civil infrastructure.Composite materials are engineered to achieve specific properties by combining two or more constituent materials with distinct properties. These constituents, often referred to as the matrix and the reinforcement, work in synergy to provide exceptional performance characteristics. The matrix, typically a resin or a metal, holds the reinforcement in place and transfers the load to it. The reinforcement, which can be fibers like carbon, glass, or aramid, provides the strength and stiffness that the composite material is known for.The engineering of composites is an art that requires a deep understanding of material science, mechanics, and manufacturing processes. Engineers must carefully select the types of matrix and reinforcement, their proportions, and the orientation of the fibers to tailor the composite to meet the specific requirements of an application. This precision engineering allows for the creation of components that arenot only lighter than their traditional counterparts but also offer superior strength-to-weight ratios and resistance to fatigue and corrosion.In the aerospace industry, composites have become indispensable, enabling the construction of aircraft that are more fuel-efficient and environmentally friendly. They are also integral to the automotive sector, where they contribute to the development of lighter and more fuel-efficient vehicles. In sports, composite materials have transformed the performance of equipment, offering athletes equipment that is lighter, stronger, and more responsive.The future of composite materials and engineering looks even more promising. With ongoing research and development, we are on the cusp of new breakthroughs that will further enhance the capabilities of composites. Innovations in nanotechnology, for instance, are paving the way for self-healing composites that can repair themselves after damage, extending the lifespan of components and reducing maintenance costs.In conclusion, the world of composite materials and engineering is a vibrant and exciting field that is continuously pushing the boundaries of what is possible. As we delve deeper into this fascinating domain, we can expect to see even more innovative applications that will shape the future of technology and industry.。

复合材料与工程英语介绍范文

复合材料与工程英语介绍范文

复合材料与工程英语介绍范文Composite materials are materials made from two or more constituent materials with significantly different physical or chemical properties. These materials when combined, work together to produce a material with characteristics different from the individual components. The resulting composites can provide unique advantages, such as increased strength, reduced weight, and improved durability.复合材料是由两种或两种以上具有明显不同物理或化学性质的组分材料制成的材料。

这些材料在结合时,共同产生具有不同于单个组分的特征的材料。

由此产生的复合材料可以提供独特的优势,例如增加强度、减轻重量和提高耐久性。

One common example of a composite material is fiberglass, which is made of glass fibers embedded in a polymer matrix. The combination of the strong, lightweight glass fibers with the flexible, durable polymer creates a material that is both strong and lightweight, making it ideal for a wide range of applications. From aerospace and automotive components to sports equipment andconstruction materials, fiberglass composites are used in diverse industries.一个常见的复合材料例子是玻璃纤维,它是由玻璃纤维嵌入聚合物基质而制成的。

nature上关于复合材料的英文文献

nature上关于复合材料的英文文献

nature上关于复合材料的英文文献Short communicationHighly stabilized alpha-NiCo(OH)2nanomaterials for high performance device applicationPaulo Roberto Martins,AndréLuis Araújo Parussulo,Sergio Hiroshi Toma,Michele Aparecida Rocha,Henrique Eisi T oma,Koiti Araki *Instituto de Química,Universidade de S?o Paulo,Av.Prof.Lineu Prestes,748,S?o Paulo,SP CEP 05508-000,Brazilh i g h l i g h t sg r a p h i c a l a b s t r a c t<="" nanostructured="" p=""><="" over="" p="" without=""><="" p="" stable="">nanomaterials.a r t i c l e i n f oArticle history:Received 14May 2012Received in revised form 15June 2012 Accepted 18June 2012Available online 23June 2012Keywords:Nickel hydroxide Mixed hydroxides Alpha-polymorph NanoparticlesNanostructured materialsa b s t r a c tImproving the charge capacity,electrochemical reversibility and stability of anode materials are main challenges for the development of Ni-based rechargeable batteries and devices.The combination of cobalt,as additive,and electrode material nanostructuration revealed a very promising approach for this purpose.The new a -NiCo mixed hydroxide based electrodes exhibited high speci ?c charge/discharge capacity (355e 714C g à1)and outstanding structural stability,withstanding up to 700redox cycles without any signi ?cant phase transformation,as con ?rmed by cyclic voltammetry,electrochemical quartz crystal microbalance and X-ray diffractometry.In short,the nanostructured a -NiCo mixed hydroxide materials possess superior electrochemical properties and stability,being strong candidates for application in high performance batteries and devices.ó2012Elsevier B.V.All rights reserved.1.IntroductionNickel hydroxides have been explored as electroactive materials of sensors [1e 6],electrochromic devices [7]and rechargeable batteries [8,9].Many efforts have been directed to improve the conductivity and reversibility of the charge/discharge processes,and to enhance the speci ?c charge capacity by incorporation oftransition and non-transition metal ions as additives (Al,Zn,Cd,Co and Mn),[10e 16]or by generating nanomaterials.Another possi-bility is by stabilizing and using the alpha-Ni(OH)2(a 4g ,433mA h g à1)instead of the conventional beta (b 4b ,289mA h g à1)polymorph,because of its superior electrochemical properties [17,18].The addition of Co ions to Ni hydroxide electrodes is knownto have bene ?cial effects,reducing the mechanical stress during charge/discharge processes,thus preventing electrode failure,and increasing the charge density [19,20].However,the absence of the characteristic cobalt waves in the mixed NiCo hydroxides*Correspondingauthor.Tel.:t551130918513;fax:t551138155640.E-mail address:***************.br(K.Araki).Contents lists available at SciVerse ScienceDirectJournal of Power Sourcesjournal h omepage:www.elsevier.co m/lo cate/jp owsour0378-7753/$e see front matter ó2012Elsevier B.V.All rights reserved./10.1016/j.jpowsour.2012.06.065 Journal of Power Sources 218(2012)1e 4voltammograms strengthened the hypothesis that only nickel is electrochemically active.Accordingly,the enhanced charge capacity[21]of mixed hydroxide materials was assigned to a higher conductivity and activation of more nickel sites rather than to contributions of cobalt sites[22].For example,Kim et al.[23]showed that the a-phase material obtained by co-precipitation of 10.2%of cobalt(II)hydroxide with nickel(II)hydroxide was totally converted to the b-phase after60consecutive redox cycles,but the material containing16.7%of cobalt was more stabilized.Similar results were described by Zhao et al.[24]by homogeneous co-precipitation of16.8and19.5%of aluminium hydroxide by the urea method.The speci?c charge capacity of b-Ni(OH)2/Ni-foam electrodes is 275mA h gà1,lower than of b-Ni(OH)2nanotubes(315mA h gà1), but higher than that of nanosheets(219.5mA h gà1),commercial micrometer grade spherical powders(265mA h gà1)and micro-tubes(232.4mA h gà1)[28].New routes for preparation of alp ha nickel hydroxide nanomaterials,showing enhanced electro-chemical properties and speci?c charge capacity,have also been reported[7,25e27]but none was stable enough for practical application.Recently we showed that nanostructured materials prepared with a-Ni(OH)2nanoparticles can be stabilized[29,30],keeping the performance for at least200consecutives electrochemical cycles. In this report we demonstrate that the combination of the two strategies,more speci?cally,cobalt additivation and nano-structuration,can further enhance the stability of alpha nickel hydroxide,resulting in more robust materials for application in batteries and other devices.In special,we disclose the electro-chemical properties of nanostructured materials prepared from sol e gel nickel/cobalt mixed hydroxide nanoparticle precursors, exhibiting high speci?c charge capacity(up to714C gà1)and stability in the a-phase(over700cycles).2.Materials and methodsAll reagents and solvents were of analytical grade and usedas received.Isopropyl alcohol,n-butyl alcohol and potassium hydroxide were purchased from Synth.Anhydrous glycerin was purchased from Sigma e Aldrich,whereas nickel acetate tetrahy-drate and cobalt acetate hydrate were obtained from Vetec.The nickel/cobalt mixed hydroxide precursors were prepared by dissolving4.82mmol of the metal acetates in25mL of glycerin and adding9.64mmol of KOH in n-butanol,at room temperature.Four samples were prepared and named according to the Ni:Co molar ratio as follows:Ni(OH)2,NiCo-80:20,NiCo-60:40and NiCo-50:50.X-ray analyses were performed using a Higaku Mini?ex powder diffractometer equipped with a Cu K a radiation source(1.541 A, 30kV,15mA,step?0.02 ),in the2q range from1.5to70 .Cyclic voltammograms(à0.15e0.44V,20mV sà1)were registered on an Autolab PGSTAT30potentiostat/galvanostat using a conventional three electrodes arrangement with a NiCo(OH)2 modi?ed?uorine doped tin oxide(FTO)as working electrode,a coiled platinum wire as auxiliary and an Ag/AgCl(in1.0mol dmà3KCl,0.222V vs SHE)reference electrode,using 1.0mol dmà3KOH as electrolyte solution.Electrochemical quartz crystal microbalance(EQCMB) measurements were carried out simultaneously with CV,using AT-cut quartz crystal electrodes(5MHz,25.4mm diameter,working area?1.37cm2)covered with a thin platinum layer,and a Maxtek PM-710equipment coupled with the Autolab PGSTAT30potencio-stat/galvanostat,using a conventional three electrodes arrangement.FTO glass plates were carefully washed with isopropanol andwater,dried in air and modi?ed by spin-coating the nickel/cobalt mixed hydroxide sol e gel nanoparticle precursors,at2500rpm. These electrodes were dried under vacuum and calcined at240 C for30min.The speci?c charge capacities per gram of nickel were determined using1.0cm2electrodes,where the amounts of nickel and cobalt were measured by ICP-AES(Arcos-SOP e Spectro)using the solutions obtained by dissolving the NiCo hydroxide?lms with a0.1mol dmà3nitric acid solution,from the working electrodes after700cycles.The quartz crystal electrodes were modi?ed ina similar way,except for the exclusion of the heat treatment.3.Results and discussionMixed alpha-NiCo(OH)2sol e gel precursors(a-NiCo-80:20, a-NiCo-60:40and a-NiCo-50:50)are convenient row materials for the preparation of nanostructured?lms by methods as simple as dip-coating and spin-coating.In fact,porous?lms constituted by agglomerated5e15nm nanoparticles,resembling sponge like nanostructures,were obtained in all cases.A typical SEM image of a NiCo-50:50sample is shown in Fig.1A where the particle size and morphology are clearly depicted.The vacuum dried material was stable enough to be washed and submitted to electrochemical cycling without signi?cant lixiviation or?aking,but the calcined materials are more stable and used throughout,except forthe Fig.1.(A)SEM image of a NiCo-50:50electrode calcined at240 C,and(B)XRD of the nanostructured nickel and cobalt mixed hydroxide materials.P.R.Martins et al./Journal of Power Sources218(2012)1e42samples for EQCMB measurements which were not submitted to heat treatment to avoid damaging the quartz crystal.The polymorphic phases of nickel hydroxide materials can be readily distinguished by X-ray diffractometry(XRD)by evaluating the inter-slab distances and the degree of organization of the lamella along the crystallographic c axis.The disordered turbos-tratic structure of a-Ni(OH)2presents inter-slab distances higher than about8 A,whereas the structure of the beta polymorph is more compact and organized presenting a much shorter inter-slab distance of4.6 A.X-ray diffractograms of Ni(OH)2,NiCo-80:20,NiCo-60:40and NiCo-50:50nanostructured materials are shown in Fig.1B.Only the 003peak was observed in the low angle region at7.91 ,7.55 ,8.16 and8.64 ,respectively corresponding to inter-slab distances of11.2, 11.7,10.9and10.3 A,in addition to lower intensity and broadened 101(34.5 )and110(60.3 )peaks,con?rming that the nano-structured materials are constituted by rather small sized crystal-lites of the a-polymorph.A tendency of decrease of inter-slab distances was observed as a function of cobalt content,but no signi?cant shift of the101and110peaks could be observed precluding the comparison of lattice parameters.However,the substitution of Ni(II)by cobalt ions in the lattice should have con-trasting effects depending on its oxidation state and extent ofsubstitution since Ni(II)ionic radii(83pm)is in between that of Co(II)and Co(III)(88.5and68.5pm,respectively).The electrochemical quartz crystal microbalance(EQCMB) experiments were carried out to shed light on possible structural changes that may be occurring along the successive charge/ discharge processes.This technique is quite sensitive and conve-nient to distinguish the alpha and beta polymorphic phases.The a-Ni II(OH)2is characterized by a positive mass change whereas the b-Ni II(OH)2shows exactly the opposite behavior associated with the oxidation process but the mechanism is not clearly de?ned.Eq.(1) can be used to explain that behavior,but the incorporation of hydrated cations and hydroxide anion concomitantly with the release of water molecules during the oxidation process have also been proposed[23].aàNieOHT2$H2OtOHà?g NiOOH$eH2OTe1txTte1àxTH2Oteà(1)A typical EQCMB experiment for the NiCo nanomaterials is illustrated in Fig.2where the results for the NiCo-50:50and the simultaneously measured CVs are depicted.The oxidation at E ap?t0.28V(Fig.2A)is associated with a positive mass change that parallels the current rise in the respective voltammogram, indicating that both are correlated and the corresponding cathodic wave at E cp?t0.23V is associated with a negative mass change,as expected for nickel hydroxide nanomaterials in the alpha poly-morphic phase.Surprisingly,the charge capacity and the EQCMB pro?le after50and200cycles were very similar clearly re?ecting theelectrochemical stability of the nanomaterial(Fig.2B).FTO electrodes modi?ed with the nanomaterials were prepared by de?ning1.0cm2areas using Scotch tape,depositing the mixed NiCo hydroxide sol e gel nanoparticle precursors,drying under vacuum and?ring at240 C.The CVs(Fig.3)are characterized by low intensity redox waves that become well de?ned in the 0.2e0.4V range after about ten redox cycles for electrode conditioning.The peak currents associated with the Ni II(OH)2/ Ni III OOH redox pair increased dramatically while small shifts on the anodic and cathodic peak potentials were observed, indicating an increase of the electroactive sites concentration as a function of the number of successive scans.The voltammetric behavior of the thermally treated mixed hydroxides was strongly dependent on the amount of cobalt ion present in the nanomaterials(Fig.3A e D).For example,the E ap and E cp of pure Ni(OH)2were found respectively att0.39andt0.30V. However,they were signi?cantly shifted to lower potentials as the amount of cobalt was increased,such that E ap was cathodically shifted to0.37,0.31and0.29V respectively after incorporation of 20,40and50%of cobalt to the Ni(OH)2,improving the reversibility and decreasing the possibility of oxygen gas evolution during the charging process.Two successive CVs were always superimposable, except for a small increase in current,indicating that all electro-chemically active sites were recovered during thereduction Fig.2.Cyclic voltammogram(black line)and voltamassogram(red line)of a-NiCo-50:50after(A)50and(B)200scan cycles,in1mol dmà3KOH electrolyte solution,at 20mV sà1.(For interpretation of the references to color in this?gure legend,the reader is referred to the web version of thisarticle.)Fig.3.Successive cyclic voltammograms of FTO electrodes modi?ed with A)Ni(OH)2, B)a-NiCo-80:20,C)a-NiCo-60:40and D)a-NiCo-50:50and submitted to heat treat-ment at240 C for30min,in1mol dmà3KOH and scan rate?20mV sà1.P.R.Martins et al./Journal of Power Sources218(2012)1e43(discharge)process despite the slower kinetics,as indicated by the less intense and broader cathodic wave.The charge/discharge curves become more symmetric as the cobalt content was increased (Figs.3and 4).The Ni:Co molar ratios in the modi ?ed electrodes were deter-mined before (77.7:22.3,56.4:43.6and 47.3:52.7)and after 700redox cycles (79.0:21.0,58.1:41.9and 53.3:46.7),and the speci ?c charge and discharge capacities per gram of nickel were evaluated from the amounts of charge under the voltammetric waves (esti-mated by integration of CVs in Fig.3)and therespective mass of nickel in the electrode determined by ICP-AES.It should be noticed that the charge capacity of the pure Ni(OH)2remained more or less constant (147C g à1(Ni))whereas those of mixed hydroxides increased progressively as a function of the number of successive charge/discharge cycles,reaching limit values as high as 355,714,and 609C g à1(Ni),respectively for the NiCo-80:20,NiCo-60:40and NiCo-50:50nanomaterials,after 700cycles.The exception seems to be the NiCo-60:40,which should reach a limit value as high as ?ve times the charge capacity of a -Ni(OH)2.This behavior suggests that the diffusion of electrolyte and consequent activation of nickel hydroxide sites is somewhat slower in this material.Considering nickel hydroxide as electrochemically active species,the coulombic ef ?ciencies were estimated as 8.9,21.6,43.4and 37.0%,respectively for a -Ni(OH)2,a -NiCo-80:20,a -NiCo-60:40and a -NiCo-50:50,indicating that almost half of the nickel hydroxide sites are electrochemically active.These results are inconsistent with a signi ?cant increase of the degree of crystallinity and conversion of the material to the b -phase polymorph,con-?rming the electrochemical stability and reversibility of the mixed hydroxide nanomaterials,in striking contrast with previously reported analogous materials.4.ConclusionMixed nickel and cobalt hydroxide nanomaterials exhibiting enhanced electrochemical reversibility and speci ?c charge and discharge capacity as a function of cobalt molar proportion up to 50%were successfully prepared from sol e gel precursors.Interest-ingly,the speci ?c charge capacity increased progressively until up to 700cycles and no change in the EQCMB pro ?le was observed con ?rming their high structural stability inthe alpha polymorphic phase.The a -NiCo-60:40showed the best performance exhibiting at least four and six times higher speci ?c charge capacity than pure a -Ni II (OH)2and b -Ni II (OH)2,respectively.Summarizing,the mixed hydroxide nanomaterials showed superior electrochemical prop-erties and phase stability making them suitable for high charge device applications.AcknowledgementsTo Funda??o de Am paro àPesquisa do Estado de S?o Paulo (FAPESP)and Conselho Nacional de Desenvolvimento Cientí?co e Tecnológico (CNPq)for the ?nancial support.Appendix A.Supplementary materialSupplementary material associated with this article can be found,in the online version,at /10.1016/j.jpowsour.2012.06.065.References[1]A.Salimi,E.Shari ?,A.Noorbakhsh,S.Soltanian,mu n.8(2006)1499.[2]M.Jafarian,M.G.Mahjani,M.G.Heli,F.Gobal,M.Heydarpoor,El ectrochem.Commun.5(2003)184.[3]P.R.Martins,M.A.Rocha,L.Angnes,H.E.Toma,K.Araki,Electroa nalysis 23(2011)2541.[4]J.Y.Park,K.S.Ahn,Y.C.Nah,H.S.Shim,Y.E.Sung,J.Sol e Gel Sci.Technol.31(2004)323.[5]M.Vidotti,C.D.Cerri,R.F.Carvalhal,J.C.Dias,R.K.Mendes,S.I.C. de Torresi,L.T.Kubota,J.Electroanal.Chem.636(2009)18.[6]M.S.M.Quintino,H.Winnischofer,K.Araki,H.E.Toma,L.Angne s,Analyst 130(2005)221.[7]J.Y.Qi,P.Xu,Z.S.Lv,X.R.Liu,A.H.Wen,J.AlloyCompd.462(2008)164.[8]W.Zhang,W.Jiang,L.Yu,Z.Fu,W.Xia,M.Yang,Int.J.Hydrogen Energy 34(2009)473.[9] A.K.Shukla,S.Venugopalan,B.Hariprakash,J.Power Sources 100(2001)125.[10]K.Provazi,M.J.Giz,L.H.Dall ’Antonia,S.I.C.de Torresi,J.Power Sources 102(2001)224.[11]K.Watanabe,M.Koseki,N.Kumagai,J.Power Sources 58(1996)23.[12]T.N.Ramesh,R.V.Kamath,Electrochim.Acta53(2008)8324.[13]Y.W.Li,J.H.Yao,C.J.Liu,W.M.Zhao,W.X.Deng,S.K.Zhong,Int.J. HydrogenEnergy 35(2010)2539.[14]S.A.Cheng,A.B.Yan,H.Liu,J.Q.Zhang,C.N.Cao,J.Power Sources 76(1998)215.[15]M.Y.Wu,J.M.Wang,J.Q.Zhang,C.N.Cao,J.Solid State Electr.10(2006)411.[16]W.H.Zhu,J.J.Ke,H.M.Yu,D.J.Zhang,J.Power Sources56(1995)75.[17]R.Barnard,C.F.Randell,F.L.Tye,J.Appl.Electrochem. 10(1980)109.[18]P.V.Kamath,M.Dixit,L.Indira,A.K.Shukla,V.G.Kumar,N.Muni chandraiah,J.Electrochem.Soc.141(1994)2956.[19]w,J.Sapjeta,J.Electrochem.Soc.136(1989)1603.[20]R.Sjovall,J.Power Sources 90(2000)153.[21]M.Oshitani,H.Yufu,K.Takashima,S.Tsuji,Y.Matsumaru,J.Ele ctrochem.Soc.136(1989)1590.[22]I.Serebrennikova,V.I.Birss,J.Electrochem.Soc.147(2000)36 14.[23]M.S.Kim,K.B.Kim,J.Electrochem.Soc.145(1998)507.[24]Y.L.Zhao,J.M.Wang,H.Chen,T.Pan,J.Q.Zhang,C.N.Cao,Int.J. HydrogenEnergy 29(2004)889.[25]F.F.Tao,M.Y.Guan,Y.M.Zhou,L.Zhang,Z.Xu,J.Chen,Cryst.Growth Des.8(2008)2157.[26]G.T.Zhou,Q.Z.Yao,X.C.Wang,J.C.Yu,Mater.Chem.Phys.98(2 006)267.[27]X.Y.Guan,J.C.Deng,Mater.Lett.61(2007)621.[28]Y.Wang,D.X.Cao,G.L.Wang,S.S.Wang,J.Y.Wen,J.L.Yin,Electr ochim.Acta 56(2011)8285.[29]M.A.Rocha,H.Winnischofer,K.Araki,F.J.Anaissi,H.E.Toma,J.Nanosci.Nanotechnol.11(2011)3985.[30]M.A.Rocha,F.J.Anaissi,H.E.Toma,K.Araki,H.Winnischofer,M ater.Res.Bull.44(2009)970.Fig.4.Plots of the speci ?c charge and discharge capacities per gram of nickel of FTO electrodes modi ?ed with stabilized pure and mixed alpha nickel hydroxides (a -Ni(OH)2,a -NiCo-80:20,a -NiCo-60:40and a -NiCo-50:50),?red at 240 C for 30min,as a function of the number of consecutive scan cycles in 1mol dm à3KOH,at 20mV s à1.P.R.Martins et al./Journal of Power Sources 218(2012)1e 44。

复合材料英语作文

复合材料英语作文

复合材料英语作文English:Composite materials, also known as composites, are engineered materials made from two or more constituent materials with significantly different physical or chemical properties. These materials are combined to produce a material with characteristics different from those of the individual components. Composites offer several advantages over traditional materials such as metals, plastics, or ceramics. They are lighter in weight, have higher strength-to-weight ratios, and can be tailored to specific applications, making them ideal for industries ranging from aerospace and automotive to construction and sports equipment. The versatility of composites lies in their ability to combine different materials strategically to optimize performance while minimizing drawbacks. By selecting the appropriate combination of materials and manufacturing processes, engineers can create composites with desired properties such as stiffness, strength, durability, and resistance to corrosion or impact. Moreover, composites often exhibit better fatigue resistance and dimensional stability compared to conventional materials, extending their lifespan and reducing maintenance requirements. However, thedesign and production of composite materials require specialized knowledge and techniques due to the complex interactions between the constituent materials and the manufacturing processes involved. Despite these challenges, the continuous advancements in composite technology promise even greater innovations and applications in various industries in the future.中文翻译:复合材料,也被称为复合材料,是由两种或两种以上具有显著不同物理或化学性质的材料组成的工程材料。

复合材料技术的报告英语作文

复合材料技术的报告英语作文

复合材料技术的报告英语作文Composite Material Technology ReportComposite materials, also known as composite materials, are materials composed of two or more different substances that have different physical or chemical properties and are combined to form a new material with unique characteristics. These materials are widely used in various industries dueto their superior strength, stiffness, and light weight.The use of composite materials has been gainingpopularity in recent years, especially in the aerospace and automotive industries. In aerospace, composite materialsare used to build aircraft and spacecraft components, such as wings, fuselage, and structural parts, due to their high strength-to-weight ratio and resistance to corrosion. Inthe automotive industry, composite materials are used to produce lightweight and fuel-efficient vehicles, as well as to improve crash safety and reduce emissions.There are several types of composite materials,including polymer matrix composites, metal matrix composites, and ceramic matrix composites. Each type hasits own unique properties and applications. For example, polymer matrix composites, such as carbon fiber reinforced polymers, are widely used in the construction of high-performance sports equipment and automotive components. Metal matrix composites are used in aerospace andautomotive applications due to their high temperature resistance and wear resistance. Ceramic matrix composites are used in high-temperature applications, such as in gas turbines and nuclear reactors.In conclusion, composite material technology has revolutionized the way we design and manufacture productsin various industries. With their unique properties and versatility, composite materials continue to play a crucial role in advancing technology and improving the performanceof modern products.复合材料技术报告复合材料,也称为复合材料,是由两种或两种以上具有不同物理或化学性质的物质组成,相互结合形成具有独特特性的新材料。

复合材料加工与应用外文翻译

复合材料加工与应用外文翻译

毕业设计之英文翻译系别:材料科学与工程系专业:复合材料加工与应用姓名:吕明学号:Z08011333指导教师:周思凯硝酸盐Ca4Al2(OH)12(NO3)2•4H2O的磨料流的加工阶段的热变形行为以及Ca4Al2(OH)12(NO3)2•2H2O中间水合物的坚定结构的研究G. Renaudin, J.-P. Rapin, B. Humbert, M. François,摘要:硝酸盐Ca4Al2(OH)12(NO3)2• 4H2O的磨料流的加工阶段是属于双氢氧化物的分层的那一类。

它是通过热失重分析法以及拉曼光谱法利用温度函数而研制的。

在室温下它的结构能够被预先决定。

混合物Ca4Al2(OH)12(NO3)2• 4H2O的中间水合物大约在70℃才能存在而被察觉。

它的结构可以在那个温度下通过单晶x-射线衍射而被分解。

其结构在70℃下能被描绘出来,它具有斜方六面体的空间三维结构,其晶胞参数a=5.731(2)A,c=48.32(1)A,z=3。

它被认为是一种柱状的层状结构,因为相邻的主要层次基团【Ca2Al(OH)6】+是通过硝酸基团而连接起来的,剩下的两个水分子仅仅是填充空间结构而不能连接主要的层次基团。

它的结构呈现出是一种有活力且无序的,因为硝酸基团能在三元轴的周围自由旋转,拉曼光谱法也说明了这种情况。

关键词:晶体结构热学分析钙铝酸盐粘合剂硝酸盐一:引言Ca4Al2(OH)12(NO3)2• 4H2O或者3CaO •Al2O3•Ca(NO3)2• 10H2O在基本的氧化物注释中是有磨料流加工阶段的,包括阴离子类型的硝酸根离子。

下面的命名法在粘合剂化学中通常被用到(例如硫化铝酸盐Ca4Al2(OH)12SO4•6H2O,羧酸铝酸盐Ca4Al2(OH)12CO3• 5H2O以及半羧酸铝酸盐Ca4Al2(OH)12(CO3)2/1•6H2O),这种化合物可被命名二级铝酸盐。

所有这些磨料属于更广泛的化合物是一种叫做水滑石。

材料类外文文献翻译

材料类外文文献翻译

本科毕业论文外文文献及译文文献、资料题目:The effects of heat treatment onthe microstructure and mechani-cal property of laser melting dep-ositionγ-TiAl intermetallic alloys 文献、资料来源:Materials and Design文献、资料发表(出版)日期:2009.10。

25院(部):材料科学与工程学院专业:材料成型及控制工程班级:姓名:学号:指导教师:翻译日期:2011。

4。

3中文译文:热处理对激光沉积γ—TiAl金属间化合物合金的组织与性能的影响摘要:Ti—47Al—2。

5V—1Cr 和Ti-40Al—2Cr (at.%)金属间化合物合金通过激光沉积(LMD)成形技术制造。

显微组织的特征通过光学显微镜(OM)、扫描电子显微镜(SEM)、投射电子显微镜(TEM)、和X射线衍射仪(XRD)检测。

沿轴向评估热处理后的沉积试样室温下的抗拉性能和维氏硬度。

结果表明:由γ—TiAl 和α2—Ti3Al构成的γ-TiAl基体试样具有全密度柱状晶粒和细的层状显微组织。

Ti-47Al—2.5V—1Cr基体合金和Ti—40Al-2Cr基体合金沿轴向的室温抗拉强度大约分别为650 MPa、600MPa,而最大延伸率大约为0。

6% 。

热处理后的Ti—47Al—2.5V-1Cr和Ti-40Al-2Cr合金可以得到不同的显微组织.应力应变曲线和次表面的拉伸断裂表明沉积和热处理后的试样的断裂方式是沿晶断裂。

1。

简介金属间化合物γ-TiAl合金由于其高熔点(﹥1450℃)、低密度(3g/cm3)、高弹性模量(160—180GPa)和高蠕变强度(直到900℃)成为很有前景的高温结构材料,一直受到广泛研究[1–4].但是对于其结构应用来说,这种材料主要缺点之一是在室温下缺少延展性。

此外,这种合金运用传统的制造工艺诸如锻压、轧制和焊接,加工起来比较困难[5].对于TiAl组份,传统的铸造技术不利条件是粗大的铸态组织导致室温下的机械性能变差。

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毕业设计外文资料翻译题目POLISHING OF CERAMIC TILES抛光瓷砖学院材料科学与工程专业复合材料与工程班级复材0802学生学号20080103114指导教师二〇一二年三月二十八日MATERIALS AND MANUFACTURING PROCESSES, 17(3), 401–413 (2002) POLISHING OF CERAMIC TILESC. Y. Wang,* X. Wei, and H. YuanInstitute of Manufacturing Technology, Guangdong University ofTechnology,Guangzhou 510090, P.R. ChinaABSTRACTGrinding and polishing are important steps in the production of decorative vitreous ceramic tiles. Different combinations of finishing wheels and polishing wheels are tested to optimize their selection. The results show that the surface glossiness depends not only on the surface quality before machining, but also on the characteristics of the ceramic tiles as well as the performance of grinding and polishing wheels. The performance of the polishing wheel is the key for a good final surface quality. The surface glossiness after finishing must be above 208 in order to get higher polishing quality because finishing will limit the maximum surface glossiness by polishing. The optimized combination of grinding and polishing wheels for all the steps will achieve shorter machining times and better surface quality. No obvious relationships are found between the hardness of ceramic tiles and surface quality or the wear of grinding wheels; therefore, the hardness of the ceramic tile cannot be used for evaluating its machinability.Key Words: Ceramic tiles; Grinding wheel; Polishing wheelINTRODUCTIONCeramic tiles are the common decoration material for floors and walls of hotel, office, and family buildings. Nowadays, polished vitreous ceramic tiles are more popular as decoration material than general vitreous ceramic tiles as they can *Corresponding author. E-mail: cywang@401Copyright q 2002 by Marcel Dekker, Inc. have a beautiful gloss on different colors. Grinding and polishing of ceramic tiles play an important role in the surface quality, cost, and productivity of ceramic tiles manufactured for decoration. The grinding and polishing of ceramic tiles are carried out in one pass through polishing production line with many different grinding wheels or by multi passes on a polishing machine, where different grinding wheels are used.Most factories utilize the grinding methods similar to those used for stone machining although the machining of stone is different from that of ceramic tiles. Vitreous ceramic tiles are thin, usually 5–8mm in thickness, and are a sintered material,which possess high hardness, wear resistance, and brittleness. In general, the sintering process causes surface deformation in the tiles. In themachining process, the ceramic tiles are unfixed and put on tables. These characteristics will cause easy breakage and lower surface quality if grinding wheel or grinding parameters are unsuitable. To meet the needs of ceramic tiles machining, the machinery, grinding parameters (pressure, feed speed, etc.), and grinding wheels (type and mesh size of abrasive, bond, structure of grinding wheel, etc.) must be optimized. Previous works have been reported in the field of grinding ceramic and stone[1 –4]. Only a few reports have mentioned ceramic tile machining[5 –8], where the grinding mechanism of ceramic tiles by scratching and grinding was studied. It was pointed out that the grinding mechanism of ceramic tiles is similar to that of other brittle materials. For vitreous ceramic tiles, removing the plastic deformation grooves, craters (pores), and cracks are of major concern, which depends on the micro-structure of the ceramic tile, the choice of grinding wheel and processing parameters, etc. The residual cracks generated during sintering and rough grinding processes, as well as thermal impact cracks caused by the transformation of quartz crystalline phases are the main reasons of tile breakage during processing. Surface roughness Ra and glossiness are different measurements of the surface quality. It is suggested that the surface roughness can be used to control the surface quality of rough grinding and semi-finish grinding processes, and the surface glossiness to assess the quality of finishing and polishing processes. The characteristics of thegrinding wheels, abrasive mesh size for the different machining steps, machining time, pressure, feed, and removing traces of grinding wheels will affect the processing of ceramic tiles[9].In this paper, based on the study of grinding mechanisms of ceramic tiles, the manufacturing of grinding wheels is discussed. The actions and optimization of grinding and polishing wheels for each step are studied in particular for manualpolishing machines.GRINDING AND POLISHING WHEELS FOR CERAMIC TILEMACHININGT he mac hi ni ng of cer ami c t i l e s i s a vol ume-pr oduc t i on pr oc e s s t ha t uses significant numbers of grinding wheels. The grinding and polishing wheels forceramic tile machining are different from those for metals or structural ceramics. In this part, some results about grinding and polishing wheels are introduced for better understanding of the processing of ceramic tiles.Grinding and Polishing WheelsCeramic tiles machining in a manual-polishing machine can be divided into four steps—each using different grinding wheels. Grinding wheels are marked as 2#, 3#, and 4# grinding wheels, and 0# polishing wheel; in practice, 2# and 3# grinding wheels are used for flattening uneven surfaces. Basic requirements of rough grinding wheels are long life, high removal rate, and lower price. For 2# and 3# gr inding wheel s, Si C a brasi ve s wi th me s h #180 (#320)a r e bonde d by m a g n e s i u m o x yc h l o r i d e c e m e n t(M O C)t o g e t h e r w i t h s o m e p o r o u s f i l l s, waterproof additive, etc. The MOC is used as a bond because of its low price, simple manufacturing process, and proper performance.T he 4# grinding wheel will refine the surface to show the brightness of ceramic tile. The GC#600 abrasives and some special polishingmaterials, etc., are bonded by MOC. In order to increase the performance such as elasticity, etc., of the grinding wheel, the bakelite is always added. The 4# grinding wheels must be able to rapidly eliminate all cutting grooves and increase the surface glossiness of the ceramic tiles. The 0# polishing wheel is used for obtaining final surface glossiness, whichis made of fine Al2O3 abrasives and fill. It is bonded by unsaturated resin. The polishing wheels must be able to increase surface glossiness quickly and make the glossy ceramic tile surface permanent.Manufacturing of Magnesium Oxychloride Cement Grinding WheelsAfter the abrasives, the fills and the bond MOC are mixed and poured into the models for grinding wheels, where the chemical reaction of MOC will solidify the shape of the grinding wheels. The reaction will stop after 30 days but the hardness of grinding wheel is essentially constant after 15 days. During the initial 15-day period, the grinding wheels must be maintained at a suitable humidity and temperature.For MOC grinding wheels, the structure of grinding wheel, the quality of abrasives, and the composition of fill will affe ct their grinding ability. All the factors related to the chemical reaction of MOC, such as the mole ratio of MgO/MgCl2, the specific gravity of MgCl2, the temperature and humidity to care the cement will also affect the performance of the MOC grinding wheels.Mole Ratio of MgO/MgCl2When MOC is used as the bond for the grinding wheels, hydration reaction takes place between active MgO and MgCl2, which generates a hard XMg e OH T2·Y e MgCl2T·ZH2O phase. Through proper control of the mole ratio of MgO/MgCl2, a reaction product with stable performance is formed. The bond is composed of 5Mg e OH T2·e MgCl2T·8H2O and 3Mg e OH T2·e MgCl2T·8H2O: As the former is more stable, optimization of the mole ratio of MgO/MgCl2 to produce more 5Mg e OH T2·e MgCl2T·8H2O is required. In general, the ideal range for the mole ratio of MgO/MgCl2 is 4–6. When the contents of the active MgO and MgCl2 are known, the quantified MgO and MgCl2 can be calculated.Active MgOThe content of active MgO must be controlled carefully so that hydration reaction can be successfully completed with more 5Mg e OH T2·e MgCl2T·8H2O: If the content of active MgO is too high, the hydration reaction time will be too short with a large reaction heat, which increases too quickly. The concentrations of the thermal stress can cause generation of cracks in the grinding wheel. On thecontrary, if the content of active MgO is too low, the reaction does not go to completion and the strength of the grinding wheel is decreased.Fills and AdditivesThe fills and additives play an important role in grinding wheels. Some porous fills must be added to 2# and 3# grinding wheels in order to improve the capacity to contain the grinding chips, and hold sufficient cutting grit. Waterproof additives such as sulfates can ensure the strength of grinding wheels in processing under water condition. Some fills are very effective in increasing the surface quality of ceramic tile, but the principle is not clear.Manufacturing of Polishing WheelsFine Al2O3 and some soft polishing materials, such as Fe2O3, Cr2O3, etc., are mixed together with fills. Unsaturated resin is used to bond these powders, where a chemical reaction takes place between the resin and the hardener by means of an activator. The performance of polishing wheels depends on the properties of resin and the composition of the polishing wheel. In order to contain the fine chips, which are generated by micro-cutting, some cheap soluble salt can be fed into the coolant. On the surface of the polishing wheel, the salt will leave uniform pores, which not only increase the capacity to contain chips and self-sharpening of the polishing wheel, but also improves the contact situation between polishing wheel and ceramic tiles.Experimental ProcedureTests were carried out in a special manual grinding machine for ceramictiles. Two grinding wheels were fixed in the grinding disc that was equipped to the grinding machine. The diameter of grinding disc was 255 mm. The rotating speed of the grinding disc was 580 rpm. The grinding and polishing wheels are isosceles trapezoid with surface area 31.5 cm2 (the upper edge: 2 cm, base edge: 5 cm, height: 9 cm). The pressure was adjusted by means of the load on the handle for different grinding procedures. A zigzag path was used as the moving trace for the grinding disc. To maintain flatness and edge of the ceramic tiles, at least one third of the tile must be under the grinding disc. During the grinding process, sufficient water was poured to both cool and wash the grinding wheels and the tiles. Four kinds of vitreous ceramic tiles were examined, as shown in Table 1.Two different sizes of ceramic A, A400 (size: 400 £400 £5mm3T and A500(size: 500 £500 £5mm3T were tested to understand the effect of the tile size. Forceramic tile B or C, the size was 500 £500 £5mm3: The phase composition of thetiles was determined by x-ray diffraction technique. Surface reflection glossiness and surface roughness of the ceramic tiles and the wear of grinding wheels were measured.The grinding and polishing wheels were made in-house. The 2# grindingwheels with abrasives of mesh #150 and 3# grinding wheels with mesh #320 were used during rough grinding. Using the ceramic tiles with different surface toughness ground by the 2# grinding wheel for 180 sec, the action of the 3# grinding wheels were tested. The ceramic tile was marked as A500-1 (or B500-1, C500-1, A400-1) with higher initial surface toughness or A500-2 (or B500-2, C500-2, A400-2) with lower initial surface toughness.Two kinds of finishing wheels, 4#A and 4#B were made with the same structure, abrasivity, and process, but different composition of fills and additives. Only in 4#B, a few Al2O3, barium sulfate, and magnesium stearate were added for higher surface glossiness. The composition of the polishing wheels 0#A and 0#B were different as well. In 0#B, a few white alundum (average diameter 1mm), barium sulfate, and chrome oxide were used as polishing additives, specially. After ground by 4#A (or 4#B) grinding wheel, the ceramic tiles were polished with 0#A (or 0#B). The processing combinations with 4# grinding wheels and 0#RESULTS AND DISCUSSIONSEffects of 2# and 3# Grinding WheelsSurface QualityIn rough grinding with a 2# grinding wheel, the surface roughness for all the tiles asymptotically decreases as the grinding time increases, see Fig. 1. The initial asymptote point of this curve represents the optimized rough grinding time, as continued grinding essentially has no effect on the surface roughness. In these tests, the surface roughness curves decrease with grindingtime and become smooth at ,120 sec. The final surface quality for different kinds of ceramic tiles is slightly different. In terms of the initial size of the tile, the surface roughness of ceramic tile A400 e £400 £5mm3T is lower than that of A500 e500 £500 £5mm3T: The surface roughness ofc e r a m i c t i l e B500r a p id l y d r o p s a s t he g r i n d i n g t i m e i n c r e a s e s.Thus, it is easier to remove surface material from the hardest of thethree kinds of the ceramic tiles (Table 1). However, as the final surface roughness of ceramic tile A500 is the same as that of ceramic tile C500, the hardness of theceramic tile does not have a direct relationship with the final surface quality.In the 3# grinding wheel step, all craters and cracks on the surface of ceramic tiles caused by the 2# grinding wheel must be removed. If residual cracks and craters exist, it will be impossible to get a high surface quality in the next step. The surface roughness obtained by the 2# grinding wheel willalso affect the surfaceFigure 1. Surface roughness of several ceramic tiles as a function of grinding time for 2# grindingwheel.quality of next grinding step by the 3# grinding wheel. In Fig. 2, the actions of the 3# grinding wheels are given using the ceramic tiles with different initial R a, which were ground by the 2# grinding wheel for 180 sec. The curves of surface vs. grinding time rapidly decrease in 60 sec. Asymptotic behavior essentially becomes constant after 60 sec. In general, the larger the initial surface roughness, the worse the final surface roughness. For example, for ceramic tile B500-1, the initial R a was 1.53mm, the finial R a was 0.59mm after being ground by the 3# grinding wheel. When the initial R a was 2.06mm for ceramic tile B500-2, the finial R a was 0.67mm. In Ref. [8], we studied the relations between abrasive mesh size and evaluation indices of surface quality, such as surface roughness and surface glossiness. In rough grinding, the ground surface of ceramic tile shows fracture craters. These craters scatter the light, so that the surface glossiness values are almost constant at a low level. It is difficult to improve the surface glossiness after these steps. Figure 3 shows the slow increase in surface glossiness with time by means of the 3# grinding wheel. It can be seen that the glossiness of ceramic tile B500-1 is the highest. The surface glossiness of ceramic tile A400-1 is better than that of A500-1 because the effective grinding times per unit area for former is longer than for latter. These trends are similar to those for surface r o u g h n e s s i nFig. 2.Wear of Grinding WheelsThe wear of grinding wheels is one of the factors controlling the machining cost. As shown in Fig.4, the wear of grinding wheels is proportional to grindingFigure 2. Surface roughness of several ceramic tiles as a function of grinding time for 3# grindingwheel.Figure 3. Surface glossiness of several ceramic tiles as a function of grinding time by 3# grindingwheel.time for both the grinding wheels and the three types of ceramic tiles. The wear rate of the 3# grinding wheel is larger than the 2# grinding wheel. It implies that the wear resistance of the 3# grinding wheel is not as good as 2# for constant grinding time of 180 sec. When the slope of thecurve is smaller, life of thegrinding wheels will be longer. Comparison of the ceramic tiles hardness (Table 1) with the wear resistance behavior in Fig. 4 does not reveal a strong dependency. Therefore, the hardness of the ceramic tile cannot be used to distinguish the machinability. The difference ofFigure 4. Wear of grinding wheels of several ceramic tiles as a function of grinding time for 2# and3# grinding wheels.initial surface roughness of ceramic tile will affect the wear of grinding wheel. In Fig. 4, the wear of the 3# grinding wheel for ceramic tile B500-1 is smaller than that for ceramic tile B500-2. The initial surface roughness of the latter is higher than that of the former so that additional grinding time is required to remove the deeper residual craters on the surface. Improvement of the initial surface roughness can be the principal method for obtaining better grinding quality and grinding wheel life during rough grinding.Effects of 4# Grinding Wheels and 0# Polishing WheelsSurface QualityThe combination and the performance of 4# grinding and 0# polishingwheels show different results for each ceramic tile. The grinding quality vs. grinding (polishing) time curves are presented in Fig. 5, where all the ceramic tiles were previously ground by 2# and 3# grinding wheels to the same surface quality.The surface glossiness is used to assess surface quality because the surface roughness is nearly constant as finishing or polishing time increases[8]. In this test, the ceramic tile A400 were fast ground by 4#A and 4#B grinding wheels [Fig. 5(a)]. The surface glossiness increased rapidly during the initial 90 sec and then slowly increased. The surface glossiness by grinding wheel 4#B is higher than by 4#A. Afterwards, polishing was done by four different combinations of finishing wheel and polishing wheel. By means of polishing wheels 0#A and 0#B, we processed the surface finished by 4#A grinding wheel (described as 4#A–0#A and 4#A–0#B in Fig. 5), and the surfacef i n i s h e d b y4#Bg r i n d i n g wh e e l (described as 4#B–0#A and 4#B–0#B in Fig. 5). The curves of surface glossiness vs. polishing timeshow parabolic behavior. After 60 sec of polishing, the surface glossiness reaches to ,508, then slowly increases. The polishing wheel 0#B gives a better surface quality than 0#A.In Fig. 5(a), the maximum surface glossiness of ceramic tile A400 is about ,75 by 4#B–0#B.The relation between initial surface glossiness and the final surface quality is not strong. The effect of pre-polishing surface glossiness can be observed by 0#B polishing wheel as polishing ceramictile A500 [Fig. 5(b)]. The maximum surface glossiness that can be achieved is 748 in 240 sec by4#A–0#B or 4#B–0#B. This value is lower than that of ceramic tile A400 [Fig. 5(a)].The final surface glossiness by 4#A grinding wheel is highly different from that by 4#B grinding wheel for ceramic tile B500, as shown in Fig. 5(c), but the final polishing roughness is the same when 0#A polishing wheel is used. The better performance of 0#B polishing wheel is shown because the surface glossiness canincrease from 17 to 228 in 30 sec. The maximum surface glossiness is 658 by 4#B–0#B. Thecurves of polishing time vs. surface glossiness in Fig. 5(d) present the same results as polishing of ceramic tile B500 [Fig. 5(c)]. With 0#A polishingFigure 5. Surface glossiness for ceramic tiles (a) A400, (b) A500, (c) B500, and (d) C500 as afunction of grinding (polishing) time for 4# grinding wheels and 0# polishing wheels.wheel, the action of pre-polishing surface glossiness is significant. The best value of surface glossiness in 240 sec is 708 by 4#B–0#B as polishing ceramic tile C500. The results discussed earlier describe that the surface glossiness by 0# polishing wheel will depend not only on the pre-polishing surface glossiness formed by 4# grinding wheel, but also on the characteristics of the ceramic tiles and the performance of 0# polishing wheel. The differences of initial surface glossiness and final surface glossiness are larger for 4#A and 4#B. If the prepolishing surfaceroughness is lower, the final surface glossiness will be higher.Figure 5. Continued.The polishing time taken to achieve the maximum surface glossiness will be also shorter. The initial surface quality will limit the maximum value of polishing surface glossiness that can be obtained. To reach a final surface glossiness of above 608, the minimum pre-polishing surface glossiness must be above 208.The performance of the polishing wheel is the key to good surface quality. The polishing ability of the polishing wheels depends on the properties of the ceramic tiles as well. Even if the same grinding and polishing wheels are used, on all four ceramic tiles, the maximum surface glossiness values of ceramic tiles are different. The ceramic tile A500 shows the best surface glossiness, and ceramictile B500 shows the worst, although it is easier to roughly grind ceramic tile B500. The peak valueof the surface glossiness is also limited by the properties ofWear of Grinding and Polishing WheelsThe life of 4# grinding wheels and 0# polishing wheels (Fig. 6) are longer than those of the rough grinding wheels (Fig. 4). For finer grinding (Fig. 6), it is impossible to distinguish the relation between grinding wheels and ceramic tiles. Polishing wheels have longer life because they produce more plastic deformation than removal.SUMMARY OF RESULTS(1) The performance of grinding and polishing wheels will affect its life and the surface quality of ceramic tiles.(2) In ceramic tile machining, the surface quality gained in the previous step will limit the final surface quality in the next step. The surface glossiness of pre-polishing must be higher than 208 inorder to get the highest polishing quality. The optimization of the combination of grinding wheels and polishing wheels for all the steps will shorten machining time and improve surface quality. Optimization must be determined for each ceramics tiles.Figure 6. Wear of grinding wheels 4# and polishing wheels 0# for several ceramic tiles as afunction of grinding time.(3) The effect of hardness of ceramic tiles is not direct, thus the hardness of ceramic tiles cannot be used for evaluating the machinability ofACKNOWLEDGMENTThe authors thank Nature Science Foundation of Guangdong Province and Science Foundation of Guangdong High Education for their financial support.REFERENCES1. Wang, C.Y.; Liu, P.D.; Chen, P.Y. Grinding Mechanism of Marble. AbrasivesGrinding 1987, 2 (38), 6–10, (in Chinese).2. Inasaki, I. Grinding of Hard and Brittle Materials. Annals of the CIRP 1987, 36 (2),463–471.3. Zhang, B.; Howes, D. Material Removal Mechanisms in Grinding Ceramics. Annalsof the CIRP 1994, 45 (1), 263–266.4. Malkin, S.; Hwang, T.W. Grinding Mechanism for Ceramics. Annals of the CIRP1996, 46 (2), 569–580.5. Black, I. Laser Cutting Decorative Glass, Ceramic Tile. Am. Ceram. Soc. Bull. 1998,77 (9), 53–57.6. Black, I.; Livingstone, S.A.J.; Chua, K.L. A Laser Beam Machining (LBM) Database for the Cutting of Ceramic Tile. J. Mater. Process. Technol. 1998, 84 (1–3), 47–55.7. Jiang, D.F. Mirror Surface Polishing of Ceramic Tile. New Building Mater. 1994, 20(11), 27–30, (in Chinese).8. Ma, J.F. Analysis on Man-Made Floor Brick and Manufacture of Grinding SegmentUsed for Floor Brick. Diamond Abrasive Eng. 1996, 6 (95), 35–46, (in Chinese). 9. Wang, C.Y.; Wei, X.; Yuan, H. Grinding Mechanism of Vitreous Ceramic Tile. Chin.J. Mech. Eng. 1998, 9 (8), 9–11, 46 (in Chinese).材料与制造工艺17(3), 401–413 (2002)抛光瓷砖王CY,* 魏X, 袁H制造技术研究所,广东工业大学科技,广州510090,中国P.R.摘要研磨和抛光,是装饰玻璃陶瓷砖的生产中的重要步骤。

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