Influence of surface micro-beams with large deflection on the resonance frequency of a qua

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超快贝塞尔光束在硫化锌晶体表面制备纳米孔

270 μm。
关键词：硫化锌晶体；高深径比纳米孔；光子器件；高斯-贝塞尔光束
中图分类号：TN249
文献标志码：A
doi：10.37188/CO.2020-0101
1 Introduction
The mid-infrared photonics has attracted considerable attention because its wavebands cover thermal imaging bands, multiple atmospheric windows (3~5 μm and 8~14 μm) necessary for free space communication, as well as main absorption bands of most chemical and biological molecules. It is an inevitable trend for photonic integration to cut costs, improve performance and miniaturize special optical instruments, for example, micro-scale photonic circuits are manufactured in optical materials with a transparent window up to 20 μm. The application of integrated photonics has promoted the rapid development of optical communication technology and the expansion of applied wavelength from near infrared to middle and far infrared. However, the infrared window materials in medium and long wave bands are very limited, mainly including GaAs, GaP, ZnSe, ZnS, InSb, etc.[1-4]. Considering the optical and mechanical properties of these materials, ZnS crystal has become one of the most

AMS2015年全年分类目录

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Haeri · A. Khaloo · M.F. Marji: Fracture analyses of different pre-holed concrete specimens undercompression2015, 31(6): 855S.-Q. Yang · Y.-H. Huang · P.G. Ranjith · Y.-Y. Jiao · J. Ji: Discrete element modeling on the crack evolution behavior of brittle sandstone containing three ﬁ ssures under uniaxial compression2015, 31(6): 871X. Gao · H. Ma: A modiﬁ ed model for concurrent topology optimization of structures and materials2015, 31(6): 890 J. Gao · J.-S. Luo · X.-S. Wu: Receptivity of hypersonic boundary layer due to fast-slow acousticsinteraction2015, 31(6): 899P. Verma · S.K. Arya · R. Gopal: Lumped parameter analytic modeling and behavioral simulation of a 3-DOF MEMS gyro-accelerometer2015, 31(6): 910DYNAMICS, VIBRATION, AND CONTROLY. Bi · Z. Yang · X. Meng · Q. Lu: Noise-induced bistable switching dynamics through a potential energylandscape2015, 31(2): 216L. Chen · W. Jiang: A piezoelectric energy harvester based on internal resonance2015, 31(2): 223J. Xu · Y. Sun: Experimental studies on active control of a dynamic system via a time-delayedabsorber2015, 31(2): 229Y. Liu · A. Fischer · P. Eberhard · B. Wu: A high-order full-discretization method using Hermite interpolationfor periodic time-delayed differential equations2015, 31(3): 406L.K. Abbas · Q. Zhou · H. Hendy · X. Rui: Transfer matrix method for determination of the natural vibration characteristics of elastically coupled launch vehicle boosters2015, 31(4): 570X.-J. Song · B.-Z. Yue · W.-J. Wu: Investigation on attitude disturbance control and vibration suppression for fuel-ﬁ lled ﬂ exible spacecraft2015, 31(4): 581Y.-W. Kim: Effect of partial elastic foundation on free vibration of ﬂ uid-ﬁ lled functionally graded cylindricalshells2015, 31(6): 920BIOMECHANICSX.-G. Wu · W.-L. Yu · H.-P. Cen · Y.-Q. Wang · Y. Guo · W.-Y. Chen: Hierarchical model for strain generalized streaming potential induced by the canalicular ﬂ uid ﬂ ow of an osteon2015, 31(1): 112C.-J. Ji · K. Sugiyama · S. 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Zhang: Numerical analysis of the three-dimensional aerodynamics of a hovering rufous hummingbird (Selasphorus rufus)2015, 31(6): 931Q. Luo · N. Chen · Y.-H. Zhou · Q.-G. Rong: The effect of low ﬂ uoride concentrations on microdamage accumulation in mouse tibias under impact loading2015, 31(6): 944。

论文翻译——超表面理论及应用

超表面理论及应用—超材料的平面化An Overview of the Theory and Applications of Metasurfaces: The Two-Dimensional Equivalents of MetamaterialsChristopher L。

Holloway1, Edward F. Kuester2, Joshua A。

Gordon1, John O'Hara3，Jim Booth1，and David R。

Smith4 三碗译摘要超材料通常由按一定规律排布的散射体或者通孔构成，由此来获得一定的性能指标。

这些期望的特性通常是天然材料所不具备的，比如负折射率和近零折射率等.在过去的十年里，超材料从理论概念走到了市场应用。

3D超材料也可以由二维表面来代替，也就是超表面,它是由很多小散射体或者孔组成的平面结构，在很多应用中，超表面可以达到超材料的效果。

超表面在占据的物理空间上比3D超材料有着优势，由此，超表面可以提供低耗能结构。

文章中将讨论到超表面特性的理论基础和它们不同的应用。

我们也将可以看出超表面和传统的频率选择表面的区别。

在电磁领域超表面有着很广泛的应用（从微波到可见光波段），包括智能控制表面、小型化的谐振腔、新型波导结构、角独立表面、吸收器、生物分子设备、THz调制和灵敏频率调节材料等等。

文中综述了近几年这种材料或者表面的发展，并让我们更加接近一百年前拉姆和Pocklington或者之后的Mandel和Veselago所提出的令人惊讶的观点.引言最近这些年，超材料这方面一直引领着材料的潮流。

超材料是一种新的人工合成材料来得到自然材料所不具备的一些特性。

在电磁背景中，这方面最早的实例就是人工电介质。

之后，我们将会看到和经典结构完全不同的超材料和超表面，比如光子能带隙结构（PBG)、频率选择表面(FSS）.双负指数（DNG)超材料是一种盛行的超材料，也叫作负指数材料(NIM）、左手材料等（LHM）。

同济大学研究生《高等混凝土结构理论》复习要点与教学大纲

这是同济大学《高等混凝土结构理论》期末考试的复习要点，希望对考博选考3007高等混凝土与钢结构这门课的同学有所帮助。

1．Stress-strain curves of concrete under monotonic, repeated and cyclic uniaxial loadings. 单轴受力时混凝土在单调、重复、反复加载时的应力应变曲线。

2．Creep of concrete (linear and nonlinear) 混凝土的徐变（线性、非线性徐变）3．Components of deformation of concrete 混凝土变形的多元组成4．Process of failure of concrete under uniaxial compression 混凝土在单向受压时破坏的过程。

5．Strength indices of concrete and the relations among them 混凝土的强度指标及其之间关系6．Features of stress-strain envelope curve of concrete under repeated compressive loading. 混凝土单向受压重复加载时的应力应变关系的包络线的特征。

7．The crack contact effect of concrete and its representation in stress-strain diagram. 混凝土的裂面效应及其在应力应变关系图上的表示。

8．The multi-level two-phase system of concrete. 混凝土的多层次二相体系。

9．The rheological model of concrete. 混凝土的流变学模型。

10.Influence of stress gradient on strength of concrete. 应力梯度对混凝土强度的影响。

Influence of micro-blasting on the microstructure and residual stresses of CVD κ-Al2O3 coatings

In ﬂuence of micro-blasting on the microstructure and residual stresses of CVD κ-Al 2O 3coatingsC.Barbatti a ,b ,J.Garcia c ,d ,⁎,R.Pitonak e ,H.Pinto a ,A.Kostka a ,A.Di Prinzio f ,M.H.Staia f ,A.R.Pyzalla caMax-Planck-Institut für Eisenforschung GmbH,40237Düsseldorf,GermanybCorus Research,Development and Technology,P.O.Box 10000,1970IJmuiden,The Netherlands cHelmholtz Zentrum Berlin fuer Materialien und Energie GmbH,14109Berlin,Germany dRuhr Universität Bochum,Materials Technology,44780Bochum,Germany eR&D,Boehlerit GmbH &Co.KG,8605Kapfenberg,Austria fSchool of Metallurgy and Materials Science,Universidad Central de Venezuela,P.O.Box 47885,Los Chaguaramos,1041Caracas,Venezuelaa b s t r a c ta r t i c l e i n f o Article history:Received 10February 2009Accepted in revised form 3June 2009Available online 17June 2009Keywords:CVD κ-Al 2O 3Cemented carbides Micro-blasting Residual stressesSynchrotron X-ray diffractionCemented carbides coated with CVD multilayers are commonly used in metal cutting turning and milling operations.For many applications,a micro-blasting ﬁnishing procedure based on an impact treatment of the surfaces is carried out in order to smooth the coated surface and reduce sharp cutting edges.In this work,micro-blasting with corundum in aqueous solution at pressures between 0.05and 0.3MPa was applied to CVD TiN/Ti(C,N)/κ-Al 2O 3multilayer coatings deposited onto cemented carbides in order to investigate its in ﬂuence on the micro-topography,microstructure and residual stresses.The results showed that the micro-blasting reduces the surface roughness and affects the coating thickness.TEM investigations revealed no signi ﬁcant changes on the microstructure of the κ-Al 2O 3top layer.Synchrotron X-ray investigations showed that the residual stress state of the as-deposited κ-Al 2O 3top layer is not affected by the micro-blasting treatment under the conditions investigated.©2009Elsevier B.V.All rights reserved.1.IntroductionCoated cemented carbides are commonly used in the metal cutting industry for machining of iron-base alloys.In order to increase the tool life of cutting inserts,cemented carbides are coated with wear resistant coatings by chemical vapour deposition (CVD)or physical vapour deposition (PVD).Al 2O 3is considered an ideal coating layer in high-speed metal cutting due to its high chemical stability,high hardness and favourable thermal properties at the high temperatures reached during metal cutting [1–3].Due to the mixed ionic and covalent bonding,the material is highly insulating [4,5],thus being usually applied as a top layer to act as a thermal and diffusion barrier.The CVD technique is commonly employed since it is the only deposition method that allows the economical large-scale production of high-quality alumina coatings [6].In addition to the stable α-Al 2O 3,alumina can be obtained in two other metastable modi ﬁcations by CVD,namely κ-Al 2O 3and γ-Al 2O 3[7,8].A typical multilayer combination is that of Ti(C,N)to provide wear resistance,followed by an Al 2O 3top layer,which enhances the thermal resistance of the tool.Due to adhesion problems between the Ti(C,N)and the Al 2O 3coating,the use of an intermediate layer made of Ti(C,N,O)is proposed[9,10].These intermediate layers of Ti-based compounds favour the nucleation of κ-Al 2O 3[11,12].More recently,a novel method for producing an adequate bonding of the Al 2O 3top layer onto the Ti(C,N)by the formation of a nano-transition needle-like phase arrangement has proved to be advantageous [13].This method also leads to the formation of κ-Al 2O 3.Micro-blasting is a ﬁnishing procedure based on an impact treatment of the surfaces.Generally,this procedure is applied to coatings to clean,smooth the surface and reduce sharp cutting edges [14–16].This process involves the use of high pressure and abrasive powders.Besides,there is still the possibility of achieving an attractive side effect,namely,the introduction of bene ﬁcial compressive residual stresses.Previous works showed that micro-blasting of ground and polished hard metal substrates can increase the cutting performance of coated tools mainly due to ﬁlm adhesion enhancement [17–20].Moreover,it has been recently shown that micro-blasting treatment of PVD coatings deposited on hard metal substrates improves its residual stress with regard to fatigue strength and cutting performance of the coated tool [21].In [22,23]it is reported that compressive residual stresses were induced on PVD/CVD multilayers by micro-blasting with pressures between 0.2and 0.6MPa.Holzschuh reports in [24]a method to introduce compressive stresses in CVD multilayers by removing the TiN top layer of a Ti(C,N)/Al 2O 3/TiN multilayer coating by micro-blasting,however,without any mention of the blastingSurface &Coatings Technology 203(2009)3708–3717⁎Corresponding author.Helmholtz Zentrum Berlin fuer Materialien und Energie GmbH,14109Berlin,Germany.Tel.:+492343228229.E-mail address:jose.garcia@helmholtz-berlin.de (J.Garcia).0257-8972/$–see front matter ©2009Elsevier B.V.All rights reserved.doi:10.1016/j.surfcoat.2009.06.021Contents lists available at ScienceDirectSurface &Coatings Technologyj o u r n a l h om e p a g e :w w w.e l s ev i e r.c o m /l o c a t e /s u r fc o a tconditions employed.In[22–24]improvements of tool life of micro-blasted Al2O3coated cutting inserts in metal cutting are presented. The reason for the increment of the tool life is reported to be related to the introduction of compressive residual stresses on the Al2O3top layer.Although not mentioned in their publications,it is to be understood from the results presented that the authors worked with α-Al2O3coatings.Nevertheless,in spite of the many publications,no systematic study on the inﬂuence of micro-blasting pressure on Al2O3coating is found in the literature.In this work,we applied micro-blasting to CVD multilayer TiN/Ti (C,N)/κ-Al2O3coatings.The micro-blasting pressure range varies between0.05and0.3MPa.We aim at investigating systematically the inﬂuence of the blasting pressure on the micro-topography and the possibility of inducing compressive residual stresses on theκ-Al2O3 top layer.The microstructure and residual stress state of theκ-Al2O3top layer were investigated for the as-deposited and micro-blasted conditions by scanning electron microscopy,transmission electron microscopy,synchrotron as well as laboratory source X-ray diffraction and roughness measurements.2.Experimental2.1.Substrate and coatingsThe coatings were deposited onto cemented carbide substrates (90wt.%WC–10wt.%Co)with a size of14mm×14mm×5mm, produced by state-of-the-art powder metallurgy sintering techniques.A TiN/Ti(C,N)/κ-Al2O3multilayer was applied on the hard metal substrate by CVD in a standard hot-wall CVD reactor working at 1015°C and15kPa.The TiN and Ti(C,N)layers were deposited from the gas mixture TiCl4–CH4–N2–H2.The Al2O3layer was deposited on top of the Ti(C,N)layer from the gas mixture AlCl3–ClH2–CO2.Due to the deposition conditions employed,κ-Al2O3was produced as a top coating layer.2.2.Micro-blastingAfter deposition,the coatings were subjected to a micro-blasting treatment performed using an injector-type system in a commercial industrial blasting furnace.Standard industrial parameters were employed.The grit blasting material used was320-mesh(average diameter within~50µm)corundum shots in aqueous solution.The micro-blasting treatment was carried out for30s to ensure full coverage of the surfaces.The pressure was varied within the range from0.05MPa to0.3MPa in steps of0.05MPa.2.3.MicroscopyScanning electron microscopy(SEM)was performed on non-polished surfaces and fractured cross-sections.Specimens for transmission electron microscopy(TEM)analyses were prepared by using a gallium source JEOL JEM-9320focused ion beam(FIB)system operating at30kV.A JEOL2200F TEM/STEM operating at200kV and equipped with an EDX system was used for studying the microstructure of coatings in the as-deposited and micro-blasted state.2.4.RoughnessThe surface roughness(R a and R z)of as-deposited and micro-blasted coatings was determined from atomic force microscopy pictures.Four areas were measured in order to determine an average value.The measurements were carried out in a Nano-scratch tester equipped with an atomic force microscope(CSM Instruments).2.5.Phase and residual stress analysesIn order to assess the phase constitution within the as-deposited and micro-blasted coatings,X-ray diffraction(XRD)diffractograms were obtained using synchrotron radiation at the experimental station G3at DORIS III at HASYLAB at DESY,Hamburg.The radiation energy was 6.9keV(λCo=1.7904A˚´).The beam size was set as 4mm×1mm.The residual stresses within theκ-Al2O3coatings were determined on a laboratory four-circle diffractometer operating with Co–K a radiation and parallel-beam geometry using the sin2ψmethod[25]. Owing to the weak macroscopic texture of theκ-Al2O3coating, unrestricted lattice spacing measurements could be performed for24 sample directions deﬁned by the inclination angleψbetween0°and 89.8°at the azimuthsφ=0°and180°.Considering the stress state in the coatings to be biaxial and of rotational symmetry,the fundamental relationship of X-ray stress analysis can be solved to provide the depth-dependence of the in-plane residual stressesσ//[26]:σ==τeffðÞ=eψτeffðÞ12s21ÀÁð1Þwhereɛψis the measured lattice strain,σ//is the in-plane residual stress,τeff is the information depth,and1/2s2and s1are the phase-speciﬁc diffraction elastic constants(DEC).The concept of effective information depthτeff is usually applied in diffraction studies of thinﬁlms to deﬁne the depth from which the diffraction information comes,since the penetration depthτof the radiation into a certain material may be much larger than theﬁlm thickness.According to its deﬁnitionτeff can be tuned within theﬁlm thickness by changing theψ-angle[27]:τeff=R DzÁe−zτd zRe−zτd z=τ−De−Dτ1−e−Dτð2Þwhereτis the average penetration depth for an inﬁnitely thick sample,which is a function of theψ-tilt,and D is the thickness of theκ-Al2O3layer.In this approach the maximum achievable information depth approaches the limit of half layer thickness(D/2) as the ratio D/τin Eq.(2)decreases towards zero.The lattice strains were measured for the{135}diffraction line of κ-Al2O3.This reﬂection was chosen based on a compromise between the ease for separating this line from neighboring ones,its intensity and the highest possible2θ-angle.The DEC were estimated using the mechanical values of Young's modulus E=361.7GPa and Poisson's ratioν=0.24forκ-Al2O3at room temperature available in[5].The integral breadth of the selected reﬂection was also determined as a function of the micro-blasting conditions.This quantity is related to the density of crystalline defects(dislocations,stacking faults)and small size of crystallites(i.e.domains over which diffraction is coherent)[28].The integral breadth for each condition represents an average on the results obtained at differentψ-angles byﬁtting the {135}diffraction lines using pseudo-Voigt functions.3.Results3.1.Microstructure of the as-deposited coatingsThe as-deposited layer system is shown in Fig.1.The CVD TiN/ TiCN/κ-Al2O3layers show good adhesion to the cemented carbides, hence no pores,brittle phase formation nor spallation between the substrate and the coating are observed.The layer thickness is homogeneous across the coating,the thickness of the TiN is of about 0.2µm,for the intermediate Ti(C,N)layers is about3µm and the thickness of theκ-Al2O3is about4µm±0.05.3709C.Barbatti et al./Surface&Coatings Technology203(2009)3708–3717The alumina layer is composed of columnar grains that grow directly from the nucleation surface (here,the intermediate Ti(C,N)layer).The length of the columnar grains is mostly equivalent to the thickness of the alumina layer.A change in the morphology towards the surface can be observed,with the formation of hexagonal-shaped grains (Fig.1b and c).Some cracks (mainly transgranular)can also be observed.They are typical cracks as a consequence of the different thermal expansion coef ﬁcients between the substrate and the coating and cannot really be avoided in commercial CVD cutting inserts.Several isolated large grains with average diameter larger than 5µmformed as a single crystal or a polycrystalline structure in a random distribution throughout the surface (Fig.2).Their number increases towards the edge of the inserts.Crack initiation seems to be associated with these outgrowths.The average surface roughness R a measured was 0.110±0.008(Table 1).The penetration depth of the X-rays in alumina is about 18µm.Hence,we have full penetration of the radiation into the coating system.The X-ray diffraction (XRD)patterns for the as-deposited sample are shown in Fig.3.The contribution of the substrate is also registered,indicated by the peaks associated with WC re ﬂections.The XRD measurements also reveal that the intermediate layer is composed of Ti (C 0.3N 0.7).The intensity ratio between peaks shows no marked texture in the layers.Although the observation of the κ-→α-Al 2O 3phase transformation already during the deposition process is generally reported in literature [29],there is no evidence for the occurrence of such transformation,since the XRD diffractograms only revealed re ﬂections associated with κ-Al 2O 3.This indicates that the super ﬁcial cracks observed in the as-deposited coatings arise upon cooling due to the differences in thermal coef ﬁcient between the coating and the substrate,and not originating from volume contraction that occurs in phase transformation.Fig.4shows a STEM micrograph of the as-deposited coating.The darkest areas at the bottom correspond to the cemented carbide substrate (WC grains are seen in black).The TiN layer with a thickness of 0.5µm lies adjacent to the substrate.Onto the TiN layer,the Ti(C,N)layer shows a changing grain morphology (Fig.4),making it appear as two distinct structures.The ﬁrst sub-layer consists of columnar grains with a width of about 0.1µm.The following sub-layer has signi ﬁcantly smaller grains with a needle-like morphology and appears randomly oriented.The uppermost layer consists of κ-Al 2O 3(in lighter contrast)and shows grains grown along the CVD deposition direction perpendicular to the substrate.The columnar microstructure istypicalFig.2.SEM image (BSE mode)of κ-Al 2O 3surface topography (top view)after coating.Isolated large Al 2O 3grains (with average size of 5µm)form in a random distribution throughout the surface.Crack initiation seems to be associated with these large grains (see arrows around the large Al 2O 3grain).Table 1Values of R a ,R z and thickness for the κ-Al 2O 3top layer as a function of micro-blasting pressure.Micro-blasting pressure [MPa]R a roughness [µm]R z roughness [µm]Thickness [µm]00.110±0.0080.690±0.04 4.20±0.050.050.096±0.0050.540±0.04 4.20±0.050.10.079±0.0060.480±0.04 4.00±0.050.150.038±0.0040.190±0.03 3.40±0.050.20.045±0.0030.250±0.03 3.00±0.050.250.074±0.0040.440±0.03 2.50±0.050.30.084±0.0040.540±0.042.50±0.05Fig.1.SEM images of (a)fracture cross-section of the coated cemented carbide,(b)top view of the surface topography of as-deposited CVD κ-Al 2O 3coating and (c)higher magni ﬁcation (top view)of the surface topography showing hexagonal-shaped grains.3710 C.Barbatti et al./Surface &Coatings Technology 203(2009)3708–3717for coatings deposited at low gas pressures and low temperatures compared to the melting point temperature [30].Besides the STEM mode,conventional Bragg diffraction contrast TEM was applied to investigate the evidence of defects within the κ-Al 2O 3top layer.A TEM micrograph in bright ﬁeld (BF)mode is shown in Fig.5a.No dislocations but a high concentration of planar defects (twin-related faults)were observed (Fig.5a).All obtained electron diffraction patterns(e.g.Fig.5b)only reveal the presence of the κ-Al 2O 3phase.No evidence of phase transformation was obtained.The two possible variations of alumina (i.e.the metastable κ-Al 2O 3and the stable polymorph α-Al 2O 3)have strikingly different symmetry,which could have been easily distinguished if the latter were present.EDX analysis reveals almost no chemical intermixing,which suggests good separation of the layers.3.2.Microstructure of micro-blasted coatingsMicrographs of surface morphology and fracture cross-section of the samples micro-blasted at pressures in the range 0.05–0.15MPa are presented in Fig.6.Lower micro-blasting pressures,i.e.0.05and 0.1MPa cause no signi ﬁcant changes in grain morphology,although a decrease in the average roughness is measured.At blasting pressures as low as 0.05MPa few isolated areas already appear deformed.As from 0.15MPa,signi ﬁcant loss of coating material begins to occur and the number of cracks increases.Crack propagation typically occurs in a transgranular mode,but seems to be con ﬁned to the near-surface zone of the upper coating.Micro-blasting at 0.2MPa causes a ﬂattening of the grains and ﬂaking of the coating as a consequence of the strong abrasive effect due to micro-blasting (Fig.7).Higher micro-blasting pressures (0.25and 0.3MPa)lead to strong changes in the surfacemicro-topographyFig.3.X-ray diffractogram of the as-deposited κ-Al 2O 3/Ti(C,N)coatings taken at ψ=0°with synchrotron radiation energy of 6.9keV (λCo =1.7904A˚´).The arrow indicates the position of the κ-Al 2O 3(135)re ﬂection used for the residual stressevaluation.Fig. 4.(a)STEM micrograph showing the cross-section microstructure of the as-deposited coating.(b)Higher magni ﬁcation of the top κ-Al 2O 3layer.Fig.5.TEM micrograph in bright ﬁeld (BF)mode showing planar defects within the as-deposited κ-Al 2O 3layer.(b)Selected area diffraction pattern (SADP)corresponding to κ-Al 2O 3.3711C.Barbatti et al./Surface &Coatings Technology 203(2009)3708–3717and an increase in the number and length of the cracks.The microstructure of the Ti(C,N)intermediate layer does not seem affected by the impact of the alumina shots.STEM micrographs of the cross-section microstructure of coatings micro-blasted at 0.1MPa and 0.3MPa are shown in Fig.8.By comparing the microstructure of the micro-blasted samples at different conditions,the only difference corresponds to the signi ﬁcant reduced thickness of the alumina layer micro-blasted at 0.3MPa.The in ﬂuence of micro-blasting pressure on the thickness of the κ-Al 2O 3layer is shown in Table 1.On the other hand,the results clearly show that the micro-blasting does not affect the adherence of the layer.Moreover,the Ti(C,N)is not affected by the mechanical treatment,the reduction in layer thickness being con ﬁned to the top alumina layer.The TEM micrograph in BF mode (Fig.8c)shows the typical planar defects also observed within the alumina layer of the micro-blasted coatings (here we only show the example of the sample micro-blasted at 0.3MPa).The concentration of the twin-related faults observed in samples in all conditions seems to be identical,which directly suggests that the micro-blasting process has no in ﬂuence on the defect density observed in the top κ-Al 2O 3layers.Besides,not a single dislocation was observed in the analyzed micro-blasted top κ-Al 2O 3layers.Micro-blasting leads to a decrease in the roughness of the alumina coating,showing a minimum at blasting pressures between 0.15and 0.2MPa (Table 1).Increasing the blasting pressure above 0.2MPa increases the roughness due to deterioration of the coating layer.ThisFig.6.SEM micrographs showing the changes on the κ-Al 2O 3thickness (fracture cross-sections)and surface topography (top view images)as a function of micro-blasting pressure:(a)and (b)at 0.05MPa;(c)and (d)at 0.1MPa;(e)and (f)at 0.15MPa.3712 C.Barbatti et al./Surface &Coatings Technology 203(2009)3708–3717is related to the extensive loss of the top layer material that occurs with increasing pressures.The removal of top coating material causes an increase in the line intensity of the WC re ﬂections,since more contribution from the substrate is being registered (Fig.9).No changes in the intensity ratio between peaks with increasing micro-blasting pressures are observed.3.3.Residual stress analysesThe sin 2ψcurves of the κ-Al 2O 3layers in the as-deposited and micro-blasted (at 0.1and 0.3MPa)conditions are presented in Fig.10.The obtained d –sin 2ψdistributions are shown to be linear with positive slopes up to sin 2ψ~0.92in all conditions,indicating the presence of average residual stresses of tensile nature within the κ-Al 2O 3layer,which still predominate in the micro-blasted state.On top of the coatings (at large ψangles,thus,at small penetration depths),however,the d ψhkl–sin 2ψdistributions tend to curve downwards,suggesting the presence of near-surface gradients of the in-plane residual stresses in the as-deposited as well as in the micro-blasted conditions.ψ-splittingin the d ψhkl–sin 2ψplots does not occur,indicating the absence of shear stress components in all cases investigated.The in-plane residual stresses averaged over the entire κ-Al 2O 3layer are 355±41MPa,349±45MPa,and 392±39MPa in the as-deposited,0.1and 0.3MPa conditions,respectively (Table 2).Based on the sin 2ψdistributions (Fig.10),the in-depth distribution of the residual stresses in the κ-Al 2O 3coatings was determined using Eq.(1).The stress-depth pro ﬁles for the as-deposited and micro-blasted coatings are similar as presented in Fig.11.In the as-depositedstate,Fig.7.SEM micrographs showing the changes on the κ-Al 2O 3thickness (fracture cross-sections)and surface topography (top view images)as a function of micro-blasting pressure:(a)and (b)at 0.2MPa;(c)and (d)at 0.25MPa;(e)and (f)at 0.3MPa.3713C.Barbatti et al./Surface &Coatings Technology 203(2009)3708–3717the residual stress in the ‘bulk ’of the layer was found to be σ//(τ≈1.5µm)=699MPa,whereas the obtained value at the outer surface decreases down to σ//(τ≈0)=−32MPa.This indicates thatthe stresses become gradually less tensile towards the free surface,eventually turning into low compression at the surface.A similar behaviour is observed for the specimen micro-blasted at 0.1MPa:the tensile residual stress within the coating is slightly lower σ//(τ≈1.5µm)=603MPa,whereas at the surface low compressive residual stresses σ//(τ≈0)=−42MPa are also obtained.For the specimen micro-blasted at 0.3MPa,the stress values are σ//(τ≈1.5µm)=546MPa and σ//(τ≈0)=153MPa within the coating and close to the surface,respectively (Table 2).The analysis of the average integral breadth of the {135}diffraction line of κ-Al 2O 3suggests that the density of lattice imperfections does not signi ﬁcantly increase with increasing micro-blasting pressures.This information corroborates the TEM investigations,which reveal low dislocation densities,even with increasing micro-blasting pressures.4.Discussion4.1.Effect of micro-blasting on microstructure and roughnessOur results indicate that the micro-blasting procedure only affects the κ-Al 2O 3top coating layer.SEM and TEM images show that there are no disturbances in the integrity of the intermediate Ti(C,N)layer.Strong deformation of the coatings appears as a ﬂattening effect on the near-surface zone,mainly at pressures higher than 0.1MPa.ThisFig.8.STEM micrographs showing the cross-section microstructure of coatings micro-blasted at (a)0.1MPa and (b)0.3MPa.(c)TEM micrograph (BF)showing planar defects within the alumina layer of the coating micro-blasted at 0.3MPa.Fig.9.X-ray diffractograms of micro-blasted coatings as a function of micro-blasting pressure showing no change in the intensity ratio between peaks with increasing micro-blasting pressures.3714 C.Barbatti et al./Surface &Coatings Technology 203(2009)3708–3717ﬂattening is produced on the one hand by the overlapping of the several localized deformations caused by the impact of the alumina shots on the surface.On the other hand,the impacts also remove material from the alumina coating,which also results in a smoothing of the protruding irregularities on the surface (Table 1).The lower roughness in the contact zone of the coating decreases the mechanical contact between asperities of the tribological pair tool-workpiece.This leads to a lower friction coef ﬁcient and thus,a contribution for extended tool life of the inserts.4.2.Origin of stresses and defects4.2.1.Stress development upon CVD depositionCVD coatings are known to evolve relevant thermal mismatch residual stresses upon cooling from the high deposition temperatures [31].The strain and stress state in the layers change due to thermal strain introduced by differences in the coef ﬁcients of thermal expansion between the individual layers and the substrate.The maximum thermal stresses induced by cooling (without taking stress relieving processes into account)can be estimated by using the Dietzel equation [32]:σc =E c αc −αs ðÞΔT f g =1−v c ðÞ+1−v s ðÞ=E s ½ d c =d s f gð3Þwhere αis the linear coef ﬁcient of thermal expansion,νis the Poisson ratio,E is the Young's modulus,d is the thickness,c stands for coating and s for substrate.The thermal expansion coef ﬁcient(TEC)Fig.10.The sin 2ψdistributions of the κ-Al 2O 3(135)re ﬂection for φ=0°of the coatings (a)as-deposited,(b)micro-blasted at 0.1MPa and (c)micro-blasted at 0.3MPa.Table 2Values of internal stresses in the κ-Al 2O 3top layer as a function of micro-blasting pressure.Micro-blasting pressure [MPa]Average in-plane residual stresses [MPa]Stress value near the outer surface of κ-Al 2O 3[MPa]Stress value in the “bulk ”of κ-Al 2O 3[MPa]0355±41σ//(τ≈0)=−32σ//(τ≈1.5µm)=6990.1349±45σ//(τ≈0)=−42σ//(τ≈1.5µm)=6030.3392±39σ//(τ≈0)=153σ//(τ≈1.5µm)=546Fig.11.Depth pro ﬁle of the in-plane residual stresses obtained from the evaluation of the sin 2ψdistributions shown in Fig.11for the coatings (a)as-deposited,(b)micro-blasted at 0.1MPa and (c)micro-blasted at 0.3MPa.3715C.Barbatti et al./Surface &Coatings Technology 203(2009)3708–3717ofκ-Al2O3and Ti(C,N)usually lies within8.0–9.0×10−6K−1[33], whereas in the case of WC–Co cemented carbides it is in the range within 4.0–7.0×10−6K−1depending on the composition[34]. Hence,tensile stresses will necessarily develop in theκ-Al2O3coating sinceακ-Al2O3Nαs.Our results clearly show that average tensile stresses develop within theκ-Al2O3layer,indicating that thermal strains represent the major source of residual stresses in the present case.The low compressive stress values towards the surface could be attributed to the relaxation of the tensile residual stresses existent in the‘bulk’of the layer,since the interaction between the substrate and the coatings tends to decrease when approaching the free surface. Besides,the crack propagation,which seems to be conﬁned to the zone closest to the surface,might also play a role in the relaxation mechanism.4.2.2.Stresses and defects induced by micro-blastingThe residual stresses are generally classiﬁed into three types: macro-stresses,micro-stresses,and root mean square(r.m.s.)stresses [25].Macro-stresses often develop during sample manufacturing, extending homogeneously over macroscopic distances,i.e.several grains.In contrast,micro-stresses arise over microscopic volumes, typically grain sizes,due to the mismatches in thermal and mechanical properties of the individual phases or grain orientations. Both cause diffraction line shifts since they are related to average lattice strains of grains with speciﬁc orientations.As discussed in the Section4.2.1,they are of thermal origin in the present case,and are not affected by the applied micro-blasting treatment.The third type of stresses(r.m.s.stresses),which is inhomogeneous within subgrains or crystallites due to the presence of lattice imperfections and vary on the atomic scale,does not induce line shifts but only diffraction line broadening,since any disturbance in the regularity of the crystal lattice is reﬂected in lattice parameter ﬂuctuations.Typical causes for diffraction line broadening are therefore lattice distortions that arise from crystal defects(e.g.dislocations and planar faults),changes in the diffraction coherence length(domain size)and domain-size distribution[28].Based on evidences provided by both TEM and XRD investigations, we conclude that theκ-Al2O3top layer does not undergo plastic deformation during micro-blasting.In particular,TEM imaging indicates practically the absence of dislocations,even at a micro-blasting pressure as high as0.3MPa,which promotes extensive loss of theκ-Al2O3layer and strong changes in layer micro-topography.Planar defects in the form of twin-related faults are the only type of crystalline defects observed and already predominate in the as-deposited state,the density of which is not affected by the micro-blasting process.The crystal structure of the metastableκ-Al2O3is well established. It has an orthorhombic crystal structure(space group Pna21)with lattice parameters a=4.844Å,b=8.330Å,c=8.955Åformed from a pseudo-closed-packed stacking ABAC of oxygen atoms with Al in octahedral and tetrahedral environments in a3:1ratio[35,36]. Supposedly,due to the rather complex crystalline structure,distortion of the lattice occurs differently according to the crystallographic direction leading to twinning as the predominant deformation mechanism inκ-Al2O3phase in contrast toα-Al2O3,in which dislocation is the type of recurrent defects observed.5.ConclusionsMicro-blasting at pressures ranging from0.05up to0.3MPa was applied to CVDκ-Al2O3/Ti(C,N)/TiN multilayer coatings in order to investigate the potentiality of this procedure to control the surface micro-topography and modify the residual stress state of the coating. Our investigations reveal that:1.Theκ-Al2O3growth occurs in columnar direction,perpendicular tothe substrate.Noκ→αphase transformation of the Al2O3isinduced by micro-blasting according to both synchrotron X-ray diffraction and TEM studies.2.The effects of the micro-blasting treatment on the TiN/Ti(C,N)/κ-Al2O3multilayer under the conditions investigated are con-ﬁned to theκ-Al2O3top layer,as revealed by the TEM and STEM investigations.3.Increasing the micro-blasting pressure leads to the formation andpropagation of cracks.SEM and TEM investigations show that crack propagation is conﬁned to the zone closest to the surface.4.Increasing micro-blasting pressure leads to a reduction in roughnessfrom R a:0.110±0.008/R z:0.690±0.04in the as-deposited coatings up to R a:0.038±0.004/R z:0.190±0.03in coatings micro-blasted at0.15MPa,which is mainly associated with the loss of coating material.Blasting pressures above0.2MPa lead to coating degradation.5.TEM investigations showed high density of planar defects in theκ-Al2O3in the form of twin-related faults(Figs.5and8).TEM and XRD investigations reveal that theκ-Al2O3top layer does not undergo plastic deformation during micro-blasting.6.The residual stresses are of tensile nature and thermally induced andare not affected by the applied micro-blasting treatment.The average stress values over theκ-Al2O3layer are355±41MPa,349±45MPa, and392±39MPa in the as-deposited,0.1MPa and0.3MPa conditions.These tensile stresses ease towards the free surface.It can be in general concluded that,under the conditions investigated,the more remarkable effect of the micro-blasting treat-ment on theκ-Al2O3top layer was a reduction of the surface roughness for blasting pressures up to0.15MPa and a strong coating degradation for blasting pressures above0.2MPa.Neither the morphology nor the residual stress state of theκ-Al2O3top layer was affected by the micro-blasting.This is a main difference in the response to the treatment compared with the reported values forα-Al2O3[22,24,26],pointing out that the generation of compressive internal stresses by micro-blasting depends strongly on the crystalline structure of the Al2O3phase.This observation may be supported by previous investigations indicating a higher degree of plasticity ofα-Al2O3[37]compared toκ-Al2O3.On the other hand,the different physical characteristics of the metastable CVD κ-Al2O3compared to the CVDα-Al2O3,such as a smaller grain size,a lower pore density and an epitaxial growth,may also have an inﬂuence on the internal stress conditions after micro-blasting treatment[35]. AcknowledgementsThe authors(J.Garcia and H.Pinto)thank theﬁnancial support of the DFG project444Bra-113/25/0-1to carry out part of this work.Anna di Prinzio thanks ADEMAT Network,Alfa-project Nr.II-0240-B1-AT-RT-CT forﬁnancial support.Dr.A.Rothkirch(Hasylab),Dr.C.Juricic and Mr.P. Brito(MPIE)are kindly acknowledged for their support during the synchrotron X-ray measurements.Thanks to Mr.U.Föckeler(Ruhr Universität Bochum)for atom force microscopy measurements. References[1]F.Bunshah,Handbook of Hard Coatings,Noyes Publications/William AndrewPublishing,LLC,Norwich,New York,USA,2001.[2]P.K.Mehrothra,D.T.Quinto,High Temp.High Press.18(1980)199.[3]B.M.Kramer,N.P.Suh,J.Eng.Ind.102(1980)303.[4]R.H.French,J.Am.Ceram.Soc.73(1990)477.[5]B.Holm,R.Ahuja,Y.Yourdshhyan,B.Johansson,B.I.Lundqvist,Phys.Rev.,B59(1999)12777.[6]S.Ruppi,Int.J.Refract.Met.Hard Mater.23(2005)306.[7]S.Ruppi,rsson,Thin Solid Films388(2001)50.[8]S.Ruppi,rsson,A.Flink,Thin Solid Films516(2008)5959.[9]H.Holzschuh,Patent US6,436,519B2,20.08.2002.[10]H.Halvarsson,S.Vuorinen,Surf.Coat.Technol.56(1993)165.[11]M.Halvarsson,H.Nordén,S.Vuorinen,Surf.Coat.Technol.68–69(1994)266.[12]M.Halvarsson,J.E.Trancik,S.Ruppi,Int.J.Refract.Met.Hard Mater.24(2006)32.[13]R.Pitonak,J.Garcia,R.Weissenbacher,K.Udier,Patent EP1948842,30.07.2008.[14]D.M.Kennedy,J.Vahey,D.Hanney,Mater.Des.26(2005)203.[15]J.Qu,A.J.Shih,R.O.Scattergood,J.Luo,J.Mater.Process.Technol.166(2005)440.3716 C.Barbatti et al./Surface&Coatings Technology203(2009)3708–3717。

微尺度Ni解读

微尺度Ni 悬臂梁的腐蚀和疲劳性能张强1, 2 郭兴蓬1, 21.华中科技大学化学系，武汉430074；2.材料化学与服役失效湖北省重点实验室，武汉430074摘要：采用飞秒激光器制备了纯镍微悬臂梁试样（尺寸为（50μm×50μm×80μm(h ×W×L)），进行了宏试样和微试样的静态腐蚀实验．结果表明，宏试样表面出现明显的局部腐蚀特征，而微试样表面主要表现为全面腐蚀特征．用疲劳测试平台研究了制备的微Ni试样的疲劳性能．结果表明，应力幅和介质中Cl-的含量对试样的疲劳寿命有显著的影响；试样在疲劳断裂前，最大载荷逐渐降低．关键词：悬臂梁；腐蚀疲劳；镍；微系统中图分类号：TG 172.9 文献标识码：ACORROSION AND FATIGUE BEHA VIOR OF MICRO-SIZED NiCANTILEVER BEAMSZHANG Qiang1, 2GUO Xing-peng1, 21.Chemistry Department, Huazhong University of Science and Technology, Wuhan 430074；2.Key Laboratory of Materials Chemistry & Service Failure of Hubei Province, Wuhan 430074 ABSTRACT: The micro-sized Ni cantilever beams with the dimensions of 50μm×50μm×80μm(h×W×L) were fabricated by femtosecond laser processing.Static corrosion tests were carried out on the micro-sized Ni cantilever beams and ordinary-sized Ni plates. The results indicate that the micro-sized specimens exhibit general corrosion behavior on the surface of specimens compared with the localized corrosion behavior on the surface of ordinary-sized plates. The corrosion fatigue properties of micro-sized Ni specimens were studied by using a special fatigue testing machine. The results indicate that the fatigue lives of micro-sized specimens were significantly influenced by load amplitudes and Cl- contents in corrosive solution, and 定稿日期：作者简介：张强(1976-)，男，博士研究生；武汉：华中科技大学化学系(430074)E-mail: whzhang0077@163com基金项目：国家自然科学基金资助项目（50671040）the maximum bending loads of micro-sized Ni specimens decreased gradually prior to final fractureKEY WORDS: cantilever beam; corrosion fatigue; nickel; micro-system 微系统组件尺度被认为是微米级的，其机械性能往往不同于大尺度试样[1]．生物医学微系统中的运动组件易受到循环应力和腐蚀介质的影响，为保证微系统长时间工作的稳定性，有必要研究微系统材料在微尺度下的疲劳性能．近年来，随着微加工技术的发展，用于微系统的材料范围不断得到拓展，镍及其合金因具有良好的机械性能而广泛用于微系统，微尺度镍的机械性能得到了广泛的研究[2]．Ivars Gutmanis 在2002年美国陆军腐蚀高级研讨会上指出，微系统中存在着污染物腐蚀、缝隙腐蚀、腐蚀疲劳、电偶腐蚀及点蚀等各种腐蚀形态[3].但相关的研究工作国内尚没有报告，国外亦少有发表.微系统的腐蚀行为有别于宏观大器件的腐蚀行为，也不同于宏系统中的微区腐蚀.因此，研究微系统的腐蚀及与宏系统的差异性，不仅对微系统的发展和应用具有重要意义，也是腐蚀科学自身发展的要求.本文采用微动实验台研究由飞秒激光器加工的镍微悬臂梁试样（50μm×50μm×80μm(h×W×L)）的疲劳性能,比较微试样与宏试样的静态腐蚀行为的差异性，探讨难以产生大阴极小阳极和酸化自催化条件的微尺度Ni悬臂梁试样腐蚀和疲劳的本征机制，并研究腐蚀介质中Cl- 浓度及载荷幅的变化对微试样疲劳寿命的影响.1 实验方法1.1 Ni 微悬臂梁试样的制备用飞秒激光器将50 µm 厚的Ni(纯度99.95%)薄膜，加工成尺寸为50μm×50μm×80μm(h×W×L)的悬臂梁，形状和尺寸见图1.Fig.1 (a) Notched cantilever-beam-type micro-sized specimens prepared byfemtosecond laser processing, (b) schematic of the cantilever beam geometry used in the investigation.加载位置距固定端60 μm，切口距离固定端20 μm，深度为11 μm，宽度为3 μm.试样的固定端用307胶密封固定于尺寸为（10mm×10mm×6mm(B×W×L)）PETF基底上，悬臂梁外露并伸出于基体.试样和基底全浸在3.0% NaCl 溶液中.溶液由于表面张力的作用不能到达微切口内部，因此将试样和溶液放入抽滤瓶抽真空，用CCD观察，直到溶液充满切口区.1.2 疲劳实验台腐蚀疲劳实验在特制的仪器上进行，如图2所示．微动工作台可以提供X,Y 方向最大220μm位移，Z方向最大位移为160μm，位移分辨率为0.1μm，最大响应频率100 Hz．不锈钢杆一端与三维微动平台相连，另一端与金刚石测针连接，测针尖端最小直径10μm．测针附近的CCD系统对试样的空间位置和疲劳实验动态监测．微力传感器用于测量试样受到的力，分辨率为10-5 N．信号发生器可提供正弦，方波及三角波等信号，输出频率0～3MHz．Fig. 2 Block diagram of the fatigue testing machine for micro-sized specimens used in this investigation.1.3 静态弯曲和疲劳实验疲劳实验前，先用无切口试样进行静态弯曲实验，以确定腐蚀疲劳外加载荷大小.为减小探针对试样表面的影响，探针尖端尽量磨钝.用微动平台调节测针空间位置，加载位置距离固定端60μm，调整加载速率使试样形变速率为0.3μm/s，记录微力传感器的读数.疲劳实验中最大载荷控制在0.2到0.7 P B，P B为微试样最大静态弯曲强度.每组5个试样，在不同时间停止实验来获得各实验阶段裂纹起始和生长速率的数据.在空气中加载频率为10 Hz ，在3.0% NaCl 溶液中加载频率为2 Hz . 试样在腐蚀疲劳实验中全浸在同条件的3.0% NaCl 溶液中.溶液的温度为室温，pH 值为7.0±0.3，每12h 补充一次去离子水.溶液表面与实验室空气相通，以确保有充足气体扩散到试样表面.信号发生器将正弦信号传输至微动平台，微动台带动测针振动实现对试样循环加载. 图3为载荷和位移与时间的关系曲线，可见，载荷为75 mN 时，试样产生的位移是26.2 µm .用微力传感器随时测量最大载荷数值，疲劳实验后，用SEM 观察试样表面形貌.010l o a d /m N time/s 010010d i s p l a c e m e n t /m i c r o n time/sFig. 3 Typical load (a) and displacement (b) versus time curves during fatigue test.1.4 静态腐蚀实验为比较宏试样（0.05mm ×20mm ×20mm(h ×W ×L )）和微试样（50μm ×50μm ×80μm(h ×W ×L)）静态腐蚀特征异同，将两种试样各4组进行静态腐蚀，腐蚀时间为1d 、10d 、20d 和30d .溶液温度为室温.将两种试样全浸在3.0%NaCl 溶液中，隔12h 补充一次去离子水.用SEM 观察静态腐蚀后两种试样表面. 2 结果与讨论2.1 静态腐蚀图5a 为10d 静态腐蚀后宏试样的表面腐蚀形貌，可见，宏试样表面出现了明显的晶间腐蚀和点蚀.宏试样在循环应力和腐蚀介质的作用下，易在这种晶间腐蚀处形成裂纹源，随着裂纹的扩展，腐蚀介质进入裂纹导致二次点蚀. 在循环应力的作用下，产生的主裂纹转变成穿晶腐蚀疲劳裂纹，最终导致材料失效[4].图5b 为10d 静态腐蚀后微试样的表面腐蚀形貌，可见，微试样表面没有明显的晶间腐蚀和点蚀特征，表现为均匀腐蚀特征，清除腐蚀产物膜后，也没有明显的局部腐蚀痕迹. 当试样小到电解质扩散层厚度以及接近材料晶粒大小尺度时，腐蚀行为从一个近似面反应过程转变为一个体反应过程，难以形成大阴极小阳极和酸化自催化条件；同时，由于试样表面积很小，若微试样与宏试样的亚稳态点蚀发生几率相同，依宏试样的腐蚀规律，微试样难于产生缝隙腐蚀和点蚀[5].(a)(b)Fig.5 (a) Pits and intergranular corrosion on the surface of the ordinary-sized specimens exposed to 3.0% NaCl solution for 10 days, (b) Typical appearance of unnotched micro-sized specimen after 10d pre-corrosion in 3.0% NaCl solution.2.2 载荷幅和介质中Cl-含量对疲劳寿命的影响微尺度Ni悬臂梁试样的腐蚀疲劳实验正弦加载的平均载荷为67.08 mN，加载频率为2 Hz.图6为载荷幅不同时微尺度试样的疲劳寿命，可见，随着载荷幅增加，试样的腐蚀疲劳寿命降低.01010loadamplitude/mNnumber of cycles, N (×104)Fig. 6 Fatigue life plot of the Ni micro-sized specimens tested in 3.0% NaCl solution at room temperature.图6中箭头表示试样经过106次循环加载仍然没有疲劳，相应的载荷幅被称为临界载荷幅，本实验测得的临界载荷幅约为15 mN . 实际上，在腐蚀环境中，试样的S-N 曲线永远不会达到水平，因此，不存在严格意义上的腐蚀疲劳临界载荷幅.临界载荷幅和平均载荷对微系统结构的设计具有重要意义，由于宏尺度Ni 的腐蚀疲劳方面数据缺乏，难以实现二者比较.疲劳实验的循环加载参数如：应力比、加载波形、应力强度因子及腐蚀环境中Cl -浓度对腐蚀疲劳会产生较大影响[6]. 图7为腐蚀介质中Cl -含量不同时Ni 微悬臂试样腐蚀疲劳寿命的变化，可见，3组试样的腐蚀介质NaCl 的质量浓度分别为1%、2% 和 3%时，试样的平均腐蚀疲劳寿命分别为 1.2×105, 8.1×104,6.4×104 次循环.当NaCl 的含量小于3wt%时，随着Cl -浓度的增加，试样的平均疲劳寿命明显降低. Cl -浓度增加，会加速材料表面裂纹的起始和扩展过程. 实验中加载的应力幅为75mN ，应力比R =0.3，加载频率均为2 Hz .10010Cl - content /mol/L n u m b e r o f s y c l i c s , N (×10 5)Fig. 7 Effect of Cl -content on corrosion fatigue lifetime of micro-sized Ni cantilever beams with a 3 μm width notch tested at room temperature.2.3 Ni 微尺度试样的腐蚀疲劳性能图8为腐蚀疲劳断裂后微Ni 悬臂梁试样和断口形貌，可见，试样断裂首先发生在切口处，试样固定端出现明显的局部腐蚀特征；疲劳断面上有明显的点蚀坑，没有发现明显的腐蚀疲劳长裂纹．金属在3.0% NaCl 溶液中腐蚀疲劳机理被认为受阳极溶解控制[7]，这个机理同样适用于本实验的微尺度试样．纯镍具有良好的耐蚀性能，但在循环应力和腐蚀介质共同作用下，具有最大弯曲应力的切口区及较大弯曲应力的固定端，均产生了明显的局部腐蚀．在循环加载作用下，微小裂纹处会产生比Ni 的强度极限更大的弯曲拉应力，而导致点蚀区材料的塑性变形．持续的塑性变形导致了金属表面活性点的增加和已有活性区活性程度的增大，进而加速了裂纹尖端材料的溶解过程．因此，微系统表面的微小缺陷和粗糙度在其加工过程中应备受重视[8]．Fig. 8 (a) Scanning electron micrograph of the notched specimen after fatigue failure, (b) Fatigue fracture surfaces of micro-sized Ni cantilever beam with 3 μm breadth notch tested in 3.0% NaCl solution at room temperature.循环应力增加了试样切口底部材料的电化学活性，促使局部腐蚀向深度方向发展．另外，微尺度试样面体比较大，表面原子在力作用下，易产生缓慢移动[9]，从而使点蚀沿水平方向扩展．微试样表面点蚀体积增大不利于应力的集中，同时加速了局部腐蚀区与外界的物质交换，不易导致酸化自催化的发生．微尺度Ni 试样有较高的抵抗裂纹的能力，这使得在其表面难以形成裂纹源[10]．这是微尺度金属薄膜材料具有较长疲劳寿命的主要原因．图9为微尺度Ni悬臂梁试样在腐蚀疲劳实验中最大载荷随时间的变化曲线，可见，在断裂前最大载荷的数值不断降低，预腐蚀时间增加，最大载荷下降越显著．最大载荷数值不断降低说明疲劳实验中Ni微尺度材料在循环应力和腐蚀介质的作用下产生了不可恢复的蠕变变形．Ni在较低温度下产生蠕变变形已有相关报道[11]．微尺度材料的疲劳和蠕变等性能的研究可以为微系统的设计和加工提供重要的依据．010010m a x i m u m l o a d /m N time/hFig. 9 Maximum load relaxation of micro-sized Ni cantilever beams with different pre-corrosion durations at room temperature.3 结论(1) 静态腐蚀20后，宏试样表面有明显的局部腐蚀特征，微试样表面则表现为均匀腐蚀特征．(2)增加应力幅，疲劳寿命降低；当介质中NaCl 的质量浓度小于3.0%时，Cl -的含量增加，试样的疲劳寿命降低．(3)腐蚀疲劳断裂首先发生在试样的切口区，断面有明显的局部腐蚀特征．疲劳过程中最大弯曲载荷不断降低，说明微尺度Ni 在常温下容易产生蠕变变形．参考文献：[1] C W Beak, Y K Kim, Y Ahn, et al ．Measurement of the mechanical properties ofelectroplated gold thin films using micromachined beam structures[J].SensActuators A, 2005, 117(1): 17.[2] T Du, A vijayakumar, K B Sundaram, et al .Chemical mechanical polishing ofNickel for application in MEMS devices[J].Microelectron Eng, 2004, 75 :234.[3] I.Gutmanis .Corrosion affects on microelectromechanical systems(MEMS) [A]. Army corrosion summit ,Petersburg ,FL ,USA ,March, 2002, pp :6.[4] J Xie, A T Alpas, D Northwood .The role of heat treatment on theerosion-corrosion behavior of AISI 52100 steel[J]. Mater Character, 2002, 48:273.[5] V N Myunga, D Y Parkb, B Y Yoob, et al.Development of electroplatedmagnetic materials for MEMS[J].J Magnetism Magnetic Mater, 2003, 265: 189.[6] K Genel, M Demirkol, T Gulmez.Corrosion fatigue behavior of ion nitridedAISI 4140 steel[J]. Mater Sci Eng A , 2000, 288:93.[7] Z Wang, J Li, J Wang.The influence of loading waveform on corrosion fatiguecrack propagation[J].Corros Sci,1995, 37(10):1552.[8] X Li, B Bhushan, K Takashima.Mechanical characterization of micro/nanoscale structures for MEMS/NEMS applications using nanoindentation techniques[J]. Ultramicroscopy,2003,97:485.[9] W Merlijn, V Spengen.MEMS reliability from a failure mechanismsperspective[J]. Microelectronics Reliability,2003,43 :1052.[10] X Li, B Bhushan.A review of nanoindentation continuous stiffnessmeasurement technique and its applications[J]. Mater Character,2002, 48:11.[11] N Wang, Z Wang, K T Aust, et al.Room temperature creep behavior ofnanocrystalline nickel produced by an electroplating technique[J].Mater Sci Eng, 1997, 237:156.。

光学中光滑的英文

光学中光滑的英文Title: The Optical Phenomenon of Surface SmoothnessLight, a fundamental aspect of our physical world, has fascinated scientists and philosophers for centuries. One of the intriguing phenomena associated with light is the concept of surface smoothness and its optical implications. In the realm of optics, the smoothness of a surface plays a crucial role in the behavior of light as it interacts with various materials and surfaces.At the most basic level, the smoothness of a surface can be described as the absence of significant irregularities or deviations from a perfectly flat or uniform surface. When light encounters a smooth surface, it interacts with the surface in a predictable manner, exhibiting specific optical properties that are distinct from those observed when light interacts with a rough or uneven surface.One of the primary consequences of surface smoothness in optics is the phenomenon of specular reflection. Specular reflection occurs when light is reflected off a smooth surface in a manner where the angle of reflection is equal to the angle of incidence. This type of reflection is often observed in everyday life, such as the reflection of lightoff a mirror or a still body of water. The smoothness of the surface is a critical factor in determining the quality and clarity of the reflected image, as any irregularities or imperfections on the surface can distort or scatter the reflected light.In contrast, when light encounters a rough or uneven surface, the reflection of light is diffuse, meaning that the light is scattered in multiple directions rather than being reflected in a single, predictable direction. This diffuse reflection is responsible for the appearance of many everyday objects, such as matte painted surfaces or rough-texturedmaterials, where the light is scattered in a more random and unpredictable manner.The smoothness of a surface can also influence the refractive properties of light as it passes through the material. Refraction is the bending of light as it transitions from one medium to another, such as from air to glass or water. When light passes through a smooth surface, the refraction is consistent and predictable, allowing for the precise control and manipulation of light beams. This property is essential in the design and manufacture of optical components, such as lenses and prisms, where the smooth surfaces are crucial for achieving desired optical outcomes.Furthermore, the smoothness of a surface can also impact the transmission of light through the material. In the case of transparent materials, such as glass or certain plastics, the smoothness of the surfaces can minimize the scatteringand absorption of light, allowing for efficient transmission and the preservation of image quality. This is particularly important in the design of optical devices, such as camera lenses, where the quality of the transmitted light is crucial for capturing high-resolution images.The importance of surface smoothness extends beyond the realm of optics and has significant implications in various scientific and technological fields. In the field of materials science, the smoothness of a surface can influence the adhesive properties, friction, and wear characteristics of a material. Smooth surfaces can exhibit reduced friction and improved resistance to wear, making them valuable in applications such as mechanical engineering, tribology, and surface coatings.In the semiconductor industry, the smoothness of surfaces is critical for the fabrication of high-performanceelectronic devices. The manufacturing of integrated circuitsand microchips requires the creation of extremely smooth surfaces, often at the nanoscale level, to ensure the accurate deposition of thin films and the precise patterning of features. Any irregularities or roughness on the surface can lead to defects and performance issues in the final devices.Moreover, the smoothness of surfaces plays a crucial role in the development of advanced materials and technologies, such as in the field of nanotechnology. The ability to engineer and control surface smoothness at the nanoscalelevel has opened up new possibilities for the creation of novel materials with unique optical, electronic, and mechanical properties. These materials find applications in areas like quantum computing, energy storage, and medical diagnostics.In conclusion, the optical phenomenon of surface smoothness is a multifaceted and profoundly important aspectof the study of light and its interactions with various materials. The smooth or rough nature of a surface can significantly impact the behavior of light, influencing phenomena such as reflection, refraction, and transmission. The understanding and optimization of surface smoothness have far-reaching implications in a wide range of scientific and technological fields, from optics and materials science to semiconductor fabrication and nanotechnology. As our understanding of the optical properties of smooth surfaces continues to evolve, the potential for innovativeapplications and groundbreaking discoveries in these fields remains vast and exciting.。

femfat 4.8资料

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FEMFAT 4.7
BASIC Theory Mareviations
IFK2 IFK3 f1,af f2,af ftot,af fGS,af fTI,af fTP,af fm,af fm,sf fm,cf fGR,af fGR,sf fGR,cf fST,af fDF,af fSR,af fSP,af fRO,af fCH,af fNI,af fCN,af fIH,af fFH,af KC KM Ncf,M Ncf,C σUTS σy Slope exponent of the incipient fracture S/N curve Material group-dependent exponent Combined factor for surface roughness and degree of forging influencing the endurance stress limit Combined factor for the technological treatment of surfaces influencing the endurance stress limit Overall factor influencing the endurance stress limit General surface factor influencing the endurance stress limit Temperature-dependent factor influencing the endurance stress limit Technological parameter influencing the endurance stress limit Mean stress factor influencing the endurance stress limit Mean stress factor influencing the slope Mean stress factor influencing the endurance cycle limit Stress gradient factor influencing the endurance stress limit Stress gradient factor influencing the slope Stress gradient factor influencing the endurance cycle limit Statistical factor influencing the endurance stress limit Factor of the degree of forging (can be defined by user) influencing the endurance stress limit Surface roughness factor influencing the endurance stress limit Shot peening factor influencing the endurance stress limit Rolling factor influencing the endurance stress limit Carburizing factor influencing the endurance stress limit Nitriding factor influencing the endurance stress limit Carbonitriding factor influencing the endurance stress limit Induction hardening factor influencing the endurance stress limit Flame hardening factor influencing the endurance stress limit Slope of the local component S/N curve Slope of the material S/N curve Endurance cycle limit of the material S/N curve Endurance cycle limit of the local component S/N curve Ultimate tensile stress 0.002 strain offset yield strength of the material

华新电阻规格书

Functional code X : Thick film low ohm M : Metal low ohm N : Metal low ohm, high power W : Thick film low TCR P : Thick film low TCR high power ( 2512 size=2 watt, 2010 size=1 watt, 1210 size=0.5 watt, 1206 size=0.5 watt,
R002
Tolerance F : +/- 1% J : +/- 5% P : Jumper
Packaging code P : 4” reel taping T : 7” reel taping A : 7” reel taping 15Kpcs Q : 10” reel taping G : 13” reel taping R : 0603 2mm pitch taping B : Bulk K : Bulkcase
Termination code L = Sn base (Lead free) 5 3E SSP (total)
WW
25
M
F
T
L
Type code WW: R< 1ohm MW: R< 1ohm Automotive SW: R< 1ohm Anti-sulfuration
Size code 25 : 2512 (6432) 20 : 2010 (5025) 18 : 1218 (3248) 12 : 1206 (3216) 10 : 1210 (3225) 08 : 0805 (2012) 06 : 0603 (1608) 04 : 0402 (1005)

土木工程专业毕业设计外文文献及翻译

英文原文：Rehabilitation of rectangular simply supported RC beams with shear deficiencies using CFRP compositesAhmed Khalifa a,＊, Antonio Nanni ba Department of Structural Engineering，University of Alexandria，Alexandria 21544，Egyptb Department of Civil Engineering，University of Missouri at Rolla，Rolla，MO 65409，USAReceived 28 April 1999；received in revised form 30 October 2001；accepted 10 January 2002AbstractThe present study examines the shear performance and modes of failure of rectangular simply supported reinforced concrete(RC) beams designed with shear deficiencies。

These members were strengthened with externally bonded carbon fiber reinforced polymer （CFRP）sheets and evaluated in the laboratory. The experimental program consisted of twelve full—scale RC beams tested to fail in shear. The variables investigated within this program included steel stirrups, and the shear span-to—effective depth ratio, as well as amount and distribution of CFRP。

微结构几何参数对铝合金表面结冰性能的影响

表面技术第51卷第1期 ·272· SURFACE TECHNOLOGY 2022年1月收稿日期：2021-04-09；修订日期：2021-05-31 Received ：2021-04-09；Revised ：2021-05-31基金项目：国家自然科学基金联合基金项目（U19A20103）；吉林省科技发展计划项目（20190101005JH ，20180101324）Fund ：National Natural Science Foundation of China Joint Fund Project (U19A20103); Jilin Province Science and Technology Development Plan Project (20190101005JH, 20180101324) 作者简介：弯艳玲（1979—），女，博士，副教授，主要研究方向为微纳制造、功能表面。

Biography ：WAN Yan-ling (1979—), Female, Doctor, Associate professor, Research focus: micro-nano manufacturing, functional surface. 引文格式：弯艳玲, 严灿东, 王博, 等. 微结构几何参数对铝合金表面结冰性能的影响[J]. 表面技术, 2022, 51(1): 272-279.WAN Yan-ling, YAN Can-dong, WANG Bo, et al. The Influence of Microstructure Geometric Parameters on the Icing Properties of Aluminum 微结构几何参数对铝合金表面结冰性能的影响弯艳玲，严灿东，王博，于化东（长春理工大学跨尺度微纳制造教育部重点实验室，长春 130000）摘要：目的制备具有稳定性的抗结冰表面，并探讨表面微结构几何参数对表面结冰性能的影响。

现浇预应力混凝土空心板国外文献

查新点：1、研究了现浇混凝土空心板正交各向异性，确定了不同直径、不同间距圆孔形成的现浇混凝土空心板的正交异性板参数。

2、研究出现浇混凝土空心正交各向异性板等效为各向同性板的计算方法。

3、研究出现浇混凝土空心板横孔方向肋部与翼缘双控抗剪承载力计算方法。

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谢谢！查新点1-2：下面的文献如果相关的话，请标明与哪个查新点相关（注明查1、查2即可）2/7/1 (Item 1 from file: 2) DIALOG(R)File 2:INSPEC (c) 2010 The IET. All rts. reserv. 02717754Title: Equilibrium equations of multilayer hollow shells and platesAuthor(s): Rasskazov, A.O.1; Sokolovskaya, I.I.1; Shul'ga, N.A.1Affiliation(s): 1 Kiev Automobile & Highway Inst., Kiev, Ukrainian SSR, USSR Journal: Prikladnaya Mekhanika , vol.16 , no.5 , pp.45-50Country of Publication: Ukrainian SSR, USSRPublication Date: May 1980ISSN: 0032-8243ISSN Type: printCODEN: PKMKALTranslation Journal: Soviet Applied Mechanics, vol.16, no.5, pp.395-9Publication Date of Translation Journal: May 1980Country of Publication of Translation Journal: USACODEN of Translation Journal: SOAMBTISSN of Translation Journal: 0038-5298ISSN Type of Translation Journal: printLanguage: EnglishDocument Type: Journal Paper Translation Abstracted (JP)Treatment: Theoretical or Mathematical (T)Abstract: Equilibrium equations were derived for multilayer hollow shells with orthotropic layers. Transforming this system by introducing stress functions not only simplifies the formulation and solution of the defined class of problems, but also allows the general features of the stress-strain state in hollow shells and plates to be discerned in certain cases. ( 9 refs.)（无关）2/7/2 (Item 1 from file: 8) DIALOG(R)File 8:Ei Compendex(R) (c) 2010 Elsevier Eng. Info. Inc. All rts. reserv.0014732508 E.I. COMPENDEX No: 2001095487415Study on the application of large aluminum hollow extrusion profiles to ship structures Seo, Seung Il; Son, Kon Ho; Park, Jae HongCorresp. Author/Affil: Seo, Seung Il: Hanjin Heavy Industries Co Ltd, Seoul, Korea, Republic ofJournal of Ship Production ( J Ship Prod ) 1999 15/3 (179-190)Publication Date: 19991201Publisher: Soc of Naval Architects & Marine EngineersCODEN: JSPRE ISSN: 8756-1417Document Type: Article; Journal Record Type: AbstractTreatment: T; (Theoretical)Language: English Summary Language: EnglishNumber of References: 7Aluminum is much useful material for high speed light crafts due to high strength and light weight. Large aluminum hollow extrusion profiles have another merits such as easy production of complicated shapes, reduction of welding and cutting lines, easy fabrication, high quality and labor cost-down. In this paper, a design method for aluminum hollow extrusion profiles was developed. Detailed finite element analysis was carried out to comprehend the structural behaviors of the hollow extrusion profiles subjected to normal pressure and compression. Simple formulas were proposed to analyze structural characteristics of the hollow extrusion profiles based on orthotropic plate theory and plate buckling theory. By comparison with the detailed analysis results, it was shown that simple formulas have good accuracy and efficiency. For practical application of the proposed simple formulas, optimization for reduction of weight under strength and production constraints was carried out and useful results were obtained.（无关）2/7/3 (Item 2 from file: 8) DIALOG(R)File 8:Ei Compendex(R) (c) 2010 Elsevier Eng. Info. Inc. All rts. reserv.0014244095 E.I. COMPENDEX No: 1999014449829Determination of connection strength between longitudinal plates and RHS columns Cao, J.J.; Packer, J.A.; Kosteski, N.Corresp. Author/Affil: Cao, J.J.: Univ of Toronto, Toronto, CanadaConference Title: Proceedings of the 1998 2nd World Conference on Steel in Construction Conference Location: San Sebastian, PR, USA Conference Date: 19980511-19980513 E.I. Conference No.: 49223Journal of Constructional Steel Research ( J Constr Steel Res ) 1998 , 134 46/1-3 (243-244)Publication Date: 19981201Publisher: Elsevier Sci LtdCODEN: JCSRD ISSN: 0143-974XItem Identifier (DOI): 10.1016/S0143-974X(98)80025-4Document Type: Article; Journal Record Type: AbstractTreatment: T; (Theoretical)Language: English Summary Language: EnglishThe strength of welded connections between longitudinally-oriented plates and rectangular hollow section (RHS) members is investigated. A yield line analysis model is developed for general application to RHS connections. In this model, the connecting face of the main member is considered to be orthotropic, not isotropic, and included the influence of the compression load applied to the main member. The thickness of the RHS wall and the size of the weld between the two members is also taken into account for the locations of yield lines on the connecting face. Based on the yield analysis, a method that computes the yield strength of longitudinal plate to RHS connection is developed. （无关）2/7/4 (Item 3 from file: 8) DIALOG(R)File 8:Ei Compendex(R) (c) 2010 Elsevier Eng. Info. Inc. All rts. reserv.0012874924 E.I. COMPENDEX No: 1992060513505Determination of the thermal stress state of orthotropic laminated plates Pankratova, N.D.; Mukoed, A.A.Corresp. Author/Affil: Pankratova, N.D.: Ukrainian Acad of Sciences, Kiev, Ukraine Soviet applied mechanics ( Sov Appl Mech ) 1992 27/8 (770-775) （查新点1）Publication Date: 19920101CODEN: SOAMB ISSN: 0038-5298Document Type: Article; Journal Record Type: AbstractTreatment: T; (Theoretical); X; (Experimental)Language: English Summary Language: EnglishNumber of References: 7Thermal stresses in laminated plates were examined the obtained results show that it is convenient to determine jointly the temperature fields and stresses and displacements for the heterogeneous anisotropic plates. The results can be used to evaluate the suitability of applied models of calculating thermal stresses.2/7/5 (Item 4 from file: 8) DIALOG(R)File 8:Ei Compendex(R) (c) 2010 Elsevier Eng. Info. Inc. All rts. reserv.0010728017 E.I. COMPENDEX No: 1979070008334APPLICATION OF A SIMPLIFIED METHOD OF CALCULATING LONGITUDINAL MOMENTS TO THE ONTARIO HIGHWAY BRIDGE DESIGN CODE.Bakht, Baidar; Cheung, M.S.; Aziz, T.S.Corresp. Author/Affil: Bakht, BaidarCanadian Journal of Civil Engineering ( Can J Civ Eng ) 1979 6/1 (36-50)Publication Date: 19790101CODEN: CJCEB ISSN: 0315-1468Document Type: Journal Record Type: AbstractLanguage: Unspecified Summary Language: EnglishNumber of References: 22A manual method for calculating the design live load longitudinal moments in superstructures of most right bridges is presented. The bridge types that can be analyzed by this method are: slab bridges, beam and slab bridges incorporating both steel and concrete beams, bridges incorporating wooden beams, and slabs on hollow trapezoidal or other such torsionally stiff beams. The proposed method was developed by orthotropic plate theory, and was checked by the grillage analogy method. The basis of the method and details of development methodology are presented. The effect of the various parameters on transverse distribution of longitudinal moments is discussed. (无关)2/7/6 (Item 5 from file: 8) DIALOG(R)File 8:Ei Compendex(R) (c) 2010 Elsevier Eng. Info. Inc. All rts. reserv.0010184399 E.I. COMPENDEX No: 1973040001018Dismantable Elevated Steel Roadway in Belgrad.AnonStahlbau Rundschau ( Stahlbau Randsch ) 1972 -/39 (10-12)Publication Date: 19721201ISSN: 0561-7855Document Type: Journal Record Type: AbstractLanguage: German Summary Language: EnglishThe temporary elevated roadway crosses a two-lane highway in a 200 m long 120-m radius arc of 5. 5% longitudinal and 2% transverse inclination. It consists of 10. 5 m long, 3. 5 m wide prefabricated single-panel T-shaped girders, an orthotropic floor plate with 12 mm thick deck plate stiffened with longitudinal hollow ribs and cross beams, and two main plate girders. Four such elements and a wedge piece are assembled into 22. 3 m long, 7 m wide bridge girders supported on welded portal frames. The deck surface is covered with an adhesive two-layered tar-epoxy resin coat and a 5 cm thick mastic asphalt. （无关）2/7/7 (Item 6 from file: 8) DIALOG(R)File 8:Ei Compendex(R) (c) 2010 Elsevier Eng. Info. Inc. All rts. reserv.0010097296 E.I. COMPENDEX No: 1972010001979Hollow reinforced concrete slabs supported along four edges, (Vierseitig gelagerte Stahlbetonhohlplatten)ASTER HCorresp. Author/Affil: ASTER HDeut Ausschuss Stahlbeton 1970 -/213 (i-ix plus 109p)Publication Date: 19701201Document Type: Journal Record Type: AbstractLanguage: German Summary Language: EnglishNumber of References: 19A reinforced concrete slab with parallel cylindrical hollows extending over the whole span is treated as an orthogonal anisotropic plate. The torsional rigidity of such slab may be estimated as a product of concrete's elasticity modulus and square root of the product of inertia moments along x and y axes. This approximation leads to the value of the deformation coefficient kappa equal to unity. As a result, all tables for isotropic plates with kappa equals unity may be used in designing orthotropic hollow slabs, provided that the different flexural rigidities are considered by introducingthe concept of a distorted plate. Parallel to the cylindrical hollows, the flexural rigidity is calculated on the whole section, and in the normal direction, on the sections of the continuous concrete cover above and below the hollows only. The design of the hollow slab follows the rules of reinforced concrete design. Normal to the cylindrical openings additional checks of secondary stresses, resulting from the system behaving as Vierendeel truss, are necessary in certain sections for both sides of the plate and for the webs between the hollows. （查新点1）2/7/8 (Item 7 from file: 8) DIALOG(R)File 8:Ei Compendex(R) (c) 2010 Elsevier Eng. Info. Inc. All rts. reserv.06019177 E.I. COMPENDEX No: 19570000759Buckling problem of rectangular orthotropic plates with hollow sectionsPflueger, A.Zeitschrift fuer Flugwissenschaften v 5 n 6 June 1957 ( Duesseldorf Germany), p 178-181 Publication Year: 1957Document Type: JA; (Journal Article)Language: GermanStudy of plates under compression, with anisotropy generated by panel of constant thickness carrying series of stiffeners of closed hollow section; torsional rigidity thus generated has considerable influence on value of buckling stress; pertinence to stiffening of rectangular sheets in aircraft wings or fuselage. （查新点1）2/7/9 (Item 1 from file: 34) DIALOG(R)File 34:SciSearch(R) Cited Ref Sci (c) 2010 The Thomson Corp. All rts. reserv.21145894 Genuine Article#: 657CO Number of References: 31Title: Generalized thermoelastic waves in functionally graded plates without energy dissipationAuthor: Yu JG (REPRINT) ; Zhang XM; Xue TLAuthor Email Address: yu@Corporate Source: Henan Polytech Univ,Sch Mech & Power Engn,Jiaozuo 454003//Peoples R China/ (REPRINT); Henan Polytech Univ,Sch Mech & Power Engn,Jiaozuo 454003//Peoples R China/Journal: COMPOSITE STRUCTURES , 2010 , V 93 , N1 ( DEC ) , P 32-39ISSN: 0263-8223 Publication Date: 20101200Digital Object Identifier: 10.1016/pstruct.2010.06.020Publisher: ELSEVIER SCI LTD , THE BOULEVARD, LANGFORD LANE, KIDLINGTON, OXFORD OX5 1GB, OXON, ENGLANDFunding: The work is supported by the National Natural Science Foundation of China (No. 10802027) and by the high-performance grid computing platform of Henan Polytechnic University. The authors also wish to express their sincere thanks to the reviewers for their careful comments.Funding Organization -- Grant Number:National Natural Science Foundation of China -- 10802027Henan Polytechnic UniversityLanguage: English Document Type: ARTICLEAbstract: In this paper, a dynamic solution of the propagating thermoelastic waves in functionally graded material (FGM) plate subjected to stress-free, isothermal boundary conditions is presented in the context of the Green-Naghdi (GN) generalized thermoelastic theory. The FGM plate is composed of two orthotropic materials. The materials properties are assumed to vary in the direction of the thickness according to a known variation law. The coupled wave equation and heat conduction equation aresolved by the Legendre orthogonal polynomial series expansion approach. The convergency of the method is discussed through a numerical example. The dispersion curves of the inhomogeneous thermoelastic plate and the corresponding pure elastic plate are compared to show the characteristics of thermal modes and the influence of the thermoelasticity on elastic modes. The displacement, temperature and stress distributions of elastic modes and thermal modes are shown to discuss their differences. A plate with a different gradient variation is calculated to illustrate the influence of the gradient field on the wave characteristics. (C) 2010 Elsevier Ltd. All rights reserved. （查新点1）2/7/10 (Item 2 from file: 34) DIALOG(R)File 34:SciSearch(R) Cited Ref Sci (c) 2010 The Thomson Corp. All rts. reserv.20843744 Genuine Article#: 621IA Number of References: 38Title: Three-dimensional analysis of thermal stresses in four-parameter continuous grading fiber reinforced cylindrical panelsAuthor: Aragh BS (REPRINT) ; Yas MHAuthor Email Address: behnamsobhani@Corporate Source: Razi Univ,Dept Mech Engn,Kermanshah 6734667149//Iran/ (REPRINT); Razi Univ,Dept Mech Engn,Kermanshah 6734667149//Iran/Journal: INTERNATIONAL JOURNAL OF MECHANICAL SCIENCES , 2010 , V 52 , N8 ( AUG ) , P 1047-1063ISSN: 0020-7403 Publication Date: 20100800Digital Object Identifier: 10.1016/j.ijmecsci.2010.04.006Publisher: PERGAMON-ELSEVIER SCIENCE LTD , THE BOULEVARD, LANGFORD LANE, KIDLINGTON, OXFORD OX5 1GB, ENGLANDLanguage: English Document Type: ARTICLEAbstract: In this paper, three-dimensional analysis of thermal stresses infour-parameter continuous grading fiber reinforced cylindrical panel subjected to thermal load is studied. The cylindrical panel is assumed to be made of an allotropic material. The continuous grading fiber reinforced panel has a smooth variation in matrix volume fraction in the radial direction. A generalization of the power-law distribution presented in literature is proposed. Symmetric and asymmetric volume fraction profiles are presented in this paper. Suitable temperature and displacement functions that identically satisfy the boundary conditions at the simply supported edges are used to reduce the thermoelastic equilibrium equations to a set of coupled ordinary differential equations with variable coefficients, which can be solved by generalized differential quadrature method. The fast rate of convergence of the method is demonstrated and to validate the results, comparisons are made with the available solutions for orthotropic shells. The main contribution of this work is to illustrate the influence of the power-law exponent, of the power-law distribution choice and of the choice of the four parameters on the thermal behaviour of continuous grading fiber reinforced cylindrical panels. (C) 2010 Elsevier Ltd. All rights reserved. （无关）2/7/11 (Item 3 from file: 34) DIALOG(R)File 34:SciSearch(R) Cited Ref Sci (c) 2010 The Thomson Corp. All rts. reserv.16773229 Genuine Article#: 202CF Number of References: 25Title: Vibration and buckling of cross-ply laminated composite circular cylindrical shells according to a global higher-order theoryAuthor: Matsunaga H (REPRINT)Corporate Source: Setsunan Univ,Dept Architecture,17-8 Ikeda Nakamachi/Osaka 5728508//Japan/ (REPRINT); Setsunan Univ,Dept Architecture,Osaka 5728508//Japan/ Journal: INTERNATIONAL JOURNAL OF MECHANICAL SCIENCES , 2007 , V 49 , N9 ( SEP ) , P 1060-1075ISSN: 0020-7403 Publication Date: 20070900Publisher: PERGAMON-ELSEVIER SCIENCE LTD , THE BOULEVARD, LANGFORD LANE, KIDLINGTON, OXFORD OX5 1GB, ENGLANDLanguage: English Document Type: ARTICLEAbstract: Natural frequencies and buckling stresses of cross-ply laminated composite circular cylindrical shells are analyzed by taking into account the effects of higher-order deformations such as transverse shear and normal deformations, and rotatory inertia. By using the method of power series expansion of displacement components, a set of fundamental dynamic equations of a two-dimensional higher-order theory for laminated composite circular cylindrical shells made of elastic and orthotropic materials is derived through Hamilton's principle. Several sets of truncated approximatehigher-order theories are applied to solve the vibration and buckling problems of laminated composite circular cylindrical shells subjected to axial stresses. The total number of unknowns does not depend on the number of layers in any multilayered shells. In order to assure the accuracy of the present theory, convergence properties of the first natural frequency and corresponding buckling stress for the fundamental mode r = s = 1 are examined in detail. The internal and external works are calculated and compared to prove the numerical accuracy of solutions. Modal transverse shear and normal stresses can be calculated by integrating the three-dimensional equations of equilibrium in the thickness direction, and satisfying the continuity conditions at the interface between layers and stress boundary conditions at the external surfaces. It is noticed that the present global higher-order approximate theories can predict accurately the natural frequencies and buckling stresses of simply supported laminated composite circular cylindrical shells within small number of unknowns. (c) 2006 Elsevier Ltd. All rights reserved. （无关）2/7/12 (Item 4 from file: 34) DIALOG(R)File 34:SciSearch(R) Cited Ref Sci (c) 2010 The Thomson Corp. All rts. reserv.15766467 Genuine Article#: 104SB Number of References: 56Title: Free-edge and ply cracking effect in cross-ply laminated composites under uniform extension and thermal loadingAuthor: Zhang DX; Ye JQ (REPRINT) ; Sheng HYCorporate Source: Univ Leeds,Sch Civil Engn,Leeds LS2 9JT/W Yorkshire/England/ (REPRINT); Univ Leeds,Sch Civil Engn,Leeds LS2 9JT/W Yorkshire/England/; Hefei Univ Technol,Inst Civil Engn,Hefei 230009//Peoples R China/Journal: COMPOSITE STRUCTURES , 2006 , V 76 , N4 ( DEC ) , P 314-325ISSN: 0263-8223 Publication Date: 20061200Publisher: ELSEVIER SCI LTD , THE BOULEVARD, LANGFORD LANE, KIDLINGTON, OXFORD OX5 1GB, OXON, ENGLANDLanguage: English Document Type: ARTICLEAbstract: The interlaminar stresses and displacements near the free-edges and ply cracks are investigated by using the state space equation method for general cross-ply laminates subjected to extension and/or thermal loading. By this approach, a laminated plate may be composed of an arbitrary number of orthotropic layers, each of which may have different material properties and thickness. The method takes into account all independent material constants and guarantees continuous fields of all interlaminar stresses across interfaces between material layers. Numerical solutions are compared with results obtained from other methods. It is found that the theory provides a satisfactory approximation to the stress singularity occurring in the vicinity of the free-edges and ply cracks. (c) 2005 Elsevier Ltd. All rights reserved. （无关）2/7/13 (Item 5 from file: 34) DIALOG(R)File 34:SciSearch(R) Cited Ref Sci (c) 2010 The Thomson Corp. All rts. reserv.14366704 Genuine Article#: 963PW Number of References: 14Title: Transient thermal stresses of orthotropic functionally graded thick strip due to nonuniform heat supplyAuthor: Ootao Y (REPRINT) ; Tanigawa YAuthor Email Address: ootao@me.osakafu-u.ac.jpCorporate Source: Univ Osaka Prefecture,Grad Sch Engn, Dept Mech Engn,1-1 Gakuen Cho/Sakai/Osaka 5998531/Japan/ (REPRINT); Univ Osaka Prefecture,Grad Sch Engn, Dept Mech Engn,Sakai/Osaka 5998531/Japan/Journal: STRUCTURAL ENGINEERING AND MECHANICS , 2005 , V 20 , N5 ( JUL 30 ) , P 559-573 ISSN: 1225-4568 Publication Date: 20050730Publisher: TECHNO-PRESS , PO BOX 33, YUSEONG, DAEJEON 305-600, SOUTH KOREA Language: English Document Type: ARTICLEAbstract: This paper is concerned with the theoretical treatment of transient thermal stresses involving an orthotropic functionally graded thick strip due to nonuniform heat supply in the width direction. The thermal and thermoelastic constants of the strip are assumed to possess orthotropy and vary exponentially in the thickness direction. The transient two-dimensional temperature is analyzed by the methods of Laplace and finite sine transformations. We obtain the exact solution for the simply supported strip under the state of plane strain. Some numerical results for the temperature change, the displacement and the stress distributions are shown in figures. Furthermore, the influence of the orthotropy and nonhomogeneity of the material is investigated. （无关）2/7/14 (Item 1 from file: 35) DIALOG(R)File 35:Dissertation Abs Online (c) 2010 ProQuest Info&Learning. All rts. reserv.01372009 ORDER NO: AAD94-25253PREDICTIVE AND DIAGNOSTIC ANALYSIS OF REINFORCED CONCRETE MASONRY BUILDINGS Author: KURKCHUBASCHE, ALBERT GEORGDegree: PH.D.Year: 1994Corporate Source/Institution: UNIVERSITY OF CALIFORNIA, SAN DIEGO ( 0033 )Chair: FRIEDER SEIBLESource: Volume 5504B of Dissertations Abstracts International.PAGE 1558 . 308 PAGESAs a tool for the derivation of rational design guidelines for reinforced concrete masonry (RCM) buildings in seismic zones, an analytical model has been developed under the U.S.-TCCMAR (Technical Coordinating Committee for Masonry Research) program to predict and diagnose the behavior of RCM structures under monotonic increasing lateral loads. The phenomenological model is based on the finite element method and can trace the nonlinear load-deformation response of RCM structures from the initial undamaged state through the critical limit states when cracking, yielding, and crushing commence. In order to minimize the computational requirements for the nonlinear analysis of complete three-dimensional structures, the wall and floor elements, arranged in the principal Cartesian coordinates, are connected only by translational compatibility requirements, while out-of-plane bending of the walls is ignored.The masonry walls are discretized by plane stress elements. To improve the bending behavior of the four-node plane stress element a quadratic displacement field has been added. The concrete floors are discretized by layered flat shell elements. Refinements to the slab element include prestressing and the representation of the orthotropic, voided cross-section of the topped precast, prestressed, hollow-core floor system. The biaxial constitutive relationships for concrete and concrete masonry are based on an equivalent uniaxial stress-strain laws for reinforced concrete, and a smeared and rotating crack model. The reinforcement is treated as an overlaid element, with displacement compatibility at the element nodes. In the structural walls, reinforcement may be treated as either smeared or discrete.The developed finite element model was validated and calibrated by direct comparison with numerous experimental results from full-scale structural component and subassembly tests. The validated model was applied to predict and diagnose the response of the U.S.-TCCMAR five-story RCM research building tested under simulated seismic loads at the University of California, San Diego. Comparisons of the model with experimental results show that the accuracy of the model is satisfactory, and that the model can be used as a predictive and a diagnostic research tool to investigate the dominant nonlinear response phenomena in RCM structural systems. （无关）2/7/15 (Item 1 from file: 63) DIALOG(R)File 63:Transport Res(TRIS) (c) fmt only 2010 Dialog. All rts. reserv.00606683 DATITLE: ALUMINIUM EXTRUSION BRIDGE REHABILITATION SYSTEM. BRIDGE MANAGEMENT. INSPECTION, MAINTENANCE, ASSESSMENT AND REPAIR. PAPERS PRESENTED AT THE FIRST INTERNATIONAL CONFERENCE ON BRIDGE MANAGEMENT, UNIVERSITY OF SURREY, GUILDFORD, MARCH 28-30, 1990 Author: Svensson, L; Pettersson, LCorporate Source: Elsevier Applied Science Publishers Limited, Crown House, Linton Road, Barking, Essex IG11 8JU, England Pag: pp 777-783Publication Date: 19900000 Publication Year: 1990Language: English Subfile: HRIS IRRD (H 9101 I) ISBN: 1-85166-456-4Data Source: Transport and Road Research LaboratoryAbstract: The deterioration of road bridges is becoming a serious problem in Sweden. An increasing number of bridge decks are in such poor condition that they must be replaced. This is due mainly to a severe climate, the use of road salt in winter time, and increasing traffic volume and loads. In certain cases major reinforcement of bridge foundations or replacement of bridges has been called for to guarantee safety, often at great cost.A system is described for replacing damaged bridge decks. The system utilises an orthotropic plate that consists of hollow aluminium extrusions fitted together by tongue and groove. Major reduction of dead loads is achieved which allows increased trafficloads without reinforcing foundations or the structural system.(A) For the covering abstract of the conference see IRRD 830553. （无关）2/7/16 (Item 1 from file: 118) DIALOG(R)File 118:ICONDA-Intl Construction (c) 2010 Fraunhofer-IRB. All rts. reserv.0962300 ICONDA Accession Number: 1986(08):1002454 ICONDATables of curves for the determination of the buckling load of orthotropic plates with hollow stiffenersPflueger A (Editor) ; Stern J (Author)Series Title: Mitteilungen des Instituts fuer Statik der Universitaet Hannover; 1 ISSN: 0073-030011 p, figsPublisher: in-house publishing , Hannover Publication Date: 19590000Language: GermanDocument Type: Mongraph which is not commercially available; Irregular serial Medium Type: Print on PaperLocation Mark: DEIRB 2386Cross Reference: RSWB 1983(05):9700071File Segment: DEIRB (无关)2/7/17 (Item 2 from file: 118) DIALOG(R)File 118:ICONDA-Intl Construction (c) 2010 Fraunhofer-IRB. All rts. reserv.0934250 ICONDA Accession Number: 1989(06):1001381 ICONDABeispiele aus dem StrassenbrueckenbauExamples from road bridge constructionSahmel P (Author)Series Title: DVS-Berichte; 86 ISSN: 9414-2149p.6-9 , figs.,refsPublisher: Dt.Verlag f.Schweisstechnik , Duesseldorf Publication Date: 19830000 Language: GermanDocument Type: Book or monograph which is commercially published; Irregular serial Medium Type: Print on PaperLocation Mark: DEIRB 27SahCross Reference: RSWB 1985(11):9030679File Segment: DEIRB (无关)2/7/18 (Item 3 from file: 118) DIALOG(R)File 118:ICONDA-Intl Construction (c) 2010 Fraunhofer-IRB. All rts. reserv.0823094 ICONDA Accession Number: 1987(01):1000180 ICONDAFly-over in the middle of Fulda. The first railway bridge with trapezoidal longitudinal stiffenersWagner Peter (Author)Stahlbauv.54, no.1 p.1-8 , figs.,refsCountry Of Publication: GermanyISSN: 0038-9145 Publication Date: 19850000Language: German Summary Language: EnglishDocument Type: Journal articleMedium Type: Print on PaperLocation Mark: DEIRB Z 62aCross Reference: RSWB 1985(03):9960028File Segment: DEIRB (无关)2/7/19 (Item 4 from file: 118) DIALOG(R)File 118:ICONDA-Intl Construction (c) 2010 Fraunhofer-IRB. All rts. reserv.0822519 ICONDA Accession Number: 1986(07):1032447 ICONDAAnalysis of box-girder bridges by grillage and orthotropic plate methodsCheung M.S (Author) ; Bakht Baidar (Author) ; Jaeger Leslie G (Author)Canadian journal of civil engineering v.9, no.4 p.595-601 , figs.,refsCountry Of Publication: Canada。

激光专业英语

2011年技术物理学院08级（激光方向）专业英语翻译重点！！！作者：邵晨宇Electromagnetic电磁的principle原则principal主要的macroscopic宏观的microscopic微观的differential微分vector矢量scalar标量permittivity介电常数photons光子oscillation振动density of states态密度dimensionality维数transverse wave横波dipole moment偶极矩diode 二极管mono-chromatic单色temporal时间的spatial空间的velocity速度wave packet波包be perpendicular to线垂直be nomal to线面垂直isotropic各向同性的anistropic各向异性的vacuum真空assumption假设semiconductor半导体nonmagnetic非磁性的considerable大量的ultraviolet紫外的diamagnetic抗磁的paramagnetic顺磁的antiparamagnetic反铁磁的ferro-magnetic铁磁的negligible可忽略的conductivity电导率intrinsic本征的inequality不等式infrared红外的weakly doped弱掺杂heavily doped重掺杂a second derivative in time对时间二阶导数vanish消失tensor张量refractive index折射率crucial主要的quantum mechanics 量子力学transition probability跃迁几率delve研究infinite无限的relevant相关的thermodynamic equilibrium热力学平衡（动态热平衡）fermions费米子bosons波色子potential barrier势垒standing wave驻波travelling wave行波degeneracy简并converge收敛diverge发散phonons声子singularity奇点（奇异值）vector potential向量式partical-wave dualism波粒二象性homogeneous均匀的elliptic椭圆的reasonable公平的合理的reflector反射器characteristic特性prerequisite必要条件quadratic二次的predominantly最重要的gaussian beams高斯光束azimuth方位角evolve推到spot size光斑尺寸radius of curvature曲率半径convention管理hyperbole双曲线hyperboloid双曲面radii半径asymptote渐近线apex顶点rigorous精确地manifestation体现表明wave diffraction波衍射aperture孔径complex beam radius复光束半径lenslike medium类透镜介质be adjacent to与之相邻confocal beam共焦光束a unity determinant单位行列式waveguide波导illustration说明induction归纳symmetric 对称的steady-state稳态be consistent with与之一致solid curves实线dashed curves虚线be identical to相同eigenvalue本征值noteworthy关注的counteract抵消reinforce加强the modal dispersion模式色散the group velocity dispersion群速度色散channel波段repetition rate重复率overlap重叠intuition直觉material dispersion材料色散information capacity信息量feed into 注入derive from由之产生semi-intuitive半直觉intermode mixing模式混合pulse duration脉宽mechanism原理dissipate损耗designate by命名为to a large extent在很大程度上etalon 标准具archetype圆形interferometer干涉计be attributed to归因于roundtrip一个往返infinite geometric progression无穷几何级数conservation of energy能量守恒free spectral range自由光谱区reflection coefficient（fraction of the intensity reflected）反射系数transmission coefficient（fraction of the intensity transmitted）透射系数optical resonator光学谐振腔unity 归一optical spectrum analyzer光谱分析grequency separations频率间隔scanning interferometer扫描干涉仪sweep移动replica复制品ambiguity不确定simultaneous同步的longitudinal laser mode纵模denominator分母finesse精细度the limiting resolution极限分辨率the width of a transmission bandpass透射带宽collimated beam线性光束noncollimated beam非线性光束transient condition瞬态情况spherical mirror 球面镜locus（loci）轨迹exponential factor指数因子radian弧度configuration不举intercept截断back and forth反复spatical mode空间模式algebra代数in practice在实际中symmetrical对称的a symmetrical conforal resonator对称共焦谐振腔criteria准则concentric同心的biperiodic lens sequence双周期透镜组序列stable solution稳态解equivalent lens等效透镜verge 边缘self-consistent自洽reference plane参考平面off-axis离轴shaded area阴影区clear area空白区perturbation扰动evolution渐变decay减弱unimodual matrix单位矩阵discrepancy相位差longitudinal mode index纵模指数resonance共振quantum electronics量子电子学phenomenon现象exploit利用spontaneous emission自发辐射initial初始的thermodynamic热力学inphase同相位的population inversion粒子数反转transparent透明的threshold阈值predominate over占主导地位的monochromaticity单色性spatical and temporal coherence时空相干性by virtue of利用directionality方向性superposition叠加pump rate泵浦速率shunt分流corona breakdown电晕击穿audacity畅通无阻versatile用途广泛的photoelectric effect光电效应quantum detector 量子探测器quantum efficiency量子效率vacuum photodiode真空光电二极管photoelectric work function光电功函数cathode阴极anode阳极formidable苛刻的恶光的irrespective无关的impinge撞击in turn依次capacitance电容photomultiplier光电信增管photoconductor光敏电阻junction photodiode结型光电二极管avalanche photodiode雪崩二极管shot noise 散粒噪声thermal noise热噪声1.In this chapter we consider Maxwell’s equations and what they reveal about the propagation of light in vacuum and in matter. We introduce the concept of photons and present their density of states.Since the density of states is a rather important property，not only for photons，we approach this quantity in a rather general way. We will use the density of states later also for other(quasi-) particles including systems of reduced dimensionality.In addition,we introduce the occupation probability of these states for various groups of particles.在本章中，我们讨论麦克斯韦方程和他们显示的有关光在真空中传播的问题。

医用镁合金微弧氧化

第52卷第12期表面技术2023年12月SURFACE TECHNOLOGY·315·医用镁合金微弧氧化/有机复合涂层的研究现状及演进方向冀盛亚a，常成b，常帅兵c，倪艳荣a，李承斌a（河南工学院 a.电缆工程学院 b.车辆与交通工程学院c.电气工程与自动化学院，河南新乡 453003）摘要：医用镁及镁合金过快的降解速率严重缩短了其有效服役时间，过高的析氢速率引发局部炎症，束缚了其临床应用前景。

微弧氧化（MAO）/有机复合涂层良好的抑蚀降析性能，在医用镁及镁合金表面改性领域展现出巨大的应用潜力。

首先，从有机材料（植酸（PA）、壳聚糖（CS）、硬脂酸（SA）、多巴胺（DA）、聚乳酸-乙醇酸共聚物（PLGA）、聚乳酸（PLA）、聚已内酯（PCL））自身的组织及性能特征入手，分析了单一有机涂层提高镁及镁合金耐蚀性的作用机理，并指出单一涂层自身的性能弱点（单一MAO涂层微孔和裂纹的不可避免，单一有机涂层与镁合金结合强度低，易于剥落）限制了对镁合金降解保护效能。

其次，从结合强度、耐蚀性、多功能性（生物安全性、生物相容性、诱导再生性、抑菌抗菌性、载药缓释性等）的角度，详细阐述了各MAO/有机复合涂层的结构特点、优势特征。

在此基础上，明确指出以MAO/PCL （MAO/CS）复合涂层为基底涂层，通过PCL（CS）涂层与其他涂层的交叉组合，是实现医用镁合金植入材料的生物活性及多功能性的最佳路径。

最后，对镁合金MAO/有机复合涂层的演进方向进行了科学展望。

关键词：镁合金；微弧氧化；有机材料；复合涂层；演进方向中图分类号：TG174.4 文献标识码：A 文章编号：1001-3660(2023)12-0315-20DOI：10.16490/ki.issn.1001-3660.2023.12.026Research Status and Evolution Direction of Micro-arc Oxidation/Organic Composite Coating on Medical Magnesium Alloy SurfaceJI Sheng-ya a, CHANG Cheng b, CHANG Shuai-bing c, NI Yan-rong a, LI Cheng-bin a(a. School of Cable Engineering, b. School of Vehicle and Traffic Engineering, c. School of Electrical Engineering andAutomation, Henan Institute of Technology, Henan Xinxiang 453003, China)ABSTRACT: Good biosafety, biocompatibility and valuable self-degradation properties endow medical magnesium and magnesium alloys with great potential to replace inert implant materials in the field of traditional clinical applications.The excessive degradation rate of magnesium alloy, however, leads to its premature loss of structural integrity and mechanical support, being unable to complete the effective service time necessary for tissue healing of the implant site. At the same time, it is also its excessive degradation rate that leads to the intensification of hydrogen evolution reaction of收稿日期：2023-02-01；修订日期：2023-05-14Received：2023-02-01；Revised：2023-05-14基金项目：河南省科技攻关项目（222102310337，222102240104，232102241029）；博士科研资金（9001/KQ1846）Fund：Henan Province Science and Technology Research Project (222102310337, 222102240104, 232102241029); Doctoral Research Funding (9001/KQ1846)引文格式：冀盛亚, 常成, 常帅兵, 等. 医用镁合金微弧氧化/有机复合涂层的研究现状及演进方向[J]. 表面技术, 2023, 52(12): 315-334.JI Sheng-ya, CHANG Cheng, CHANG Shuai-bing, et al. Research Status and Evolution Direction of Micro-arc Oxidation/Organic Composite·316·表面技术 2023年12月magnesium alloy. Because it cannot be absorbed by the human body in a short time, the excessive H2 will easily gather around the implant or form a subcutaneous airbag, which will not only cause the inflammation of the implant site, but also hinder the adhesion and growth of cells in the implant, limiting its clinical application prospects. Surface modification technology can effectively delay the degradation rate of medical magnesium and magnesium alloys, and reduce the rate of hydrogen evolution.Firstly, starting from the structure and performance characteristics of organic materials (phytic acid (PA), chitosan (CS), stearic acid (SA), dopamine (DA), polylactic acid glycolic acid copolymer (PLGA), polylactic acid (PLA), and polycaprolactone (PCL)), the mechanism of improving the corrosion resistance of magnesium and magnesium alloys by a single organic coating was analyzed, and the performance weaknesses of a single coating were also pointed out: ①Micro arc oxidation (MAO) is an anodic oxidation process that generates a highly adhesive ceramic oxide coating on the surface of an alloy immersed in an electrolyte through high voltage (up to 300 V) spark discharge. The continuous high voltage discharge and the bubbles generated by the reaction bring about the inevitable occurrence of a large number of volcanic micropores and cracks in the coating. The diversity of discharge modes also gives rise to the unpredictable morphology of micropores and cracks. Therefore, the preparation of a single MAO coating on different alloy surfaces does not only require proper adjustment of MAO electrical parameters (current density, voltage, duty cycle, frequency, oxidation time) and the coupling effect of its electrolyte system to decrease (small) the pores and cracks on the MAO coating surface, but also increases the sealing process at the later stage. ② A single organic coating has a low bonding strength with magnesium alloy, being easy to flake off. These performance weaknesses limit the protection effect of a single coating on magnesium alloy degradation.Secondly, from the perspectives of bonding strength, corrosion resistance, and versatility (biosafety, biocompatibility, induced regeneration, antibacterial and antibacterial properties, drug loading and sustained-release properties, and so on), the structural characteristics and advantages of each MAO/organic composite coating were elaborated in detail. It has revealed that MAO/organic composite coating has an enormous application potentiality in the field of surface modification of medical magnesium and magnesium alloys, thanks to its good corrosion inhibition and degradation performance. On this basis, it is clearly pointed out that, in order to achieve the biological activity and versatility of medical magnesium alloy implant materials, the best way is to adopt the MAO/PCL (MAO/CS) composite coating as the base coating and make the cross combination of PCL (CS) coating and other coatings. Finally, the evolution direction of magnesium alloy MAO/organic composite coating is scientifically predicted.KEY WORDS: magnesium alloy; micro-arc oxidation; organic materials; composite coating; evolution direction作为人体所必须的营养元素，镁不但辅助600多种酶的合成(包括参与、维护DNA和RNA聚合酶的正确结构和活性)，而且改善胰岛素稳定和糖类正常代谢、舒张血管、降低冠心病、高血压及糖尿病的患病风险[1]。

气科院大气物理面试英语专业词汇[1]

大气科学系微机应用基础Primer of microcomputer applicationFORTRAN77程序设计FORTRAN77 Program Design大气科学概论An Introduction to Atmospheric Science大气探测学基础Atmospheric Sounding流体力学Fluid Dynamics天气学Synoptic Meteorology天气分析预报实验Forecast and Synoptic analysis生产实习Daily weather forecasting现代气候学基础An introduction to modern climatology卫星气象学Satellite meteorologyC语言程序设计 C Programming大气探测实验Experiment on Atmospheric Detective Technique云雾物理学Physics of Clouds and fogs动力气象学Dynamic Meteorology计算方法Calculation Method诊断分析Diagnostic Analysis中尺度气象学Meso-Microscale Synoptic Meteorology边界层气象学Boundary Layer Meteorology雷达气象学Radar Meteorology数值天气预报Numerical Weather Prediction气象统计预报Meteorological Statical Prediction大气科学中的数学方法Mathematical Methods in Atmospheric Sciences专题讲座Seminar专业英语English for Meteorological Field of Study计算机图形基础Basic of computer graphics气象业务自动化Automatic Weather Service空气污染预测与防治Prediction and Control for Air Pollution现代大气探测Advanced Atmospheric Sounding数字电子技术基础Basic of Digital Electronic Techniqul大气遥感Remote Sensing of Atmosphere模拟电子技术基础Analog Electron Technical Base大气化学Atmospheric Chemistry航空气象学Areameteorology计算机程序设计Computer Program Design数值预报模式与数值模拟Numerical Model and Numerical Simulation接口技术在大气科学中的应用Technology of Interface in Atmosphere Sciences Application海洋气象学Oceanic Meteorology现代实时天气预报技术（MICAPS系统）Advanced Short-range Weather Forecasting Technique(MICAPS system)1) atmospheric precipitation大气降水2) atmosphere science大气科学3) atmosphere大气1.The monitoring and study of atmosphere characteristics in near space as an environment forspace weapon equipments and system have been regarded more important for battle support.随着临近空间飞行器的不断发展和运用,作为武器装备和系统环境的临近空间大气特性成为作战保障的重要条件。

微弧氧化时间对TA15合金陶瓷膜表面形貌和性能的影响

MATERIALS REPORTS2019,Vol.33,微弧氧化时间对TA15合金陶瓷膜表面形貌和性能的影响王先,于思荣，赵严"，张鹏，刘恩洋，熊伟中国石油大学（华东）材料科学与工程学院，青岛266580以NaAlO2、NaF、KOH为电解液对TA15钛合金进行不同时间的微弧氧化处理，在其表面制备一层致密的陶瓷膜，以提高TA15钛合金的表面硬度和耐蚀性。

对不同氧化时间下陶瓷膜的表面形貌、成分、物相组成进行表征分析，并对不同氧化时间下陶瓷膜的显微硬度、表面粗糙度及耐蚀性进行对比研究。

结果表明，微弧氧化陶瓷膜表面布满细小的蜂窝状微纳米级孔洞，随氧化时间延长，陶瓷膜表面逐渐平整化，时间过长会出现凸起、凹坑等缺陷，导致陶瓷膜粗糙度增大。

陶瓷膜所含元素主要为O、Ti、AI等，物相组成主要为金红石型TiO2、AI2O3及Al2Ti3相。

随氧化时间的延长，陶瓷膜表面显微硬度逐渐增大,50min时可达332.82HV,比基体提高了59.2%。

粗糙度呈先下降后上升的趋势,40min时陶瓷膜平整光滑，孔洞分布均匀，粗糙度最小（1.420滋m）,膜厚约10um。

耐蚀性呈先上升后下降趋势,40min时陶瓷膜的自腐蚀电位为+222.24mV,比基体提高了约530 mV,腐蚀电流密度为1.73x10-9A/cm2，降低为基体的3%,耐蚀性最佳。

关键词TA15钛合金微弧氧化技术（MAO）氧化时间表面形貌耐蚀性中图分类号:TB31文献标识码:AThe Influence of Micro-arc Oxidation Time on the Surface Morphology and Properties of Ceramic Coating Developed on TA15AlloyWANG Xian,YU Sirong,ZHAO Yan><,ZHANG Peng,LIU Enyang,XIONG WeiCollege of Materials Science and Engineering，China University of Petroleum，Qingdao266580D ense ceramic coatings were fabricated on TA15by micro-arc oxidation for improving its hardness and corrosion resistance with NaAIO z,NaFand KOH as electrolyte.Surface morphology,chemical composition and phase composition of coatings were analyzed.Microhardness,surface roughness and corrosion resistance of coatings for different oxidation time were investigated.The results show that tiny honeycomb-like micro-nano pores could be seen on coatings.With the increase of oxidation time,the surface of coatings gradually became smooth.When the time was too long,pits,bulges and other defects were appeared.The surface roughness of the coatings firstly decreased and then increased.The coating was composed of TiO z,AI2O3and A^Ti s phases.The surface microhardness of the coating always increased with the increase of oxidation time.The microhardness of the50min treated coating was332.82HV,which increased by59.2%compared to the matrix.The corrosion potential of the40min treated coating was+222.24mV,which was530mV higher than that of the matrix.The corrosion current density of the40min treated coating was1.73x10-9A/cm2,which was reduced to3%of the matrix.The40min treated coating exhibited the best corrosion resistance.Key words TA15alloy,micro-arc oxidation,oxidation time,surface topography,corrosion resistance0引言钛及钛合金因比强度高、耐蚀性好、储量丰富⑴，成为近年来金属材料领域的研究热点之一，应用前景非常广阔［2-5］。

211114949_强流脉冲电子束M2_高速钢表面改性组织和耐磨性能

第52卷第4期表面技术2023年4月SURFACE TECHNOLOGY·147·强流脉冲电子束M2高速钢表面改性组织和耐磨性能陈军1a,2，王帅夫3，李伟2，司立坤1b，马海涛1a，郝胜智1a,2（1.大连理工大学 a.材料科学与工程学院 b.机械工程学院，辽宁大连 116024；2.大连理工大学鞍山研究院，辽宁鞍山 114051；3.鞍钢集团国际经济贸易有限公司，辽宁鞍山 114002）摘要：目的改善M2高速钢表面组织，提高其耐磨性和红硬性。

方法利用强流脉冲电子束（HCPEB）进行M2高速钢表面辐照改性处理，工作参数包括加速电压25 kV，脉冲宽度2.5 s，能量密度4 J/cm2，脉冲次数3、8和15次。

采用MEF-4型光学显微镜和Zygo 9000型3D表面光学轮廓仪观察辐照前后样品表面形貌。

采用XRD-6000型X射线衍射仪分析改性层组成。

采用DMH-2LS型努氏显微硬度计测量样品表面和截面硬度。

采用CFT-I型摩擦磨损试验机测量表面耐磨性能。

在600 ℃下保温1 h后空冷，测量样品表面硬度变化用以比较红硬性。

结果 HCPEB改性M2高速钢样品表面重熔并出现熔坑，随脉冲次数增加，熔坑数量减少且尺寸增加，表面粗糙度下降，15次脉冲处理样品表面形成大量孪晶，熔坑内部出现熔孔和微裂纹。

重熔层组织细化致密，碳化物类型改变，碳化物颗粒尺寸减小，残余奥氏体数量增加。

相对于未改性样品，15次脉冲处理样品表面硬度提高53.5%，磨损体积减小16.5%，红硬性提高19.2%。

结论 HCPEB可有效改善M2高速钢表面组织，使表面显微硬度、耐磨性和红硬性指标均有明显提高。

关键词：强流脉冲电子束；表面改性；M2高速钢；显微组织；耐磨性；红硬性中图分类号：TH117 文献标识码：A 文章编号：1001-3660(2023)04-0147-08DOI：10.16490/ki.issn.1001-3660.2023.04.011Microstructure and Wear Resistance of M2 High Speed Steel after High Current Pulsed Electron Beam Surface ModificationCHEN Jun1a,2, WANG Shuai-fu3, LI Wei2, SI Li-kun1b, MA Hai-tao1a, HAO Sheng-zhi1a,2(1. a. School of Material Science and Engineering, b. School of Mechanical Engineering, Dalian University of Technology,Liaoning Dalian 116024, China; 2. Anshan Institute, Dalian University of Technology, Liaoning Anshan 114051, China;3. Ansteel Group International Economy and Trade Co., Ltd., Liaoning Anshan 114002, China)ABSTRACT: As a new type of high energetic beam technique, high current pulsed electron beam (HCPEB) has been rapidly developed in recent years. Under HPCEB irradiation, the beam energy can be deposited with the featured characteristics including high density, fast heating speed, large depth and spot area. As a result, the material modification process is realized收稿日期：2022–03–09；修订日期：2022–10–27Received：2022-03-09；Revised：2022-10-27通讯作者：陈军（1965—），男，博士，副教授，主要研究方向为材料表面改性。

涡旋光束拓扑电荷数的测量（攻略）

华侨大学硕士研究生毕业论文1 学校代码: 1 0 3 8 5密级: 硕士学位论文涡旋光束拓扑电荷数的测量作者姓名:李阳月指导教师姓名:蒲继雄职称:教授学科、专业: 物理电子学研究方向: 光电子材料与器件论文提交日期:2 0 1 1年4月论文答辩日期:2 0 1 1年5月华侨大学学位评定委员会校址:福建省泉州市华侨大学硕士研究生毕业论文 2 原创性声明本人声明兹呈交的学位论文是本人在导师指导下完成的研究成果。

论文写作中不包含其他人已经发表或撰写过的研究内容,如参考他人或集体的科研成果,均在论文中以明确的方式说明。

本人依法享有和承担由此论文所产生的权利和责任。

学位论文作者签名: 日期: 学位论文版权使用授权声明本人同意授权华侨大学有权保留并向国家机关或机构送交学位论文和磁盘,允许学位论文被查阅和借阅。

论文作者签名: 指导教师签名:签名日期:签名日期: 华侨大学硕士研究生毕业论文3 论文摘要涡旋光束自发现以来,其传输特性受到了人们的广泛关注。

对涡旋光束的研究也具有越来越重要的意义。

涡旋光束是具有螺线形相位分布的光束,其表达式中带有相位因子exp( ) ilθ ,光束中的每个光子携带lh 的轨道角动量,其中l 称为拓扑荷数。

涡旋光束在光学微操纵、生物医学、信息传输等领域都有重要的应用价值。

因此,涡旋光束具有广泛的应用前景。

本论文对涡旋光束的产生、传输特性以及涡旋光拓扑电荷数的测量方法进行了研究,同时对分数阶涡旋光束进行了重点研究。

论文的主要内容为: 1 、基于全息光学的方法,利用空间光调制器我们在实验中获得了涡旋光束。

首先,用数值模拟的方法得到平面波与涡旋光束干涉的计算全息图,并加载到空间光调制器上。

然后用扩束后的近平面波照在空间光调制器上,产生了涡旋光束。

通过改变计算全息图,就可以产生带有不同拓扑电荷数的涡旋光束。

2 、分别从理论上和实验上研究了涡旋光束的产生和干涉现象。

理论上分析了分数阶和整数阶涡旋光束同球面波以及平面波的干涉情况,并从实验上得出了其干涉图形,且实验结果和理论模拟基本上一致。

土木工程专业英语课后翻译

一.1.受压构件是只承受轴向压力的结构构件。

Compression members are those structural elements that are subjected only to axial compressive forces.2.公式1.1要成立，构件必须是弹性的并且其两端能自由转动但不能横向移动。

For Eq.1.1 to be valid,the member must be elastic,and it's ends must be free to rotate but not translate laterally.3.临界荷载有时被称为欧拉荷载或欧拉屈服荷载。

The critical load is sometimes referred to as the Euler load or the Euler buckling load.4.图1.2中的应力-应变曲线不同于延性钢的应力-应变曲线，因为它有明显的非线性区域。

The stress-strain curve in Fig.1.2 is differet from the ones for ductile steel because it has a pronounced region of nonlinearity.5.其他因素，像焊接和冷弯，都能影响残余应力，但冷却过程是残余应力的主要来源。

Other factors,such as welding and cold bending to create curvature in a beam, can contribute to be the residual stress,but the cooling process is the chief source.二1。

作用在结构上的力被称为荷载The forces that act on a structure are called loads.2．恒载就是固定不变的荷载，包括结构自身的重量。

微梁力学性能尺寸效应的研究的开题报告

微梁力学性能尺寸效应的研究的开题报告一、选题背景与意义随着科技的发展和应用的需求，微纳米材料和结构的制备和应用越来越受到人们的关注。

微小材料和结构的尺寸效应在材料力学、结构设计等领域都具有很大的影响，因此对尺寸效应的研究也变得越来越重要。

微梁作为微小结构之一，因其结构简单、制备方便、适用于多种应用场合等特点而受到广泛关注。

但由于微梁的尺寸通常非常小，其力学行为与宏观材料存在较大差别，需要通过实验和理论方法进行深入研究。

本课题旨在研究微梁尺寸效应对其力学行为的影响，深入探讨微梁的力学性能和尺寸效应规律，对微梁的设计和应用具有重要的指导作用。

二、研究内容及方法1. 研究微梁的力学性能，包括拉伸、弯曲等力学行为。

2. 探究微梁尺寸效应对其力学行为的影响，分析微梁在不同尺寸下的变形、破坏等规律。

3. 建立微梁力学性能模型，预测微梁在不同尺寸下的力学行为。

4. 进行实验验证和模拟分析，比较模型预测值与实验结果的一致性。

此外，本课题还将运用纳米制造和微纳机电系统等技术制备微梁，并采用能谱分析、电子显微镜等手段对微梁进行表征，为后续的研究提供实验数据和依据。

三、预期成果及应用价值1. 研究微梁的力学性能、尺寸效应等规律，并建立相关的力学模型，预测微梁在不同尺寸下的力学行为。

2. 通过实验验证和模拟分析，比较模型预测值与实验结果的一致性。

3. 推进微梁材料及其应用领域的研究，并提供基础理论和技术支持，为微纳机电系统、纳米材料制备等领域提供新的思路和方法。

四、研究进度安排1. 完成文献阅读和理论研究，针对微梁力学性能和尺寸效应进行分析和整理，明确研究方向和目标（1-2周）。

2. 制备微梁样品并进行材料表征实验，获取微梁的形貌和力学性能等基础数据（2-4周）。

3. 设计并建立微梁力学模型，根据模型预测研究微梁在不同尺寸下的力学行为（2-3周）。

4. 进行实验验证和模拟分析，比较模型预测值与实验结果的一致性（2-3周）。