化学专业英语文献+翻译关于二氧化钛的论文

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妙文翻译公司翻译样稿3.我们研发的烟气脱硝催化剂有什么创新?What’s the innovation of our flue gas De-NOx catalyst?我们研发的烟气SCR脱硝催化剂有什么创新?概括为下列四个创新点:What’s the innovation of our flue gas SCR De-NOx catalyst? In general, there are four innovations (as follows):3.1原料二氧化钛从颜料型改性为材料型3.1 Raw titanium dioxide is modified from pigment-type to material-type我国的钛白粉厂生产的二氧化钛都是颜料型的,它从颜料角度对二氧化钛的质量从白度、着色力、遮盖力、吸油量、储缶稳定性等考虑。

而生产SCR脱硝催化剂的二氧化钛必须要从材料角度对二氧化钛提出比表面、孔容、最可几孔径分布、表面酸性、晶粒大小、结晶庋好坏……方面考虑。

因为国内钛白粉厂还没有掌握颜料型二氧化钛向材料型二氧化钛改性技术。

因此,生产的二氧化钛不能用于SCR脱硝催化剂生产。

被迫材料型二氧化钛必须花大量外汇进口。

三龙公司通过大量实践,另辟捷径,掌握了二氧化钛从颜料型改性为材料型的“绝窍”。

而且制备的材料型二氧化钛从比表面、孔容、最可几孔径分布、表面酸性、晶粒大小、结晶庋好坏……等方面都超过进口的二氧化钛。

The titanium dioxide produced by China’s t itanium dioxide plants are of pigment-type, which will consider the quality from the pigment aspect: whiteness, tinting strength, hiding capacity, oil absorption, storage stability and so on. However, the titanium dioxide used for SCR De-NOx catalyst production must consider from the material aspect: specific surface area, pore volume, most probable distribution of diameter, surface acidity, grain size, crystalline status and so on. Since the domestic titanium dioxide plants have not mastered the modification technology from pigment-type to material-type, the produced titanium dioxide cannot be used for SCR De-NOx catalyst production. As a result, the material-type titanium dioxide must be imported with large foreign exchange. Through plentiful practice, Zhejiang Sanlong Catalyst Co., LTD has open up a ne w shortcut and has mastered the “wizardry” of modification. And the produced material-type titanium dioxide has exceeded the imported titanium dioxide from the aspects of specific surface area, pore volume,most probable distribution of diameter, surface acidity, grain size, crystalline status and so on.3.2辅助催化剂的优势3.2 Advantages of secondary catalyst三龙公司在开发国产SCR脱硝剂过程中,别具一格、独具匠心地在辅助催化剂上有创新。

CO_B_H_0286_1_Eff_Util_of_TiO2

Effective Utilization of Titanium DioxideIntroductionCoatings formulators and manufacturers are interested in producing and marketing low-cost, high-quality products to enhance profit. In many coatings, TiO2 has an important effect on both quality and cost. So, it becomes worthwhile for a coating producer to answer the following questions with a high degree of certainty:•Am I using TiO2 at high efficiency to achieve opacity in my products?•Am I using the best TiO2 grade?•Do I have the right amount of TiO2 per gallon or am I using too much or too little for the quality I want to achieve?•How can I use TiO2 and toners to get the balance of brightness and opacity that I wish?Often, answers to these questions have been qualita-tive with a low degree of certainty. Good answers are important and useful, especially when titanium dioxide is in tight supply worldwide and likely to remain so for some time.To determine hiding power or opacity, coatings people generally use either visual or instrumental methods. In a visual comparison of two coatings, the observer will say that one coating has higher, lower, or perhaps equal opacity relative to the other. He/she may even guess how much. The story is much the same with contrast ratios, but observer bias is reduced.For example, if Coating A has a contrast ratio of0.920 and Coating B has a contrast ratio of 0.900, about all that can be said is Coating A has higher opacity than Coating B. We can say it is 0.020 higher, but it is not clear how to use this number to formulate Coating B to have equal hiding. Also, this is not helpful in deciding what to change in order to improve opacity.Fortunately, quantitative answers to the questions above can be obtained with a reasonable amount of lab work using the equations of Kubelka and Munk. This approach is familiar to many workers in the field. We feel that using this technique is greatly facilitated by our user-friendly computer program. This paper will be devoted to explaining such a method and providing examples of how it can be used.BackgroundIn 1931, Kubelka and Munk published equations showing the relationship among contrast ratio, brightness, and the quantity of light-scattering material in pigmented film. The equations are quite complex and involve mathematical calculations that are tedious. Throughout the years, the equations have been modified1 and even simplified to table or graphical forms.2,3,4,5,6,7 The widespread use of computers by coatings manufacturers prompted us to develop an easy-to-use software program of Kubelka-Munk calculations for accuracy with speed and less tedium compared to other techniques.The Kubelka-Munk general equation:SX(1R∞–R∞) R = (Rg–R∞)/R∞–R∞(Rg–1/R∞)eSX(1/R∞–R∞)(Rg–R∞)–(Rg/R∞)eIt expresses the reflectance, R, of film over a back-ground of reflectance Rg as a function of the film’s scattering power SX and R∞—the reflectance of a film so thick that further thickness increases do not change the reflectivity. This relationship can be used to determine a coating’s scattering power, SX.2SX is a dimensionless product; S is the scattering coefficient, and X is the amount of scatteringmaterial. S is a constant characteristic of a particular coating and a direct measure of the effectiveness of TiO 2 in building opacity and brightness. The scatter-ing power of SX of that coating can only be changed by varying X, the amount of light-scattering mate-rial. X can be expressed as film thickness in mil or gal/ft 2 (the units of S will be the reciprocal of X, for example, mil –1 or ft 2/gal).X can also be expressed in terms of the amount of TiO 2 present in the coating, commonly g/m 2, that is,grams of TiO 2 over each square meter of coated surface. Again, the units of S will be the reciprocal of X, for example, m 2/g.*A graphical form of the Kubelka-Munk equations is shown in Figure 1. It interrelates reflectance over black, R ∞, contrast ratio, and SX. By experimentally determining contrast ratio and reflectance overblack, Figure 1 can be used to find both SX and R ∞.Using the same data, we can calculate the spreading rate needed for each paint to achieve complete hiding.** As seen in Figure 1, Paint A requires an SX of 6.7 to reach complete hiding; graphically, this is seen at the point defined by contrast ratio of 0.98and R ∞ of 0.81. Because S is a constant, in order to increase SX, film thickness (X) must increase by a factor of 6.7/4.3 = 1.55. Because spreading rate is inversely proportional to X, the spreading rate for complete hiding is 800/1.55 = 510 ft 2/gal.Similarly, Paint B requires an SX of 7.7 for complete hiding, meaning that film thickness X must increase by the factor 7.7/4.3 = 1.8 to achieve complete hiding. Its spreading rate at complete hiding by the dry film will be 800/1.8 = 445 ft 2/gal.Our computer program, following the same concepts and using the same inputs, gives more accurate results than a chart or table because interpolation is not required.Computer ProgramA user-friendly computer program is available on a floppy disk to facilitate the calculations. This program will generate optical information, including scattering coefficients for TiO 2 and paint spreading rates at complete hiding, for the purpose of assessing perfor-mance of TiO 2 and coatings.Inputs and outputs for the computer program are shown in Table 2.The inputs are reflectances and other information that the paint chemist often measures. Practical coatings also depend on absorption of light as well as scattering to develop opacity. Light absorption by a coating can be quantitatively described by its absorption coefficient K. K/S is uniquely related to R ∞, and when R ∞ and S are known, K can be calculated. This is also done by our computer program.An example of computer results is shown in Table 3. The thickness of the drawdown film of this commercial paint was 2.397 mil, calculated from measured drawdown weight and area and measured paint density. This film produced a contrast ratio of 0.971.Table 1Example of Paint Comparison by Light-Scattering Power Contrast Applied Spreading PaintRatioR ∞SX Rate, ft 2/galA 0.940.81 4.3800B0.930.854.3800Figure 1.Kubelka-Munk InterrelationshipsScattering coefficients are affected by many factors in paint formulas. They provide quantitative mea-sures useful in comparing paint formulas, different TiO 2 grades, and the effects of formulation changes.The advantage of working with light-scattering coefficients, rather than contrast ratio alone, can be illustrated using the data in Table 1 taken from the examples in Figure 1.Both paints in this case have the same SX value of 4.3, indicating equal light-scattering power; Paint A does have more total hiding (higher contrast ratio)by virtue of more absorption (shown by lower R ∞).Paint B toned down to 0.81 brightness would match Paint A. In this example, X, expressed as spreading rate, is the same for both paints.*Some workers may express X in microns, representing the thickness of TiO 2 in a cross section of the film; then S would have the units of micron.1**In this discussion, we will arbitrarily define complete hiding as a contrast ratio of 0.98 developed by the dry film. Other definitions are possible.R e f l e c t a n c e o v e r B l a c kContrast RatioCalculations based on the input data show that the drawdown had a contrast ratio of 0.971 and SX of 6.344, corresponding to a scattering coefficient for the paint film of 2.647 per mil or a scattering coefficient for the TiO2 of 0.309 m2/g.From this information, the computer program can predict the SX needed for complete hiding and therefore the spreading rate at complete hiding.At a spreading rate of 579 ft2/gal, this paintwould produce a contrast ratio of 0.98.These data would suggest that this paint is more than adequate for the usual objective of complete hiding at 450 ft2/gal, and that savings in raw materials are possible by lowering TiO2 content, total solids, or some combination of these.Experimental ProceduresThe output of a mathematical operation is no better than the input data, which depend on the design and execution of the experimental work. The experimental program should be planned to use as little effort as needed to get useful results. Table 4 lists equipment we use for the experimental work. Many paint companies already have this equipment. A vacuum plate to hold paper charts gives more uniform films than a plate with no vacuum, and the automatic drawdown equipment is better yet, because the coating is drawn down at a uniform speed.Table 2Spreading Rate Program InformationInputs•Measured White Substrate Reflectance •Measured Reflectance over Black•Measured Reflectance over White•Measured Weight of Wet Paint on Drawdown •Measured Drawdown Area•Measured Density of Paint•Known TiO2 Concentration in Paint (Optional, required to obtain S in m2/g)Outputs•SX•Contrast Ratio•X•S, per mil of Coating•S, m2/g for TiO2 in Coating•Spreading Rate–Of Drawdown as Prepared for Above Measurements–At Goal Contrast Ratio–At Goal SX•K/S•K, per mil of Coating•R∞ = R Inf•Tabulation of Inputs for Future ReferenceTable 3Example of Computer OutputPredicted atSample Complete Hiding Substrate Reflectance0.8100.810 Thickness in mils 2.397 2.772 Reflectance over Black0.8050.813 Reflectance over White0.8290.830 Contrast Ratio0.9710.980SX 6.3447.336S per mil 2.647 2.647S m2/g0.3090.309Spreading RatesSample as is:670 ft2/gal CR = 0.980:579 ft2/galor or16 m2/L14 m2/LTable 4Experimental Equipment and Procedures EquipmentDrawdown Plate, Gardner CalculatorBird Applicators, Gardner Charts, Leneta Form 14H Top Weighing Balance, Mettler ComputerReflectometerProcedure1.Measure green reflectance of white portion of contrastratio chart and record.2.Weigh contrast ratio chart and record.3.Affix chart to vacuum plate and draw down coating usingan appropriate applicator.4.Weigh coated chart and record.5.Repeat steps 1–4 three more times to make a total offour weighed drawdowns.6.Allow coatings to dry overnight.7.Read green reflectance over black and white areasand record each value.8.Determine average reflectance over white and averagereflectance over black.9.Calculate coating weight on each chart and calculate average.10.Repeat for each coating.ing computer program, input: substrate reflectance,reflectance over black, reflectance over white, coatingweight, drawdown area, density of wet paint, and (if known)TiO2 concentration in paint.The film thickness at which measurements are made is not as critical with the computer program as it is when charts and tables are used. Error due to interpolation are minimized or eliminated. Table 5 shows the effect of various drawdown blade clearances on the calcu-lated information. Note that S is constant, within experimental error, for thickness of 0.003–0.010 mil clearance drawdown. We recommend using a blade clearance of 0.005 mil to be in the mid-range.The procedure of Table 4 gives the basic informa-tion needed to determine SX, as well as S per mil of coating, S related to TiO2 concentration, and X in g/ m2 of TiO2. With this information, a number of comparisons and predictions can be made. Some of the possibilities are shown below.3Practical Applications Comparison of Coatings We tested two purchased commercial medium-quality flat emulsion paints for scattering power. We experimentally determined all of the inputs listed in Table 2 except TiO2 concentration, which was shown on the labels.Paint B, although less expensive, shows better covering power, higher brightness, and better scattering, as shown in Table 6.It would appearto be a better value to painters.Of importance to paint manufacturers, the scattering coefficients suggest that Producer A should work on getting improved efficiency from the TiO2, by perhaps changing grades.If the chemist noted the difference in brightness and removed toner from Paint A, he/she would observe a loss of hiding power. They should focus on improving the TiO2 scattering coefficient.Toning EffectsToning of white paints is used as an inexpensive means for improving opacity through light absorption. To illustrate the efficiency of toning, two semigloss emulsion paints containing the same amount of TiO2 were prepared: A (with no toner) and G (toned to a brightness of 0.811 with carbon black). Five other paints were made by blending A and G. Results from studies of these paints are shown in Table 7.The following observations can be made:•The scattering coefficient S of the TiO2 is about the same in each of the paints, as it should be.•Untoned Paint A would have to be applied at267 ft/gal to get complete hiding. This is too low to be practical.•Paints F and G, toned to brightness of 0.825 and 0.811 respectively, have practical spreading rates at complete hiding.•The absorption coefficient K is proportional to the concentration of carbon black, as it should be when no flocculation occurs.Our computer program calculates R∞ from the inputs described in Table 2.It is clear from Table 7 that, at high brightness, R∞ deviates from brightness measured on drawdowns of reasonable thickness. Untoned laboratory paints, like Paint A, sometimesTable 5Effect of Drawdown Blade Clearance on Calculated Optical Properties of Two PaintsSpreading Rate atContrast Complete Hiding,S,S–1,Clearance Ratio ft2/gal m2/g mil R∞Paint B0.00250.8872980.272 1.8610.9240.0030.9203150.277 1.8990.9160.0040.9463230.278 1.9030.9110.0050.9593360.283 1.9350.9060.0060.9713130.271 1.8530.9090.0080.9863120.266 1.8220.9070.0100.9913240.272 1.8600.903Avg.317Paint G0.00250.9164570.282 1.9320.8140.0030.9454590.285 1.9520.8140.0040.9664590.282 1.9310.8130.0050.9774530.279 1.9110.8130.0060.9894510.278 1.9010.8120.0080.9964330.265 1.8150.8120.0100.9994600.282 1.9290.811Avg.453Table 6Comparison of Two Commercial Emulsion PaintsTiO2 Selling Spreading Rate ScatteringPrice,TiO2,Measured at Complete Coefficient, Paint$/gal lb/gal Brightness Hiding m2/g A14.98 2.10.874700.236 B13.95 2.10.885300.2734give data that appear in imaginary space of the Kubelka-Munk analysis, such space apparently corresponding to R∞ greater than 1.00.The reason for this is that these films deviate from the ideal films considered by Kubelka and Munk. This phenomenon is well known and was discussed by Ross.1 Our computer program will indicate such a circumstance by printing “R lnf = 1.000.”Binder EffectsAs might be expected, binders have a significant effect on TiO2 performance and opacity of the dry paint film. Table 8 shows results from a proprietary emulsion paint formula, prepared at equal volume solids and PVC, using two different binders—one an acrylic and one a vinyl-acrylic. The binders produce films that clearly are different in brightness, scatter-ing power, spreading rate, and TiO2 efficiency.One can consider several mechanisms by which binders can affect dry film opacity; we made noeffort to separate or prioritize these. These effects are significant and can be quantitatively studied using the procedures advocated here.A formulator, seeing the results of Table 8, should next consider the value of the more expensive acrylic binder in relation to opacity. If the opacity of the vinyl-acrylic film is satisfactory, he/she could assess using the acrylic binder with less TiO2.These data show that the two paints have about equal spreading rates, but that Grade 1 gives a higher brightness (0.880 vs. 0.886), owing to a higher scattering coefficient (0.296 vs. 0.278).Two ways to take advantage of the higher scatter-ing coefficient of Grade 1 are toning and reducing TiO2 levels.The paint made with Grade 1 can be toned to the brightness of Grade 2, with the benefit that the higher scattering at equal brightness would result in a higher spreading rate. The data verifying the merits of this approach are shown in Table 10. Scattering properties of the Grade 1 paint remain unchanged as expected, but the added toner reduces brightness, increases absorption, and significantly improves spreading rate.Table 7Effect of Toning on Coating OpticsCalculated CalculatedContrast Measured Spreading Rate,TiO2,Calc.Calc.K, Paint Ratio Brightness ft2/gal*m2/g R∞K/S mil–1 A0.8870.9232670.2790.9780.0002470.0004 B0.8870.8962980.2720.9240.003120.0058 C0.8990.8993540.2810.8890.006930.013 D0.9020.8663750.2780.8660.01040.020 E0.9120.8394170.2860.8440.01440.028 F0.9140.8254320.2820.8290.01760.034 G0.9160.8114570.2820.8140.02130.041Avg.0.280Substrate reflectance, 0.800Drawdown blade clearance: 0.0025 in for hiding power, 0.008 in for brightness measurements.*At complete hiding, defined as contrast ratio = 0.98.Table 8Optical Properties of Emulsion Paint Films: Binder EffectsVinyl-Acrylic Acrylic R∞0.9600.945 SX 6.66 5.74 S, per mil 2.30 1.99 S, m2/g0.3030.265 Spreading Rate at Complete Hiding, ft2/gal398298Selecting a Grade of TiO2The approach suggested in this paper can be used to compare grades of TiO2, based on relative optical performance and therefore cost-effectiveness. Table 9 shows measurements on dry films made using two domestically produced chloride-route rutile grades of TiO2 in a good-quality, acrylic emulsion, semigloss paint. Both paints had equal quantitiesof carbon black toner.Table 9Optical Properties of Emulsion Paint Films: Two Grades of TiO2 with Equal Amounts of TonerTiO2Grade 1Grade 2 R∞0.8800.866 SX 3.82 3.63 S, per mil 2.03 1.90 S, m2/g0.2960.278 Spreading Rate at Complete Hiding, ft2/gal38237556The other way to exploit the superior scattering ofGrade 1 would be to match the effect of Grade 2using a lower concentration of Grade 1 in the dry film. The results of Table 9 suggest using 6% less of Grade 1 (0.278/0.296 = 0.94). This was experimen-tally confirmed as shown in Table 11. Volumesolids was maintained constant, by adding barites in place of the TiO 2 reduction. The increase in scatter-ing efficiency of TiO 2 Grade 1 is probably real, as explained by Fitzwater and Hook.8average-quality flat paints, representing an estimated 50% of the interior emulsion flat paint market. Type 3 are ceiling-quality paints with high porosity (low “SX, OD”) and, owing to the large amount of dry flat hiding, no need for high TiO 2 content beyond what will provide the desired level of wet hide.Paints of any type can give good initial opacity,indicated by “Dry SX.” However, lower “SX, O/D”indicates less film physical integrity, which is why we refer to Type 3 as “ceiling quality.”To assess the efficiency of using TiO 2, we can look at “Oiled S.” This ranges from 0.236–0.369. This is partially explained by the effect of particle crowding on scattering efficiency (see Table 12). If we compare,however, two Type 2 paints at 12% TiO 2 PVC, we see scattering coefficients of 0.264 and 0.358. The TiO 2 in the best paint is performing 36% better than the TiO 2in the poorest paint. The poorer paint is getting high spreading rates by toning to a low brightness (0.815 vs.0.875). We would say that the chemist for this pro-ducer should work on improving the TiO 2 efficiency;with improvement, he/she could make the same quality with less TiO 2 or get higher brightness from the same TiO 2 concentration.Table 11Optical Properties of Semigloss Paint:Two Grades of TiO 2 with Equal Amounts of Toner, But 6% Reduced Concentration of Grade 1TiO 2Grade 1Grade 2R ∞0.8640.866SX3.70 3.63S, per mil 1.96 1.90S, m 2/g0.3050.278Spreading Rate at Complete Hiding, ft 2/gal389375Table 12Survey of Commercial Interior Flat PaintsSpreading Rate Dry SX,TiO 2at Complete Oiled Measured SX O/D PVCHidingSBrightness Type 1 (High Quality)6.340.92225800.2860.8324.730.92194200.2940.8394.660.81204300.2830.8065.020.89243700.2640.8854.440.93184700.2360.815Type 2 (Medium Quality)7.230.72196300.3200.8395.670.70124200.3580.8754.980.72173300.2910.8945.130.67164100.3490.8564.620.57124100.2640.8155.540.60145200.3280.8416.620.58184700.2360.872Type 3 (Ceiling Quality)7.660.51226600.3370.8416.420.32104500.3020.8885.270.53125000.3400.8374.840.53104100.3690.8624.700.49142600.2640.833Table 10Optical Properties of Semigloss Paint:Two Grades of TiO 2 Toned to Equal BrightnessTiO 2Grade 1Grade 2R ∞0.8630.866SX3.81 3.63S, per mil 2.02 1.90S, m 2/g0.2950.278Spreading Rate at Complete Hiding, ft 2/gal407375Commercial PaintsTable 12 shows results from a survey of interior off-the-shelf trade sales emulsion flat paints. In this table, “Dry SX” indicates the scattering power of the dry film, obtained as before. “Oiled S” is the scatter-ing coefficient of TiO 2 calculated from measure-ments on films to which mineral oil had been applied to eliminate dry flat hiding or scatteringfrom voids. An apparent S could be calculated for an unoiled film, but this would ascribe all scattering,from both TiO 2 and voids, to the TiO 2 and would therefore not be a suitable index of the TiO 2 perfor-mance; “SX, O/D” is the ratio of the SX of the oiled film to the SX of the dry or unoiled film. A value of 1 would indicate no porosity. A low value of “SX,O/D” indicates considerable porosity.We have separated these paints into three groups that we feel describe the three types into which most emulsion flat paints can be classified. Type 1 are high-quality paints, typified by high TiO 2 PVC,large amounts of TiO 2 applied per unit area, and good film integrity (high “SX, O/D”). Type 2 areFigure 2 shows Oiled S plotted against TiO2 PVC for non-flocculated paints. The relationship shown represents the expected relationship between TiO2 scattering power and crowding: scatter efficiency decreases as TiO2 particles become more crowded. The magnitude of the changes and the linear rela-tionship are compatible with theory.8Figure 2.TiO2 Scattering Coefficients vs. TiO2PVCReferences1.Ross, W. D., “Kubelka-Munk Formulas Adaptedfor Better Computation,”Jnl. Coat. Tech. 39(1967) 515.2.Mitton, P. B., and Jacobsen, A. E., “New Graphfor Computing Scattering Coefficient and HidingPower,” Off. Dig. 35 (1963) 871.3.Judd, D. B., Color in Business Science andIndustry, John Wiley & Sons, Inc.4.Mitton, P. B., “Easy, Quantitative Hiding PowerMeasurements,”Jnl. Coat. Tech. 42 (1970) 159.5.Clark, H. B., and Ramsay, H. L., “PredictingOptical Properties of Coated Papers,”TAPPI48 (1965) 609.6.Ramsay, H. L., “Simplified Calculation forPredicting Optical Properties of Coated Board,”TAPPI 49 (1966) 116A.7.ASTM D 2805-85, “Standard Test Method forHiding Power of Paints by Reflectometry.”8.Fitzwater, S., and Hook, J. W., “DependentScattering Theory: A New Approach to Predict-ing Scattering in Paints,”Jnl. Coat. Tech. 57(1985) 39.AcknowledgementsAll of the experimental work was ably done byRichard F. Hopkins, who also contributed in manyhelpful discussions. The computer program wasdeveloped by William R. Mendenhall, who patientlyand effectively worked with us to arrive at a correctand practical procedure. We are grateful to DuPont forthe opportunity to work on this subject.SummaryA method has been presented that enables a coatingformulator to quantitatively determine the hidingefficiency of TiO2 in different formulas and to comparehiding efficiency of different TiO2 products.The procedure can also be used to study the effect oftoning on hiding power and brightness and to predictreasonably accurately what formulation changes arenecessary to achieve given optical properties. Theexperimental work required is quite reasonable.Many paint labs already have the equipment neededto use the method.7DuPont Titanium TechnologiesBarley Mill Plaza, Bldg. 36-1172P.O. Box 80036Wilmington, DE 19880-0036(302) 992-5936(800) 441-9485Fax: (302) 992-5273The information set forth herein is furnished free of charge and based on technical data that DuPont believes to be reliable. It is intended for use by persons having technical skill, at their own risk. Because conditions of use are outside our control, we make no warranties, express or implied, and assume no liability in connection with any use of this information. Nothing herein is to be taken as license to operate under or a recommendation to infringe any patents. The DuPont oval logo, DuPont™, The miracles of science™ and Ti-Pure® are trademarks or registered trademarks of DuPont.Copyright © 2002 E.I. du Pont de Nemours and Company. All rights reserved.(1/02)P-200067Printed in U.S.A.[Replaces: H-10286]Reorder No.: H-10286-1。

化学专业外文文献原稿和译文

外文文献原稿和译文原稿Facile synthesis of hierarchical core–shell Fe3O4@MgAl–LDH@Au as magnetically recyclable catalysts for catalytic oxidation of alcoholsA novel core–shell structural Fe3O4@MgAl–LDH@Au nanocatalyst was simply synthesized via supporting Au nanoparticles on the MgAl–LDH surface of Fe3O4@MgAl–LDH nanospheres. The catalyst exhibited excellent activity for the oxidation of 1-phenylethanol, and can be effectively recovered by using an external magnetic field.The selective oxidation of alcohols to the corresponding carbonyl compounds is a greatly important transformation in synthesis chemistry. Recently, it has been disclosed that hydrotalcite (layered double hydroxides: LDH)-supported Cu, Ag and Au nanoparticles as environmentally benign catalysts could catalyse the oxidation of alcohol with good efficiency. In particular, the Au nanoparticles supported on hydrotalcite exhibit high activity for the oxidation of alcohols under atmospheric O2 without additives. It has been extensively demonstrated that the activity of the nanometre-sized catalysts will benefit from decreasing the particle size. However, as the size of the support is decreased, separation using physical methods, such as filtration or centrifugation, becomes a difficult and time-consuming procedure. A possible solution could be the development of catalysts with magnetic properties, allowing easy separation of the catalyst by simply applying an external magnetic field. From the green chemistry point of view, development of highly active, selective and recyclable catalysts has become critical. Therefore, magnetically separable nanocatalysts have received increasing attention in recent years because the minimization in the consumption of auxiliary substances, energy and time used in achieving separations canresult in significant economical and environmental benefits.Magnetic composites with a core–shell structure allow the integration of multiple functionalities into a single nanoparticle system, and offer unique advantages for applications, particularly in biomedicine and catalysis. However it is somewhat of a challenge to directly immobilize hierarchical units onto the magnetic cores. In our previous work, the Fe3O4 submicro-spheres were first coated with a thin carbon layer, then coated with MgAl–LDH to obtain an anticancer agent-containing Fe3O4@DFUR–LDH as drug targeting delivery vector. Li et al. prepared Fe3O4@MgAl–LDH through a layer-by-layer assembly of delaminated LDH nanosheets as a magnetic matrix for loading W7O24as a catalyst. These core–shell structural nanocomposites possess the magnetization of magnetic materials and multiple functionalities of the LDH materials. Nevertheless, these reported synthesis routes need multi-step and sophisticated procedures. Herein, we design a facile synthesis strategy for the fabrication of a novel Fe3O4@MgAl–LDH@Au nanocatalyst, consisting of Au particles supported on oriented grown MgAl–LDH crystals over the Fe3O4 nanospheres, which combines the excellent catalytic properties of Au nanoparticles with the superparamagnetism of the magnetite nanoparticles. To the best of our knowledge, this is the first instance of direct immobilization of vertically oriented MgAl–LDH platelet-like nanocrystals onto the Fe3O4 core particles by a simple coprecipitation method and the fabrication of hierarchical magnetic metal-supported nanocatalysts via further supporting metal nanoparticles.As illustrated in Scheme 1, the synthesis strategy of Fe3O4@MgAl–LDH@Au involves two key aspects. Nearly monodispersed magnetite particles were pre-synthesized using a surfactant-free solvothermal method. First, the Fe3O4 suspension was adjusted to a pH of ca. 10, and thus the obtained fully negatively charged Fe3O4spheres were easily coated with a layer of oriented grown carbonate–MgAl–LDH via electrostatic attraction followed by interface nucleation and crystal growth under dropwise addition of salts and alkaline solutions. Second, Au nanoparticles were effectively supported on thus-formed support Fe3O4@MgAl–LDH by a deposition–precipitation method (see details in ESI).Fig. 1 depicts the SEM/TEM images of the samples at various stages of the fabrication of the Fe3O4@MgAl–LDH@Au nanocatalyst. The Fe3O4nanospheres (Fig. 1a) show asmooth surface and a mean diameter of 450 nm with a narrow size distribution (Fig. S1, ESI). After direct coating with carbonate–MgAl–LDH (Fig. 1b), a honeycomb like morphology with many voids in the size range of 100–200 nm is clearly observed, and the LDH shell is composed of interlaced platelets of ca. 20 nm thickness. Interestingly, the MgAl–LDH shell presents a marked preferred orientation with the c-axis parallel to, and the ab-face perpendicular to the surface of the magnetite cores, quite different from those of a previous report. A similar phenomenon has only been observed for the reported LDH films and the growth of layered hydroxides on cation-exchanged polymer resin beads. The TEM image of two separate nanospheres (Fig. 1d) undoubtedly confirms the core–shell structure of the Fe3O4@MgAl–LDH with the Fe3O4 cores well-coated by a layer of LDH nanocrystals. In detail, the MgAl–LDH crystal monolayers are formed as large thin nanosheet-like particles, showing a edge-curving lamella with a thickness of ca. 20 nm and a width of ca. 100 nm, growing from the magnetite core to the outer surface and perpendicular to the Fe3O4surface. The outer honeycomb like microstructure of the obtained core–shell Fe3O4@MgAl–LDH nanospheres with a surface area of 43.3 m2g_1 provides abundant accessible edge and junction sites of LDH crystals making it possible for this novel hierarchical composite to support metal nanoparticles. With such a structural morphology, interlaced perpendicularly oriented MgAl–LDH nanocrystals can facilitate the immobilization of nano-metal particles along with avoiding the possible aggregation.Scheme 1 The synthetic strategy of an Fe3O4@MgAl–LDH@Au catalyst.Fig. 1 SEM (a, b and c), TEM (d and e) and HRTEM (f) images and EDX spectrum (g) of Fe3O4 (a), Fe3O4@MgAl–LDH (b and d) and Fe3O4@MgAl–LDH@Au (c, e, f and g).Fig. 2 XRD patterns of Fe3O4 (a), Fe3O4@MgAl–LDH (b) and Fe3O4@MgAl–LDH@Au(c).The XRD results (Fig. 2) demonstrate that the Fe3O4@MgAl–LDH nanospheres are composed of an hcp MgAl–LDH (JCPDS 89-5434) and fcc Fe3O4 (JCPDS 19-0629). It canbe clearly seen from Fig. 2b that the series (00l) reflections at low 2θ angles aresignificantly reduced compared with those of single MgAl–LDH (Fig. S2, ESI), while the (110) peak at high 2θangle is clearly distinguished with relatively less decrease, as revealed by greatly reduced I(003)/I(110) = 0.8 of Fe3O4@MgAl–LDH than that of MgAl–LDH (3.9). This phenomenon is a good evidence for an extremely well-oriented assembly of MgAl–LDH platelet-like crystals consistent with the c-axis of the crystals being parallel to the surface of an Fe3O4core. The particle dimension in the c-axis is calculated as ~ 25 nm using the Scherrer equation (eqn S1, ESI) based on the (003) line width (Fig. 2b), in good agreement with the SEM/TEM results. The energy-dispersive X-ray (EDX) result (Fig. S3, ESI) of Fe3O4@MgAl–LDH reveals the existence of Mg, Al, Fe and O elements, and the Mg/Al molar ratio of 2.7 close to the expected one (3.0), indicating the complete coprecipitation of metal cations for MgAl–LDH coating on the surface of Fe3O4.The FTIR data (Fig. S4, ESI) further evidence the chemical compositions and structural characteristics of the composites. The as-prepared Fe3O4@MgAl–LDH nanosphere shows a sharp absorption at ca. 1365 cm_1 being attributed to the ν3 (asymmetric stretching) mode of CO32_ ions and a peak at 584 cm_1 to the Fe–O lattice mode of the magnetite phase, indicating the formation of a CO32–LDH shell on the surface of the Fe3O4 core. Meanwhile, a strong broad band around 3420 cm_1 can be identified as the hydroxyl stretching mode, arising from metal hydroxyl groups and hydrogen-bonded interlayer water molecules. Another absorption resulting from the hydroxyl deformation mode of water, δ(H2O), is recorded at ca. 1630 cm_1.Based on the successful synthesis of honeycomb like core–shell nanospheres, Fe3O4@MgAl–LDH, our recent work further reveals that this facile synthesis approach can be extended to prepare various core–shell structured LDH-based hierarchical magnetic nanocomposites according to the tenability of the LDH layer compositions, such as NiAl–LDH and CuNiAl–LDH (Fig. S3, ESI).Gold nanoparticles were further assembled on the honeycomb likeMgAl–LDH platelet-like nanocrystals of Fe3O4@MgAl–LDH. Though the XRD pattern (Fig. 2c) fails to show the characteristics of Au nanoparticles, it can be clearly seen by the TEM of Fe3O4@MgAl–LDH@Au (Fig. 1e) that Au nanoparticles are evenly distributed on the edgeand junction sites of the interlaced MgAl–LDH nanocrystals with a mean diameter of 7.0 nm (Fig. S5, ESI), implying their promising catalytic activity. Meanwhile, the reduced packing density (large void) and the less sharp edge of LDH platelet-like nanocrystals can be observed (Fig. 1c and e). To get more insight on structural information of Fe3O4@MgAl–LDH@Au, the HRTEM image was obtained (Fig. 1f). It can be observed that both the Au and MgAl–LDH nanophases exhibit clear crystallinity as evidenced by well-defined lattice fringes. The interplanar distances of 0.235 and 0.225 nm for two separate nanophases can be indexed to the (111) plane of cubic Au (JCPDS 89-3697) and the (015) facet of the hexagonal MgAl–LDH phase (inset in Fig. 1f and Fig. S6 (ESI)). The EDX data (Fig. 1g) indicate that the magnetic core–shell particle contains Au, Mg, Al, Fe and O elements. The Au content is determined as 0.5 wt% upon ICP-AES analysis.Table 1 Recycling results on the oxidation of 1-phenylethanol The VSM analysis (Fig. S7, ESI) shows the typical superparamagnetism of the samples. The lower saturation magnetization (Ms) of Fe3O4@MgAl–LDH (20.9 emu g_1) than the Fe3O4 (83.8 emu g_1) is mainly due to the contribution of non-magnetic MgAl–LDH coatings (68 wt%) to the total sample. Interestingly, Ms of Fe3O4@MgAl–LDH@Au is greatly enhanced to 49.2 emu g_1, in line with its reduced MgAl–LDH content (64 wt%). This phenomenon can be ascribed to the removal of weakly linked MgAl–LDH particles among the interlaced MgAl–LDH nanocrystals during the Au loading process, which results in a less densely packed MgAl–LDH shell as indicated by SEM. The strong magnetic sensitivity of Fe3O4@MgAl–LDH@Au provides an easy and effective way to separate nanocatalysts from a reaction system.The catalytic oxidation of 1-phenylethanol as a probe reaction over the present novel magnetic Fe3O4@MgAl–LDH@Au (7.0 nm Au) nanocatalyst demonstrates high catalytic activity. The yield of acetophenone is 99%, with a turnover frequency (TOF) of 66 h_1,which is similar to that of the previously reported Au/MgAl–LDH (TOF, 74 h_1) with a Au average size of 2.7 nm at 40 1C, implying that the catalytic activity of Fe3O4@MgAl–LDH@Au can be further enhanced as the size of Au nanoparticles is decreased. Meanwhile, the high activity and selectivity of the Fe3O4@MgAl–LDH@Au can be related to the honeycomb like morphology of the support Fe3O4@MgAl–LDH being favourable to the high dispersion of Au nanoparticles and possible concerted catalysis of the basic support. Five reaction cycles have been tested for the Au nanocatalysts after easy magnetic separation by using a magnet (4500 G), and no deactivation of the catalyst has been observed (Table 1). Moreover, no Au, Mg and Al leached into the supernatant as confirmed by ICP (detection limit: 0.01 ppm) and almost the same morphology remained as evidenced by SEM of the reclaimed catalyst (Fig. S8, ESI).In conclusion, a novel hierarchical core–shell magnetic gold nanocatalyst Fe3O4@MgAl–LDH@Au is first fabricated via a facile synthesis method. The direct coating of LDH plateletlike nanocrystals vertically oriented to the Fe3O4 surface leads to a honeycomb like core–shell Fe3O4@MgAl–LDH nanosphere. By a deposition–precipitation method, a gold-supported magnetic nanocatalyst Fe3O4@MgAl–LDH@Au has been obtained, which not only presents high 1-phenylethanol oxidation activity, but can be conveniently separated by an external magnetic field as well. Moreover, a series of magnetic Fe3O4@LDH nanospheres involving NiAl–LDH and CuNiAl–LDH can be fabricated based on the LDH layer composition tunability and multi-functionality of the LDH materials, making it possible to take good advantage of these hierarchical core–shell materials in many important applications in catalysis, adsorption and sensors.This work is supported by the 973 Program (2011CBA00508).译文简易合成易回收的分层核壳Fe3O4@MgAl–LDH@Au磁性纳米粒子催化剂催化氧化醇类物质一种新的核壳结构的Fe3O4@MgAl–LDH@Au纳米催化剂的制备只是通过Au离子负载在已合成的纳米粒子Fe3O4@MgAl–LDH球体的MgAl–LDH的表面上。

光催化剂二氧化钛研究现状

光催化剂二氧化钛研究现状王君钊摘要：二氧化钛是当今光催化剂中的主导材料，在国内外得到了广泛的研究，本文介绍了二氧化钛的各种应用及研究现状，包括纳米二氧化钛，二氧化钛复合材料,二氧化钛薄膜以及它们各个的优劣势、前景展望，并论述了二氧化钛矿化有机物的反应机理。

关键字：光催化剂；二氧化钛；矿化有机物；薄膜The study present condition of photocatalyst of 2TiOWang Jun ZhaoAbstract: 2TiO is the dominant material of the photocatalyst nowadays. It is subjected to extensive of research in and out of the country. this paper introduce readers to the Various application of the 2TiO and the study present condition, including na rice 2TiO , 2TiO compound material ，2TiO film and theirs excellent bad situation and the foreground prospect . in the meantime ,we expatiate the reaction course of 2TiO oxidize organic matter.Key words: photo catalyst ; 2TiO ; 2TiO film光催化氧化法是近20年来迅速发展的一种高级氧化技术，尤其是二氧化钛光催化剂在难降解有机废水的处理，空气净化降解有机污染。

综观当今的科研成果，主要集中在纳米二氧化钛，二氧化钛活性碳复合材料吸附以及二氧化钛薄膜等，这些都将要具有广阔的前景。

纳米二氧化钛表面快速金属化的研究_英文_

Journal of Southeast University (E nglish Edition ) Mar .　2002　Vol .18　No .1　I SSN 1003—7985Investigation on Quick Surface Metallizationof Nano Titania PowderXu Lina 1,2　Zhou Kaichang 1　Liu Chunping 2　Ou Danlin 2　Gu Ning 1　Liu Juzheng 2　Chen Kunji 3(1National Laboratory of Molecular and Biomolecular Electronics ,Southeast University ,Nanjing 210096,China )(2Department of Chemistry and Chemical Engineering ,Southeast University ,Nanjing 210096,China )(3Laboratory of Solid State Microstructures ,Nanjing University ,Nanjing 210008,China )A bstract :　Quick surface metallization of titania powder was carried out by electroless chemical deposition of nickel .Thefabricated product was characterized by XRD ,SEM ,FTIR and cro ss -section metallography .The analy sis results show that titania particles are completely coated by a thin nickel shell about 600nm thick ,composed of nano -sized crystalline nickel particles .Mechanis m of nickel chemical deposition on nano powder is proposed .Key words :　electroless chemical deposition ,nickel metallization ,nano titania　Received 2001-12-07.The project supported by the National Natural Science Foundation of China (69890220)and Open Project Foundation of Laborat ory of Solid State Mi -cros tructures of Nanjing University . Born in 1969,female ,graduate . Metal -ceramic composites can improve application properties of the materials such as hardness tensile ,compressive strength ,wear and abrasion resistance .How to fabricate the composites has been highly focused on .Many techniques have come forth ,such as liquid metallurgy techniques including casting or infiltration processes ,liquid phase sintering ,and etc .The most promising fabrication method might be the electroless plating technique which permits ceramic dispersed homogeneously with metal in an aqueous solution and improves the properties of composites in wettability and conductivity .These kinds of productshave been widely used as strengthened [1,2],electriccontact materials [3,4].Up to now ,almost all of the core ceramic particles for the metal electroless plating weremicro -sized powders [5,6],except that nano powder were practised by Wang ,et al .recently [7].It is well known that nano titania possesses especial physical and chemical properties and has a wide range of applications such as catalysis ,dope ,solar energy cell ,electronic information ,UV absorbing materials ,bactericide .Considering that pure black nickel has good conductivity and high light -absorbing rate ,we expect that the Ni -TiO 2composite may benovel materials with light -weighted and specialelectro -magnetic effect .The present study has been concerned with ultrasonic -assisted electroless plating of pure nickel on nano titania powder ,using palladium as the catalyst and hydrazine as the reducing agent .1　Experimental SectionsA given amount of nano titania powder were dispersed and directly catalyzed by immersing into palladium chloride solution for ten minutes ,followed by reduction pretreatment using hydrazine aqueous solution of low concentration .Then the catalyzed nano titania particles were introduced into the electroless plating bath which is consisted of NiSO 4·6H 2O ,7.5g /L ;N 2H 4·H 2O ,2.5mL /L ;K 2C 4H 4O 6·1/2H 2O ,8g /L and a very little amount of composite stabilizer .The pH of the plating solution was firstly adjusted to 11using ammonia and then adjusted to 1213using sodium hydroxide .The mixture was placed into water bath keeping temperature at 85℃,homogenized continuously using an ultrasonic stirrer .Twenty minutes later ,the suspension was cooled quickly to room temperature and separated by magnetic force .The obtained black product was rinsed with water followed by magnetic centrifugal separation over three times ,and dried at 80℃in a vacuum oven .SEM analysis of the product was carried out on a JSM -6300type scanning electronic microscope .Cross -section metallography was obtained with MEF -3type optical microscopy .XRD patterns were recorded using a D /max RA X -ray diffractometer .FTIR analysis was performed on a Nicolet -750type apparatus .2　Results and DiscussionsFig .1shows the XRD patterns of nano titania pow -Fig .1　XRD patterns .(a )pure titania powder ;(b )the productder (a )and the product (b ),respectively .Compared Fig .1(a )with (b ),it can be clearly seen that there is an obvious peak at the 2θangle about 44.5°in Fig .1(b ),which is the characteristic of Ni (111)crystal face diffraction .It can be confirmed that the product is of Ni -TiO 2composite .Based on Scherrer formula C ′=0.9λW ′cos θ,the size of the nickel particles is calculated tobe 10.8nm according to the Ni (111)main peak .Fig .2shows the SE M micrographs of titania and the product .It is obvious in Fig .2(a )that nano titania were apt to aggregating due to its high surface energy.Fig .2　SEM images .(a )pure titania powder ;(b )the productThe nickel coated product ,semispheres with narrow dimensional distribution approximately arranged from 5μm to 20μm ,shows good dispersity .The cross -section image of the product is shown in Fig .3.As can beseen ,the product has a uniform and bright shell ofmetallic nickel about 600nm thick .Besides ,the dimension and micrograph of the core layer suggest that multi -particles are enwrapped by the nickel shell .Fig .3　Cross -section image of the productThe nickel coatings can be confirmed by the FTIRanalysis .Fig .4shows TiO 2has three distinct absorbancepeaks at 3451cm -1,1637cm -1,1384cm -1,respec -tively ,and there are hardly any peaks observed in the product spectrum .This indicates that the product hasn 't any naked TiO 2,TiO 2particles must become the cores completely covered by nickel films .Fig .4　FTIR spectra .(a )titania ;(b )the productThe phenomena may be interpreted by the following mechanism .Reaction (1)was quickly initiated by palladium catalyst absorbed on the surfaces of nano titania powder at 85℃,nickel ions were reduced to black nickel metal by hydrazine in the alkaline solution ,and then deposited on titania with the palladium as the nucleator .2Ni 2++N 2H 4+4OH -※2Ni +N 2←+4H 2O (1)The original formed ultrafine Ni coated TiO 2particles ,auto -catalytically active ,induced the redox reaction and fast deposition of later produced nickel on them with the earlier -produced nickel as the nucleator .However ,the ultrafine particles have strong self -aggregation tendency due to the high surface energy .Earlier fromed Ni -TiO 2congregated simultaneously under the continuous strong collision and assembled into stabilized semispheres .And then the freshly formed nickel was deposited on those congeries and93Investigation on Quick Surface Metallization of Nano Titania Powderformed a metallic shell steadily and continuously. Finally,bright nickel shell coated semispheres were fabricated.Nano titania powder was completely covered by metal.It may be infered that it is very difficult to fabricate single dispersed metal composite only cored with a single nano particle by this method due to its uncontrollable,fast auto-catalytic deposition.3　ConclusionElectroless chemical deposition of nickel on nano TiO2powder had been successfully performed,using palladium as the catalyst and hydrazine as the reducing agent.Ni-TiO2composites were fabricated and characterized by XRD,SE M,FTIR and cross-section metallography.Analy sis results show that multi-titania particles are completely enwrapped by a thin nickel shell,which is about600nm thick and composed of nano-sized cr ystalline nickel particles.The metallized semispheres possess good dispersibility.Thereout, mechanism of nickel chemical deposition on nano powder is proposed.References[1]Leon C A,Drew R A L.Preparation of nickel-coated powdersAl2O3and SiC as precursors to reinforce MMCs[J].J M ater Sci,2000,35:4763-4768.[2]Lin L,Xue Q J,Zhao J Z.Microstructure and tribological be-haviour of electroless Ni-P plating reinforced by fine TiN pow-ders[J].Trib ology,1995,15(2):104-104.[3]Chang S Y,Lin J H,Lin S J,et al.Processing copper and sil-ver matrix composites by electroless plating and hot pressin g [J].M etallur&Mater Trans A,1999,30(4):1119-1136.[4]Joshi P B,Murti N S S,Gad geel V L,et al.Preparation andcharacterization of Ag-ZnO powders for applications in electri-cal contact materials[J].J M ater Sci Lett,1995,14:1099-1101.[5]Harizanov O A,Stefchev P L,Iossifova A.Metal coated alu-mina powder for metalloceramics[J].Mater Lett,1998,33(5-6):297-299.[6]Wen G W,Guo Z X,Davies C.Electroless plating for the en-hancement of material performance[J].Mater Tech,1999,14: 210-217.[7]Wang C Y,Zhou Y,Zhu Y R,et al.Synthesis and character-ization of NiP-TiO2ultrafine composite particles[J].Mater Sci&Eng,2000,B77(1):135-137.[8]Li Y D,Li C W,Wang H R,et al.Preparation of nickel ul-trafine powder and crystalline film b y chemical control reduc-tion[J].M ater Chem&Phys,1999,59:88-90.纳米二氧化钛表面快速金属化的研究徐丽娜1,2　周凯常1　刘春平2　欧丹林2　顾　宁1　刘举正2　陈坤基3(1东南大学分子与生物分子电子学教育部重点实验室,南京210096)(2东南大学化学化工系,南京,210096)(3南京大学固体微结构开放实验室,南京210008)摘　要　采用镍的无电子化学沉积方法研究了纳米二氧化钛粉末表面的快速金属化.所得产物经XRD、SE M、FTIR及剖面金相显微术进行了表征.分析结果表明二氧化钛粒子完全被金属镍包覆,金属壳层600nm厚,由镍的纳米晶粒组成.由此提出了镍在纳米粉末上的化学沉积机理.关键词　无电子化学沉积,镍金属化,纳米二氧化钛中图分类号　O647.1194Xu Lina,Zhou Kaichang,Liu Chunping,Ou Danlin,Gu Ning,Liu Juzheng,and Chen Kunji。

专业英语+二氧化钛+英文文献+翻译

二氧化钛纳米颗粒对废水脱氮除磷的效果以及对活性污泥中细菌群落改变的长期影响熊正1陈银光* 吴瑞2同济大学环境科学与工程学院污染控制与资源再生国家重点实验室，中国上海市四平路1239号，200092摘要：二氧化钛纳米颗粒〔TiO2NPs〕在很多领域的广泛应用引起了人们对其在环境中的潜在影响问题的关注。

然而，人们在TiO2NPs对生物脱氮除磷以及活性污泥中细菌群落影响的领域的调查研究确是很少的。

本实验是针对TiO2NPs在厌氧序批式反应器处于低溶解氧〔0.15—0.50mg/L〕环境下对于生物营养物质去除率的影响的评价。

研究发现，1—50mg/L浓度的TiO2NPs在与废水经过短期接触〔1天〕的情况下，对水体脱氮除磷不具有明显的效果。

然而，研究观察显示，50mg/L浓度〔高于其在环境中的相关浓度〕的TiO2NPs却使水体总氮的去除率出现明显的下降，在与废水经过长期接触反应〔70天〕后，总氮的去除率从80.3%降到24.4%，反之，生物除磷效率却没有受到影响。

变性梯度凝胶电泳图谱显示50mg/L 浓度的TiO2NPs明显减少了活性污泥中的微生物种群多样性。

荧光原位杂交分析结果说明，大量的硝化细菌，尤其是氨氧化菌在TiO2NPs与废水充分接触反应后出现急剧死亡，这也就是氨氧化菌急剧退化死亡的主要原因。

进一步的研究显示，50mg/L浓度的TiO2NPs在与废水长期充分接触之后抑制了氨单氧酶和亚硝酸盐氧化复原酶的活性，但是却对外切聚磷酸酶和多聚磷酸盐激酶没有明显的影响。

同时，TiO2NPs对于细菌细胞中的聚羟基脂肪酸酯和糖原的转变的影响也与实验所观察到的生物脱氮除磷的影响规律保持一致。

引言纳米材料因其特殊的物理和化学性质而被广泛的应用在大量的工业生产和消费产品中。

[1]特别是TiO2NPs被广泛的应用在了催化剂、遮光剂和水处理工艺中。

[2]这些TiO2NPs的广泛应用无疑会在环境中产生残留。

最近，人们在土壤、地表水、排污废水以及城市污泥中均发现有TiO2NPs的存在。

翻译-(终稿)

介孔Pt /二氧化钛纳米复合材料作为高活性催化剂氧化二氯乙酸摘要：介孔Pt /二氧化钛纳米复合材料合成的两个途径:(1)原位制备Pt /二氧化钛纳米复合材料使用一步法合成的Pt 和TiO2的前体下嵌段共聚物溶液作为结构导向剂，其次是干燥、煅烧和减少气体H2。

（2）铂粒子光化学沉积到介孔二氧化钛。

在450 °C 下煅烧的介孔Pt/TiO2 纳米复合材料的透射电镜图像表明TiO2纳米粒子的平均直径约10 nm 无结块、大小和形状均匀一致。

光分解沉积后，Pt纳米粒子分散良好统一高度统一,表现出直径约3nm；然而,原位制备时Pt粒子直径约15nm,最有可能是在高温下煅烧和减少H2引起的。

光催化活性的新合成介孔光催化剂是衡量和比较赢创德固赛原装气相法二氧化钛P25和Pt/TiO2 P 25在光降解二氯乙酸(DCA) 的过程中释放H离子的速度来确定有机碳的含量。

这两种制备路线是增加了Pt的岛屿和Pt粒子的大小。

介孔Pt /二氧化钛纳米复合材料比赢创德固赛原装气相法二氧化钛P25光催化降解DCA高出2倍的活性。

更大感光的介孔Pt /二氧化钛纳米复合材料归因于光分解沉积过程中的高分散性和Pt粒子的小尺寸(3nm)。

就我们所知,光子降解沉积效率ξ= 7.95%是目前ξ值最高的报道。

1 前言二氧化钛具有良好定义的介孔结构的设计是一种很有希望实现高光催化活性的方法。

由于自有序介孔通道能方便底物分子的分子快速转移[1]。

在另一方面,高度结晶的催化剂有利于快速的光分解沉积在二氧化钛粒子表面，从而抑制他们的重组,增强的光子效率[2]。

然而，半导体氧化物的制备表现出有序介孔结构和高度结晶孔壁通常是一个具有挑战性的任务[3]。

虽然安东内利和同事在1995年已经合成了介孔二氧化钛[4]，但是有关报道有序介孔二氧化钛的合成的文献数量还是很有限。

最近纳米尺度的贵金属颗粒和集群吸引了大量关注由于其独特的性质和潜在的应用在光化学、电化学、光学、电子、和催化等方面[6，8]。

二氧化钛光催化英文论文

Proceedings of the World Congress on Engineering and Computer Science 2010 Vol II WCECS 2010, October 20-22, 2010, San Francisco, USASynthesized Oxygen-Vacant TiO2 Nanopowders with Thermal Plasma Torch Evaporation Condensation ProcessC.-Y. Tsai, H.-C. Hsi and K.-S. Fanprecursors were required for processing. Theoretically, TiO2 nanoparticles with a high purity can be obtained by a direct combination of titanium atom and oxygen. The high melting point of titanium metal (i.e., 1941 K) makes the direct combination difficult to process. The sufficient energy provided by thermal plasma can vaporize metals with high melting points and makes the direct combination process possible [12]. Oxygen-deficient TiO2 (TiO2-X) has been extensively studied due to its photocatalytic properties under a visible light (VL) environment. Nakamura et al. prepared TiO2-X for NO removal. A ST-01 sample (Ishihara Sangyo Kaisha, 100% anatase) was treated with radio-frequency discharge using a reducing gas (H2) as the plasma gas. The authors concluded that the appearance of the VL activity was attributed to the newly formed oxygen vacancy state between the valence and the conduction bands in the TiO2 band structure [13]. Ihara et al. manufactured TiO2-X by calcinating the hydrolysis products of Ti(SO4)2 with NH3 in an ordinary electric furnace in dry air at 400 °C [14]. TiO2-X was generally developed by further modifying available TiO2 via reduction reactions or thermal treatments, thus a multiple step synthetic process was needed. Few studies were shown to produce TiO2-X in a single step. This study aimed at preparing TiO2-X nanopowders by direct combination of vaporized Ti atoms with oxygen. A single-step evaporation condensation was established using a transferred DC plasma torch as the heating source. The mixture of argon (Ar) and helium (He) was used as the plasma gas to achieve a high-temperature environment [15]. We considered this single-step process a potential method to produce high-quality nanoscale TiO2-X with clean surface and a narrow particle size distribution.Abstract—The objective of this research is to establish a novel process for preparing the oxygen-vacant titanium dioxide (TiO2-X) nanoparticles with a clean surface, high purity, and controllable size and dimension. Samples were synthesized via the gas-phase evaporation condensation method with transferred DC plasma torch as the heating source. TiO2-X nanopowders were fabricated using different ratios of Ar/He as the plasma gases. The formed TiO2-X nanoparticle was characterized with TEM, EDS and XRD. Experimental results showed that increasing the He addition to Ar plasma gas elevated the plasma temperature. High plasma temperature can cause the tungsten cathode to melt, gasify, and dope into TiO2 structure, which inhibited the size growth and the crystallinity of formed anatase. TiO2-X nanoparticles with anatase phase and particle size at 5−10 nm can be developed at the Ar/He = 75/25. The oxygen vacancy turned the color of TiO2 from white to yellow. Index Terms—oxygen vacancy, titanium dioxide, thermal, transferred DC plasma torch.I. INTRODUCTION Titanium dioxide (TiO2) has been used in numerous applications as a photocatalyst. The manufacturing process of TiO2 strongly influences the purity and physical properties of resulting nanoparticles; these properties subsequently affect the characteristics of TiO2 photocatalytic reactions. TiO2 nanoparticles can be synthesized via solution and vapor synthesis methods, such as sol-gel [1]–[3], thermal hydrolysis [4], hydrothermal processing [5], chemical vapor deposition [6] and evaporation condensation [7], [8]. Evaporation condensation has shown to possess advantages to develop nanoparticles and film with clean surface and a narrow particle size distribution. The heating sources for evaporation condensation include electron beam, laser and plasma [8]–[10]. Plasma has been referred to as an economic heating source and can provide sufficient energy to directly vaporize TiO2 precursors. Cold plasma such as microwave [11] was successfully used to prepare TiO2 photocatalyst. However, because the temperature of cold plasma was generally around room temperature, gaseousC.-Y. Tsai is with the Department of Safety, Health and Environment Engineering, National Kaohsiung First University of Science and Technology, 1, University Rd., Kaohsiung 824, Taiwan (e-mail: u9315918@.tw) H.-C. Hsi is with the Institute of Environmental Engineering and Management, National Taipei University of Technology, 1, Sec. 3, Chung-hsiao E. Rd., Taipei 106, Taiwan (corresponding author; phone: +886 -2-27712171ext4126; fax: +886-2-87732954; e-mail: hchsi@.tw) K.-S. Fan is with the Department of Safety, Health and Environment Engineering, National Kaohsiung First University of Science and Technology, 1, University Rd., Kaohsiung 824, Taiwan (e-mail: ksfan@.tw)II. EXPERIMENTAL Fig. 1 shows the schema of experimental apparatus for preparing TiO2-X nanoparticles using a thermal plasma torch. The system comprised a DC transferred plasma torch connected to a 5 kW DC power supply (Model PLA-250 A, Taiwan Plasma Corp., Taiwan), a water-cooled stainless steel reaction chamber, a stainless steel powder filter (Tee-Type Filters, Swagelok) and a vacuum pump for shifting the particle floated in the exhaust gas. The plasma torch consisted of a tungsten cathode, which was cooled in the central tunnel with water and in the suburbs with sheath gases (O2). Titanium metal with 99.8% purity was used as the anode; TiO2-X nanopowder was formed by the direct combination of evaporated titanium atoms from the anode target with oxygen gas (99.99% purity) within the thermal plasma environment. TiO2-X was synthesized at variousWCECS 2010ISBN: 978-988-18210-0-3 ISSN: 2078-0958 (Print); ISSN: 2078-0966 (Online)Proceedings of the World Congress on Engineering and Computer Science 2010 Vol II WCECS 2010, October 20-22, 2010, San Francisco, USAHe/Ar volume ratio (0/100, 15/85, 25/75, and 50/50) as plasma gas (total flow rate of 2 L/min; from position A in Fig. 1), the operating current of 110 A has been evaluated to be the optimal applied current for nanopowder synthesis. O2 was used as both the reacting gas and the shelter gas of plasma torch (2 L/min; from position B in Fig. 1). The tail gas containing the formed TiO2-X nanoparticles was passed through a stainless steel powder filter and a buffer tank induced by a vacuum pump.Reaction & Sheath gas Plasma gas Waternanoparticles at high plasma temperature. A more detailed discussion will be presented later in this paper. (a) (b)(c)(d)BAABTiTiO2Fig. 1. Schematic diagram of transferred DC plasma torch for producing oxygen-vacant TiO2 nanoparticles. The formed TiO2-X nanoparticles were collected using DI water from the stainless steel powder filter for sample characterization. A drop of suspension was dispersed in ethanol, placed onto a carbon-coated Cu grid followed by air-drying to remove the solvent, and then analyzed with a transmission electron microscope (TEM, Philips CM-200) to investigate samples’ morphology and particle size. The purity of nanoparticles was identified using an energy dispersive X-ray analyzer (EDS, OXFORD, JEOL JEM-2100F) operated at 200 kV accelerating voltage. Nanoparticles which placed on silver membrane filter paper. Powder X-ray diffraction (XRD, Shimadzu XRD-6000) was used for crystal structure identification. The scan range 2θ was between 20 and 80o with a scanning rate of 0.02o/s. III. RESULTS AND DISCUSSION Fig. 2 shows the TEM images of nanopowders synthesized at a fixed current of 110 A with various ratios of He/Ar as the plasma gas. It was observed that the diameter of the nanoparticles was 5−10 nm with 100% Ar as the plasma gas. When the He/Ar ratio increased to 15/85, the size of formed nanopowders appeared to increase to 5−50 nm. The size of nanoparticles grew at a larger He/Ar ratio is attributed to the greater thermal conductivity of He (0.144 at 273 K) as compared to that of Ar (0.0173 at 273 K). Therefore, the plasma formed at He/Ar = 15/85 possessed a higher temperature that caused the growth of TiO2 nuclei. If this proposed mechanism hold, TiO2 nanoparticles with a much larger size should be observed as the He/Ar mixing ratio greater than 15/85. The particle sizes of formed TiO2 at He/Ar = 25/75 and 50/50, however, were approximately 5−10 nm, indicating that the expected growth of TiO2 nuclei at an evaluated He/Ar ratio greater than 15/85 was not observed. The observed phenomena may be resulted by an unwanted tungsten contamination in the formed TiO2Fig. 2. TEM images of TiO2-X powders synthesized at a 110 A plasma current and He/Ar ratio of (a) 0/100, (b) 15/85, (c) 25/75 and (d) 50/50. (a)(b)Fig. 3. EDS images of TiO2 powders synthesized a 110 A plasma current and He/Ar ratio of (a) 0/100 and (b) 50/50. The EDS results for TiO2 prepared at a current of 110 A and 100/0 and 50/50 (Ar/He) plasma gases are shown in Fig. 3. The acquired results indicated that TiO2 nanopowders with a very high degree of purity were developed under the 100/0 plasma gas condition. A small amount of W was observed to melt and subsequently gasify from the plasma cathode and doped into the TiO2 nanopowders when 50% He was added to the plasma gas. Accompanying with the results obtained from the TEM analyses, it appeared that the gasified W doped into the formed TiO2 may restrain particles growth [16]–[18]. Lee et al. prepared nano-sized Al-doped TiO2 powders using a DC plasma jet as the heating source andWCECS 2010ISBN: 978-988-18210-0-3 ISSN: 2078-0958 (Print); ISSN: 2078-0966 (Online)Proceedings of the World Congress on Engineering and Computer Science 2010 Vol II WCECS 2010, October 20-22, 2010, San Francisco, USATiCl4 and AlCl3 as precursors. SEM results indicated that the size of particles decreased as increasing the amount of Al dopant [18]. The size reduction was attributed to the suppression of particle growth by Al species introduced into TiO2 crystal [19]. This consequence can interpret the doped metal restraining the nanoparticles growth, which is consonant with the upshot of TEM shown in Fig. 2.Ag A Ag Ag Ag A: anatase (d) Intensity (a.u.) A A(c)(b)temperature, which is elevating by adding 25% He into the Ar plasma gas. Notably, the anatase peaks for the sample synthesized at the He/Ar ratio of 50/50 are less sharp as compared to those obtained at the He/Ar ratio of 25/75. It was suspected that the melted W doped into the formed TiO2-X, causing defects in the crystal structure of anatase. A number of literatures [13], [14], [20], [22] presented that the TiO2 powder color changed from white to yellow due to oxygen vacancy in the crystal lattice of TiO2. The photographs of TiO2 nanopowders synthesized in the thermal plasma system showed that the color turned from white to yellow as increasing the He/Ar ratio (Fig. 5). Because the addition of He to Ar plasma gas elevated the plasma jet temperature, these observed results confirmed again that increasing the reaction temperature resulted in the oxygen vacancy of TiO2. IV. CONCLUSION(a)203040506070802 ThetaFig. 4. XRD patterns of the nanopowders synthesized at the He/Ar ratio of (a) 0/100, (b) 15/85, (c) 25/75 and (d) 50/50. (a) (b)TiO2-X nanoparticles was synthesized using a gas-phase evaporation condensation method with transferred plasma torch as the heating source. Results showed that TiO2 nanopowders with a very high degree of purity can be developed using 100% Ar as the plasma gas. The characteristics of synthesized nanopowders markedly affected by the amount of He added to the plasma gas. When 15% He was added to Ar plasma gas, the nanoparticles size grew to 5−50 nm at a plasma current of 110 A. Oxygen-vacant TiO2 (i.e., TiO2-X) was formed as He was added to the Ar plasma gas, which increased the plasma temperature. The tungsten melted and gasified from the plasma cathode doped into the TiO2 nanopowders, which influenced the crystal structures and powder size of formed TiO2-X. XRD examination demonstrated that the single crystal of anatase was obtained at 110 A and 25% He/Ar ratio = 25/75. The oxygen vacancy in TiO2 caused the color turning from white to yellow. ACKNOWLEDGMENT This work was supported by National Council of Taiwan (NSC94-2622-E-327-003-CC3) and Taiwan Plasma Corp., Kaohsiung, Taiwan. REFERENCES[1] H. Yamashita, M. Harada, J. Misaka, M. Takeuchi, K. Ikeue, and M. Anpo, “Degradation of propanol diluted in water under visible light irradiation using metal ion-implanted titanium dioxide photocatalysts,” J. Photochem. Photobiol. (a), vol. 148, pp. 257-261, 2002. S. P. Qiu, and S. J. Kalita, “Synthesis, processing and characterization of nanocrystalline titanium dioxide,” Mater. Sci. Eng. (a), vol. 435, pp. 327-332, 2006. M. Kanna, and S. Wongnawa, “Mixed amorphous and nanocrystalline TiO2 powders prepared by sol-gel method: Characterization and photocatalytic study,” Mater. Chem. Phys., vol. 110, pp. 166-175, 2008. M. C. Hidalgo, and D. Bahnemann, “Highly photoactive supported TiO2 prepared by thermal hydrolysis of TiOSO4: Optimisation of the method and comparison with other synthetic routes,” Appl. Catal. (b), vol. 61, pp. 259-266, 2005. X. H. Xia, Y. Liang, Z. Wang, J. Fan, Y. S. Luo, and Z. J. Jia, “Synthesis and photocatalytic properties of TiO2 nanostructures,” Mater. Res. Bull., vol. 43, pp. 2187-2195, 2008.(c)(d)Fig. 5. Photographs of the nanopowders synthesized at the He/Ar ratio of (a) 0/100, (b) 15/85, (c) 25/75 and (d) 50/50. Fig. 4 shows the XRD patterns of the TiO2 nanopowders synthesized at different He/Ar ratios. Because the TiO2-X nanopowders were laid on a silver membrane filter paper for XRD examination, four significant diffractive peaks contributed by Ag were shown. The XRD results clearly indicated that anatase was formed in the thermal plasma system, based on the observation of diffraction angle at 2θ = 25.28°. These results also suggested that anatase TiO2 with the greatest integrity of crystalline was obtained at the He/Ar ratio of 25/75. This result is expected because amorphous TiO2 can transform into anatase or rutile as increasingISBN: 978-988-18210-0-3 ISSN: 2078-0958 (Print); ISSN: 2078-0966 (Online)[2] [3][4][5]WCECS 2010Proceedings of the World Congress on Engineering and Computer Science 2010 Vol II WCECS 2010, October 20-22, 2010, San Francisco, USA[6] [7] [8] X. W. Zhang, M. H. Zhou, and L. C. Lei, “Preparation of anatase TiO2 supported on alumina by different metal organic chemical vapor deposition methods,” Appl. Catal. (a),vol. 282, pp. 285-293, 2005. U. Backman, U. Tapper, and J. K. Jokiniemi, “An aerosol method to synthesize supported metal catalyst nanoparticles,” Synth. Met., vol. 142, pp. 169-176, 2004. T. Sakai, Y. Kuniyoshi, W. Aoki, S. Ezoe, T. Endo, and Y. Hoshi, “High-rate deposition of photocatalytic TiO2 films by oxygen plasma assist reactive evaporation method,” Thin Solid Films, vol. 516, pp. 5860-5863, 2008. Y. Suda, H. Kawasaki, T. Ueda, and T. Ohshima, “Preparation of high quality nitrogen doped TiO2 thin film as a photocatalyst using a pulsed laser deposition method,” Thin Solid Films, vol. 453-54, pp. 162-166, 2004. S. H. Wang, T. K. Chen, K. K. Rao, and M. S. Wong, “Nanocolumnar titania thin films uniquely incorporated with carbon for visible light photocatalysis,” Appl. Catal. (b), vol. 76, pp. 328-334, 2007. M. Addamo, M. Bellardita, D. Carriazo, A. Di Paola, S. Milioto, L. Palmisano, and V. Rives, “Inorganic gels as precursors of TiO2 photocatalysts prepared by low temperature microwave or thermal treatment,” Appl. Catal. (b), vol. 84, pp. 742-748, 2008. C. J. Liu, G. P. Vissokov, and B. W. L. Jang, “Catalyst preparation using plasma technologies,” Catal. Today, vol. 72, pp. 173-184, 2002. I. Nakamura, N. Negishi, S. Kutsuna, T. Ihara, S. Sugihara, and E. Takeuchi, “Role of oxygen vacancy in the plasma-treated TiO2 photocatalyst with visible light activity for NO removal,” J. Mol. Catal. (a), vol. 161, pp. 205-212, 2000. T. Ihara, M. Miyoshi, Y. Iriyama, O. Matsumoto, and S. Sugihara, “Visible-light-active titanium oxide photocatalyst realized by an oxygen-deficient structure and by nitrogen doping,” Appl. Catal. (b), vol. 42, pp. 403-409, 2003. A. M. Fudolig, H. Nogami, J.-I. Yagi, K. Mimura, and M. Isshiki, “Prediction of surface temperature on metal beads subjected to argon-hydrogen transferred arc plasma impingement,” ISIJ, vol. 37, pp. 623-629, 1997. K.-N. P. Kumar, K. Keizer, and A. J. Burggraar, “Textural evolution and phase transformation in titania membranes: Part 1.–Unsupported membranes,” J. Mater. Chem., vol. 3, pp. 1141-1149, 1993. B. Xia, H. Z. Huang, and Y. C. Xie, “Heat treatment on TiO2 nanoparticles prepared by vapor-phase hydrolysis,” Mater. Sci. Eng. (b), vol. 57, pp. 150-154, 1999. J. E. Lee, S. M. Oh, and D. W. Park, “Synthesis of nano-sized Al doped TiO2 powders using thermal plasma,” Thin Solid Films, vol. 457, pp. 230-234, 2004. M. L. Taylor, G. E. Morris, and R. S. Smart, “Influence of aluminum doping on titania pigment structural and dispersion properties,” J. Colloid Interface Sci, vol. 262, pp. 81-88, 2003. T. Sekiya, K. Ichimura, M. Igarashi, and S. Kurita, “Absorption spectra of anatase TiO2 single crystals heat-treated under oxygen atmosphere,” J. Phys. Chem. Solids, vol. 61, pp. 1237-1242, 2000. T. Sekiya, S. Ohta, S. Kamei, M. Hanakawa, and S. Kurita, “Raman spectroscopy and phase transition of anatase TiO2 under high pressure,” J. Phys. Chem. Solids, vol. 62, pp. 717-721, 2001. K. S. Rane, R. Mhalsiker, S. Yin, T. Sato, K. Cho, E. Dunbar, and P. Biswas, “Visible light-sensitive yellow TiO2-XNX and Fe-N co-doped Ti1-yFeyO2-XNX anatase photocatalysts,” J. Solid State Chem., vol. 179, pp. 3033-3044, 2006.[9][10] [11][12] [13][14][15][16] [17] [18] [19] [20] [21] [22]ISBN: 978-988-18210-0-3 ISSN: 2078-0958 (Print); ISSN: 2078-0966 (Online)WCECS 2010。

英文文献有道翻译

制备和表征Fe3O4 /二氧化硅/ Bi2MoO6复合作为磁分离光催化剂Yanlong Xuemei侯,1日田b,1,张翔b,b Shuliang斗,Lei锅b,b Wenjia王,姚明李娜,久鹏赵,⇑化学工程与技术学院的,哈尔滨工业大学,92号,Xidazhi街,南港地区,哈尔滨,中国b复合材料中心,哈尔滨工业大学,哈尔滨,中国摘要Fe3O4 /二氧化硅/ Bi2MoO6微球制备简单水热法。

的扫描电子显微镜(SEM)结果显示,花三维(3 d)Bi2MoO6微球大多以Fe3O4 /二氧化硅磁性纳米颗粒。

的紫外可见漫反射光谱显示扩展吸收在可见光范围内与纯Bi2MoO6相比。

我们评估的光催化活动Fe3O4 /二氧化硅/ Bi2MoO6微球的降解可见光照射下罗丹明B(RhB),发现获得的综合表现光催化活性高于纯Bi2MoO6和project。

此外,Fe3O4 /二氧化硅/ Bi2MoO6复合展示优秀的稳定性和重用后对其光催化活性有所下降5周期。

同时,复合材料可以很容易地通过一个外部磁场分离。

捕获的实验结果表明,超氧化物自由基O2和羟基自由基哦发挥重要作用在Fe3O4 /二氧化硅/ Bi2MoO6可见光辐照下系统。

的结合花三维(3 d)Bi2MoO6微球和Fe3O4 /二氧化硅磁性团簇提供一个有用的策略设计多功能纳米结构和增强光催化材料活动在水净化的潜在应用。

1。

介绍许多概念收获和储存可再生能源(阳光、风、水)直接或辅助过程正在开发,以减少我们对化石能源的依赖来源。

在各种各样的绿色地球和可再生能源项目宽,半导体光催化已收到兴趣,因为它提供了一种简便的方法直接利用能源的自然日光或人工室内照明[1 - 4]。

沿着这条线,丰富光催化材料(如金属氧化物、硫化物和氮氧化物)一直在发展有机污染物的降解和分裂的水[5 - 7]。

尽管如此,仍有一个问题与困难复苏的光催化剂纳米颗粒混合系统。

因此,它是一个关键环节,寻求简单的恢复方法光催化剂纳米光催化的大规模应用流程。

论文摘要翻译

Abstract—The environmental prevalence of engineered nanomaterials, particularly nanoparticulate silver (AgNP), is expected to increase substantially. The ubiquitous use of commercial products containing AgNP may result in their release to the environment, and the potential for ecological effects is unknown. Detecting engineered nanomaterials is one of the greatest challenges in quantifying their risks. Thus, it is imperative to develop techniques capable of measuring and characterizing exposures, while dealing with the innate difﬁculties of nanomaterial detection in environmental samples, such as low-engineered nanomaterial concentrations, aggregation, and complex matrices. Here the authors demonstrate the use of inductively coupled plasma–mass spectrometry, operated in a single-particle counting mode (SP-ICP-MS), to detect and quantify AgNP. In the present study, two AgNP products were measured by SP-ICP-MS, including one of precisely manufactured size and shape, as well as a commercial AgNP-containing health food product. Serialdilutions, ﬁltration, and acidiﬁcation were applied to conﬁrm that the method detected particles. Differentiation of dissolved and particulate silver (Ag) is a feature of the technique. Analysis of two wastewater samples demonstrated the applicability of SP-ICP-MS at nanograms per liter Ag concentrations. In this pilot study, AgNP was found at 100 to 200 ng/L in the presence of 50 to 500 ng/L dissolved Ag. The method provides the analytical capability to monitor Ag and other metal and metal oxide nanoparticles in fate, transport, stability, and toxicity studies using a commonly available laboratory instrument. Rapid throughput and element speciﬁcity are additional beneﬁts of SP-ICP-MS as a measurement tool for metal and metal oxide engineered nanoparticles. Environ. Toxicol. Chem. 2012;31:115–121.翻译环境中工程纳米材料的含量，尤其是纳米银，看起来正在增长。

化学专业英语摘要翻译6篇

Asymmetric C(sp)-C(sp2) bond formation to give enantiomerically enriched1,3-butadienyl-2-carbinols occurred through a homoallenylboration reaction between a 2,3-dienylboronic ester and aldehydes under the catalysis of a chiral phosphoric acid (CPA). A diverse range of enantiomerically enriched butadiene-substituted secondary alcohols with aryl,heterocyclic, and aliphatic substituents were synthesized in very high yield with high enantioselectivity. Preliminary density functional theory (DFT) calculations suggest that the reaction proceeds via a cyclic six-membered chairlike transition state with essential hydrogen-bond activation in the allene reagent.The catalytic reaction was amenable to the gram-scale synthesis of a chiral alkyl butadienyl adduct, which was converted into an interesting optically pure compound bearing a benzo-fused spirocyclic cyclopentenone framework.在手性磷酸（CPA）催化剂条件下，2,3-硼酸酯和醛通过反应生成了富对映体的1,3-丁二烯-2-甲醇，这里面含有不对称的碳（sp杂化）碳（sp2杂化）键。

二氧化钛英文资料翻译

试验系统的构造和操作
图2是粒子特征描述系统的硬件组成及其位置的结构示意图。粉体悬浮分散在圆形烧杯内的透明有机溶剂中，以此来充当光学单元，该单元安装在中央的平台上，学探测器安装在一个可旋转的平台上。通过光路上的缓凝剂和偏振片来调整分散和光的散射。
图2.椭圆偏振光实验结构示意图
在一个简单的液体环境中，粒子间的作用力可以通过借用适当的分散媒介来进行调整或按要求改变，改变溶液的PH值(Widegren,2002)和离子浓度，或者使用表面活性剂或高分子材料吸附在粒子表面。这些不同的方法能在许多环境中迅速的改善粒子分散度，但是他们的使用常常受到很多方面的限制。在较高PH值或较低PH值的分散介质中加入化学试剂往往会产生像化学腐蚀之类的好的影响。因此，跟为复杂的化学反应常常被用来稳定分散(Stein,1996).各种用于提高粒子在不同溶剂和聚合物系统中分散性能的纳米粉体的化学处理方法都是在硅烷和钛酸盐涂料的基础上总结出来的。最近，在一种新的粉体技术的指导下得到了一种分散良好的纳米陶瓷粒子溶液。使用类似氧化钼(MoO3)，氧化钨(WO3)的其他强酸性金属氧化物来修改纳米氧化物粒子的表面特性，提高粒子表面的路易斯酸度，从而提高粒子在水中分散的稳定性。
对于凝聚物结构的探查，偏振光散射是一个十分优越的方法。单个原始粒子分散辐射的干扰模式与散射角有很大的关系。简单地说，就是利用波的矢量公式q=4πλ-1 sin(θ/2)来计算凝聚物结构的。当初始粒子相互间的分散距离小于1/q时，分散就会分段并且会导致相互干涉。当凝聚物的回转半径小于规定尺寸1/q时，分散反应的剧烈程度就与分体分散面积的总和（或粒子的数量）成比例。当回转半径在1/q这个区间内时，分散是不均匀的而且分散辐射的强度和普通粒子的分散面积总和成比例。相反的，如果长度标准1/q小于原始粒子的尺寸，那么入射光束就只会识别光滑的粒子表面而忽略凝聚结构。如果凝聚体中粒子数目通过等式（4）与分形维数直接联系，那么入射光的强度和分形维数也会产生重要的联系(Freltoft等.,1986):

二氧化钛的研究

纳米TiO2的制备与应用的研究摘要：TiO2由于其优良的性能，在太阳能储存、净化环境、传感器、涂料、美容产品、废水处理、催化剂、等方面引起了特别大的关注。

本文主要介绍了运用模板法、水热法、化学气相沉积发来制备纳米TiO2，同时介绍了每一种方法的优点和缺点。

除此此外还有阳极氧化的方法、液相沉积法、微乳液法等等。

同时也阐述了纳米TiO2在光催化降解水，抗菌，解决有机污染物等方面的应用，并对纳米TiO2的前景进行了展望。

关键词：纳米TiO2 催化剂光生电子1.引言随着经济社会的快速发展，药品、个人护理产品、杀虫剂、表面活性剂、化工原料的使用日益增多，加上大部分人对环境保护认识不足，从而对环境造成了严重的影响。

此外随着绿色化学的发展，人们越来越提倡尽运用化学的技术和方法，除去对环境，对人类有害的物质，也要尽可能利用像太阳光这样清洁而又丰富的资源。

而二氧化钛由于其具有化学稳定性、能够和生物很好相容、相当强的氧化能力、以及抗化学腐蚀，抗光腐蚀的能力,更重要是是价格低廉,因此在储存太阳能、处理废水、净化环境、传感器、涂料、美容产品、催化剂、填充剂等诸多领域引起了人们极大的关注[1]，鉴于二氧化钛如此多优点，它的制备方法及其在光催化领域的应用显得尤为重要。

2.纳米TiO2的制备尽管二氧化钛是一种非常有潜力的催化剂材料，但是TiO2的禁带宽度有3.2ev[2]，只有占太阳光5%的短波长的紫外线（λ﹤387 nm）能够将TiO2激发，但是因为光激发而产生的电子和空穴非常容易发生复合，使量子产率下降，这严重降低了二氧化钛的光催化效率[3]。

为了提高太阳光的利用效率，从而改善TiO2的光催化效率，已经有人把过渡金属和稀土元素掺杂在里面，或者是沉积贵金属（银、金、铂等）、掺杂非金属（碳、氮等）、修饰半导体的表面、或者是敏化等[4]。

2.1模板法20世纪90 年代发展起来的模板法是一种合成一维纳米材料的有效方法。

它可以用来合成纳米管和纳米线。

二氧化钛

密度泛函理论是一种研究多电子体系电子结构的量子力学方法。密度泛函理论在物理和化学上都有广泛的应用，特别是用来研究分子和凝聚态的性质，是凝聚态物理和计算化学领域最常用的方法之一。
纳米二氧化钛纳米粉体是指颗粒粒径小于 100nm 的粒子。纳米二氧化钛不但具有纳米粉体的表面效应、体积效应、小尺寸效应、久保效应等，而且具有其独特的性能。因此具有广阔的应用前景。
性能 TiO2%（最小）密度/(g/cm3) 表面积/(m2/g) 类型Ⅰ 97 4.20 6.6-7.7 类型Ⅱ 93 4.05 12.0-12.8 19 30 3.5 中等类型Ⅲ 92 4.05 11.0-18.0 15-19 30 3.6 中等类型Ⅳ 91 4.00 17.7 24 35 4.9 高类型a b 82 3.70 28.8 30 55 13.0 低
Task：寻找2013.08发布在JACS的有关二氧化钛文章，翻译其摘要并介绍二氧化钛的相关知识。
主讲人：高恩鹏韩晓妮海红莲小组成员:高恩鹏韩晓妮海红莲王变变
Lithium Insertion into Titanium Dioxide (Anatase): A Raman Study with 16/18O and 6/7Li Isotope Labeling
缺点
因经过重结晶，所以制得的粉体纯度高。水热法合成 TiO2的关键问题是设备要经历高温、高压，因而，对材质和安全要求较严，操作复杂，而且成本较高。
固相法
固相法合成纳米二氧化钛是利用固态原料热分解或固－固反应进行的。主要有惰性气体蒸发原位加压制备法、非晶晶化法、溶胶－凝胶法、电解沉淀法、高速超微粒子沉淀法、直接沉淀法、烧结－锻压法、反应球磨技术等。

英文文献及翻译_纳米二氧化钛掺杂氧化锌的合成、表征、光催化性能研究

外文文献及翻译纳米二氧化钛掺杂氧化锌的合成、表征、光催化性能研究摘要在这项研究中,氧化锌掺入纳米二氧化钛合成了水热过程。

在水作为溶剂下用含氧化锌前驱和市售二氧化钛纳米粒(P25)加热在140 °C 2 h。

利用合成粒子场发射扫描电镜(FE-SEM)、透射电镜(TEM)和x射线衍射(XRD)对材料的形态和结构特征进行测定发现,纳米粒还附加了二氧化钛表面上的氧化锌。

我们注意到,在二氧化钛在热液的解决方案可能纳米粒充分减少的尺寸氧化锌。

复合纳米结构,具有独特的形态,利用这个方便的方法在低的温度,更少的时间,更少数量的试剂时可以获得，而且发现在紫外光照射下光催化剂是有效的。

关键词: 纳米复合材料;水热合成;陶瓷氧化物;光催化剂1、介绍最近的发现了一个在水介质中改进的氧化和催化降解的有机化合物溶解的实验。

光催化,被称为绿色技术,提供了巨大的潜力可以完全消除有毒化学物质在环境中通过其效率和广泛的适用性。

半导体金属氧化物,如二氧化钛、氧化锌、硫化锌、cd、Fe2O3纳米颗粒(NPs)迄今为止,被证明是最有前途的材料在此领域。

在这些半导体金属氧化物、氧化锌,二氧化钛等已经被认为是最出色的材料因其优异的电子、化学、光学特性与高感光度。

然而,电子的速度的洞(e-h)重组在光催化过程限制这些材料的应用在紫外光照射下。

此外,纳米粒子(具有高比表面积)被发现是更有效的光催化剂但是复苏从反应体系非常困难,这限制了其应用程序环境(二次污染)、经济(损失催化剂)。

各种已经尝试解决上述缺点。

掺杂进光催化剂的新型金属晶格和耦合半导体是有效的方法来减少在这里组合过程而提供一个固定的表面有足够的表面积(如高分子纳米纤维)增强其耐久性为了重复使用。

我们以前的工作表明Ag加载二氧化钛/尼龙6电纺垫能防止损失和催化剂可反复使用。

水晶二氧化钛和氧化锌,不管是在纯粹的形式或作为一个组合,是半导体氧化物广泛用于光催化反应。

原则上,耦合的二氧化钛和氧化锌似乎有用,以实现更有效的e-h对辐射下的分离,因此,更高光降解速率。

论文-TiO2

二氧化钛薄膜的应用邢琪3110702011，金属1101班，材料科学与工程学院摘要：本文对二氧化钛薄膜的性质进行了概述，对近年来二氧化钛薄膜及掺杂二氧化钛薄膜在环境、能源、生物、医学等方面的应用作了简要介绍，同时也对研究中存在的问题和将来研究发展的方向进行了简单评述。

），薄膜，光催化，亲水性。

关键词：二氧化钛（TiO21.引言（标题靠左侧写，不空格，加粗，宋体，四号）二氧化钛（化学式：TiO2），白色固体或粉末状的两性氧化物，是一种白色无机颜料，具有无毒、最佳的不透明性、最佳白度和光亮度，被认为是目前世界上性能最好的一种白色颜料。

广泛应用于涂料、塑料、造纸、印刷油墨、化纤、橡胶、化妆品等工业。

它的熔点很高，也被用来制造耐火玻璃，釉料，珐琅、陶土、耐高温的实验器皿等。

早在上个世纪，科学家已经对半导体光电化学和光催化两个相关领域不但在理论上进行了大量研究，而且在应用研究方面也有了重大突破，如：二氧化钛薄膜的双亲性，这一发现引发了人们对二氧化钛光催化剂研究的又一热潮，近年来，人们对二氧化钛功能薄膜的光催化和亲水性进行了大量的研究，并在理论和应用中取得了可喜的成果，本文现对其研究进展进行简要总结。

1．二氧化钛薄膜的特性二氧化钛有着其独特的性能：第一，即众所周知的光催化性，能分解有机物，具有抗菌防污功能；第二，即超亲水性，利用这一性质可生产防雾、自清洁产品。

这两种现象虽然能同时发生在二氧化钛薄膜上，但在本质上是不同的两个过程。

在具体情况下，所表现出的亲水性和光催化活性程度也不同。

人们已对其机理进行了大量研究，其中光催化机理已趋完善，而亲水性机理迄今为止尚不完全清楚，还存在分歧，有待于更进一步深。

2.二氧化钛薄膜在环境保护方面的应用2.1空气净化室内空气主要有害物质是甲醛、甲苯，市场上有很多清除甲醛、甲苯等有毒气体的产品，效果不是很理想，现在的纳米TiO2光催化剂能很好的解决这一问题，它有很强的氧化能力，可以将其分解为CO2和H2O。

N掺杂文献翻译

一种简单的方法制备N掺杂二氧化钛空心球及其在可见光下高光催化活性的研究摘要以碳球为模板，采用水热法制备了氮掺杂二氧化钛空心球。

用X射线衍射仪（XRD），透射电子显微镜（TEM），比表面积测试仪（BET），X射线光电子能谱（XPS）和紫外可见漫反射光谱（DRS）对制备的空心球进行了表征。

以P25二氧化钛为基准，研究了TiO2空心球对活性艳红X-3B的光催化性能（CI活性红2）。

结果显示，二氧化钛空心球的光催化活性增强了很多。

二氧化钛空心球的表观速率常数几乎是P25二氧化钛的17倍。

1、引言由于纳米二氧化钛（TiO2）在降解污染物、制氢和金属去除领域广阔的应用前景，使其光催化性能得到了广泛的研究。

为了使这项处理技术运用到中，改善二氧化钛的制备方法是非常重要的。

形貌和微观结构对二氧化钛的光催化活性是非常重要的，并且受制备条件和方法的影响。

因为二氧化钛空心微球低密度、高比表面积、良好的表面渗透性以及很高的捕光效率，最近制备技术引起了极大的关注。

预期用二氧化钛空心微球作为光催化剂来提高能源转换效率和光催化活性。

另一方面，由于二氧化钛的禁带（锐钛相3.2eV）宽，工艺技术应用受到几个因素限制，其中最受限制的是利用紫外光（波长（λ）<387nm）作为激发源。

因此，对太阳光的吸收还达不到照射地面的10%。

由于对阳光的有效利用或对光谱的可见光区的利用的缘故，增大二氧化钛对光谱吸收的范围这项技术可能还会出现一个有吸引力的挑战，目的是创造新一代的光催化剂。

许多研究说，非金属元素掺杂TiO2（如氮，硫，碳）把二氧化钛光吸收边转向低能源，从而增加了在可见光区的光催化活性。

最近，Sun等报道了胶体碳球的制备。

碳球可以作为制备具有中空结构的金属氧化物的模板。

胶体碳球的表面是亲水性的，具有-OH和-C=O基团，这样就没有必要再进行表面改性了。

在本文中，为了提高二氧化钛可见光驱动光催化活性，我们用胶体碳球为模板制备了可见光响应N掺杂二氧化钛空心球。

二氧化钛(TiO2)的表面有机化及其在聚合物中的应用--本科毕业论文

目录摘要 (1)1.前言 (2)1.1TiO2的性质 (2)1.1.2物理性质 (3)1.1.2.1相对密度 (3)1.1.2.2熔点和沸点 (3)1.1.2.3介电常数 (3)1.1.2.4电导率 (3)1.1.3化学性质 (4)1.2有机处理 (4)1.3硅烷偶联剂 (5)2实验部分 (5)2.1实验药品 (5)2.2实验仪器 (6)2.3实验过程 (6)2.4性能测试 (7)2.4.1拉伸试验: (7)2.4.2冲击试验: (8)3结果和讨论 (8)3.1红外光谱分析 (8)3.2纳米TiO2/聚丙烯复合材料的力学性能 (9)3.3纳米TiO2/聚丙烯复合材料流变性能 (11)3.4结论 (13)4.TiO2在聚合物中的应用 (14)4.1二氧化钛在涂料工业中的应用 (14)4.2二氧化钛在塑料中的应用 (14)4.3二氧化钛在造纸中的应用 (14)4.4二氧化钛在油墨工业中的应用 (15)4.5二氧化钛在化纤中的应用 (15)4.6二氧化钛在化妆品中的应用 (16)4.7二氧化钛在橡胶中的应用 (16)4.8二氧化钛在搪瓷、陶瓷中的应用 (17)参考文献 (18)答谢 (19)诚信申明毕业论文（设计）是对我大学四年学习的总结和检阅，本人申明所呈交的论文，是我个人在教师指导下从相关调研活动基础上进行的研究成果（或搜集相关资料，运用所学理论进行分析、研究的成果）。

尽我所知，除了文章中特别加以标注和致谢的地方外，论文中不包含其他人已经发表或撰写过的研究成果，更不是其他人已经发表过的论文的翻版。

特此申明。

申明人：年月日TiO2的表面有机化及其在聚合物中的应用专业：高分子材料与工程姓名：** 指导老师：**摘要本文利用硅烷偶联剂（KH-570）对二氧化钛的表面进行有机改性处理，采用红外光谱（IR）分析手段对表面改性前后的纳米TiO2进行了表征，红外光谱表明，KH-570通过化学键形式结合在纳米TiO2表面，且形成有机包覆层；之后用熔体共混的方式制备了纳米TiO2/聚丙烯(PP)的复合材料，用简支梁冲击试验机和万能拉伸机对所制复合材料的力学性能和流动性能的研究，研究结果结果表明：复合材料的力学性能随纳米TiO2含量的增加呈现出拉伸强度下降,伸长率下降,模量和冲击强度提高的趋势。