纳米CaCO3/弹性体/PP杂化材料的性能及应用研究

采用母料共混法,制备了纳米CaCO3/弹性体/PP杂化材料,研究了力学性能和微观形态,以及在汽车保险杠中的应用。结果表明,纳米CaCO3/弹性体/PP杂化材料冲击强度较高,尤其是低温冲击强度。纳米CaCO3粒子具有使弹性体颗粒细化的作用。纳米CaCO3/弹性体/PP杂化材料应用于汽车保险杠料,可使低温冲击强度大幅度提高,弯曲弹性模量也同时提高。     

聚丙烯/轻质CaCO_3复合材料的力学性能研究

采用熔融共混的方法制备了PP/CaCO3复合材料,并研究了轻质CaCO3的表面处理、含量及粒径对材料的拉伸强度和缺口冲击强度两大主要力学性能的影响,着重对实验结果作了科学的理论分析。实验结果表明,钛酸酯类偶联剂能很好地改善CaCO3粒子与PP基体的界面相容性,从而使复合材料的力学性能提高;经表面处理后的超细轻质CaCO3(纳米级)所填充复合材料的拉伸强度和缺口冲击强度明显优于普通轻质CaCO3(微米级);而且处理后的纳米级CaCO3在填充量为10%时对PP的增强增韧效果最佳。     

PVC/VC-BA/纳米碳酸钙复合体系组成及加工工艺对材料力学性能的影响

对纳米碳酸钙(nano-CaCO3)表面恰当处理后,与聚氯乙烯(PVC)、氯乙烯-丙烯酸丁酯共聚弹性体(VC-BA)组成三元复合体系,详细研究了该复合体系的加工工艺及其组成与所制材料力学性能之间的关系。当复合母粒中VC-BA与CaCO3的质量比为2∶3时,材料的力学性能最佳,CaCO3对材料具有补强作用,并且CaCO3和VC-BA能协同增韧PVC,使材料的冲击强度得到大幅度提高,当PVC和复合母粒质量比为100∶20时,材料的冲击强度达到49.5kJ/m2,拉伸强度仍高达51.0MPa。     

纳米CaCO_3/EVA/PP共混制备多孔聚丙烯纤维

以纳米CaCO3为成孔剂,与聚丙烯(PP)、乙烯-乙酸乙烯酯嵌段共聚物(EVA)相混合制得共混纤维,将共混纤维进行酸处理和醇解处理后得到多孔聚丙烯纤维。研究了纳米CaCO3/EVA/PP共混物的力学性能,考察了纳米CaCO3/EVA/PP共混纤维的回潮率与表面形态。结果表明:随着EVA含量的增加,纳米CaCO3/EVA/PP共混纤维的力学性能下降,回潮率上升,纤维表面的微孔更加密集、均匀。     

不同形态的CaCO_3对聚丙烯的泡孔结构和力学性能的影响

通过熔融共混法制备聚丙烯/马来酸酐接枝聚丙烯/碳酸钙(PP/PP-g-MAH/CaCO3)复合材料母粒,利用"二次开模"法注塑成型制得PP/PP-g-MAH/CaCO3复合微孔发泡材料。通过对不同形态的CaCO3粒子对聚丙烯纳米复合材料发泡行为的影响研究,讨论了CaCO3粒子在聚合物微孔发泡中的作用机理,分析了CaCO3粒子对聚丙烯的力学性能及泡孔结构的影响规律。结果表明,不同形态的CaCO3粒子的加入都能够显著降低聚丙烯的泡孔直径和增加泡孔密度;CaCO3粒子使聚丙烯的缺口冲击强度下降;发泡材料的拉伸强度低于未发泡材料的拉伸强度。     

高流动性高韧性PP/POE共混材料研制

用聚烯烃弹性体(POE)代替传统的弹性体,对聚丙烯(PP)增韧改性,探讨了基体树脂、POE、HDPE、滑石粉、纳米CaCO3以及加工助剂EBS的用量对共混体系力学性能和流动性的影响.并通过扫描电镜观察冲击断面,研究共混物的形态结构.结果表明,POE能大幅度的改善材料的冲击韧性,HDPE和POE具有协同增韧效应,加工助剂EBS能改善PP共混材料的流动性,制得的PP改性材料具有高韧性和离流动性,可用于制造汽车装饰件.     

高流动性高韧性PP/POE共混体系材料研究

用聚烯烃弹性体（POE）代替传统的弹性体，对聚丙烯（PP）增韧改性。探讨了基体树脂、POE、高密度聚乙烯（HDPE）、滑石粉、纳米CaCO3以及润滑剂乙撑双硬脂酸酰胺（EBS）的用量对共混体系力学性能和流动性的影响。并通过扫描电镜观察冲击断面，研究共混物的形态结构。结果表明，POE能大幅度地改善材料的冲击韧性，HDPE与POE具有协同增韧效应，加工助剂EBS能改善PP共混材料的流动性，所制得的改性材料可用于制造汽车装饰件。     

PP/POE/CaCO3复合材料的性能研究

采用熔融共混工艺制备了聚丙烯/聚烯烃弹性体/碳酸钙(PP/POE/CaCO3)复合材料,研究了POE及CaCO3用量对复合材料力学性能、流变性能及热性能的影响。结果表明:随着POE含量的增加,复合材料的冲击强度显著增大,当POE含量为12%时,冲击强度较纯PP增加233%;同时拉伸强度随POE含量的增加缓慢下降。随着CaCO3含量增加,冲击强度先增加后缓慢下降。     

纳米CaCO3填充ABS/PP合金复合物研究

通过熔融共混使纳米CaCO3粒子周围包覆上一层TPE橡胶,制备出纳米CaCO3母料,用其与PP、ABS共混复合制备出ABS/PP合金纳米填料复合物.该复合材料力学性能及熔体流动性能测试结果表明,纳米CaCO3含量在试验用量范围内,ABS纳米CaCO3复合物的拉伸强度随填料含量的增加而增加,当母料含量为17%,母料中纳米CaCO3填料含量为60%左右时有较佳的冲击性能;ABS/PP纳米CaCO3复合物在PP含量9%～10%时有最好的拉伸强度和冲击强度;纳米CaCO3填料含量对复合物的拉伸强度影响不大,随其用量增加对冲击强度有明显的提高;熔体流动性能在PP含量10%左右时达最大,但随填料含量增加而下降.     

聚丙烯/弹性体/纳米CaCO3复合体系

研究了聚丙烯（PP）／弹性体和PP／弹性体／纳米CaCO3两种复合体系。结果表明，弹性体的加入使体系的冲击强度有很大提高，而拉伸和弯曲强度明显下降；添加8 phr左右的纳米CaCO3，体系的拉伸强度和弯曲强度得到较大提高。通过扫描电子显微镜观察冲击试样断面的形貌，可以很好地解释力学性能的变化。     

Polymorphism of LiGa5O8 and of LiGa5O8-MgGa2O4Solid Solutions

High-temperature X-ray diffraction and differential thermal analyses showed that LiGa₅O₈ exists in two polymorphs related by the first-order transition at 1138°±3°C of the low-temperature simple-cubic form, space group (probably) O⁷, to the high-temperature spinel (fcc) form, space group O _h ⁷. The transition is rapid, and the high-temperature form in pure LiGa₅O₈ could not be quenched to room temperature under the conditions used. However, the high-temperature polymorph can be quenched under equilibrium conditions when 40 mol% or more MgGa₂O₄ is present. The subsolidus equilibrium relations in the system MgGa₂O₄-LiGa₅O₈ are discussed.     

Magnetoresistance of CuxCo1-xFe2O4 Ferrites

Magnetoresistance measurements (Δ/R) were carried out on Cu _x Co_{1- x} Fe₂O₄ samples with x =1, 0.75, 0.50, 0.25 and cobalt ferrite in the range of magnetic intensity (H) from 1.0 to 4.5 kG. Linear plots were obtained between log (Δ/R) and log H for all compositions except that of cobalt ferrite. The values of n at x =0.5 do not agree with the results of some authors. The discrepancy may be attributed to the value of magnetic field intensity at which such measurements were carried out. The similarity of features of n and μ_D with composition leads us to believe that the magnetoresistance may arise from the scattering of conduction electrons by localized electrons involving the s-d exchange interaction.     

Sintering of Si3N4-Y2O3-Al2O3

Sintering kinetics of the system Si₃N4-Y2O₃-Al₂O3 were determined from measurements of the linear shrinkage of pressed disks sintered isothermally at 1500° to 1700°C. Amorphous and crystalline Si₃N₄ were studied with additions of 4 to 17 wt% Y₂O₃ and 4 wt% A1₂O₃. Sintering occurs by a liquid-phase mechanism in which the kinetics exhibit the three stages predicted by Kingery's model. However, the rates during the second stage of the process are higher for all compositions than predicted by the model. X-ray data show the presence of several transient phases which, with sufficient heating, disappear leaving mixtures of β ' -Si₃N₄ and glass or β '-Si₃N₄, α '-Si₃N₄, and glass. The compositions and amounts of the residual glassy phases are estimated.     

Expansive properties of the mixture C4ASH12 − 2CS III. Effects of temperature and restraint

The effects of temperature and restraint upon the hydration and the expansion of $\text{C}{}_4\text{A}\text{S}\text{H}{}_{12}\text{? 2}\text{C}\text{S}$ mixture compacts in different contact solutions have been investigated. Temperatures above 20°C do apparently hinder the formation of an impervious felt-like layer of ettringite around the $\text{C}{}_4\text{A}\text{S}\text{H}{}_{12}$ particles, thus greatly reducing the retarding effect of the lime. An uniaxial restraint of 1 Kg/cm² is enough to reduce sensibly the expansions which remain however high (about 100%). The results can be satisfactorily interpreted by the reaction and expansion mechanism hypothesized in our previous papers.     

Raman Study of Glasses of Ba2TiSi2O8 and Ba2TiGe2O8

Raman spectra are reported for fresnoite (Ba₂Ti(Si,Ge)₂O₈ glasses, and comparison is made between the Raman spectra of the corresponding crystalline powders and glasses of Ba₂TiSi₂O₈ and Ba₂TiGe₂O₈. The Ba₂TiGe₂O₈ glass spectra show correspondence with the Ba₂TiGe₂O₈ crystalline Raman spectra; the v _s(Ge–O–Ge) mode occurs at 518 cm⁻¹ in the glass and at 521 cm⁻¹ in the crystalline material. Five-fold coordinated titanium is the majority species present in the Ba₂TiGe₂O₈ glass as revealed by a strong band at 824 cm⁻¹ in the I glass spectrum. The Ba₂TiSi₂O₈ glass spectra are similar to the Ba₂TiSi₂O₈ crystalline spectrum; the strongest band is found at 836 cm⁻¹ in the I glass spectrum. Through comparison with the previous Raman data of other titania silicate glasses, we conclude that the Ba₂TiSi₂O₈ glass has a structure similar to the crystalline phase.     

Preparation and properties of poly(Nε,Nε-dicarboxymethyl-l-lysine)

A new ampholytic homopolypeptide, $\text{poly}\text{(N}{}^{\mathrm{\epsilon }}\text{,N}{}^{\mathrm{\epsilon }}\text{-}\text{dicarboxy-methyl-}\text{l}\text{-lysine}\text{)}$, which has one tertiary amino and two carboxyl groups in the side chain has been derived from a hydrochloride salt of poly(L-lysine). The polymer in aqueous solution seems to be in the coil form with locally extended structure (LES) at neutral pH. In both the acidic and alkaline regions, the molar ellipticity of the polymer changes as a result of change in net charge on the side chain. The conformational changes may be from the coil with LES to other coiled forms. 5–7 M NaClO₄ and 80% aqueous methanol induce the α-helix in the polymer at neutral pH. Divalent cations, Cu²⁺ and Ca²⁺, do not induce any remarkably ordered structures such as α-helix or β-structure in the polymer in aqueous solution at any pH. Ultraviolet absorption studies show an absorption peak of the polymer-Cu²⁺ complex near 240 nm. Dependence of the peak intensity on pH at various q values ($\text{q =}\text{[}\text{Cu}{}^{\mathrm{2+}}\text{]}\text{[}\text{residue}\text{]}$) indicates the two steps of the complex formation. At q less than 0.64, the formation is described only with the first step. An average coordination number for Cu²⁺ at the first step was calculated to be about 2 by the method of Mandel and Leyte. The association constant of Cu²⁺ with the residue at the step was determined from the absorption data to be far smaller than that for the Cu²⁺-EDTA complex. The second step of the formation occurs in the case of large q but the absorption data for the second step cannot be obtained exactly due to precipitation.     

Effects of metal-support interactions on the hydrogenation of CO over PdSiO2 and PdLa2O3

A study of CO hydrogenation over $\text{Pd}\text{SiO}{}_2$ and $\text{Pd}\text{La}{}_2\text{O}{}_3$ has been carried out for the purpose of identifying the effects of Pd dispersion, Pd morphology, and support composition on the catalytic activity of supported Pd. The specific activity of each catalyst for methanol and methane synthesis was determined from microreactor studies carried out at a fixed set of reaction conditions. Palladium dispersion was measured by H₂O₂ titration, and the morphology of the Pd crystallites, as expressed by the distribution of Pd(100) and Pd(111) planes, was determined from in situ infrared spectra of adsorbed CO. The crystallite morphology of the $\text{Pd}\text{SiO}{}_2$ catalysts is the same, independent of Pd weight loading: 90% of the surface is comprised of Pd(100) planes and 10% of the surface is comprised of Pd(111) planes. By contrast, the crystallite morphology of the $\text{Pd}\text{La}{}_2\text{O}{}_3$ catalysts changes with Pd loading. Primarily Pd(100) planes are exposed at low-weight loadings while Pd(111) planes are exposed at high-weight loadings. The Pd dispersion has little effect on the methanol turnover frequency over both $\text{Pd}\text{SiO}{}_2$ and $\text{Pd}\text{La}{}_2\text{O}{}_3$, for dispersions between 10 and 20%. On the other hand, the methane turnover frequency is independent of Pd dispersion over $\text{Pd}\text{SiO}{}_2$, but increases with decreasing dispersion over $\text{Pd}\text{La}{}_2\text{O}{}_3$. It is further observed that the Pd morphology influences the specific activity of $\text{Pd}\text{La}{}_2\text{O}{}_3$ for methanol synthesis: Pd(100) is nearly threefold more active than Pd(111). For a fixed morphology, the specific methanol synthesis activity of $\text{Pd}\text{La}{}_2\text{O}{}_3$ is a factor of 7.5 greater than that of $\text{Pd}\text{SiO}{}_2$.     

In situ laser raman spectroscopy of the sulfiding of Moγ-Al2O3 catalysts

Raman spectra of sulfided $\text{Mo}\text{γ-}\text{Al}{}_2\text{O}{}_3$ catalysts were obtained using in situ techniques for two sulfiding methods. For samples sulfided by 10% $\text{H}{}_2\text{S}\text{H}{}_2$ at 400 °C, MoS₂ structures were observed. A stepwise sulfiding using 10% $\text{H}{}_2\text{S}\text{H}{}_2$, with spectra recorded at 150, 250, and 350 °C, resulted in observation of molybdenum oxysulfide, reduced molybdate, and surface “MoS₂” phases. Reexposure of these samples to air led to radical modification of the oxysulfide structures as well as transformation of some sulfide phases. A model incorporating terminal and bridging MoS bonding and anion vacancies is proposed. This model is based on the conversion of isolated and aggregated molybdate and MoO₃ species to oxysulfide and reduced molybdenum phases. Conversion of reduced molybdenum phases to sulfides is observed to be slow.     

Wet Milling of Fe/Al/Al2O3 and Fe2O3/Al/Al2O3 Powder Mixtures

Wet milling of Al₂O₃-aluminide alloy (3A) precursor powders in acetone has been investigated by milling Fe/Al/Al₂O₃ and Fe₂O₃/Al/Al₂O₃ powder mixtures. The influence of the milling process on the physical and chemical properties of the milled powders has been studied. Particle refinement and homogenization were found not to play a dominant role, whereas plastic deformation of the metal particles leads to the formation of dislocations and a highly disarranged polycrystalline structure. Although no chemical reactions among the powder components in Fe₂O₃/Al/Al₂O₃ powder mixtures were observed, the formation of a nanocrystalline, ordered intermetallic FeAl phase in Fe/Al/Al₂O₃ powder mixtures caused by mechanical alloying was detected. Chemical reactions of Fe and Al particle surfaces with the atmosphere and the milling media lead to the formation of highly porous hydroxides on the particle surfaces. Hence the specific surface area of the powders increases, while the powder density decreases during milling. The fraction of Fe oxidized during milling was determined to be 0.13. The fraction of Al oxidized during milling strongly depends on the metal content of the powder mixture. It ranges between 0.4 and 0.8.