氧化石墨烯/氟橡胶复合材料的制备及性能研究

采用机械共混法制备氧化石墨烯/氟橡胶复合材料,研究复合材料的硫化特性、耐绝缘介质苄基甲苯浸渍性能、阻尼性能和物理性能,并对其加工性能进行优化。结果表明：氧化石墨烯/氟橡胶复合材料的耐苄基甲苯浸渍性能优异;氧化石墨烯能够有效增大复合材料的拉伸强度;阻尼填料受阻酚HP1098能够增大复合材料的损耗因子,扩宽阻尼温域;惰性端基液体氟弹性体能够有效提高复合材料的加工性能。     

液体氟弹性体/固体氟橡胶复合材料的制备与性能研究

制备液体氟弹性体/固体氟橡胶复合材料,并研究液体氟弹性体/固体氟弹性体用量比（简称液固比）对复合材料性能的影响。结果表明：与固体氟橡胶相比,液体氟弹性体/固体氟橡胶复合材料的加工性能明显提高,物理性能、耐热性能、耐油性能和阻尼性能略有降低,但变化不大;液固比为5/95的复合材料综合性能较好。     

碳化硅/环氧树脂复合材料的制备及性能研究

分别采用固化剂D230、9035、acamine2636与环氧树脂E51混合,然后分别与用硅烷偶联剂(KH550、KH560、A171)处理的碳化硅颗粒混合,采用浇注法制备了碳化硅/环氧树脂复合材料。以材料的弯曲强度为评价方法,研究了3种不同固化剂构成的环氧树脂体系以及3种硅烷偶联剂对碳化硅/环氧树脂复合材料性能的影响,以及复合材料弯曲强度与材料中环氧树脂含量的关系。结果表明,3种固化剂中以D230、9035制备的材料性能为好;采用KH550、KH560处理碳化硅颗粒后的材料性能比不处理或采用A171处理碳化硅颗粒后的材料性能为好。随着复合材料中环氧树脂相含量的增加复合材料的弯曲强度下降。     

氟橡胶/丁腈橡胶共混体系性能研究

将氟橡胶与丁腈橡胶以不同比例进行共混,考察了共混体系的硫化特性、力学性能以及不同温度条件下的耐介质性能。结果表明,随着丁腈橡胶并用比例的增加,胶料的硫化速率减慢,硬度提高,伸长率增大,相对密度减小。在耐久性方面,随着丁腈橡胶并用比例的增加以及各种介质温度的升高,胶料的质量变化率增大,在并用比例为85/15时共混胶具有较好的综合性能。     

白炭黑增强氟橡胶体系的耐等离子体刻蚀性能研究

以高氟橡胶生胶、白炭黑等为主要原料,制备了过氧化物硫化氟橡胶。研究了体系的硫化特性、力学性能、热稳定性和耐等离子体性能。研究结果表明：白炭黑用量对焦烧时间影响不大,且都具有较好的稳定性。当白炭黑用量为15～20质量份时,力学性能最优,最大拉伸强度和撕裂强度分别为19.8 MPa和36.4 kN/m。添加白炭黑的氟橡胶体系都具有优异的热稳定性和耐等离子体性能,初始分解温度都在405℃左右,刻蚀后的重量损失率都在3.4%～3.8%之间,表面变化更加均匀。进一步分析等离子体刻蚀造成的化学变化,在等离子体刻蚀条件下表面的C—F键大大减少,失去F原子屏蔽的主链发生断裂,低分子降解产物和白炭黑“颗粒”都逸出材料表面。     

石墨烯/氟橡胶复合材料及其制备方法

正授权公告号:CN 105968658B授权公告日:2018年5月1日专利权人:中国工程物理研究院化工材料研究所发明人:聂福德、曾贵玉、林聪妹等本发明公开了一种石墨烯/氟橡胶复合材料的制备方法,具体步骤如下。第1步:将石墨烯置于乙酸乙酯中超声分散得到石墨烯分散液;第2步:将氟橡胶加入石墨烯分散液中,搅拌均匀得到混合液;第3步:将混合液在搅拌下加热回流,再在75～85℃下冷凝回流,得到石墨烯/氟橡胶复合材料。该复合材料结构均匀,分散性好,且制备过程简单,材料易得,可降低成本。     

碳化硅/环氧树脂导热复合材料的制备与性能

采用浇铸成型法制备碳化硅/环氧树脂(SiC/EP)导热复合材料,研究了SiC种类、粒径、用量和表面改性方法对SiC/EP复合材料的导热性能、力学性能和热性能等影响。结果表明:SiC/EP复合材料的导热系数随纳米级SiC用量增加而增大,当φ(纳米级SiC)=17.80%时,导热系数为0.954 6 W/(m.K);SiC/EP复合材料的弯曲强度和冲击强度随纳米级SiC用量增加均呈先升后降态势,当φ(纳米级SiC)=3.50%时,两者均达到最大值。SiC经表面改性后可有效提高复合材料的导热性能和力学性能,并且改性SiC的加入可有效降低EP的玻璃化转变温度。     

机械混炼法制备氟橡胶/有机蒙脱土纳米复合材料的结构与性能

选择实验室自制的3种有机蒙脱土，采用双辊混炼法制备了氟橡胶／有机蒙脱土复合材料。力学性能测试结果表明，氟橡胶／2^#有机蒙脱土复合材料具有优异的力学性能。研究了复合材料的微观结构及其应力应变行为、动态力学性能和热稳定性能。结果表明，实验制备出了一种插层型纳米复合材料；该复合材料具有较小的滚动阻力和优异的热稳定性能。     

碳纤维/硅橡胶/氟橡胶复合材料的制备

以硅橡胶(MVQ)/氟橡胶(FKM)并用胶为基相、碳纤维(CF)为补强相制备CF/MVQ/FKM复合材料。最佳配方为:FKM混炼胶90,MVQ混炼胶10,白炭黑20,硅烷偶联剂KH590 2.5,CF(纤维长度为12 mm)8;其中FKM混炼胶配方为FKM 100,氢氧化钙6,氧化镁3,3~#硫化剂3;MVQ混炼胶配方为MVQ 100,氧化锌3,三氧化二铁1,防老剂D 1,硫化剂DCP 5,促进剂M 1.5。最佳一段和二段硫化条件分别为170℃/10 MPa×30 min和200℃(常压)×2 h。     

Silicon Carbide Platelet/Silicon Carbide Composites

α-silicon carbide platelet/β-silicon carbide composites have been produced in which the individual platelets were coated with an aluminum oxide layer. Hot-pressed composites showed a fracture toughness as high as 7.2 MPa·m^1/2. The experiments indicated that the significant increase in fracture toughness is mainly the result of crack deflection and accompanying platelet pullout. The coating on the platelets also served to prevent the platelets from acting as nucleation sites for the α- to β-phase transformation, so that the advantageous microstructure remains preserved during high-temperature processing.     

Silicon Carbide/Silicon and Silicon Carbide/Silicon Carbide Composites Produced by Chemical Vapor Infiltration

Composites of SiC/Si and SiC/SiC were prepared from single yarns of SiC. The use of carbon coatings on SiC yarn prevented the degradation normally observed when chemically vapor deposited Si is applied to SiC yarn. The strength, however, was not retained when the composite was heated at elevated temperatures in air. In contrast, the strength of a SiC/C/SiC composite was not reduced after this composite was heated at elevated temperatures, even when the fiber ends were exposed.     

Mechanical Properties of Alumina/Silicon Carbide Whisker Composites

The improvement of mechanical properties of Al₂O₃/SiC whisker composites has been studied with emphasis on the effects of the whisker content and of the hot-pressing temperature. Mechanical properties such as fracture toughness and fracture strength increased with increasing whisker content up to 40 wt%. In the case of the high SiC whisker content of 40 wt%, fracture toughness of the sample hot-pressed at 1900° decreased significantly, in spite of densification, compared with one hot-pressed at 1850°. Fracture toughness strongly depended on the microstructure, especially the distribution of SiC whiskers rather than the grain size of the Al₂O₃ matrix.     

Stress-Corrosion Cracking of Silicon Carbide Fiber/Silicon Carbide Composites

Ceramic-matrix composites are being developed to operate at elevated temperatures and in oxidizing environments. Considerable improvements have been made in the creep resistance of SiC fibers and, hence, in the high-temperature properties of SiC fiber/SiC (SiC_f/SiC) composites; however, more must be known about the stability of these materials in oxidizing environments before they are widely accepted. Experimental weight change and crack growth data support the conclusion that the oxygen-enhanced crack growth of SiC_f/SiC occurs by more than one mechanism, depending on the experimental conditions. These data suggest an oxidation embrittlement mechanism (OEM) at temperatures <1373 K and high oxygen pressures and an interphase removal mechanism (IRM) at temperatures of ≳700 K and low oxygen pressures. The OEM results from the reaction of oxygen with SiC to form a glass layer on the fiber or within the fiber–matrix interphase region. The fracture stress of the fiber is decreased if this layer is thicker than a critical value ( d > d _c) and the temperature below a critical value ( T < T _g), such that a sharp crack can be sustained in the layer. The IRM results from the oxidation of the interfacial layer and the resulting decrease of stress that is carried by the bridging fibers. Interphase removal contributes to subcritical crack growth by decreasing the fiber-bridging stresses and, hence, increasing the crack-tip stress. The IRM occurs over a wide range of temperatures for d < d _c and may occur at T > T _g for d > d _c. This paper summarizes the evidence for the existence of these two mechanisms and attempts to define the conditions for their operation.     

Reaction Bonding and Mechanical Properties of Mullite/Silicon Carbide Composites

Based on the RBAO technology, low-shrinkage mullite/SiC/ Al₂O₃/ZrO₂ composites were fabricated. A powder mixture of 40 vol% Al, 30 vol% A1₂O₃ and 30 vol% SiC was attrition milled in acetone with TZP balls which introduced a substantial ZrO₂ wear debris into the mixture. The precursor powder was isopressed at 300–900 MPa and heattreated in air by two different cycles resulting in various phase ratios in the final products. During heating, Al oxidizes to Al₂O₃ completely, while SiC oxidizes to SiO₂ only on its surface. Fast densification (at >1300°C) and mullite formation (at 1400°C) prevent further oxidation of the SiC particles. Because of the volume expansion associated with the oxidation of Al (28%), SiC (108%), and the mullitization (4.2%), sintering shrinkage is effectively compensated. The reaction-bonded composites exhibit low linear shrinkages and high strengths: shrinkages of 7.2%, 4.8%, and 3%, and strengths of 610, 580, and 490 MPa, corresponding to compaction pressure of 300, 600, and 900 MPa, respectively, were achieved in samples containing 49–55 vol% mullite. HIPing improved significantly the mechanical properties: a fracture strength of 490 MPa and a toughness of 4.1 MPa^.m^1/2 increased to 890 MPa and 6 MPa^.m^1/2, respectively.     

Microstructure of Silicon Carbide/Carbon Composites and Relationships with Mechanical Properties

Three different 2-D SiC/C composites, analyzed by TEM, have mechanical performances directly controlled by the interfacial structure resulting from processing. Localized attachment of the fibers to a brittle matrix constituent is shown to be responsible for composite weakening by impeding interface debonding and sliding. Moreover, the particulate phase used in the matrix is found to have a strong influence. There is a consequent sensitivity of composite strength to the particulate properties. Finally, it is demonstrated that the hindrance of debonding and sliding caused by the brittle matrix phase can be suppressed by using a C fiber coating.     

Silicon Carbide Platelet/Alumina Composites: II, Mechanical Properties

The mechanical properties, i.e., Young's modulus, fracture toughness, and flexural strength, of SiC-platelet/Al₂O₃ composites with two different platelet sizes were studied. Both Young's modulus and the fracture toughness of composites using small platelets (12 μm) increased with increasing SiC volume fraction. Maximum values for toughness and Young's modulus of 7.1 MPa·m^1/2 and 421 GPa were obtained for composites containing 30 vol% platelets. Composites fabricated using larger platelets (24 μm), however, showed spontaneous microcracking at SiC volume fractions of ≤0.15. The presence of microcracks decreased Young's modulus and the fracture toughness substantially. Two types of radial microcracks were identified by optical microscopy and found to be consistent with a residual stress analysis. Anisotropy in fracture toughness was identified with a crack length indentation technique. Cracks propagating in a plane parallel to platelet faces experienced the least resistance, which was the the lowest toughness plane in platelet composites with preferred orientation. Enhanced fracture toughness was found in the plane parallel to the hot-pressing direction, but no anisotropy in toughness was observed in this plane. The flexural strength of alumina showed a decrease from 610 to 480 MPa for a 30 vol% composite and was attributed to the presence of the platelets.     

Effect of Composition on Properties of Alumina/Titanium Silicon Carbide Composites

In the present study, the room-temperature properties of Al₂O₃-Ti₃SiC₂ composites with different Ti₃SiC₂ contents are determined. The composites are prepared by attrition milling Al₂O₃ and Ti₃SiC₂ mixture powders followed by spark plasma sintering (SPS) under vacuum. From a closer examination of the dependencies of the electrical conductivity on compositions in this system, we determined the percolation threshold at which an interconnected network of electrically conductive phase arises. Since the hardness of Ti₃SiC₂ is lower than that of Al₂O₃, the Vickers hardness decreased with the increasing of Ti₃SiC₂ content while the fracture toughness and the strength increased. The maximum strength (673 MPa) and the maximum toughness (9.3 MPa·m^1/2) were reached in the pure Ti₃SiC₂ material.