泡沫碳化硅陶瓷表面原位生长碳化硅晶须

采用固相和液相反应法在泡沫碳化硅陶瓷骨架表面原位生长碳化硅晶须,研究了催化剂和反应温度的影响．结果表明,催化剂氯化镍的作用使硅与碳直接反应生长出细长的碳化硅晶须．在适当的反应温度下生长的碳化硅晶须的表面光滑,线径比较大,有少量的呈弯曲状或竹节状;反应温度过高使得硅晶须的缺陷较多．在泡沫碳化硅陶瓷骨架的表面原位生长出碳化硅晶须属于LS生长机理．具有表面晶须的碳化硅陶瓷以深床体积过滤的方式用于过滤柴油机汽车尾气中的碳颗粒,表面晶须既能提高泡沫陶瓷过滤器的过滤能力,又有利于过滤器的再生．     

碳化硅表面改性和光学镜面加工的研究现状

为了获得满足光学应用要求的碳化硅光学镜面, 通常采取碳化硅表面改性和改进光学镜面加工的方法. 碳化硅表面改性的主要方式是在碳化硅表面镀致密化涂层. 本文介绍了在碳化硅表面化学气相沉积碳化硅和物理气相沉积硅两种碳化硅表面改性技术, 并对碳化硅光学镜面加工的研究现状进行了综述.     

在泡沫碳化硅载体上原位生长silicalite-1型沸石晶体

以多晶硅颗粒为硅源,在泡沫碳化硅载体上原位水热合成silicalite-1型沸石晶体。研究了硅颗粒加入量、NaOH浓度以及合成时间等因素对沸石晶体的负载量、晶体尺寸和沸石晶体/泡沫碳化硅复合材料比表面积的影响。结果表明,以多晶硅颗粒为硅源控制硅酸根的释放速度,使沸石晶体在碳化硅载体表面异质界面形核,从而实现沸石晶体在泡沫碳化硅载体表面的连续生长;当多晶硅量过少时,溶液中的硅酸根浓度过低,不能在载体表面形成连续生长的沸石层;而当多晶硅量过大时,溶液中硅的浓度过高,部分沸石晶体在溶液当中形核,使沸石晶体在载体表面的负载量下降;提高溶液中NaOH的浓度,加快硅的溶解,使溶液中硅的饱和浓度升高,沸石晶体的形核率也随之升高,使沸石晶体的负载量增加。在最优条件下制备的silicalite-1/泡沫碳化硅复合材料其沸石晶体的比表面积为81.28 m~2g~(-1)。     

在泡沫碳化硅载体上原位生长silicalite-1型沸石晶体

以多晶硅颗粒为硅源, 在泡沫碳化硅载体上原位水热合成silicalite--1型沸石晶体。研究了硅颗粒加入量、NaOH浓度以及合成时间等因素对沸石晶体的负载量、晶体尺寸和沸石晶体/泡沫碳化硅复合材料比表面积的影响。结果表明,
以多晶硅颗粒为硅源控制硅酸根的释放速度, 使沸石晶体在碳化硅载体表面异质界面形核, 从而实现沸石晶体在泡沫碳化硅载体表面的连续生长; 当多晶硅量过少时, 溶液中的硅酸根浓度过低, 不能在载体表面形成连续生长的沸石层;
而当多晶硅量过大时, 溶液中硅的浓度过高, 部分沸石晶体在溶液当中形核, 使沸石晶体在载体表面的负载量下降; 提高溶液中NaOH的浓度, 加快硅的溶解, 使溶液中硅的饱和浓度升高, 沸石晶体的形核率也随之升高, 使沸石晶体的负载量增加。在最优条件下制备的silicalite--1/泡沫碳化硅复合材料其沸石晶体的比表面积为81.28 m²g^-1。     

溶胶凝胶原位成型陶瓷结合剂砂轮中碳化硅的改性

使用硅烷偶联剂KH550作为表面活性剂对碳化硅微粉表面进行改性,使用扫描电镜、X射线衍射仪、激光粒度分析仪和红外光谱仪等手段研究了改性前后微粉的形貌、表面性质、粒度分布及烧结体微观形貌。结果表明,硅烷偶联剂与碳化硅通过接枝反应在其表面形成包覆层,但是不改变其物相和结构。改性后碳化硅微粉的团聚减少,因此平均粒径减小;颗粒间的静电斥力和空间位阻增大,改善了碳化硅颗粒在溶胶中的悬浮稳定性和分散性。与未改性的SiC相比,用溶胶凝胶原位成型SiC/陶瓷复合材料改性后SiC与陶瓷的烧结体结构均匀,抗弯强度较高。     

陶瓷/树脂/纤维超混杂复合材料的界面控制

以具有不同表面状态的泡沫SiC陶瓷为基本骨架,以改性酚醛树脂为基体,加入短切高硅氧玻璃纤维制备了陶瓷/纤维/树脂超混杂复合材料,研究了界面控制对超混杂复合材料界面粘结强度的影响.结果表明,对于泡沫SiC陶瓷骨架,在表面生长多孔过渡层或表面堆积SiC颗粒等方法可提高树脂陶瓷之间界面的粘结强度.通过良好的界面控制,可显著提高复合材料的弯曲强度和弯曲模量,模量的提高比强度的提高幅度更大.偶联剂处理使高硅氧纤维与树脂基体的粘结强度增加,从而提高复合材料的弯曲强度.     

泡沫碳化硅陶瓷的导电性能

采用高分子热解和反应烧结方法制备出泡沫碳化硅陶瓷，研究了泡沫碳化硅陶瓷的体积分数变化和钛的掺杂对泡沫碳化硅陶瓷骨架导电性能的影响．结果表明：随着泡沫碳化硅陶瓷的体积分数提高，泡沫碳化硅陶瓷的电阻率降低，这是泡沫碳化硅陶瓷筋中部碳化硅的面积增加所引起的；掺杂的钛转变成TiSi2导电相改善了泡沫碳化硅陶瓷的导电性能．TiSi2呈现离散和团聚两种形态分布，以不规则的形状位于碳化硅晶界之间，在碳化硅中作为施主杂质．泡沫碳化硅陶瓷表现出的正或负温度系数取决与掺杂的钛量的多少．     

碳化硅泡沫陶瓷的制备

碳化硅泡沫陶瓷具有气孔率高、热稳定性好等优良性能,被广泛用作金属溶液过滤器、高温气体和离子交换过滤器、催化剂载体等.重点介绍了碳化硅泡沫陶瓷的种类,阐述了碳化硅泡沫陶瓷的制备方法和影响碳化硅泡沫陶瓷产品性能的因素,展望了碳化硅泡沫陶瓷的发展前景.     

碳化硅吸波性能改进的研究

采用三种不同的方法对碳化硅粉在2-18GHz范围的吸波性能进行了改进。化学还原的方法制备出粒度约为0.2μm左右的超细镍粉，与碳化硅混和，在一定的配比下制备成吸波涂层材料大幅度改善了吸波性能。吸波涂层最小反射率能够达到-23.59dB，提出了微观层复合的设想，并利用化学镀的方法对碳化硅粉表面进行了改性处理，使金属镍沉积在碳化硅颗粒的表面，材料在合理配比下的最小反射率为-22.07dB，采用宏观层复合的方法，将超细镍粉涂层与碳化硅涂层复合制备成多层吸波材料，改善了吸收峰值和吸收带宽。     

泡沫碳化硅

1.前言碳化硅作为非氧化物陶瓷的代表,具有很高的耐热性和热导率、优良的耐药品性等特长。泡沫碳化硅,就是将碳化硅成型为泡沫的一种陶瓷类多孔体。它在碳化硅原有特性的基础上又新增加了好几种特长。下面仅就日本东海炭素公司制造并销售的泡沫碳化硅的特性及应用实例加以介绍。该公司的泡沫碳化硅具有三维网状骨架结构,气孔率非常高,通气性良好,具有能够通电发热的性能。只要把它的三维网状结构和陶瓷物质、通电发热等特点结合起来,就有希望在各种领域开发用途。     

CVD SiC涂层SiC纤维增强SiC复合材料的研究

本文采用CVD技术对KD-1 SiC纤维作涂层处理,再通过聚碳硅烷浸渍裂解法制备单向SiCf/SiC复合材料.研究了不同沉积时间的CVDSiC涂层对SiCf/SiC复合材料性能的影响,同时运用SEM研究了SiC纤维表面SiC涂层的形貌.结果表明:经过5小时CVDSiC涂层SiCf/SiC复合材料具有良好的力学性能和抗氧化性能.     

Growth of SiC particles in reaction sintered SiC

For reaction sintered SiC (RSSC) prepared at 1600°C by conventional melt infiltration technique, experimentation with two different particle sizes of initial SiC, viz., 0.2 and 23.65 μm, showed that the large SiC particles remained unaltered and the sizes of the fine-grained SiC increased several times yielding well-developed faceted crystals in the final material. To study the process further, compacts of SiC powder of particle sizes varying between 0.20 and 8.99 μm were reacted with pure Si at 1600°C and the resulting SiC–Si boundaries were studied by optical microscopy. A distinct boundary layer with no penetration of Si in the compact of SiC of 0.2 μm was observed and the width of the SiC–Si boundary was found to be increasing linearly with time. Detailed SEM examination establishes the growth of the SiC upto around 4 μm from 0.2 μm starting powder. No such growth was observed in the case of starting SiC powder coarser than 0.2 μm. The growth of SiC is explained in terms of solution-reprecipitation mechanism.     

Long-term strength of SiC fibers with nanocrystalline SiC coatings

The long-term strength σ_t of SiC fibers coated with SiC nanoparticles is approximately equal to30·10 ⁷ pa for t=200h at 1500K. The long-term strength of coated fibers is lower than for fibers without coatings by 25–50%. Owing to their enhanced reaction characteristics, the nanocrystalline SiC coatings are sintered at T<1500K, which is lower than the temperature of sintering of self-bonded SiC by 500 K. For this reason, we can recommend coated SiC fibers for manufacturing SiC/SiC composites by sintering at a temperature of 1500K because, at this temperature, SiC fibers do not degrade. Shevchenko National University, Kiev, Ukraine. Translated from Problemy Prochnosti, No. 1, pp. 95 – 99, January – February, 1998.     

Fatigue behaviour of 3-d SiC/SiC Composites

A tension–tension fatigue damage analysis was performed using 3-d silicon carbide fibre reinforced (orthogonal) silicon carbide matrix (SiC/SiC) composites. Two groups of SiC/SiC specimens were tested. The first group consisted of samples without any oxidation protective top layer coating, whilst the latter one contained samples covered with a well fitting, chemical vapour deposited (CVD) SiC system. This coating is necessary for the material to sustain high temperatures. Both the coated and uncoated material had a fibre volume fraction of about 36% equally distributed in three rectangular directions. Load control fatigue tests were conducted at room temperature. The fatigue life was found to decrease by increasing the cyclic stress level. A power-law equation is proposed, which correlates the applied maximum stress during the fatigue test with the number of cycles to failure. In general, the presence of the coating layer decreases the static strength of the material. However, the nominal maximum cyclic stress for which the endurance fatigue limit appeared, remained unaffected by the presence of the oxidation protective SiC coating. Microstructural examination has also been performed on the fractured specimens and it reveals some of the failure mechanisms of the composite that appeared under quasi-static and dynamic loading.     

不同界面SiC/SiC复合材料的断裂行为研究

碳化硅纤维增强碳化硅复合材料(SiC/SiC)是极具前景的高温结构材料。通过先驱体浸渍裂解(PIP)工艺分别制备了PyC界面和CNTs界面SiC/SiC复合材料, 对两种SiC/SiC复合材料的整体力学性能以及界面剪切强度等进行了测试表征, 并对材料中裂纹的产生与扩展进行了原位观测。结果表明, 两种界面SiC/SiC复合材料弯曲强度相近, 但PyC界面SiC/SiC复合材料的断裂韧性约为CNTs界面SiC/SiC复合材料的两倍。在PyC界面SiC/SiC复合材料中, 裂纹沿纤维-基体界面扩展, PyC涂层能够偏转或阻止裂纹, 材料呈现伪塑性断裂特征; 而在CNTs界面SiC/SiC复合材料中, 裂纹在扩展路径上遇到界面并不偏转, 初始裂纹最终发展为主裂纹, 材料呈现脆性断裂模式。     

SiC及a-SiC：H薄膜的辐照及其进展

SiC是一种宽带隙半导体材料,在高温,高频在,大功率,光电子及抗辐射等方面具有巨大的应用潜力,介绍了国外对该材料及其薄膜进行辐照的一些结果,并指出开展SiC及其薄膜辐照效应研究的重要意义,预测了其发展方向和应用前景。     

Localized mechanical property assessment of SiC/SiC composite materials

SiC fiber-reinforced SiC matrix composites (SiC/SiC) are under consideration as a structural material for a range of nuclear applications. While these materials have been studied for decades, recently new small scale materials testing techniques have emerged which can be used to characterize SiC/SiC materials from a new perspective. In this work cross section nanoindentation was performed on SiC/SiC composites revealing that both the hardness and Young’s modulus was substantially lower in the fiber compared to the matrix despite both being SiC. Using scanning electron microscopy it was observed that the grain growth of the matrix during formation was radially out from the fiber with a changing grain structure as a function of radius from the fiber center. Focused ion beam machining was used to manufacture micro-cantilever samples and evaluate the fracture toughness and fracture strength in the matrix as a function of grain orientation in the matrix. Additionally microstructural characterization techniques like Raman spectroscopy, X-ray diffraction, and microtomography were used to evaluate differences in the matrix and fibers of the composite.     

An approach to the mechanical behaviour of SiC/SiC and C/SiC ceramic matrix composites

The mechanical behaviour of two woven composites C/SiC and SiC/SiC was investigated at room temperature. The non-linear load-displacement curves and the damaging process were closely related to the specific structure of the composites, consisting of a network of impregnated bundles of fibres. The damage in the bundles proceeded by multiple cracking in the matrix before fibre failure, and dictated the response to the applied load. Other mechanisms, consisting mainly of distortions in bundles and their framework, induced a residual deformation and an energy dissipation. The behaviour was characterized according to the damaging process. Stress-electric strain curves revealed a mechanical response similar to those observed in unidirectional composites, although some effect of the specimen geometry on the curves was observed. Residual strains were similar in tensile and bending conditions. The work of fracture was consistently described by a volumetric rate of energy absorption, related to the applied strain, but the respective contributions of different damage mechanisms could not be determined.