316L纤维尺寸和含量对HA-ZrO2(CaO)/316L纤维复合生物材料性能的影响

研究了316L纤维的长度、直径与含量对HA-ZrO_2（CaO）/316L纤维生物复合材料的力学性能的影响规律.结果表明：纤维直径为40μm的复合材料力学性能优于纤维直径为50μm的复合材料;纤维长度为0.8～1.2mm的复合材料力学性能优于纤维长度为2～3mm的复合材料;随着纤维体积分数增大,纤维之间相互接触而导致在复合材料中形成的微孔增多,并成为微裂纹源,导致材料力学性能下降.含20vol%直径为40μm、长度为0.8～1.2mm的316L纤维的HA-ZrO_2（CaO）/316L纤维生物复合材料的综合力学性能最佳,其抗弯强度、杨氏模量、断裂韧性和相对密度分别为140.1MPa、117.8GPa、5.81MPa·m~（1/2）和87.1%.复合材料微观组织随HA粉末和316L纤维成分的变化呈规律性变化,没有出现明显的裂纹或孔隙,316L纤维与HA-ZrO_2（CaO）基体紧紧地咬合在一起,其结合主要靠基体对316L纤维的物理附着力所致.基体中发生微量Fe元素扩散,但在316L纤维中不发生基体Ca、P元素的扩散.含5%316L纤维复合材料表现为脆性断裂,而含10%、20%、40%316L纤维复合材料均表现为韧性断裂,且韧性程度随316L纤维含量的增加而增大.     

HA-316L不锈钢纤维非对称功能梯度生物材料制备与显微组织

用低压热等静压方法在1100℃下制备了HA(ZrO₂)-316L不锈钢纤维非对称FGM,其中316L不锈钢纤维含量按体积比20%→15%→10%→5%呈非对称梯度变化.并通过金相显微镜、SEM、EDXA分析了材料的微观结构和微区元素含量.结果表明,HA(ZrO₂)-316L不锈钢纤维非对称FGM微观上表现为316L不锈钢纤维在FGM中呈无序、均匀分布状态,316L不锈钢纤维包裹于HA(ZrO₂)基体中,两者结合紧密,界面表现为部分凹凸不平,316L不锈钢纤维与HA(ZrO₂)基体紧紧的咬合在一起.在FGM基体中发生了微量的韧化相Fe元素扩散,韧化相316L不锈钢纤维不发生基体相Ca、P元素的扩散,基体与韧化相均相对独立,二者之间不发生任何化学反应.随着HA含量增加,HA(ZrO₂)-316L不锈钢纤维复合材料的断裂韧性和弹性模量逐渐减小,体现了FGM中各梯度层的力学性能缓和设计.HA(ZrO₂)-316L不锈钢纤维FGM中,分析认为,增韧机理主要为纤维拔出增韧和层间裂纹偏转增韧.     

HA(ZrO2)/316L不锈钢纤维对称功能梯度生物材料

制备了HA(ZrO2)/316L不锈钢纤维对称功能梯度材料(FGM),316L不锈钢纤维的含量(体积分数)按20%→10%→0→10%→20%呈轴向对称梯度变化.分析了材料的微观结构和微区元素含量,研究了材料的性能与316L不锈钢纤维含量的关系.结果表明,在HA(ZrO2)/316L不锈钢纤维对称FGM中,316L不锈钢纤维在微观上呈无序和均匀分布状态,它被包裹于HA(ZrO2)基体中,两者紧密结合.316L不锈钢纤维与HA(ZrO2)基体间的界面表现为部分凹凸不平,紧紧地咬合在一起.在FGM基体中发生了微量的韧化相Fe元素扩散,在韧化相316L不锈钢纤维不发生基体相Ca、P元素的扩散,基体与韧化相之间不发生化学反应.随着316L不锈钢纤维含量的增加,HA(ZrO2)/316L不锈钢纤维复合材料的断裂韧性和弹性模量逐渐增加,体现了FGM中各梯度层的力学性能缓和设计.按Miao模型计算HA(ZrO2)/316L不锈钢纤维FGM中的残余热应力为515 MPa,FGM的增韧机理主要为纤维的拔出增韧和层间的裂纹偏转增韧.     

碳纤维表面改性增强Fe3Al-Al2O3复合材料的制备及组织性能

采用溶胶-凝胶分散和热压烧结制备了短切碳纤维（CF_s）/Fe₃Al-Al₂O₃复合材料。分别通过电化学镀Cu和化学气相沉积SiC对CF_s表面修饰和改性,研究了Cu镀层和SiC涂层对CF_s/Fe₃Al-Al₂O₃复合材料显微组织、相组成、力学性能及断裂行为的影响。结果表明,未修饰的CF_s在Fe₃Al-Al₂O₃基体中受到严重侵蚀,CF_s/Fe₃Al-Al₂O₃复合材料致密度低,抗弯强度仅为239.0 MPa,与Fe₃Al-Al₂O₃强度相当;表面镀Cu可有效保护CF_s不被侵蚀,同时提高了CF_s/Fe₃Al-Al₂O₃复合材料的烧结致密性和界面结合强度,从而明显提高了复合材料的断裂强度,但断裂过程中纤维拔出较短;CF_s表面沉积SiC的CF_s/Fe₃Al-Al₂O₃复合材料组织均匀致密,表面涂层完整,且与纤维及基体之间结合力相当,断裂过程中,涂层既可随纤维一起拔出基体,也可与CF_s分离而留在基体之中,SiC涂层与纤维及基体之间的弱相互作用很大程度上促进了纤维脱黏和拔出,从而促进CF_s/Fe₃Al-Al₂O₃复合材料韧化所需的渐进破坏机制。      

316L不锈钢在不同浓度Cl-和CO2条件下的腐蚀行为

为了探明在辽河油田采出水环境中Cl^-和CO₂对316L不锈钢腐蚀行为的影响,通过浸泡实验、交流阻抗(EIS)和极化曲线技术分别研究了不同Cl^-浓度和CO₂分压对316L不锈钢的影响,其中Cl^-浓度梯度为0,0.030 0,0.051 5,0.070 0 mol/L,CO₂分压为0.2,0.4,0.6 MPa,并结合X射线衍射技术(XRD)对腐蚀产物进行了分析。结果表明：Cl^-浓度的增大使容抗弧直径减小,弥散指数降低,腐蚀情况加剧;容抗弧的直径随着CO₂分压的增大先变小后变大,弥散指数先降低后升高,腐蚀情况先加剧后减缓。这是由于Cl^-会破坏316L表面的钝化膜,而CO₂会与基体反应生成FeCO₃,随着CO₂分压升高,FeCO₃保护膜愈加致密。     

微观结构对中间相沥青基炭/炭复合材料力学性能的影响

借助偏光显微镜、扫描电镜、透射电镜以及力学性能测试研究了微观结构对中间相沥青基炭/炭复合材料力学性能的影响. 结果表明: 基体炭在偏光显微镜下呈现出光学各向异性, 在SEM和TEM下呈片层条带状结构. 基体炭与纤维之间的界面不连续, 为“裂纹型”界面. 材料受载破坏时裂纹通过改变扩展路径而延缓其扩展速度, 在纤维-基体界面处以及基体炭层片之间引起滑移, 在断口形貌上体现出断裂台阶适中且与纤维拔出交替进行, 表现出韧性破坏的断裂特征. 材料具有较高的力学性能, 抗弯强度达到257MPa, 断裂韧性达到11.4MPa·m ^1/2.     

化学气相渗透2D-SiCf/SiC复合材料的蠕变性能及损伤机理

研究了采用化学气相渗透工艺制备2D-SiC_f/SiC复合材料的真空蠕变性能, 蠕变温度为 1200、1300和1400 ℃, 应力水平范围为100~140 MPa。用扫描电子显微镜(SEM)和高分辨透射电子显微镜(TEM)分别观察分析了2D-SiC_f/SiC复合材料的蠕变断口形貌和微观结构。结果表明, 2D-SiC_f/SiC复合材料的主要蠕变损伤模式包括基体开裂、界面脱粘和纤维蠕变。桥接裂纹的纤维发生蠕变并促进了基体裂纹的张开、位移增大, 进一步导致复合材料蠕变断裂, 在复合材料蠕变过程中起决定性作用。2D-SiC_f/SiC复合材料的蠕变性能与SiC纤维微观结构的稳定性密切相关。在1200 ℃/100 MPa时, 纤维晶粒没有长大, 复合材料的蠕变断裂时间大于200 h; 蠕变温度为1400 ℃时, 纤维晶粒明显长大, 2D-SiC_f/SiC复合材料蠕变断裂时间缩短至8.6 h, 稳态蠕变速率增大了三个数量级。     

聚醚醚酮和烯丙基化合物改性双马来酰亚胺复合材料微观结构及力学性能

采用浓H₂SO₄氧化聚醚醚酮（PEEK）得到磺化聚醚醚酮（SPEEK）,以3,3'-二烯丙基双酚A （BBA）、双酚A双烯丙基醚（BBE）为活性稀释剂、SPEEK为改性剂、双马来酰亚胺（BMI）树脂为基体,浇注成型制备SPEEK/BBA-BBE-BMI复合材料,同时研究了SPEEK的改性效果及复合材料微观形貌与力学性能。结果表明：SPEEK改性效果较好,在FTIR中存在明显的磺酸基团特征峰,SEM和能谱分析表明,SPEEK微观形貌变化明显,硫元素含量较高;SPEEK/BBA-BBE-BMI复合材料的微观形貌显示,SPEEK在基体中呈现直径为2 μm左右的多孔状两相结构,且分散均匀,此多孔结构改善了复合材料的断裂形貌,由脆性断裂转变为韧性断裂,当断裂纹遇到SPEEK组分时受阻而出现不规则发散,此变化会赋予复合材料更加优异的性能。力学性能测试结果显示,当SPEEK含量为5wt%时,SPEEK/BBA-BBE-BMI复合材料的弯曲强度和冲击强度达到最佳,分别为147.93 MPa和15.74 kJ/mm²,分别比基体提高了49.47%和66.21%。     

真空退火对原位Al2O3/Fe-Cr-Ni增强复合材料性能的影响

铁铬镍合金具有良好的高温强韧性和抗蠕变性,被广泛应用于制造航空发动机、工业燃气轮机等设备。利用原位合成和热压烧结工艺制备Al2O3/Fe-Cr-Ni复合材料。为减少脆性相对复合材料性能的影响,将热压烧结试样在1000℃下真空保温2h后退火。采用XRD和SEM等测试方法,研究热处理后Al2O3/Fe-Cr-Ni复合材料的微观结构和常温力学性能。结果表明:Al2O3/Fe-Cr-Ni复合材料主要由Fe-Cr-Ni合金相、Fe-Cr相和Al2O3陶瓷增强相组成。热压烧结试样的维氏硬度、抗弯强度和断裂韧度分别为4.16GPa、298.31MPa和8.04MPa·m1/2。经1000℃高温热处理后,复合材料中Fe-Cr相发生奥氏体转变和合金基体晶粒长大,导致硬度下降至2.98GPa。Fe-Cr-Ni合金基体中韧性相含量和基体连续性增加,使该复合材料的抗弯强度和断裂韧度明显上升,其值分别为459.33MPa和12.81MPa·m1/2。     

纤维预热温度对连续Al2O3f/Al复合材料力学性能的影响

选用Nextel610型Al₂O₃纤维为增强体、ZL210A连续氧化铝合金为基体,采用真空压力浸渗法制备纤维增强铝基复合材料(Al₂O_3f/Al),纤维的体积分数为40%,预热温度分别为500、530、560和600℃,研究了纤维预热温度对Al₂O_3f/Al复合材料的微观组织、纤维损伤和力学性能的影响。结果表明：随着纤维预热温度的提高复合材料的致密度随之提高,最大达到99.2%,材料的组织缺陷最少,纤维的分布均匀;随着纤维预热温度的提高从复合材料中萃取出来的Al₂O₃纤维的拉伸强度不断降低,纤维预热温度为600℃的复合材料中Al₂O₃纤维的拉伸强度仅为1150 MPa,纤维表面粗糙,有大尺寸附着物。纤维的预热温度对Al₂O_3f/Al复合材料的拉伸强度有显著的影响。预热温度为500、530、560和600℃的复合材料其拉伸强度分别对应于298、465、498和452 MPa。组织缺陷、纤维损伤和界面结合强度,是影响连续Al₂O_3f/Al复合材料强度的主要因素。     

Characterization of hydroxyapatite– and bioglass–316L fibre composites prepared by spark plasma sintering

To improve the mechanical properties of pure hydroxyapatite (HA) ceramics and pure 45S5 bioglasses, HA–316L fibre composites and bioglass 45S5–316L fibre composites were produced by spark plasma sintering (SPS) at 950 and 850 °C, respectively. While the HA phase in the HA–316L fibre composites did not decompose after the SPS process, microcracks were found around the 316L fibres in the composites. Consequently, the HA–316L fibre composites could not effectively improve the mechanical properties of the pure HA ceramics. In contrast, the bioglass 45S5–316L fibre composites showed no microcracks around the 316L fibres and thus exhibited bending strengths of up to 115 MPa.     

Hydroxyapatite-316L fibre composites prepared by vibration assisted slip casting

To prepare hydroxyapatite (HA, or HAp)-stainless steel 316L fibre composites with up to 30 vol% 316L fibres (1 mm long and 50 m in diameter), slip casting assisted by vibration (frequency: 55 Hz; amplitude: 5 mm) was carried out, followed by both cold isostatic pressing (CIPing) and hot isostatic pressing (HIPing). With the addition of around 0.5 wt% sodium carboxymethylcellulose (Na-cmc), solids loadings up to 44 vol% were obtained in calcined HA powder-derived slips, which were castable only under the vibration. The slips were concentrated and viscous so that the preferential sedimentation of the dense and large 316L fibres could be avoided. Subsequent CIPing was able to increase the relative density of the cast and dried green compacts from 46% after casting to 60% after CIPing. With the dense and uniform green compacts of the HA-316L mixtures, final HIPing at 950 °C resulted in HA-316L fibre composites of 99% relative density. The HA-316L fibre composites had improved fracture toughness of 3.6 ± 0.3 MPa.m^0.5, due to the bridging effect of the ductile 316L fibres. However, the mechanical strength of the composites was limited by the presence of residual thermal stresses and circumferential microcracks. The HA-316L fibre composites were biocompatible and exhibited favourable bone-bonding characteristics.     

Plasma surface modification of advanced organic fibres

The interlaminar shear strength, interlaminar fracture energy, flexural strength and modulus of extended-chain polyethylene/epoxy composites are improved substantially when the fibres are pretreated in an ammonia plasma to introduce amine groups on to the fibre surface. These property changes are examined in terms of the microscopic properties of the fibre/matrix interface. Fracture surface micrographs show clean interfacial tensile and shear fracture in composites made from untreated fibres, indicative of a weak interfacial bond. In contrast, fracture surfaces of composites made from ammonia plasma-treated fibres exhibit fibre fibrillation and internal shear failure as well as matrix cracking, suggesting stronger fibre/matrix bonding, in accord with the observed increase in interlaminar fracture energy and shear strength. Failure of flexural test specimens occurs exclusively in compression, and the enhanced flexural strength and modulus of composites containing plasma-treated fibres result mainly from reduced compressive fibre buckling and debonding due to stronger interfacial bonding. Fibre treatment by ammonia plasma also causes an appreciable loss in the transverse ballistic impact properties of the composite, in accord with a higher fibre/matrix interfacial bond strength.     

Plasma surface modification of advanced organic fibres

A marked improvement in the interlaminar shear strength and flexural strength of aramid/ epoxy composites is observed when the fibres are pretreated in an ammonia or ammonia/ nitrogen gaseous discharge (plasma) to introduce amine groups on to the fibre surface. Scanning electron and optical microscopic observations are used to examine the microscopic basis for these results. Scanning electron micrographs of shear fracture surfaces show clean fibre/matrix separation in composites made from untreated fibres, indicative of weak interfacial bonding. In contrast, shear fracture surfaces of composites containing plasma-treated fibres exhibit clear evidence of fibre fibrillation and matrix cracking, suggesting stronger interfacial bonding. Optical microscopic examination of flexure specimens shows that enhanced strength results mainly from reduced compressive fibre buckling and debonding, due to an increase in fibre/matrix interfacial bond strength. This increase is not accompanied by any significant change in the interlaminar fracture energy or flexural modulus of the composites, but there is an appreciable loss in transverse ballistic impact properties. These results are also examined in terms of the observed increase in fibre/matrix interfacial strength.     

Atmospheric plasma fluorination as a means to improve the mechanical properties of short-carbon fibre reinforced poly (vinylidene fluoride)

The impact of fluorination of carbon fibres on the properties of short fibre reinforced polyvinylidene fluoride (PVDF) composites was studied. As received and continuously atmospheric plasma fluorinated (APF) carbon fibres were cut to an average fibre length of 2 mm. Short fibre composites (SFC) containing 5, 10 and 15 wt.% carbon fibres were manufactured using a twin-screw mixer. Test specimens were produced by injection moulding. The mechanical properties of the SFC were studied using tensile and compression testing. As expected, the incorporation of short-carbon fibres into PVDF led to an increase in strength and stiffness. The tensile strength and Young’s modulus of the SFC containing APF-treated carbon fibres increased by up to 17% and 190%, respectively. Furthermore, the compressive strength and modulus of the SFC containing APF-treated carbon fibres also increased by 19% and 35%, respectively. APF of carbon fibres results only in a marginal increase in the bulk matrix crystallinity of PVDF as determined by DSC. Scanning electron micrographs of fracture surfaces from tensile tested specimens exhibited a typical brittle failure mode with low fibre loading fraction. Despite the presence of up to 5% of voids and visible resin rich regions at fracture surface, SFC containing APF-treated fibres suggest better bonding at the fibre/matrix interface which led to the much enhanced mechanical properties.     

Characterization of aluminium-matrix composites made by compocasting and its variations

Compocasting (semisolid-semisolid, SS) and its two variations: SL (semisolid-liquid) and LL (liquid-liquid) process routes are used to make 2024Al reinforced with 3 mm and 12 mm long FP-alumina fibres. Squeeze-casting is used as a complementary casting technique. The effect of processing route on microstructure and the mechanical properties of these composites is studied. The SS route produces composites with uniform fibre distribution, but casting is difficult due to the high viscosity of the slurry. The SL route gives good fibre distribution and the casting is easy. The LL route allows addition of a large amount of fibres but gives castings with a non-uniform fibre distribution, which lowers the failure strains and reduces the strength of the composites drastically. The addition of alumina fibres to 2024Al increases its modulus of elasticity considerably. The observed modulus values show good agreement with the theoretical predictions. The strength values are somewhat lower than the theoretical predictions. This is because the composites failed at strains slightly lower than the fibre failure strain. Absence of fibre pull-out indicates that a good fibre matrix bond has been produced in each case.     

Silicon carbide (NicalonTM) fibre-reinforced borosilicate glass composites: mechanical properties

The objective of this study was to assess the applicability of an extrinsic carbon coating to tailor the interface in a unidirectional NicalonTM–borosilicate glass composite for maximum strength. Three unidirectional NicalonTM fibre-reinforced borosilicate glass composites were fabricated with different interfaces by using (1) uncoated (2) 25 nm thick carbon-coated and (3) 140 nm thick carbon coated Nicalon fibres. The tensile behaviours of the three systems differed significantly. Damage developments during tensile loading were recorded by a replica technique. Fibre–matrix interfacial frictional stresses were measured. A shear lag model was used to quantitatively relate the interfacial properties, damage and elastic modulus. Tensile specimen design was varied to obtain desirable failure mode. Tensile strengths of NicalonTM fibres in all three types of composites were measured by the fracture mirror method. Weibull analysis of the fibre strength data was performed. Fibre strength data obtained from the fracture mirror method were compared with strength data obtained by single fibre tensile testing of as-received fibres and fibres extracted from the composites. The fibre strength data were used in various composite strength models to predict strengths. Nicalon–borosilicate glass composites with ultimate tensile strength values as high as 585 MPa were produced using extrinsic carbon coatings on the fibres. Fibre strength measurements indicated fibre strength degradation during processing. Fracture mirror analysis gave higher fibre strengths than extracted single fibre tensile testing for all three types of composites. The fibre bundle model gave reasonable composite ultimate tensile strength predictions using fracture mirror based fibre strength data. Characterization and analysis suggest that the full reinforcing potential of the fibres was not realized and the composite strength can be further increased by optimizing the fibre coating thickness and processing parameters. The use of microcrack density measurements, indentation–frictional stress measurements and shear lag modelling have been demonstrated for assessing whether the full reinforcing and toughening potential of the fibres has been realized. This revised version was published online in November 2006 with corrections to the Cover Date.     

ZrO2增韧Al2O3颗粒增强Fe45复合材料拉伸断裂的有限元-离散元耦合方法仿真ZrO2增韧Al2O3颗粒增强Fe45复合材料拉伸断裂的有限元-离散元耦合方法仿真

采用有限元-离散元耦合方法（FEM-DEM方法）,进行了氧化锆增韧氧化铝颗粒增强Fe45复合材料（ZrO₂-Al₂O₃/Fe45）轴对称代表体元模型的拉伸断裂仿真分析。分析了FEM-DEM模型对单元尺寸的敏感性,结果表明采用,二阶实体单元加双零厚度内聚力单元的FEM-DEM模型降低了计算结果对单元尺寸的敏感性。ZrO₂-Al₂O₃/Fe45复合材料拉伸断裂的模拟结果表明,颗粒形状对裂纹的扩展会产生较大影响,复合材料的开裂首先在垂直于拉力方向的界面处发生,界面裂纹扩展至基体应力集中处之后基体发生开裂,裂纹由开裂的界面和基体裂纹共同组成。      

The properties of carbon fibre/SiC composites fabricated through impregnation and pyrolysis of polycarbosilane

Unidirectional carbon fibre reinforced SiC composites were prepared from four types of carbon fibres, PAN-based HSCF, pitch-based HMCF, CF50 and CF70, through nine cycles or twelve cycles of impregnation of polycarbosilane and subsequent pyrolysis at 1200°C. The polycarbosilane-derived matrix was found to be -SiC with a crystallite size of 1.95 nm. The mechanical properties of the composites were evaluated by four-point bending tests. The fracture behavior of each composite was investigated based on load-displacement curves and scanning electron microscope (SEM) observation of fracture surfaces of the specimens after tests. It was found that CF50/SiC and CF70/SiC exhibited high strength and non-brittle fracture mode with multiple matrix cracking and extensive fibre pullout, whereas HSCF/SiC and HMCF/SiC exhibited low strength and brittle fracture mode with almost no fibre pullout. The differences in the fracture modes of these carbon fibre/SiC composites were thought to be due to differences in interfacial bonding between carbon fibres and matrix. Values of flexural strengths of CF70/SiC and CF50/SiC were 967 MPa and 624 MPa, respectively, which were approximately 75% and 38% of the predicted values. The relatively lower strength of CF50/SiC, compared with CF70/SiC, was mainly attributed to the shear failure of CF50/SiC during bending tests.