碳-铝正交层板疲劳行为研究

本研究用真空热压法制备了两种铺层的C/AI正交层板(0/90/0)_s及(90/0/90)_s.在MTS NEW810上进行了一系列疲劳损伤及破坏试验.疲劳损伤的行为研究工作包括:以刚度下降为损伤参数对C/AI正交层板进行了降级应力分析,并由此来预计在△S_h以下,正交层板不会发生疲劳损伤累积.研究了C/Al正交层板在同一应力水平而不同应力范围作用下的疲劳响应,发现试样在疲劳损伤时其刚度下降值相近似,即疲劳破坏的门槛值依赖于所施加的应力水平.依据MMC对各种循环载荷的不同响应,基体的疲劳损伤状态在S-N平面上可分为三种不同的区域:无损伤区,损伤累积区和断裂区.利用扫描电镜及金相显微镜分别对其疲劳断口形貌、基体裂纹进行观察,对该正交层板的疲劳破坏行为进行分析及讨论.结果表明:C/Al正交层板的疲劳断口呈脆断型,其中主承力层(0°铺层)断口平齐,偏轴层(90°铺层)断口平齐最差,层间损伤形式有局部分层、界面连续开裂及复合丝之间基体开裂等三种形式;其疲劳破坏主导因素是层间局部严重损伤及主承力层中复合丝大量断裂由于其疲劳裂纹沿垂直于载荷方向迅速扩展,寻找适中的界面结合强度对改善C/Al层板的疲劳性能有很大影响.     

CVD-SiC界面改性涂层对气相渗硅制备C_f/SiC复合材料力学性能的影响

在气相渗硅制备C_f/SiC复合材料时,界面改性涂层非常重要。良好的界面改性涂层一方面起到保护碳纤维不受Si反应侵蚀的作用,另一方面起到调节纤维和基体界面结合状况。通过在C纤维表面制备CVD-SiC涂层来进行界面改性,研究CVD-SiC界面改性涂层对GSI C_f/SiC复合材料力学性能和断裂特征的影响,并分析其影响机制。结果表明:无CVD-SiC涂层改性的C_f/SiC复合材料力学性能较差,呈现脆性断裂特征,其强度、模量和断裂韧度分别为87.6MPa,56.9GPa,2.1MPa·m1/2。随着CVD-SiC涂层厚度的增加,C_f/SiC复合材料的弯曲强度、模量和断裂韧度呈现先升高后降低的趋势,CVD-SiC涂层厚度为1.1μm的C_f/SiC复合材料的力学性能最好,其弯曲强度、模量和断裂韧度分别为231.7MPa,87.3GPa,7.3MPa·m1/2。厚度适中的CVD-SiC界面改性涂层的作用机理主要体现在载荷传递、"阻挡"Si的侵蚀、"调节"界面结合状态3个方面。     

C/SiC复合材料应力氧化失效机理

研究了干氧和湿氧两种气氛、疲劳和蠕变两种应力下C/SiC复合材料在1300℃的应力氧化行为. 试验结果和断口形貌SEM分析表明: C/SiC复合材料在疲劳应力下比在蠕变应力下具有更强的抗氧化能力和更长的持续时间; 干氧环境中的蠕变试样以C纤维氧化失效为主; 水蒸气的存在加剧了SiC基体的氧化, 并且使受蠕变应力的C/SiC复合材料以SiC基体氧化失效为主.     

2D-C/ SiC 复合材料的宏观拉压特性和失效模式

通过拉伸、压缩实验, 从宏观上研究了平纹编织C/ SiC 复合材料在简单载荷作用下模量、残余应变及泊松比的变化。通过断口观察, 分析了材料在面内拉、压载荷作用下的损伤与失效模式。实验结果表明, 拉伸载荷作用下, 材料在低应力就开始损伤。0°纤维束表面基体开裂和层间裂纹是主要损伤形式。损伤后, 随着应力增加, 拉伸卸载模量、泊松比线性减小, 残余应变增加; 压缩应力-应变基本呈直线关系, 模量、泊松比基本不变。拉伸破坏表现为韧性断裂, 断裂机理为分层后0°纤维束的断裂、携带90°纤维束拔出; 压缩破坏形成一个与加载方向成13°的断裂平面, 破坏机理为层间裂纹、0°/ 90°纤维束之间裂纹和90°纤维束内裂纹的产生和迅速扩展、最后0°纤维束剪切断裂。      

复合材料层板中基体性能对层间应力分布的影响

本文分析了复合材料层板中基体性能的变化对层间应力的影响,差重讨论了层板自由边附近及层间界面上的应力分布.分析结果表明,基体性能的变化会对层间立力的分布产生显著的影响.因此,对于实际复合材料结构,有可能通过选用合适的基体来改变复合材料层板自由边附近的层间应力分布,从而减轻率合材料层板的分层破坏.      

温度对碳纤维平纹布正交层合板拉伸疲劳性能的影响

温度环境可降低复合材料的疲劳性能,在确定复合材料结构寿命时须考虑温度的影响.本试验测量了碳纤维平纹布正交层合板在低温干态(CTD)、常温干态(RTD)和高温干态(ETD)环境下的拉伸疲劳性能,获得了三种环境下复合材料的S-N曲线,分析了温度对复合材料疲劳性能的影响.基于试验结果,建立了温度条件下复合材料疲劳性能有限元分析模型,对复合材料的疲劳寿命进行了估算并分析了其损伤机理.线性拟合结果显示:在106 疲劳寿命下,与RTD环境疲劳最大应力相比,CTD环境疲劳最大应力略有降低,而ETD环境疲劳最大应力下降明显. CTD环境下,试验件的疲劳破坏断口比较齐整,纤维基本在同一纵向位置断裂,断口附近基体基本完好,无分层现象;RTD环境下,试验件断口处也没有明显分层现象;ETD环境下,试验件出现了明显的分层,同时还有纤维拔出,且断口处基体开裂程度严重.有限元分析表明,CTD环境下试验件的疲劳断裂呈现脆断的特征,断裂截面平整,断裂区域窄;RTD与ETD环境下试验件的纤维疲劳断裂损伤的断裂截面不平整,断口不一,断裂区域相对较宽.     

碳纤维织物/环氧复合材料销钉连接实验研究

针对1K缎纹碳纤维织物/环氧复合材料层板销钉连接,实验研究了几何参数对连接性能的影响.选取了不同的端距和边距,测试了碳纤维织物复合材料层板W/D(试样宽度/孔直径)及E/D(孔端距/孔直径)对销钉连接强度的影响,并分析了销钉连接的破坏模式.实验结果表明:1K缎纹织物/环氧复合材料层板销钉连接承载能力随着边距E和端距W的增加而增加,当E/D=2,W/D=3时,销钉连接强度达到稳定值,此后增加边距E和端距W值连接强度不会有明显的增加.     

先驱体浸渍-裂解SiC界面改性涂层对气相渗硅3D-C_f/SiC复合材料力学性能的影响

界面改性涂层对调节复合材料的力学性能起到重要作用。特别是在气相渗硅(GSI)制备C_f/SiC复合材料时,合适的界面改性涂层一方面保护C纤维不受Si反应侵蚀,另一方面调节C纤维和SiC基体的界面结合状况。通过在3D-C纤维预制件中制备先驱体浸渍-裂解(PIP)SiC涂层来进行界面改性,研究了PIP-SiC涂层对GSI C_f/SiC复合材料力学性能的影响。结果表明:无涂层改性的GSI C_f/SiC复合材料力学性能较差,呈现脆性断裂特征,其弯曲强度、弯曲模量和断裂韧性分别为87.6 MPa、56.9GPa和2.1 MPa·m~(1/2)。具有PIP-SiC界面改性涂层的C_f/SiC复合材料力学性能得到改善,PIP-SiC涂层改性后,GSI C_f/SiC复合材料的弯曲强度、弯曲模量和断裂韧性随着PIP-SiC周期数的增加而降低,PIP-SiC为1个周期制备的GSI C_f/SiC复合材料的力学性能最高,其弯曲强度、弯曲模量、断裂韧性分别为185.2 MPa、91.1GPa和5.5 MPa·m~(1/2)。PIP-SiC界面改性涂层的作用机制主要体现在载荷传递和"阻挡"Si的侵蚀2个方面。     

平纹编织SiCf/SiC复合材料的中温蠕变断裂时间及损伤机制

碳化硅纤维增强碳化硅复合材料(SiC_f/SiC)是制造下一代航空发动机热结构件的关键材料,中等温度(～800℃)下,SiC_f/SiC的蠕变断裂时间t_u显著下降。为此,研究了平纹编织SiC_f/SiC (2D-SiC_f/SiC)在空气中500～1 000℃的蠕变性能及损伤机制,应力水平为100～160 MPa。利用SEM、TEM和EDS分析了断口形貌、微观组织和化学成分。结果表明：2D-SiC_f/SiC的t_u与温度和应力水平有关。相同温度下,2D-SiC_f/SiC的t_u随着应力增加而变短。当温度为800℃、蠕变应力大于基体开裂应力(PLS)时,2D-SiC_f/SiC发生中温脆化现象,其t_u下降。2D-SiC_f/SiC的中温脆化机制为基体开裂、BN界面氧化和SiO₂替代BN界面导致的强界面/基体结合。2D-Si...     

界面过渡层对SiC/Al双连续相复合材料性能的影响

研究了界面过渡层对SiC/Al双连续相复合材料性能的影响.结果表明,界面过渡层降低了复合材料中的残余应力,改善了界面的结合,提高了复合材料的压缩性能.当界面过渡层中SiC的体积分数接近50%时,复合材料的压缩强度最高,塑性最好,但弹性模量较低.界面过渡层的存在改变了复合材料的弯曲断裂机制.SiC原始泡沫增强的复合材料在断裂时,增强体SiC泡沫先断裂,基体后破坏,断裂表面凹凸不平;含界面过渡层的复合材料断裂时,过渡层的外侧界面先被撕开,内侧界面结合良好,基体与增强体同时断裂,断口平整.     

Mechanical behavior of SiCf/SiC composites with alternating PyC/SiC multilayer interphases

In order to tailor the fiber–matrix interface of continuous silicon carbide fiber reinforced silicon carbide (SiC_f/SiC) composites for improved fracture toughness, alternating pyrolytic carbon/silicon carbide (PyC/SiC) multilayer coatings were applied to the KD-I SiC fibers using chemical vapor deposition (CVD) method. Three dimensional (3D) KD-I SiC_f/SiC composites reinforced by these coated fibers were fabricated using a precursor infiltration and pyrolysis (PIP) process. The interfacial characteristics were determined by the fiber push-out test and microstructural examination using scanning electron microscopy (SEM). The effect of interface coatings on composite mechanical properties was evaluated by single-edge notched beam (SENB) test and three-point bending test. The results indicate that the PyC/SiC multilayer coatings led to an optimum interfacial bonding between fibers and matrix and greatly improved the fracture toughness of the composites.     

化学气相浸渗2D Cf/(SiC-C)复合材料的微观结构与强韧性

采用等温等压化学气相浸渗法(ICVI)制备了二维碳纤维增韧碳化硅碳二元基复合材料(2D C_f/(SiC-C)).利用扫描电镜(SEM)和背散射电子成像(BSE)研究了其基体的微观结构, 并与二维碳纤维增韧碳化硅陶瓷基复合材料(2D C_f/SiC)比较了室温力学性能和断口形貌.结果表明：2D C_f/(SiC-C)复合材料的基体是由SiC与热解碳(PyC)组成的多层结构, PyC基体层分布均匀而连续, 且与SiC基体层结合紧密.纤维束内部PyC基体层较厚的2D C_f/(SiC-C)复合材料具有较高的强韧性, 其拉伸强度、断裂应变、断裂韧性和断裂功分别比2D C_f/SiC复合材料的提高了3%、142%、22%和58%.SiC与PyC组成的多层基体使2D C_f/(SiC-C)复合材料的纤维在拔出过程中发生了两次集中拔出, 且第一次集中拔出的纤维对复合材料的强韧性起主要作用.     

Fabrication of multi-walled carbon nanotube-reinforced carbon fiber/silicon carbide composites by polymer infiltration and pyrolysis process

Multi-walled carbon nanotube (MWNT)-reinforced carbon fiber/silicon carbide (C_f/SiC) composites were prepared using a polymer infiltration and pyrolysis (PIP) process. The MWNTs used in this study were modified using a chemical treatment. The MWNTs were found to be well dispersed in the matrix after ultrasonic dispersion, and the mechanical properties of the C_f/SiC composite were significantly improved by the addition of MWNTs. The addition of 1.5 wt.% of MWNTs to the C_f/SiC composite led to a 29.7% increase in the flexural strength, and a 27.9% increase in the fracture toughness.     

Microstructural investigation of interfaces in CMCs

This paper is focused on the importance of pyrocarbon interfaces in two types of ceramic matrix composites (C_f–SiC and SiC_f–SiBC), during creep tests under argon. The development of micromechanisms which consume energy and then allow a damage tolerance, depends on the morphology of the fiber/matrix interphase, which has been investigated by TEM and HRTEM.     

Microstructure, mechanical properties and reaction mechanism of KD-1 SiCf/SiC composites fabricated by chemical vapor infiltration and vapor silicon infiltration

Three-dimensional (3D) KD-1 silicon carbide fiber reinforced silicon carbide matrix (KD-1 SiC_f/SiC) composites were fabricated by a combining chemical vapor infiltration (CVI) and vapor silicon infiltration (VSI) process. The microstructure and mechanical properties of the resulting KD-1 SiC_f/SiC composites were studied. The results show that the resulting SiC_f/SiC composites have high bulk density and low open porosity (<6%). The mechanical properties of the resulting SiC_f/SiC composites firstly increase and then decrease with decreasing the open porosity of the SiC_f/C composites. The KD-1 SiC fibers were not severely deformed and adhered to the matrix with a weak interface during the VSI process. As a result, the composites exhibit non-catastrophic failure behavior. Additionally, the diffusion mechanism for the VSI process was also investigated in our work.     

Interfacial control of uni-directional SiCf/SiC composites based on electrophoretic deposition and their mechanical properties

Interfacial control of uni-directional SiC_f/SiC composites were performed by EPD, and their mechanical properties at room temperature were evaluated. The effect of the thickness of carbon interphase on SiC fibers by EPD on mechanical properties of uni-directional SiC_f/SiC composites was also investigated. The average thickness of carbon coating on SiC fibers increased from 42 nm to 164 nm with an increase in the concentration of colloidal graphite suspension for EPD. Dense SiC_f/SiC composites were achieved and their fiber volume fraction was 47–51%. The SiC_f/SiC composites had a bending strength of 210–240 MPa. As the thickness of carbon coating was below 100 nm, the SiC_f/SiC composites (SC01 and SC02) fractured in almost brittle manner. In contrast, the SiC_f/SiC composites (SC03) showed a pseudo-ductile fracture behavior with a large number of fiber pullout as the thickness of carbon coating was above 100 nm. The fracture energy of SC03 was 3–4 times as high as those of SC01 and SC02 and the value was about 1.7 kJ/m². In consideration of the results of mechanical properties, the thickness of carbon coating on SiC fibers should be at least 100 nm to obtain high-performance SiC_f/SiC composites. The fabrication process based on EPD method is expected to be an effective way to control the interfaces of SiC_f/SiC composites and to obtain high-performance SiC_f/SiC composites.     

基于改进遗传算法的C/SiC拉伸损伤声发射模式识别

采用层次聚类及基于改进遗传算法的无监督模式识别方法,对2D-C/SiC复合材料常温拉伸试验过程的声发射数据进行分析,结合试样断口的扫描电镜(SEM)照片,得到拉伸过程中5类损伤模式及其典型声发射特征参数。通过对各类损伤的能量分布、累计事件数和累计能量的分析,研究C/SiC复合材料的损伤演化过程,发现其过程可分为基体微裂纹和界面失效为主的初始损伤阶段、基体微裂纹停滞导致层间剥离及纤维失效占主导地位的裂纹饱和阶段、基体长裂纹和界面失效为主的损伤积累发展阶段和纤维束大量失效的宏观断裂阶段。     

The effect of the fiber/matrix interface on the flexural fatigue performance of unidirectional fiberglass composites

Fatigue tests were conducted on oriented fiberglass-reinforced polymer matrix composites using four-point bending with a stress ratio of −0·8. Composites in which the fiberglass was treated with a commercial diaminofunctional silane coupling agent were found to possess a relatively high flexural fatigue performance compared with composites without coupling agents. Using the interlaminar shear strength as an indication of the interface strength, it was found that composites having a high interface strength possess a high fatigue performance. The failure sequence of the flexural (tensile) fatigue was identified as: nucleation and growth of superficial damage (including fiber ridging, transverse matrix cracking, longitudinal matrix cracking, fiber breaking and local delamination), sudden fiber-bundle breakage and, finally, macroscopic delamination. A strong interface between fiber and matrix delayed the occurrence of fiber ridging and longitudinal matrix cracking, thus improving the fatigue performance of the unidirectional composites.     

Fabrication of SiCf/SiC composites by chemical vapor infiltration and vapor silicon infiltration

Three-dimensional (3D) silicon carbide fiber reinforced silicon carbide matrix (SiC_f/SiC) composites, employing KD-1 SiC fibers (from National University of Defense Technology, China) as reinforcements, were fabricated by a combining chemical vapor infiltration (CVI) and vapor silicon infiltration (VSI) process. The microstructure and properties of the as prepared SiC_f/SiC composites were studied. The results show that the density and open porosity of the as prepared SiC_f/SiC composites are 2.1 g/cm³ and 7.7%, respectively. The SiC fibers are not severely damaged during the VSI process. And the SiC fibers adhere to the matrix with a weak interface, therefore the SiC_f/SiC composites exhibit non-catastrophic failure behavior with the flexural strength of 270 MPa, fracture toughness of 11.4 MPa·m^1/2 and shear strength of 25.7 MPa at ambient conditions. Moreover, the flexural strength decreases sharply at the temperature higher than 1200 °C. In addition, the thermal conductivity is 10.6 W/mk at room temperature.     

Estimate Interface Shear Stress of Unidirectional C/SiC Ceramic Matrix Composites from Hysteresis Loops

The tensile-tensile fatigue behavior of unidirectional C/SiC ceramic matrix composites at room and elevated temperature has been investigated. An approach to estimate the interface shear stress of ceramic matrix composites under fatigue loading has been developed. Based on the damage mechanisms of fiber sliding relative to matrix in the interface debonded region upon unloading and subsequent reloading, the unloading interface reverse slip length and reloading interface new slip length are determined by the fracture mechanics approach. The hysteresis loss energy for the strain energy lost per volume during corresponding cycle is formulatd in terms of interface shear stress. By comparing the experimental hysteresis loss energy with the computational values, the interface shear stress of unidirectional C/SiC ceramic composites corresponding to different cycles at room and elevated temperatures has been predicted.