纺织学报 ›› 2023, Vol. 44 ›› Issue (01): 119-128.doi: 10.13475/j.fzxb.20211203910

• 纺织工程 • 上一篇    下一篇


段亚弟1, 谢巍杰2, 邱海鹏2, 王晓猛2, 王岭2, 张典堂1(), 钱坤1   

  1. 1.生态纺织教育部重点实验室(江南大学), 江苏 无锡 214122
    2.航空工业复合材料技术中心, 北京 101300
  • 收稿日期:2021-12-10 修回日期:2022-10-09 出版日期:2023-01-15 发布日期:2023-02-16
  • 通讯作者: 张典堂(1986—),男,研究员,博士。主要研究方向为先进纺织复合材料设计及制造。E-mail:zhangdiantang@jiangnan.edu.cn
  • 作者简介:段亚弟(1995—),女,硕士生。主要研究方向为陶瓷基复合材料。
  • 基金资助:

Influence of interfacial layers on fracture toughness of three-dimensional woven angle interlock SiCf/SiC composites

DUAN Yadi1, XIE Weijie2, QIU Haipeng2, WANG Xiaomeng2, WANG Ling2, ZHANG Diantang1(), QIAN Kun1   

  1. 1. Key Laboratory of Eco-Textiles (Jiangnan University), Ministry of Education, Wuxi, Jiangsu 214122, China
    2. Aerospace Composites Technology Center, Beijing 101300, China
  • Received:2021-12-10 Revised:2022-10-09 Published:2023-01-15 Online:2023-02-16


为探究界面层对SiCf/SiC复合材料性能的影响,选用国产第3代SiC纤维,通过先驱体浸渍裂解工艺制备了热解碳(PyC)、热解碳/碳化硅(PyC/SiC)、氮化硼(BN)、氮化硼/碳化硅(BN/SiC)4种界面层的三维机织角联锁SiCf/SiC复合材料。在此基础上,结合声发射技术对复合材料进行常温断裂韧性测试,并利用扫描电镜对其细观损伤模式进行评价。结果表明:界面层对三维机织角联锁SiCf/SiC复合材料的断裂强度和断裂韧性有强决定作用,但对其初始模量没有太大的影响;以PyC层为主界面层的试样具有良好的断裂韧性,试样P-SiCf/SiC和P/S-SiCf/SiC的断裂韧性分别为13.99和16.93 MPa·m1/2,而试样B-SiCf/SiC表现出强界面结合,具有最低断裂韧性6.47 MPa·m1/2;但在界面引入SiC层后,试样B/S-SiCf/SiC的断裂韧性显著提高至15.81 MPa·m1/2;声发射能量和撞击数可完整描述SiCf/SiC复合材料的实时损伤过程。

关键词: SiCf/SiC复合材料, 三维机织角联锁, 界面层, 断裂韧性, 声发射


Objective Three-dimensional woven angle interlock SiCf/SiC composites have the advantages of high temperature resistance, low density and long service life, and are an ideal candidate material for thermal aviation terminal components. At present, the research of SiCf/SiC composites mainly focuses on the first- and second-generation SiC fibers, but few studies on the mechanical properties of the third generation SiC fibers and their three-dimensional woven angle interlocking composites were reported.
Method In order to explore the influence of interfacial layer on fracture toughness of SiCf/SiC composites, the third generation SiC fibers made in China was selected. Three-dimensional woven angle interlock SiCf/SiC composites with four interface phases including pyrolytic carbon (PyC), pyrolytic carbon/silicon carbide (PyC/SiC), boron nitride (BN) and boron nitride/silicon carbide (BN/SiC) were prepared by the precursor infiltration pyrolysis processes, chemical vapor deposition process and chemical vapor infiltration process. On this basis, combined with acoustic emission technology, the normal temperature fracture toughness test was carried out, and the microscopic damage mode was evaluated by scanning electron microscopy.
Results All samples showed the characteristic of "pseudo-plastic fracture" (Fig.8). The fracture strengths of P-SiCf/SiC, P/S-SiCf/SiC,B-SiCf/SiC and B/S-SiCf/SiC are 193.36, 233.97, 89.43 and 218.49 MPa, respectively, and the modulus thereof are 33.86, 33.36, 32.03 GPa and 31.37 GPa, respectively (Fig.9). It was found that the samples with PyC as the main interfacial layer offer good fracture toughness, and the fracture toughness of P-SiCf/SiC and P/S-SiCf/SiC are 13.99 and 16.93 MPa·m1/2, respectively (Fig.10). On the other hand, the B-SiCf/SiC samples show strong interfacial bonding, with the lowest fracture toughness of 6.47 MPa·m1/2. However, the fracture toughness of B/S-SiCf/SiC samples is significantly increased to 15.81 MPa·m1/2 when the SiC layer is introduced into the interface. The results show that the interfacial layer in the SiCf/SiC composites has a strong influence on the fracture strength and fracture toughness, but has no great influence on their initial modulus, which mainly depends on the fiber structure and the stiffness of the matrix. In the microscopic damage morphology of SiCf/SiC composites, the meso-damage of the four samples all involve the matrix fracture, the interface damage, the debonding between fiber and matrix, the fiber fracture and the fiber pulling-out (Fig.11, Fig.12). However, the types of main body damage are obviously different, the sample with composite interface layer produces more AE events before the fiber failure due to the blocking effect of SiC layer on the crack (Fig.13).
Conclusion It can be concluded from the research that the introduction of SiC layer enhances the energy dissipation mechanism of the interface and prevents the crack propagation in the matrix, the cracks in PyC layer and BN layer can be deflected effectively, and the mechanical properties of SiCf/SiC composite are improved. In addition, acoustic emission (AE) event energy values and numbers of impact can completely describe the real-time damage process of SiCf/SiC composites. Several problems should be further investigated in the study of the properties of three-dimensional woven angle interlock SiCf/SiC composites. Firstly, it is difficult to distinguish SiCf/SiC composites due to their relatively complex microscopic composition and the close density of fiber and matrix. How to monitor the more detailed real-time damage process of materials in the bearing process by means of advanced characterization techniques is a focus of future research. In addition to the experimental testing, it is necessary to develop a high-fidelity numerical simulation method for three-dimensional woven angle interlock SiCf/SiC composites, establish a more accurate meso-structural model to achieve progressive damage analysis and reveal the failure mechanism.

Key words: SiCf/SiC composite, three-dimensional woven angle interlock, interface layer, fracture toughness, acoustic emission


  • TB332







试样 密度/(g·cm-3) 孔隙率/%
P-SiCf/SiC 2.80 4.74
P/S-SiCf/SiC 2.64 5.02
B-SiCf/SiC 2.80 4.88
B/S-SiCf/SiC 2.62 5.15













试样 第1界面层 第2界面层
界面类型 厚度/nm 界面类型 厚度/nm
P-SiCf/SiC PyC 188±14
P/S-SiCf/SiC PyC 188±14 SiC 1 504±22
B-SiCf/SiC BN 634±20
B/S-SiCf/SiC BN 634±20 SiC 1 504±22













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