MI SiCf/SiC-SiYBC复合材料的蠕变性能及损伤机理

doi:10.15541/jim20240289

无机材料学报 ›› 2025, Vol. 40 ›› Issue (1): 23-30.DOI: 10.15541/jim20240289 CSTR: 32189.14.10.15541/jim20240289

MI SiC_f/SiC-SiYBC复合材料的蠕变性能及损伤机理

张立¹(), 管皞阳¹, 郑琪宁¹, 洪智亮², 王佳璇¹, 邢宁¹, 李玫¹, 刘永胜¹, 张程煜¹()

1.西北工业大学超高温结构复合材料重点实验室, 西安 710072
2.中国航发商用航空发动机有限责任公司, 上海 200241

收稿日期:2024-06-13 修回日期:2024-09-02 出版日期:2025-01-20 网络出版日期:2024-09-02
通讯作者: 张程煜, 教授. E-mail: cyzhang@nwpu.edu.cn
作者简介:张立(1999-), 男, 硕士研究生. E-mail: li.zhang0606@mail.nwpu.edu.cn
基金资助:
国家自然科学基金(U2241239);国防科技基础加强计划(2023-JCJQ-LB-071)

Creep Properties and Damage Mechanisms of SiC_f/SiC-SiYBC Prepared by Melt Infiltration

ZHANG Li¹(), GUAN Haoyang¹, ZHENG Qining¹, HONG Zhiliang², WANG Jiaxuan¹, XING Ning¹, LI Mei¹, LIU Yongsheng¹, ZHANG Chengyu¹()

1. Key Laboratory of Ultra-High Temperature Structural Composites, Northwestern Polytechnical University, Xi’an 710072, China
2. AECC Commercial Aircraft Engine Co., Ltd., Shanghai 200241, China

Received:2024-06-13 Revised:2024-09-02 Published:2025-01-20 Online:2024-09-02
Contact: ZHANG Chengyu, professor. E-mail: cyzhang@nwpu.edu.cn
About author:ZHANG Li (1999-), male, Master candidate. E-mail: li.zhang0606@mail.nwpu.edu.cn
Supported by:
National Natural Science Foundation of China(U2241239);Basic Strengthening Program of China(2023-JCJQ-LB-071)

摘要/Abstract

摘要：

随着航空发动机的服役环境日益严苛, SiC_f/SiC在高温空气/水氧环境中的服役温度和应力亟需提升。为此, 研究人员尝试采用自愈合基体改性的方法提升SiC_f/SiC复合材料的抗氧化性能和抗蠕变性能。本工作研究了熔体渗透工艺(MI)制备的碳化硅纤维平纹布增强的SiYBC改性碳化硅复合材料(MI SiC_f/SiC-SiYBC)在空气中的拉伸蠕变性能及损伤机理, 蠕变温度为1300、1350和1400 ℃, 应力为60~120 MPa。结果显示: 在1300~1400 ℃范围内, MI SiC_f/SiC-SiYBC的蠕变断裂时间($t_{\mathrm{u}}$)与应力、温度密切相关, 随温度或应力升高而降低。当蠕变应力高于比例极限应力($\sigma_{\mathrm{PLS}}$)时, 基体开裂, 氧气会进入材料内部侵蚀纤维和BN界面, 使其发生氧化退化, 大幅降低$t_{\mathrm{u}}$。此时由于基体完全开裂, 载荷主要由纤维承担, $t_{\mathrm{u}}$受纤维的抗蠕变性能控制。当蠕变应力低于$\sigma_{\mathrm{PLS}}$时, $t_{\mathrm{u}}$较长, 载荷由纤维和基体共同承担, $t_{\mathrm{u}}$则受纤维和基体两者的抗蠕变性能共同控制。随着温度从1300 ℃升高至1400 ℃, 基体氧化物等物相填充界面间隙, 导致界面黏结, 促进裂纹张开和扩展。

关键词: SiC_f/SiC-SiYBC, 蠕变, 氧化, 损伤机制

Abstract:

As aeroengines operate in gradually harsher service environments, enhancement of the service temperature and stress tolerance of SiC_f/SiC is in great demand to ensure its proper work in high-temperature air/water-oxygen environments. Previously, researchers have initiated efforts to modify the matrix through self-healing techniques to enhance the oxidation resistance and creep resistance of SiC_f/SiC composites, but whether it can be modified for more severe conditions remained unknown. Here, SiYBC modified SiC_f/SiC composites (MI SiC_f/SiC-SiYBC) were prepared by melt infiltration (MI), and their tensile creep properties and damage mechanisms in air at temperatures of 1300, 1350, and 1400 ℃ with applied stresses ranging from 60 to 120 MPa were explored. The composites were reinforced with plain woven fabric of silicon carbide fibers, while the matrix was prepared by melt infiltration process. The results demonstrate that the creep rupture time ($t_{\mathrm{u}}$) is significantly influenced by stress and temperature, exhibiting a decrease with increasing temperature or stress. When test creep stress exceeds the proportional ultimate stress ($\sigma_{\mathrm{PLS}}$), the matrix cracking facilitates oxygen ingress into the material, leading to erosion of the fiber and BN interfaces and subsequent oxidative degradation, which markedly reduces $t_{\mathrm{u}}$. As a result, the matrix is fully fractured, and the load is mainly supported by the fibers, whose creep resistance becomes the principal factor influencing performance. Conversely, when the creep stress is below $\sigma_{\mathrm{PLS}}$, $t_{\mathrm{u}}$ is extended, with the load being borne by the fibers and the matrix, which is controlled by the combined creep resistance of fibers and matrix. Additionally, as the temperature increases from 1300 to 1400 ℃, the generated oxides fill the gap of the matrix/fiber interface, enhancing interfacial bonding and facilitating crack propagation and growth.

Key words: SiC_f/SiC-SiYBC, creep, oxidation, damage mechanism

中图分类号:

TB332

张立, 管皞阳, 郑琪宁, 洪智亮, 王佳璇, 邢宁, 李玫, 刘永胜, 张程煜. MI SiC_f/SiC-SiYBC复合材料的蠕变性能及损伤机理[J]. 无机材料学报, 2025, 40(1): 23-30.

ZHANG Li, GUAN Haoyang, ZHENG Qining, HONG Zhiliang, WANG Jiaxuan, XING Ning, LI Mei, LIU Yongsheng, ZHANG Chengyu. Creep Properties and Damage Mechanisms of SiC_f/SiC-SiYBC Prepared by Melt Infiltration[J]. Journal of Inorganic Materials, 2025, 40(1): 23-30.

图/表 9

图1 MI SiCf/SiC-SiYBC复合材料的微观组织

Fig. 1 Microstructure of MI SiCf/SiC-SiYBC composites

图2 蠕变和室温拉伸试样的形状和尺寸

Fig. 2 Shape and size of (a) creep specimen and (b) room temperature tensile specimen Unit: mm

表1 MI SiCf/SiC-SiYBC和国内外相关材料在空气中的蠕变断裂时间对比

Table 1 Comparison of creep rupture time of MI SiCf/SiC-SiYBC and related materials in air at home and abroad

Material	Process	Fiber	Temperature/℃	Stress/MPa	Creep rupture time/h	Source
SiC_f/SiC-SiYBC	MI	Cansas3300	1300	100	>1000	This work
			1300	120	52.70
			1350	70	>500
			1350	85	>500
			1350	100	24.18
			1400	60	>1000
			1400	70	195.12
			1400	85	1.32
			1400	100	3.78
SiC_f/SiC^[17]	CVI	Cansas-II	1200	110	>560	Northwestern Polytechnical University, China
			1300	100	70
			1400	100	1.60
SiC_f/SiC^[18]	CVI	Cansas3300	1300	100	>800
			1350	80	>1000
			1400	100	82
SiC_f/SiC^[19]	CVI	Hi-Nicalon	1300	75	111.10	DuPont Lanxide Composites, America
SiC_f/SiC^[19]	CVI	Hi-Nicalon	1300	120	0.83
Enhanced SiC_f/SiC^[16]	CVI	Hi-Nicalon	1300	90	5.28
Enhanced SiC_f/SiC^[16]	CVI	Hi-Nicalon	1300	150	0.23
SiC_f/SiC^[5,20]	MI	Hi-Nicalon Type S	1315	69	315	GE
			1315	103	190
			1400	69	150
			1400	103	38
SiC_f/SiC^[5,7,21]	MI	Sylramic-iBN	1204	165	1269
	MI	Sylramic-iBN	1315	103	500
	CVI	Sylramic-iBN	1450	86	>300
SiC_f/SiC^[22]	CVI	Hi-Nicalon Type S	1400	120	>200	SNECMA, France

图3 本工作与国内外相关SiCf/SiC蠕变后的剩余拉伸强度[5,7,17 -18]

Fig. 3 Residual tensile strength after creeping of this work and related SiCf/SiC at home and abroad[5,7,17 -18]

图4 MI SiCf/SiC-SiYBC在不同蠕变条件下的蠕变断口和裂纹分布

Fig. 4 Creep fractures and crack distributions of MI SiCf/SiC-SiYBC at different creep conditions Creep fractures: (a) 1400 ℃/70 MPa, 195.12 h; (b) 1400 ℃/100 MPa, 3.78 h; (c) 1350 ℃/100 MPa, 24.18 h Crack distributions: (d) 1400 ℃/70 MPa, 195.12 h; (e) 1400 ℃/100 MPa, 3.78 h; (f) 1350 ℃/100 MPa, 24.18 h

图5 MI SiCf/SiC-SiYBC在不同蠕变条件下的氧化损伤

Fig. 5 Oxidative damages of MI SiCf/SiC-SiYBC at different creep conditions (a) 1300 ℃/100 MPa, 1000 h; (b) 1350 ℃/100 MPa, 24.18 h; (c) 1400 ℃/70 MPa, 195.12 h; (d) 1400 ℃/100 MPa, 3.78 h

图6 100 MPa、不同蠕变温度下MI SiCf/SiC-SiYBC的物相变化

Fig. 6 Phase changes of MI SiCf/SiC-SiYBC after creep at 100 MPa and different temperatures

图7 蠕变前后氧化区的界面和纤维TEM照片

Fig. 7 TEM images of the interface and fiber in the oxidation zone before and after creep As-received: (a, c) TEM, (e, g) HRTEM images and SAED patterns of (a, e) interface and (c, g) fiber Creep at 1400 ℃/70 MPa: (b, d) TEM, (f, h) HRTEM images and SAED pattern of (b, f) interface and (d, h) fiber

图8 MI SiCf/SiC-SiYBC SiC纤维的晶粒尺寸变化图

Fig. 8 Grain size changes of SiC fibers in MI SiCf/SiC-SiYBC (a) After creep at 1400 ℃/70 MPa for 195.12 h; (b) As-received

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MI SiC_f/SiC-SiYBC复合材料的蠕变性能及损伤机理

Creep Properties and Damage Mechanisms of SiC_f/SiC-SiYBC Prepared by Melt Infiltration

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MI SiCf/SiC-SiYBC复合材料的蠕变性能及损伤机理

Creep Properties and Damage Mechanisms of SiCf/SiC-SiYBC Prepared by Melt Infiltration

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MI SiC_f/SiC-SiYBC复合材料的蠕变性能及损伤机理

Creep Properties and Damage Mechanisms of SiC_f/SiC-SiYBC Prepared by Melt Infiltration