PIP和RMI法制备SiC/SiC复合材料水氧侵蚀机理研究

doi:10.15541/jim20260011

无机材料学报 ›› 2026, Vol. 41 ›› Issue (9): 1273-1284.DOI: 10.15541/jim20260011

PIP和RMI法制备SiC/SiC复合材料水氧侵蚀机理研究

郭斐宇¹(), 沙建军¹, 陈小武², 程国峰³, 董绍明²

¹ 苏州国家实验室结构材料研究部, 苏州 215123
² 中国科学院上海硅酸盐研究所, 关键陶瓷材料全国重点实验室, 上海 200050
³ 中国科学院上海硅酸盐研究所, 无机材料分析测试中心, 上海 200050

收稿日期:2026-01-10 修回日期:2026-03-10 出版日期:2026-09-20 网络出版日期:2026-04-20
作者简介:郭斐宇(1997-), 女, 助理研究员. E-mail: guofy0507@163.com
基金资助:
中国博士后科学基金资助项目(2025M773340)

Wet-oxidation Mechanism of SiC/SiC Composites Prepared by PIP and RMI Routes

GUO Feiyu¹(), SHA Jianjun¹, CHEN Xiaowu², CHENG Guofeng³, DONG Shaoming²

¹ Research Department of Structural Materials, Suzhou National Laboratory, Suzhou 215123, China
² National Key Laboratory of High Performance Ceramics, Shanghai Institute of Ceramics, Chinese Academy of Sciences, Shanghai 200050, China
³ Analysis and Testing Center for Inorganic Materials, Shanghai Institute of Ceramics, Chinese Academy of Sciences, Shanghai 200050, China

Received:2026-01-10 Revised:2026-03-10 Published:2026-09-20 Online:2026-04-20
About author:GUO Feiyu (1997-), female, assistant professor. E-mail: guofy0507@163.com
Supported by:
China Postdoctoral Science Foundation(2025M773340)

摘要/Abstract

摘要：

SiC/SiC复合材料具有高韧性、热稳定性以及抗氧化性能等, 是航空发动机热端部件的理想候选材料。然而, 高温水氧侵蚀对SiC/SiC复合材料的工程化应用提出了严峻挑战, 揭示SiC/SiC复合材料在服役条件下的微观结构演变和性能衰退机制是预测航空发动机使用寿命的关键。基于此, 本研究采用先驱体浸渍裂解(PIP)和反应熔渗(RMI)两种液相法制备SiC/SiC复合材料, 借助原位水氧拉曼表征手段, 系统研究了SiC/SiC复合材料高温水氧环境下的退化行为。结果表明: PIP-SiC/SiC基体中残留碳在700~1100 ℃发生氧化并以气态产物形式逸出, 导致基体内部形成微孔及通道等结构缺陷, 水氧介质迅速抵达纤维和界面区域, 促使BN界面相在700 ℃发生氧化侵蚀; 1000 ℃时, SiC纤维因持续氧化作用而出现表面结构损伤; 1100 ℃时, 界面相载荷传递能力下降进一步造成PIP-SiC/SiC弯曲性能降低。相比之下, RMI-SiC/SiC基体中残留硅和SiC发生氧化形成熔融SiO₂, 在一定程度上减缓了水氧侵蚀, 其BN界面相的氧化起始温度为900 ℃, 且SiC纤维结构保持完整; 1100 ℃时, SiO₂、B₂O₃等氧化产物的填充作用提升了基体强度和界面结合力, 确保载荷从基体有效传递至纤维, 因而RMI-SiC/SiC经高温水氧侵蚀后的弯曲性能更稳定。本研究为陶瓷基复合材料的结构调控和性能优化提供了新的表征手段和理论思路。

关键词: SiC/SiC, 原位拉曼, 液相法, 水氧侵蚀, 弯曲性能

Abstract:

SiC/SiC composites, renowned for their high toughness, thermal stability and oxidation resistance, become ideal candidate materials for hot-section components in aeroengines. However, high-temperature steam environments pose significant challenges to their practical application. Investigating the microstructural evolution and performance degradation mechanisms of SiC/SiC is crucial for predicting the service life of aeroengine. Here, SiC/SiC composites were fabricated using two liquid-phase methods: precursor infiltration and pyrolysis (PIP) and reactive melt infiltration (RMI). The oxidation behavior of SiC/SiC under high-temperature wet-oxygen conditions was evaluated comprehensively by in-situ wet-oxygen Raman and conventional characterization. The results indicated that residual carbon in PIP-SiC/SiC matrix was oxidized and volatilized as gaseous products between 700 and 1100 ℃, generating structural defects such as micropores and channels in SiC matrix. Thus, the wet-oxygen corrosive gases rapidly diffused to the fiber and interphase regions, leading to the oxidation and erosion of BN interphase at 700 ℃. At 1000 ℃, continuous oxidation caused significant surface structural damage to SiC fibers. With the temperature rising to 1100 ℃, the load-transfer capability of BN interphase was degraded, which can weaken the flexural properties of PIP-SiC/SiC. In contrast, the residual silicon and SiC in RMI-SiC/SiC matrix were oxidized to form molten SiO₂, which can hinder wet-oxygen corrosion. The onset temperature of BN interphase oxidation was increased to 900 ℃, preserving the structural integrity of SiC fibers. At 1100 ℃, the filling effect of oxidation products, including SiO₂ and B₂O₃ can improve SiC matrix strength and interfacial bonding, ensuring efficient load transfer from the matrix to fibers. Consequently, RMI-SiC/SiC exhibits more stable flexural performance in high temperature wet-oxygen environments. This study provides innovative characterization and performance optimization strategies for the structural design of ceramic matrix composites.

Key words: SiC/SiC, in-situ Raman, liquid phase route, wet-oxidation, flexural property

中图分类号:

TB332

郭斐宇, 沙建军, 陈小武, 程国峰, 董绍明. PIP和RMI法制备SiC/SiC复合材料水氧侵蚀机理研究[J]. 无机材料学报, 2026, 41(9): 1273-1284.

GUO Feiyu, SHA Jianjun, CHEN Xiaowu, CHENG Guofeng, DONG Shaoming. Wet-oxidation Mechanism of SiC/SiC Composites Prepared by PIP and RMI Routes[J]. Journal of Inorganic Materials, 2026, 41(9): 1273-1284.

图/表 13

图1 原位(a)和离位(b)高温水氧实验设备原理图

Fig. 1 Schematic diagram of in-situ (a) and conventional (b) high temperature wet-oxygen equipment

图2 700~1100 ℃水氧环境下, PIP-SiC/SiC实时形貌氧化照片(a~f), 以及SiC基体(g)和SiC纤维(h)的实时拉曼图谱

Fig. 2 In-situ oxidation morphologies of PIP-SiC/SiC (a-f), along with Raman spectra of SiC matrix (g) and SiC fibers (h) in the wet-oxygen atmosphere at 700-1100 ℃

图3 PIP-SiC/SiC基体(a, b)和纤维(c, d)中各物相的峰面积(a, c)和FWHM (b, d)变化趋势图

Fig. 3 Peak area (a, c) and FWHM (b, d) of different components in PIP-SiC/SiC matrix (a, b) and fibers (c, d)

图4 700~1100 ℃水氧氧化后PIP-SiC/SiC的SEM照片(a~f)及相应的EDS结果(g, h)

Fig. 4 SEM images (a-f) and the corresponding EDS results (g, h) of PIP-SiC/SiC after wet-oxidation at 700-1100 ℃

图5 700~1100 ℃水氧氧化后PIP-SiC/SiC的XRD图谱

Fig. 5 XRD patterns of PIP-SiC/SiC after wet-oxidation at 700-1100 ℃

图6 700~1100 ℃水氧环境中RMI-SiC/SiC实时氧化的形貌(a~f), 以及SiC基体(g)和SiC纤维(h)的实时拉曼图谱

Fig. 6 In-situ oxidation morphologies of RMI-SiC/SiC (a-f), along with Raman spectra of SiC matrix (g) and SiC fibers (h) in the wet-oxygen atmosphere at 700-1100 ℃

图7 RMI-SiC/SiC基体(a, b)和纤维(c, d)中各物相的峰面积(a, c)和FWHM (b, d)的变化趋势图

Fig. 7 Peak area (a, c) and FWHM (b, d) of different components in RMI-SiC/SiC matrix (a, b) and fibers (c, d)

图8 700~1100 ℃水氧氧化后RMI-SiC/SiC的SEM照片及N元素的EDS分布图

Fig. 8 SEM images of RMI-SiC/SiC and EDS elemental mappings of N element after wet-oxidation at 700-1100 ℃

图9 700~1100 ℃水氧氧化后RMI-SiC/SiC的XRD图谱

Fig. 9 XRD patterns of RMI-SiC/SiC after wet-oxidation at 700-1100 ℃

图10 PIP-SiC/SiC和RMI-SiC/SiC在700~1100 ℃水氧环境中的质量变化曲线

Fig. 10 Weight changes of PIP-SiC/SiC and RMI-SiC/SiC under 700-1100 ℃ wet-oxygen atmosphere

图11 PIP-SiC/SiC (a)和RMI-SiC/SiC (b)经水氧侵蚀前后的载荷-位移曲线及强度保留率(c)

Fig. 11 Load-displacement curves of PIP-SiC/SiC (a) and RMI-SiC/SiC (b) before and after wet-oxidation at 1100 ℃, along with the strength retention (c)

表1 1100 ℃水氧侵蚀前后PIP-SiC/SiC和RMI-SiC/SiC的弯曲强度

Table 1 Flexural strength of PIP-SiC/SiC and RMI-SiC/SiC before and after wet-oxidation at 1100 ℃

PIP-SiC/SiC	${{\sigma }_{\text{b}}}$/MPa	RMI-SiC/SiC	${{\sigma }_{\text{b}}}$/MPa
As-received	384±43	As-received	301±10
1100 ℃	266±29	1100 ℃	338±36

图12 PIP-SiC/SiC (a~d)和RMI-SiC/SiC (e~h)的弯曲断口形貌

Fig. 12 Fracture morphologies of PIP-SiC/SiC (a-d) and RMI-SiC/SiC (e-h)

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PIP和RMI法制备SiC/SiC复合材料水氧侵蚀机理研究

Wet-oxidation Mechanism of SiC/SiC Composites Prepared by PIP and RMI Routes

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