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

doi:10.15541/jim20240289

Abstract

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

CLC Number:

TB332

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.

Figures/Tables 9

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

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

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

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

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

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

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

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

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

References 27

[1]	刘巧沐, 黄顺洲, 何爱杰. 碳化硅陶瓷基复合材料在航空发动机上的应用需求及挑战. 材料工程, 2019, 47(2): 1. DOI
[2]	李崇俊. SiC/SiC复合材料及其应用. 高科技纤维与应用, 2013, 38(3): 1.
[3]	ALMANSOUR A. Characterizing ceramic-matrix composites to improve durability. American Ceramic Society Bulletin, 2016, 95(5): 35.
[4]	KOWBEL W, BRUCE C A, TSOU K L, et al. High thermal conductivity SiC/SiC composites for fusion applications. Journal of Nuclear Materials, 2000, 283: 570.
[5]	BHATT R T, HALBIG M C. Creep properties of melt infiltrated SiC/SiC composites with Sylramic™-iBN and Hi-Nicalon™-S fibers. International Journal of Applied Ceramic Technology, 2022, 19(2): 1074.
[6]	DICARLO J A, ROODE M V. Ceramic composite development for gas turbine engine hot section components. ASME Turbo Expo 2006: Power for Land, Sea, and Air, Barcelona, 2006: 221.
[7]	BHATT R T, KISER J D. Creep behavior and failure mechanisms of CVI and PIP SiC/SiC composites at temperatures to 1650 ℃ in air. Journal of the European Ceramic Society, 2021, 41(13): 6196.
[8]	CHRISTENSEN V L, ZOK F W. Insights into internal oxidation of SiC/BN/SiC composites. Journal of the American Ceramic Society, 2023, 106(2): 1561.
[9]	VAUGHN W L, MAAHS H G. Active-to-passive transition in the oxidation of silicon carbide and silicon nitride in air. Journal of the American Ceramic Society, 1990, 73(6): 1540.
[10]	黄璇璇, 郭双全, 姚改成, 等. 航空发动机SiC/SiC复合材料环境障碍涂层研究进展. 航空维修与工程, 2017(2): 28.
[11]	TEJERO-MARTIN D, BENNETT C, HUSSAIN T. A review on environmental barrier coatings: history, current state of the art and future developments. Journal of the European Ceramic Society, 2021, 41(3): 1747.
[12]	HE F, CAO Y J, LIU Y S, et al. Self-healing and failure behavior of yttrium silicate coated SiC_f/SiC composites in air at elevated temperatures. Ceramics International, 2023, 49(3): 5335.
[13]	LI J X, LIU Y S, HE F, et al. Preparation and properties of SiC/SiC-SiYC with excellent water-oxygen corrosion resistance. Journal of the European Ceramic Society, 2023, 43(14): 6606.
[14]	ZHANG B H, LIU Y S, GAO Y Q, et al. Water and oxygen corrosion resistance of SiC_f/SiC-SiYBC composites prepared by reactive melt infiltration at 1300 ℃-1500 ℃. International Journal of Applied Ceramic Technology, 2024, 21(2): 1094.
[15]	高雨晴. 反应熔渗法制备抗水腐蚀Si-Y-C陶瓷基复合材料的工艺研究. 西安: 西北工业大学硕士学位论文, 2021.
[16]	ZHU S J, MIZUNO M, NAGANO Y, et al. Creep and fatigue behavior in an enhanced SiC/SiC composite at high temperature. Journal of the American Ceramic Society, 1998, 81(9): 2269.
[17]	JING K K, GUAN H Y, ZHU S Y, et al. Tensile creep behavior of Cansas-II SiC_f/SiC composites at high temperatures. Journal of Inorganic Materials, 2023, 38(2): 177.
[18]	管皞阳. 国产三代2D-SiC_f/SiC的高温拉伸蠕变性能及损伤机理. 西安: 西北工业大学硕士学位论文, 2024.
[19]	ZHU S J, MIZUNO M, KAGAWA Y, et al. Monotonic tension, fatigue and creep behavior of SiC-fiber-reinforced SiC-matrix composites: a review. Composites Science and Technology, 1999, 59(6): 833.
[20]	LAMON J. Properties and characteristics of SiC and SiC/SiC composites//KONINGS R J M, STOLLER R E. Comprehensive nuclear materials. Second Edition. Amsterdam: Elsevier, 2020: 400.
[21]	MORSCHER G N. Tensile creep of melt-infiltrated SiC/SiC composites with unbalanced Sylramic-iBN fiber architectures. International Journal of Applied Ceramic Technology, 2011, 8(2): 239.
[22]	LACOMBE A, SPRIET P, HABAROU G, et al. Ceramic matrix composites to make breakthroughs in aircraft engine performance. 50th AIAA/ASME/ASCE/AHS/ASC Structures, Structural Dynamics, and Materials Conference, Palm Springs, 2009: 2675.
[23]	HE F, LIU Y S, LI J X, et al. The impact of water and oxygen contents on the corrosion performance of yttrium silicate modified SiC_f/SiC composites under high temperature conditions. Journal of the European Ceramic Society, 2024, 44(4): 2065.
[24]	JACOBSON N S, MYERS D L. Active oxidation of SiC. Oxidation of Metals, 2011, 75(1): 1.
[25]	NARUSHIMA T, GOTO T, IGUCHI Y, et al. High-temperature oxidation of chemically vapor-deposited silicon carbide in wet oxygen at 1823 to 1923 K. Journal of the American Ceramic Society, 1990, 73(12): 3580.
[26]	PRESSER V, NICKEL K G. Silica on silicon carbide. Critical Reviews in Solid State and Materials Sciences, 2008, 33(1): 1.
[27]	曲诚诚. 国产SiC纤维的性能表征及抗氧化行为研究. 西安: 西北工业大学硕士学位论文, 2021.