烧结条件对制备高结晶近化学计量比SiC纤维的影响

doi:10.15541/jim20240439

无机材料学报 ›› 2025, Vol. 40 ›› Issue (4): 405-414.DOI: 10.15541/jim20240439 CSTR: 32189.14.10.15541/jim20240439

烧结条件对制备高结晶近化学计量比SiC纤维的影响

苟燕子¹(), 康伟峰¹, 王堋人²

1.国防科技大学空天科学学院, 新型陶瓷纤维及其复合材料重点实验室, 长沙 410073
2.酒泉卫星发射中心, 兰州 732750

收稿日期:2024-10-18 修回日期:2024-11-18 出版日期:2025-04-20 网络出版日期:2024-11-25
作者简介:苟燕子(1984-), 副研究员. E-mail: y.gou2012@hotmail.com
基金资助:
国家自然科学基金(52272100);湖南省自然科学基金面上项目(2022JJ30662);新型陶瓷纤维及其复合材料重点实验室基金项目(WDZC20215250507);核反应堆技术全国重点实验室(中国核动力研究设计院)基金(KGSW-0324-0301-08)

Influence of Sintering Conditions on Preparation of Nearly Stoichiometric SiC Fibers with Highly Crystalline Microstructure

GOU Yanzi¹(), KANG Weifeng¹, WANG Pengren²

1. Science and Technology on Advanced Ceramic Fibers and Composites Laboratory, College of Aerospace Science and Engineering, National University of Defense Technology, Changsha 410073, China
2. Jiuquan Satellite Launch Center, Lanzhou 732750, China

Received:2024-10-18 Revised:2024-11-18 Published:2025-04-20 Online:2024-11-25
About author:GOU Yanzi (1984-), associate professor. E-mail: y.gou2012@hotmail.com
Supported by:
National Natural Science Foundation of China(52272100);Natural Science Foundation of Hunan Province(2022JJ30662);Fund of Science and Technology on Advanced Ceramic Fibers and Composites Laboratory(WDZC20215250507);Fund of National Key Laboratory of Nuclear Reactor Technology of Nuclear Power Institute of China(KGSW-0324-0301-08)

摘要/Abstract

摘要：

细直径连续SiC纤维是先进陶瓷基复合材料的最佳增强纤维之一, 在航空航天和核工业领域具有重要的应用价值, 其中高结晶近化学计量比SiC纤维的耐温性能最好, 但是高温烧结条件对该纤维元素组成与微观结构的影响规律还不清楚。本工作研究了烧结温度和时间对纤维中SiC_xO_y相分解、晶粒长大以及纤维致密化的影响规律, 发现SiC_xO_y相分解和纤维的致密化过程均是由表层逐渐向芯部进行, 并且只有在适当的烧结温度(1800 ℃)下, 才能通过生长β-SiC晶粒来弥补SiC_xO_y相分解产生的孔隙缺陷, 最终实现纤维的致密化。值得注意的是, 过高的烧结温度会造成β-SiC晶粒分解。虽然延长烧结时间有助于消除纤维中的残余氧, 但会使β-SiC晶界处的石墨相变得更加集中, 且纤维芯部产生更多的孔隙缺陷。通过优化条件最终成功制备了致密的高结晶近化学计量比SiC纤维, 其组成为SiC_1.04O_0.02Al_<0.01, 纤维中的β-SiC晶粒均匀分布, 尺寸达到100~200 nm。纤维的拉伸强度和杨氏模量分别为1.88 GPa和373 GPa, 并且密度高达3.1 g/cm³。上述研究结果可以为进一步提升SiC纤维的综合性能奠定坚实的基础。

关键词: SiC纤维, 烧结, 近化学计量比, 密度, 高结晶

Abstract:

Fine-diameter continuous SiC fibers are considered one of the most effective reinforcing fibers for advanced ceramic matrix composites, possessing significant application potential in aerospace and nuclear industries. Among them, near-stoichiometric SiC fibers characterized by a highly crystalline microstructure have garnered considerable attention due to their exceptional high-temperature resistance. However, influence of high-temperature sintering conditions on composition and microstructure of the fibers is still unclear. Here, influences of different sintering temperatures and durations on decomposition of the SiC_xO_y phase, grain growth and densification of the fibers were systematically investigated. It was found that decomposition of SiC_xO_y and densification of fibers occur progressively from surface to core. Notably, a specific sintering temperature of 1800 ℃ was identified as optimal, wherein growth of β-SiC grains effectively compensated for the pore defects resulting from the decomposition of SiC_xO_yphase, thereby achieving fiber densification. Conversely, excessively high sintering temperature might result in decomposition of β-SiC grains. Although extending sintering duration facilitated removal of residual oxygen within the fibers, it could cause accumulation of graphite phases at β-SiC grain boundaries, leading to an increase in pore defects within the fiber core. Finally, near-stoichiometric SiC fibers with highly crystalline microstructure were successfully fabricated through optimization of sintering conditions, possessing a composition of SiC_1.04O_0.02Al_<0.01. The β-SiC grains within the fibers were uniformly distributed with sizes ranging from 100 to 200 nm. The fibers exhibited a tensile strength of 1.88 GPa and a Young’s modulus of 373 GPa, accompanied by a high density of 3.1 g/cm³. The findings of this research provide a robust foundation for further improving comprehensive properties of SiC fibers.

Key words: SiC fiber, sintering, nearly stoichiometric, density, highly crystalline

中图分类号:

TQ343

苟燕子, 康伟峰, 王堋人. 烧结条件对制备高结晶近化学计量比SiC纤维的影响[J]. 无机材料学报, 2025, 40(4): 405-414.

GOU Yanzi, KANG Weifeng, WANG Pengren. Influence of Sintering Conditions on Preparation of Nearly Stoichiometric SiC Fibers with Highly Crystalline Microstructure[J]. Journal of Inorganic Materials, 2025, 40(4): 405-414.

图/表 24

表1 Si-C-O-Al纤维及中间纤维的化学组成和力学性能

Table 1 Chemical composition and mechanical properties of Si-C-O-Al fibers and intermediate fibers

Sample	O content/(%, in mass)	C/Si atomic ratio	Tensile strength/GPa	Young’s modulus/GPa	Diameter/μm
Si-C-O-Al fiber	8.93	1.33	2.27	204	11.6
Intermediate SiC fiber	0.98	1.06	1.54	283	10.8

图1 中间纤维的SEM照片

Fig. 1 SEM images of the intermediate fibers (a) Fiber surface; (b) Magnified region 1; (c) Fiber cross section; (d) Magnified region 2; (e) Magnified region 3

图2 烧结SiC (SF)纤维的表面形貌

Fig. 2 Surface morphologies of the sintered SiC (SF) fibers (a, b) SiC (SF)-1600-1 h; (c, d) SiC (SF)-1800-1 h; (e, f) SiC (SF)-2000-1 h

图3 烧结SiC (SF)纤维的截面形貌

Fig. 3 Cross-sectional morphologies of the sintered SiC (SF) fibers (a-c) SiC (SF)-1600-1 h; (d-f) SiC (SF)-1800-1 h; (g-i) SiC (SF)-2000-1 h

表2 不同温度烧结制备的SiC (SF)纤维的化学组成(质量分数)

Table 2 Chemical composition (mass fraction) of the SiC (SF) fibers sintered at different temperatures

Sample	C/%	Si/%	O/%	Al/%	C/Si atomic ratio
SiC (SF)-1600-1 h	31.88	67.50	0.80	<1.00	1.10
SiC (SF)-1700-1 h	32.37	66.31	0.82	<1.00	1.14
SiC (SF)-1800-1 h	31.48	67.41	0.61	<1.00	1.09
SiC (SF)-1900-1 h	33.04	66.14	0.32	<1.00	1.17
SiC (SF)-2000-1 h	38.27	61.13	0.10	<1.00	1.46

图4 不同温度烧结后SiC (SF)纤维的Raman谱图(a)和XRD谱图(b)

Fig. 4 Raman spectra (a) and XRD patterns (b) of the SiC (SF) fibers sintered at different temperatures

图5 SiC (SF)纤维的HRTEM照片

Fig. 5 HRTEM images of the SiC (SF) fibers (a, b) SiC (SF)-1600-1 h; (c, d) SiC (SF)-1800-1 h; (e, f) SiC (SF)-2000-1 h

图6 高结晶近化学计量比SiC纤维的烧结致密化过程示意图

Fig. 6 Schematic diagram of the sintering densification process of nearly stoichiometric polycrystalline SiC fibers

图7 1800 ℃下烧结不同时间的SiC (SF)纤维的截面形貌

Fig. 7 Cross-sectional morphologies of the SiC (SF) fibers sintered at 1800 ℃ for different durations (a-c) SiC (SF)-1800-10 min; (d-f) SiC (SF)-1800-30 min; (g-i) SiC (SF)-1800-2 h

表3 1800 ℃下烧结不同时间的SiC (SF)纤维的化学组成(质量分数)

Table 3 Chemical composition (mass fraction) of the SiC (SF) fibers sintered at 1800 ℃ for different durations

Sample	C/%	Si/%	O/%	Al/%	C/Si atomic ratio
SiC (SF)-1800-10 min	31.82	66.93	0.75	<1.00	1.11
SiC (SF)-1800-1 h	31.48	67.41	0.61	<1.00	1.09
SiC (SF)-1800-2 h	31.54	67.96	0	<1.00	1.08

图8 1800 ℃烧结不同时间的SiC (SF)纤维的HRTEM照片

Fig. 8 HRTEM images of the SiC (SF) fibers sintered at 1800 ℃ for different durations (a, b) SiC (SF)-1800-10 min; (c, d) SiC (SF)-1800-30 min; (e, f) SiC (SF)-1800-2 h

表4 SiC (SF)和SiC (SG)纤维的力学性能

Table 4 Mechanical properties of SiC (SF) and SiC (SG) fibers

Sample	Tensile strength/ GPa	Young’s modulus/ GPa	Fiber diameter/ μm	Chemical formula
SiC (SF)	1.88	373	11.2	SiC_1.04O_0.02Al_<0.01
SiC (SG)	2.96	268	11.6	SiC_1.31O_0.05

图9 SiC (SF)和SiC (SG)纤维表面的SEM照片

Fig. 9 Surface SEM images of SiC (SF) and SiC (SG) fibers (a, b) SiC (SF) fiber; (c, d) SiC (SG) fiber

图10 SiC (SF)和SiC (SG)纤维截面的SEM照片

Fig. 10 Cross-sectional SEM images of SiC (SF) and SiC (SG) fibers (a-c) SiC (SF) fiber; (d-f) SiC (SG) fiber

图11 SiC (SF)和SiC (SG)纤维的SAED图案、TEM和HRTEM照片

Fig. 11 SAED patterns, TEM and HRTEM images of SiC (SF) and SiC (SG) fibers (a-c) SiC (SF) fiber; (d-f) SiC (SG) fiber

图S1 中间纤维(a)和Si-C-O-Al纤维(b)的XRD谱图

Fig. S1 XRD patterns of the intermediate fibers (a) and the Si-C-O-Al fibers (b)

表S1 在1600~2000 ℃烧结1 h得到的SiC (SF)纤维的Raman结果

Table S1 Raman results of the SiC (SF) fibers sintered at 1600-2000 ℃ for 1 h

Sample	D peak/cm^-1		G peak/cm^-1		I_D/I_G
Sample	Position	FWHM	Position	FWHM	I_D/I_G
SiC (SF)-1600-1 h	1357	56.0	1590	47.0	1.41
SiC (SF)-1800-1 h	1358	51.4	1593	42.2	1.01
SiC (SF)-2000-1 h	1357	49.3	1585	28.8	0.31

图S2 SiC (SF)纤维力学性能随烧结温度的变化曲线

Fig. S2 Changes of mechanical properties of the SiC (SF) fibers with sintering temperature

图S3 SiC (SF)纤维在不同温度烧结后的拉伸强度

Fig. S3 Tensile strength of SiC (SF) fibers after sintered at different temperatures (a) 1500 ℃; (b) 1600 ℃; (c) 1700 ℃; (d) 1800 ℃; (e) 1900 ℃

图S4 在1800 ℃烧结不同时间后SiC (SF)纤维的表面形貌

Fig. S4 Surface morphologies of the SiC (SF) fibers sintered at 1800 ℃ for different durations (a, b) SiC (SF)-1800-10 min; (c, d) SiC (SF)-1800-30 min; (e, f) SiC (SF)-1800-2 h

图S5 SiC (SF)纤维在1800 ℃烧结不同时间后的XRD谱图

Fig. S5 XRD patterns of the SiC (SF) fibers sintered at 1800 ℃ for different durations

图S6 1800 ℃下SiC (SF)纤维力学性能随烧结时间的关系曲线

Fig. S6 Changes of mechanical properties of the SiC (SF) fibers with sintering time at 1800 ℃

图S7 SiC (SF)纤维在1800 ℃不同烧结时间后的拉伸强度

Fig. S7 Tensile strength of SiC (SF) fibers sintered at 1800 ℃ for different durations (a) 10 min; (b) 30 min; (c) 1 h; (d) 2 h

图S8 F-1(a~c)、F-2(d~f)和F-3(g~i)断面的SEM照片[25]

Fig. S8 SEM images of fracture morphologies for the ﬁbers F-1 (a-c), F-2 (d-f) and F-3 (g-i) More details of the fracture surfaces can be found in the enlarged images for the outer parts (b, e, h) as indicated by red square 1 and the core parts (c, f, i) as indicated by red square 2[25]

参考文献 38

[1]	KANG W, CHEN J, ZHANG Y, et al. SiC fibers with different diameters exhibiting excellent high-temperature resistance and oxidation resistance. Journal of Materials Research and Technology, 2023, 23: 1559.
[2]	CHEN J, ZHANG Y, YAN D, et al. Flexible ultrafine nearly stoichiometric polycrystalline SiC fibers with excellent oxidation resistance and superior thermal stability up to 1900 ℃. Journal of the European Ceramic Society, 2022, 42(5): 1938.
[3]	XIANG Y, WU S, YU J, et al. Long-time oxidation behavior of the nearly stoichiometric polycrystal-line SiC fibers under air atmosphere at different temperatures. Journal of the European Ceramic Society, 2024, 44(6):3569.
[4]	SHAN J, MO G, SUN Q, et al. Fabrication of SiC (OAl) and SiC (Al) fibers by melt-spinning, UV curing, thermolysis and sintering of photo-sensitive polyvinylaluminocarbosilane. Journal of the European Ceramic Society, 2024, 44(6):3501.
[5]	MORSCHER G N, HURST J, BREWER D. Intermediate- temperature stress rupture of a woven Hi-Nicalon, BN-interphase, SiC-matrix composite in air. Journal of the American Ceramic Society, 2000, 83(6):1441.
[6]	KATOH Y, SNEAD L L, HENAGER C H, et al. Current status and critical issues for development of SiC composites for fusion applications. Journal of Nuclear Materials, 2007, 367: 659.
[7]	PANAKARAJUPALLY R P, MIRZA F, EL RASSI J, et al. Solid particle erosion behavior of melt-in-filtrated SiC/SiC ceramic matrix composites (CMCs) in a simulated turbine engine environ- ment. Composites Part B: Engineering, 2021, 216: 108860.
[8]	ARREGUI-MENA J D, KOYANAGI T, CAKMAK E, et al. Qualitative and quantitative analysis of neutron irradiation effects in SiC/SiC composites using X-ray computed tomography. Composites Part B: Engineering, 2022, 238: 109896.
[9]	ZHANG S, GAO X, HAN X, et al. Prediction of strength and constitutive response of SiC/SiC composites considering fiber failure. Composites Part B: Engineering, 2019, 163: 252.
[10]	BHATT R, ELDRIDGE J. Heat treatment effects on microstructure and properties of CVI SiC/SiC composites with Sylramic^TM-iBN SiC fibers. Journal of the European Ceramic Society, 2023, 43(6):2376.
[11]	ZHAO Z, LIAO W, CHEN J, et al. Advanced research on the preparation and application of carbide ceramic fibers. Journal of Advanced Ceramics, 2024, 13(9):1291.
[12]	LV X, YUE M, FENG X, et al. Rare earth mono-silicates as oxidation resistant interphase for SiC_f/SiC CMC: investigation of SiC_f/Yb₂SiO₅ model composites. Journal of Advanced Ceramics, 2022, 11(5):702.
[13]	YAJIMA S, HASEGAWA Y, OKAMURA K, et al. Development of high tensile strength silicon carbide fibre using an organosilicon polymer precursor. Nature, 1978, 273(5663):525.
[14]	YAJIMA S, OKAMURA K, HAYASHI J, et al. Synthesis of continuous SiC fibers with high tensile strength. Journal of the American Ceramic Society, 1976, 59(7/8):324.
[15]	KANG W, ZHANG Q, GOU Y. Fabrication of highly crystalline titanium-containing SiC fibers with different boron contents exhibiting excellent electromagnetic wave absorption. Journal of Materials Science, 2024, 59(7):2739.
[16]	ZHANG Q, CHEN T, KANG W, et al. Synthesis of polytitanocarbosilane and preparation of Si-C-Ti-B fibers. Processes, 2023, 11: 1189.
[17]	WU S, GOU Y, XIANG Y, et al. Effect of long-time annealing at high temperature on the microstructure and mechanical properties of different types of SiC fibers. Composites Part A: Applied Science and Manufacturing, 2024, 185: 108291.
[18]	GOU Y, KANG W, ZHANG Q. Preparation of nearly stoichiometric SiC(Ti) fibers with highly crystalline microstructure from polytitanocarbosilane. Journal of Inorganic Materials, 2024, 39(12):1377.
[19]	BUNSELL A R, PIANT A. A review of the development of three generations of small diameter silicon carbide fibres. Journal of Materials Science, 2006, 41(3):823.
[20]	WANG P, LIU F, WANG H, et al. A review of third generation SiC fibers and SiC_f/SiC composites. Journal of Materials Science and Technology, 2019, 35(12):2743.
[21]	SCHAWALLER D, CLAUSS B, BUCHMEISER M R. Ceramic filament fibers-a review. Macromolecular Materials and Engineering, 2012, 297(6):502.
[22]	ISHIKAWA T, KOHTOKU Y, KUMAGAWA K, et al. High- strength alkali-resistant sintered SiC fibre stable to 2200 ℃. Nature, 1998, 391(6669):773.
[23]	TAKEDA M, SAEKI A, SAKAMOTO J I, et al. Effect of hydrogen atmosphere on pyrolysis of cured polycarbosilane fibers. Journal of the American Ceramic Society, 2000, 83(5):1063.
[24]	BHATT R, SOLA F, EVANS L, et al. Microstruc-tural, strength, and creep characterization of Sylramic™, Sylramic™-iBN and super Sylramic™-iBN SiC fibers. Journal of the European Ceramic Society, 2021, 41(9):4697.
[25]	ZHANG Y, WU C, WANG Y, et al. A detailed study of the microstructure and thermal stability of typical SiC fibers. Materials Characterization, 2018, 146: 91.
[26]	GOU Y, JIAN K, WANG H, et al. Fabrication of nearly stoichiometric polycrystalline SiC fibers with excellent high-temperature stability up to 1900 ℃. Journal of the American Ceramic Society, 2018, 101(5): 2050.
[27]	WANG P, GOU Y, WANG H, et al. Revealing the formation mechanism of the skin-core structure in nearly stoichiometric polycrystalline SiC fibers. Journal of the European Ceramic Society, 2020, 40(6):2295.
[28]	YUAN Q, SONG Y. Effect of SiC_xO_y decomposition on densification of SiCO (Al) fibers during sintering process. Journal of Inorganic Materials, 2016, 31(12):1320. DOI
[29]	USUKAWA R, ODA H, ISHIKAWA T, et al. Conversion process of amorphous Si-Al-C-O fiber into nearly stoichiometric SiC polycrystalline fiber. Journal of the Korean Ceramic Society, 2016, 53(6):610.
[30]	OKAMURA K, SHIMOO T, SUZUYA K, et al. SiC-based ceramic fibers prepared via organic-to-inorganic conversion process-a review. Journal of the Ceramic Society of Japan, 2006, 114(1330):445.
[31]	JACOBSON N S, KLINE S E. A thermoanalytical study of the conversion of amorphous Si-Ti-C-O fibers to SiC. International Journal of Applied Ceramic Technology, 2012, 9(4):816.
[32]	SNEAD L L, NOZAWA T, KATOH Y, et al. Hand-book of SiC properties for fuel performance modeling. Journal of Nuclear Materials, 2007, 371(1/3):329.
[33]	VAN DER BERG N, MALHERBE J B, BOTHA A, et al. Thermal etching of SiC. Applied Surface Science, 2012, 258(15):5561.
[34]	ZHANG Y, CHEN J, YAN D, et al. Conversion of silicon carbide fibers to continuous graphene fibers by vacuum annealing. Carbon, 2021, 182: 435.
[35]	ZHANG Y, CHEN T, CHEN J, et al. The effects of annealing atmosphere and intrinsic component on high temperature evolution behaviors of SiC fibers. Materials Science and Engineering: A, 2022, 848: 143363.
[36]	OKUMURA H, SAKUMA E, LEE J, et al. Raman scattering of SiC: application to the identification of heteroepitaxy of SiC polytypes. Journal of Applied Physics, 1987, 61(3):1134.
[37]	DONG S, CHOLLON G, LABRUGERE C, et al. Characterization of nearly stoichiometric SiC ceramic fibres. Journal of Materials Science, 2001, 36(10):2371.
[38]	LIPOWITZ J. Structure and properties of ceramic fibers prepared from organosilicon polymers. Journal of Inorganic and Organometallic Polymers and Materials, 1991, 1(3):277.

烧结条件对制备高结晶近化学计量比SiC纤维的影响

Influence of Sintering Conditions on Preparation of Nearly Stoichiometric SiC Fibers with Highly Crystalline Microstructure

RichHTML

PDF (PC)

可视化

摘要/Abstract

引用本文

使用本文

图/表 24

参考文献 38

相关文章 15

编辑推荐

Metrics

本文评价

[1]	殷杰, 耿佳毅, 王康龙, 陈忠明, 刘学建, 黄政仁. SiC陶瓷的3D打印成形与致密化新进展[J]. 无机材料学报, 2025, 40(3): 245-255.
[2]	樊文楷, 杨潇, 李宏华, 李永, 李江涛. 无压烧结制备(Y_0.2Gd_0.2Er_0.2Yb_0.2Lu_0.2)₂Zr₂O₇高熵陶瓷及其高温抗CMAS腐蚀性能[J]. 无机材料学报, 2025, 40(2): 159-167.
[3]	李伟, 许志明, 苟燕子, 尹森虎, 余艺平, 王松. SiC纤维烧结陶瓷的制备及其性能研究[J]. 无机材料学报, 2025, 40(2): 177-183.
[4]	叶君豪, 周真真, 胡辰, 王雁斌, 荆延秋, 李廷松, 程梓秋, 吴俊林, IVANOV Maxim, HRENIAK Dariusz, 李江. 共沉淀纳米粉体制备Yb:Sc₂O₃透明陶瓷的微结构与光学性能[J]. 无机材料学报, 2025, 40(2): 215-224.
[5]	郝永鑫, 孙军, 杨金凤, 赵晨成, 刘子琦, 李清连, 许京军. 近化学计量比铌酸锂晶体的孪晶缺陷研究[J]. 无机材料学报, 2025, 40(2): 196-204.
[6]	王智祥, 陈莹, 逄清阳, 李鑫, 王根水. 碳酸锰掺杂氧化镁基陶瓷的烧结行为和介电性能[J]. 无机材料学报, 2025, 40(1): 97-103.
[7]	刘磊, 郭瑞华, 王丽, 王艳, 张国芳, 关丽丽. Pt₃Co高指数晶面氧还原过程的密度泛函理论研究[J]. 无机材料学报, 2025, 40(1): 39-46.
[8]	张婧慧, 陆晓彤, 毛海雁, 田亚州, 张山林. 烧结助剂对BaZr_0.1Ce_0.7Y_0.2O_3-_δ电解质烧结行为及电导率的影响[J]. 无机材料学报, 2025, 40(1): 84-90.
[9]	王康龙, 殷杰, 陈晓, 王力, 刘学建, 黄政仁. 颗粒级配对选区激光烧结打印结合常压固相烧结制备碳化硅陶瓷性能的影响[J]. 无机材料学报, 2024, 39(7): 754-760.
[10]	刘焱, 覃显鹏, 甘霖, 周国红, 章天金, 王士维, 陈鹤拓. 亚微米球形Y₂O₃粉体及其透明陶瓷的制备[J]. 无机材料学报, 2024, 39(6): 691-696.
[11]	王伟明, 王为得, 粟毅, 马青松, 姚冬旭, 曾宇平. 以非氧化物为烧结助剂制备高导热氮化硅陶瓷的研究进展[J]. 无机材料学报, 2024, 39(6): 634-646.
[12]	郑斌, 康凯, 张青, 叶昉, 解静, 贾研, 孙国栋, 成来飞. 前驱体转化陶瓷法制备Ti₃SiC₂陶瓷及其热稳定性研究[J]. 无机材料学报, 2024, 39(6): 733-740.
[13]	郑雅雯, 张翠萍, 张瑞杰, 夏乾, 茹红强. 硼酸碳热还原-渗硅反应烧结制备碳化硼陶瓷复合材料[J]. 无机材料学报, 2024, 39(6): 707-714.
[14]	何宗倍, 陈放, 刘佃光, 李统业, 曾强. 模拟核芯FCM燃料的振荡烧结行为研究[J]. 无机材料学报, 2024, 39(5): 501-508.
[15]	李红兰, 张俊苗, 宋二红, 杨兴林. Mo/S共掺杂的石墨烯用于合成氨: 密度泛函理论研究[J]. 无机材料学报, 2024, 39(5): 561-568.