航空材料学报
航空材料學報
항공재료학보
JOURNAL OF AERONAUTICAL MATERIALS
2010年
1期
78-84
,共7页
平纹编织C/SiC%陶瓷基复合材料%拉伸行为%损伤机理
平紋編織C/SiC%陶瓷基複閤材料%拉伸行為%損傷機理
평문편직C/SiC%도자기복합재료%랍신행위%손상궤리
plain-woven C/SiC%ceramic matrix composite%tensile behavior%damage mechanism
通过单向拉伸试验,对比研究平纹编织C/SiC陶瓷基复合材料在室温和高温(1300℃,包括惰性气氛和湿氧气氛)环境下的宏观力学特性,并采用光学显微镜和扫描电镜对试件断口进行显微观察,分析其损伤模式和破坏机理.结果表明: C/SiC复合材料的室温和高温拉伸行为通常表现为非线性特征,在低应力时就开始出现损伤;纤维与基体之间界面滑行阻力的降低使C/SiC复合材料在高温惰性气氛环境下的拉伸强度和破坏应变均比室温下的高;碳纤维的氧化严重影响材料的承载能力导致高温湿氧环境下的拉伸强度和破坏应变均比室温下的低; C/SiC复合材料室温和高温下的拉伸均呈现韧性断裂,断口较为相似,只是纤维拔出长度和断口的平齐程度有所不同,其中高温惰性气氛环境下纤维拔出最长,高温湿氧环境下试件断口有明显的被氧化痕迹;0°纤维束表面基体开裂、明显的层间分层以及0°纤维和纤维束的拔出和断裂同时携带90°纤维束拔出是C/SiC复合材料在室温和高温下的拉伸破坏机理.
通過單嚮拉伸試驗,對比研究平紋編織C/SiC陶瓷基複閤材料在室溫和高溫(1300℃,包括惰性氣氛和濕氧氣氛)環境下的宏觀力學特性,併採用光學顯微鏡和掃描電鏡對試件斷口進行顯微觀察,分析其損傷模式和破壞機理.結果錶明: C/SiC複閤材料的室溫和高溫拉伸行為通常錶現為非線性特徵,在低應力時就開始齣現損傷;纖維與基體之間界麵滑行阻力的降低使C/SiC複閤材料在高溫惰性氣氛環境下的拉伸彊度和破壞應變均比室溫下的高;碳纖維的氧化嚴重影響材料的承載能力導緻高溫濕氧環境下的拉伸彊度和破壞應變均比室溫下的低; C/SiC複閤材料室溫和高溫下的拉伸均呈現韌性斷裂,斷口較為相似,隻是纖維拔齣長度和斷口的平齊程度有所不同,其中高溫惰性氣氛環境下纖維拔齣最長,高溫濕氧環境下試件斷口有明顯的被氧化痕跡;0°纖維束錶麵基體開裂、明顯的層間分層以及0°纖維和纖維束的拔齣和斷裂同時攜帶90°纖維束拔齣是C/SiC複閤材料在室溫和高溫下的拉伸破壞機理.
통과단향랍신시험,대비연구평문편직C/SiC도자기복합재료재실온화고온(1300℃,포괄타성기분화습양기분)배경하적굉관역학특성,병채용광학현미경화소묘전경대시건단구진행현미관찰,분석기손상모식화파배궤리.결과표명: C/SiC복합재료적실온화고온랍신행위통상표현위비선성특정,재저응력시취개시출현손상;섬유여기체지간계면활행조력적강저사C/SiC복합재료재고온타성기분배경하적랍신강도화파배응변균비실온하적고;탄섬유적양화엄중영향재료적승재능력도치고온습양배경하적랍신강도화파배응변균비실온하적저; C/SiC복합재료실온화고온하적랍신균정현인성단렬,단구교위상사,지시섬유발출장도화단구적평제정도유소불동,기중고온타성기분배경하섬유발출최장,고온습양배경하시건단구유명현적피양화흔적;0°섬유속표면기체개렬、명현적층간분층이급0°섬유화섬유속적발출화단렬동시휴대90°섬유속발출시C/SiC복합재료재실온화고온하적랍신파배궤리.
Monotonic tensile experiments at room temperature and 1300℃ were performed to investigate the macro-mechanical behavior of plain-woven C/SiC ceramic matrix composites(CMCs) produced with CVI technique.Two environments including inert atmosphere and wet oxygen atmosphere were simulated at 1300℃.The microstructure of specimens were observed by optical microscope and scanning electron microscope to analyse its damage mechanism.The results indicate that, the responses of C/SiC composite under tensile loading at both room temperature and 1300℃ are nonlinear to rupture and damage appears at very low stress level. The tensile strength and failure strain at room temperature are lower than at 1300℃ in inert atmosphere but higher than at 1300℃ in wet oxygen atmosphere, respectively.The main reason of the former is the decrease of interfacial sliding resistance at 1300℃ in inert atmosphere.The main reason of the latter is fiber oxidation at 1300℃ in wet oxygen atmosphere. The tensile specimens all break in a ductile manner. Fractography analysis shows that the fracture surfaces are almost the same in the three environments except the obviously oxidative trace in wet oxygen atmosphere .The specimens in inert atmosphere have the longest pull-out length of fiber. Matrix cracks around the 0° fiber bundles, interlaminar cracks , fracture and pullout of 0° fiber and 0° bundles along with the pullout of 90°bundles are the main damage mechanisms.