高温长期时效对Hastelloy C-276合金组织和力学性能的影响
|
摘要
对Hastelloy C-276合金在800℃进行了不同时间的时效处理,分析了其微观组织与力学性能的变化及高温拉伸的断裂机制。结果表明:Hastelloy C-276合金在800℃长期时效后的析出相为μ相和少量的M6C相。合金时效处理150 h后,晶界处开始有析出相产生;时效170 h后,晶界处出现连续的析出相并布满了整个晶界;时效310 h后,晶粒内部开始出现析出相,晶界处开始有少量析出相沿晶界向晶粒内部生长;时效510 h后,晶粒内部有大量的析出相出现;时效超过700 h后,晶粒内部的析出相开始聚集长大,几乎布满了整个晶粒。时效处理后的合金高温拉伸的断裂机制为微孔聚集型断裂。
The aging treatment(800℃ for different time) of Hastelloy C-276 alloy was carried out. The change of microstructure and mechanical properties and the high temperature tensile fracture mechanism were analyzed. The results show that the precipitated phases of Hastelloy C-276 alloy after long-term aging treatment at 800 ℃ are μ phase and a small amount of phase M6 C. After aging treatment for 150 h, the grain boundaries in Hastelloy C-276 alloy begin to produce precipitates; after aging treatment for 170 h, the grain boundaries are full of continuity precipitated phases; after aging treatment for 310 h, the interior in grain begins to precipitate, and a small amount of precipitates at the grain boundaries begins to grow along grain boundaries to the interior of the grain; after aging treatment for 510 h, a large number of precipitated phases arise in the grain interior; after aging treatment for above 710 h, the precipitates in the grain interior begin to aggregate and grow, which are almost full of the whole grain. The high temperature tensile fracture mechanism of the alloy is microvoid coalescence fracture.
The aging treatment(800℃ for different time) of Hastelloy C-276 alloy was carried out. The change of microstructure and mechanical properties and the high temperature tensile fracture mechanism were analyzed. The results show that the precipitated phases of Hastelloy C-276 alloy after long-term aging treatment at 800 ℃ are μ phase and a small amount of phase M6 C. After aging treatment for 150 h, the grain boundaries in Hastelloy C-276 alloy begin to produce precipitates; after aging treatment for 170 h, the grain boundaries are full of continuity precipitated phases; after aging treatment for 310 h, the interior in grain begins to precipitate, and a small amount of precipitates at the grain boundaries begins to grow along grain boundaries to the interior of the grain; after aging treatment for 510 h, a large number of precipitated phases arise in the grain interior; after aging treatment for above 710 h, the precipitates in the grain interior begin to aggregate and grow, which are almost full of the whole grain. The high temperature tensile fracture mechanism of the alloy is microvoid coalescence fracture.
引文
[1] Ahmad M, Akhter J I, Akhtar M.Microstructure and hardness studies of the electron beam welded zone of Hastelloy C-276[J].Journal of Alloys and Compounds,2005,390(2):88-93.
[2]陈恭珉.哈氏合金及其应用[J].上海化工,2004,1(10):55-56.
[3]李立松.哈氏合金C276材料在化工压力容器中的应用[J].石油化工设计,2003,20(1):36-38.
[4] Rebak R B, Crook P.Nickel alloys for corrosive environments[J].Advanced Materials and Processes,2000,157(2):37-42.
[5] Turchi P E A, Kaufman L, Liu Z K.Modeling of Ni-Cr-Mo based alloys:part II-kinetics[J].Calphad,2007,31(2):237-248.
[6] Akhter J I, Shaikh M A, Ahmand M.Effect of aging on the hardness and impact properties of Hastelloy C-276[J].Journal of Materials Science Letters,2001,20(4):333-335.
[7]姚焕.国际合力攻关超临界水冷堆技术中材料和传热流动两大难题[J].中国核工业,2007(4):24-25.
[8]赵双群,董建新,谢锡善.Ni-Cr-Co基高温合金704℃和760℃时效组织稳定性[J].中国有色金属学报,2003,13(3):565-569.
[9]宋尽霞,肖程波,李树索,等.950℃长期时效对Ni_3Al基合金IC6的组织及力学性能的影响[J].金属学报,2002,38(3):250-254.
[10] Janowski G M, Harmon B S, Pletkn B J.Thermal-Stability of the Nickel-base superalloy B-1900+HF with tantalum variations[J].Metallurgical Transactions A,1987,18(8):1341-1351.
[11]刘锦溪,张继祥,陆燕玲,等.长期时效对C276合金组织和力学性能的影响[J].金属学报,2013,49(6):763-768.
[12]马永会,赵锴,楼琅洪.定向凝固镍基高温合金中μ相析出对室温拉伸性能的影响[J].电子显微学报,2006,25(S1):116-117.
[13]郑运荣.铸造镍基高温合金中的初生μ相[J].金属学报,1999,35(12):1242-1245.
[14]蔡玉林,郑运荣.μ相的形成及其对力学性能的影响[J].金属学报,1982,18(1):30-41.
[15]孙鸿卿,钟敏霖,刘文今,等.定向凝固镍基高温合金上激光熔覆Inconel738的裂纹敏感性研究[J].航空材料学报,2005,1(2):26-31.
[16]刘文胜,马运柱,黄伯云.钨基合金的断裂失效和强韧化研究现状[J].粉末冶金工业,2007,4(1):26-31.
[17] Raghavan M, Berkowitz B J, Scanlon J C.Electron microscopic analysis of heterogeneous precipitates in Hastelloy C-276[J].Metalllurgical Transactions A,1982,13:979-984.
[18]赵明汉,张旭瑶,焦兰英,等.GH150合金长期时效后塑性下降的原因[J].材料工程,1992(S1):121-122.
[19]潘金生,全健民,田健民.材料科学基础[M].北京:清华大学出版社,1998:200-205.
[2]陈恭珉.哈氏合金及其应用[J].上海化工,2004,1(10):55-56.
[3]李立松.哈氏合金C276材料在化工压力容器中的应用[J].石油化工设计,2003,20(1):36-38.
[4] Rebak R B, Crook P.Nickel alloys for corrosive environments[J].Advanced Materials and Processes,2000,157(2):37-42.
[5] Turchi P E A, Kaufman L, Liu Z K.Modeling of Ni-Cr-Mo based alloys:part II-kinetics[J].Calphad,2007,31(2):237-248.
[6] Akhter J I, Shaikh M A, Ahmand M.Effect of aging on the hardness and impact properties of Hastelloy C-276[J].Journal of Materials Science Letters,2001,20(4):333-335.
[7]姚焕.国际合力攻关超临界水冷堆技术中材料和传热流动两大难题[J].中国核工业,2007(4):24-25.
[8]赵双群,董建新,谢锡善.Ni-Cr-Co基高温合金704℃和760℃时效组织稳定性[J].中国有色金属学报,2003,13(3):565-569.
[9]宋尽霞,肖程波,李树索,等.950℃长期时效对Ni_3Al基合金IC6的组织及力学性能的影响[J].金属学报,2002,38(3):250-254.
[10] Janowski G M, Harmon B S, Pletkn B J.Thermal-Stability of the Nickel-base superalloy B-1900+HF with tantalum variations[J].Metallurgical Transactions A,1987,18(8):1341-1351.
[11]刘锦溪,张继祥,陆燕玲,等.长期时效对C276合金组织和力学性能的影响[J].金属学报,2013,49(6):763-768.
[12]马永会,赵锴,楼琅洪.定向凝固镍基高温合金中μ相析出对室温拉伸性能的影响[J].电子显微学报,2006,25(S1):116-117.
[13]郑运荣.铸造镍基高温合金中的初生μ相[J].金属学报,1999,35(12):1242-1245.
[14]蔡玉林,郑运荣.μ相的形成及其对力学性能的影响[J].金属学报,1982,18(1):30-41.
[15]孙鸿卿,钟敏霖,刘文今,等.定向凝固镍基高温合金上激光熔覆Inconel738的裂纹敏感性研究[J].航空材料学报,2005,1(2):26-31.
[16]刘文胜,马运柱,黄伯云.钨基合金的断裂失效和强韧化研究现状[J].粉末冶金工业,2007,4(1):26-31.
[17] Raghavan M, Berkowitz B J, Scanlon J C.Electron microscopic analysis of heterogeneous precipitates in Hastelloy C-276[J].Metalllurgical Transactions A,1982,13:979-984.
[18]赵明汉,张旭瑶,焦兰英,等.GH150合金长期时效后塑性下降的原因[J].材料工程,1992(S1):121-122.
[19]潘金生,全健民,田健民.材料科学基础[M].北京:清华大学出版社,1998:200-205.