铸造成型原位自生TiB_2/Al-Mg-Li复合材料热处理过程中的微观组织与力学性能演变
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摘要
Al-Li合金具有低密度、高比强、高比刚的特点,在航空航天工业领域有着广阔的前景。Al-Mg-Li系合金中的Mg密度低,且可通过热处理进一步提高强度和硬度。为了进一步提高该材料的强度,制备了原位TiB_2/Al-Mg-Li复合材料。相比于Al-Cu-Li体系,针对原位TiB_2/Al-Mg-Li复合材料热处理的系统研究目前仍比较缺乏。通过原位自生混合盐法,制备了原位自生TiB_2/Al-4. 5Mg-2. 4Li复合材料。差示扫描量热(DSC)实验表明,复合材料中第二相开始熔化的温度为510℃;扫描电子显微镜(SEM)观察表明,原位TiB_2颗粒倾向于在晶界处形成团簇,热处理过程中基本不发生变化; SEM和电子能谱仪(EDS)扫描结果表明,该复合材料在500℃下固溶16 h后,合金元素Mg扩散充分,元素Mg偏聚基本消除; 185℃人工时效过程中,材料硬度有显著提升,时效24 h后达到峰时效状态,最大硬度为146. 2 HV10/15。
Al-Li alloys have low density,high specific strength and high specific modulus,thus are considered potent in aviation industries. Al-Mg-Li alloys contain magnesium which has a very low density,and they can be further strengthened by proper heat treatment. To further strengthen the material,in-situ TiB_2/Al-Mg-Li composite is fabricated. In comparison with Al-Cu-Li materials,systematic studies on TiB_2/Al-Mg-Li composite's heat treatment are still inadequate. In this research,an in-situ TiB_2/Al-4. 5Mg-2. 4Li composite is fabricated. Differential scanning calorimetry( DSC) curve indicates the second phases start to melt at 510 ℃. SEM observation indicates in-situ TiB_2 particles tend to distribute near the grain boundary of the matrix. TiB_2 clusters are stable during heat treatment. SEM and EDS experiment confirm that after undergone solution treatment at 500 ℃ for 16 h,segregation of Mg in the composite no longer exists. Artificial aging significantly increases the composite's hardness. After aged at 185 ℃ for 24 h,the composite reaches peak-age state,and the maximal hardness is146. 2 HV10/15.
Al-Li alloys have low density,high specific strength and high specific modulus,thus are considered potent in aviation industries. Al-Mg-Li alloys contain magnesium which has a very low density,and they can be further strengthened by proper heat treatment. To further strengthen the material,in-situ TiB_2/Al-Mg-Li composite is fabricated. In comparison with Al-Cu-Li materials,systematic studies on TiB_2/Al-Mg-Li composite's heat treatment are still inadequate. In this research,an in-situ TiB_2/Al-4. 5Mg-2. 4Li composite is fabricated. Differential scanning calorimetry( DSC) curve indicates the second phases start to melt at 510 ℃. SEM observation indicates in-situ TiB_2 particles tend to distribute near the grain boundary of the matrix. TiB_2 clusters are stable during heat treatment. SEM and EDS experiment confirm that after undergone solution treatment at 500 ℃ for 16 h,segregation of Mg in the composite no longer exists. Artificial aging significantly increases the composite's hardness. After aged at 185 ℃ for 24 h,the composite reaches peak-age state,and the maximal hardness is146. 2 HV10/15.
引文
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[4]Rioja R J,Liu J.Metallurgical and Materials Transactions A[J],2012,43(9):3325-3337.
[5]Cui Jianzhong(崔建忠),Hu Jun(胡骏),Ma Longxiang(马龙翔).Journal of Astronautics(宇航学报)[J],1991,12(2):45-50.
[6]Fridlyander I N,Sandler V S.Material Science and Heat Treatment[J],1988,30(8):594-602.
[7]Yin Mei(尹梅),Qiang Jun(强俊).Aviation Maintenance&Engineering(航空维修与工程)[J],1996(12):11-13.
[8]Zhong Liping(钟利萍).Dissertation for Master(硕士论文)[D].Changsha:Central South University of Forestry and Technology,2003:46-58.
[9]Murken J,H9hner R,Skrotzki B.Materials Science and Engineering:A[J],2003,363(1-2):159-170.
[10]Abramov A A,Danilov A N,Zolotareva G A,et al.Metal Science and Heat Treatment[J],1990,32(8):595-597.
[11]Hogg S C,Palmer I G,Thomas L G,et al.Acta Materialia[J],2007,55(6):1885-1894.
[12]Murken J,H9hner R,Skrotzki B.Materials Science and Engineering:A[J],2003,363(1-2):159-170.
[13]Khokhlatova L B,Kolobnev N I,Fridlyander I N.Materials Science Forum[J],2006,519-521:371-376.
[14]Zhou Aijun(周爱军),Lu Zheng(陆政).Materials Science and Technology(材料科学与工艺)[J],1998(4):68-71.
[15]Le Yongkang(乐永康),Zhang Yijie(张亦杰),Chen Dong(陈东),et al.Rare Metal Materials and Engineering(稀有金属材料与工程)[J],2006,35(10):1635-1638.
[16]Xue Jing(薛菁),Wang Jun(王俊),Sun Baode(孙宝德).Hot Working Technology(热加工工艺)[J],2009,38(24):43-47.
[17]Wang M,Chen D,Chen Z,et al.Materials Science and Engineering:A[J],2014,590:246-254.
[18]Shen Y,Li X,Hong T,et al.Materials Science and Engineering:A[J],2016,655:265-268.
[19]Shen Y,Hong T,Geng J,et al.Materials Characterization[J],2017,124:25-30.
[20]Wu L,Li X,Han G,et al.Materials Characterization[J],2017,132:215-222.
[21]Li H,Tang Y,Zeng Z,et al.Materials Science and Engineering:A[J],2008,498(1-2):314-320.
[22]Dong S L,Mao J F,Yang D Z,et al.Materials Science and Engineering:A[J],2002,327(2):213-223.
[23]Dutkiewicz J,Simmich O,Scholz R,et al.Materials Science and Engineering:A[J],1997,234:253-257.
[24]Noble B,Thompson G E.Metal Science Journal[J],1972,6(1):167-174.
[25]Araullo-Peters V,Gault B,Geuser F D,et al.Acta Materialia[J],2014,66:199-208.
[26]Terrones L A H,Monteiro S N.Materials Characterization[J],2007,58(2):156-161.
[27]Bartels C,Raabe D,Gottstein G,et al.Materials Science and Engineering:A[J],1997,237(1):12-23.
[28]Khodabakhshi F,Simchi A,Kokabi A H,et al.Materials Characterization[J],2015,108:102-114.
[29]Zhang Lei(张蕾),Zhu Mingliang(祝铭亮),Huang Zheng(黄正).Materials Science and Technology(材料科学与工艺)[J],2005,13(1):86-89.
[30]Furukawa M,Berbon P B,Langdon T G,et al.Metallurgical and Materials Transactions A[J],1998,29(1):169-177.