第4期 黄进峰等:喷射沉积A☑31镁合金微观组织与力学性能 .413. 图6喷射沉积AZ31镁合金拉伸断口形貌.(a)热轧态:(b)退火态(60min,200℃) Fig.6 Morphologies of tensile fracture surface of spray formed AZ31 magnesium alloy:(a)as-hot rolled:(b)as annealed(60min.200C) (波尔特诺伊KH,列别杰夫AA,镁合金手册.林裴,译,北 3结论 京:冶金工业出版社,1959) [6]Wang L Y.Huang G S.Fan Y G,et al.Grain refinement of (1)喷射沉积AZ31镁合金柱坯为过饱和单相 wrought AZ31 magnesium alloy.Chin J Nonferrous Met.2003. α(Mg)固溶体组织,主要由细小的等轴晶粒组成,晶 13(6):594 粒平均尺寸约为20m·沉积坯中存在两种主要的 (汪凌云,黄光胜,范永革,等.变形A☑31镁合金的晶粒细 疏松或孔隙:凝固缩松和气体卷入疏松 化.中国有色金属学报,2003,13(6):594) (2)热轧过程动态再结晶使喷射沉积所得到的 [7]Yu F X.Cui JZ,Ranganathan S.et al.Fundamental differences 微细组织得到进一步细化,晶粒尺寸进一步细化至 between spray forming and other semisolid processes.Mater Sci Eng,2001,A304/A306:621 约3~5m·孪生变形积聚的畸变能和非基滑移的 [8]Hehmann F,Sommer F,Predel B.Extension of solid solubility in 启动是导致AZ31镁合金动态再结晶形核长大的根 magnesium by rapid solidification.Mater Sci Eng.1990.A125. 本原因 249 (③)随退火时间的延长和退火温度的升高,孪 [9]Zhang G Q.Mi GG F.Li Z.et al.Spray formed nickel based 晶消失,晶粒长大,硬度下降.当退火温度为175 superalloys using argon as atomization gas.Chin J Nonferrous 200℃,保温时间为60~90min时,退火再结晶基本 Met,1999,9(Sppl1):90 (张国庆,米国发,李周,等.氩气雾化喷射成形的镍基高温合 完成,得到平均晶粒尺寸为5~10m左右的细小均 金.中国有色金属学报,1999,9(增刊1):90 匀等轴晶组织 [10]Cai W D.Smugersky J.Lavernia E J.Low pressure spray (4)喷射成形AZ31镁合金柱坯经热轧和退火 forming of 2024 aluminum alloy.Mater Sci Eng.1998.A241: 60 处理后,表现出良好的力学性能,尤其是屈服强度大 幅度提高,而延伸率下降较多.轧制态试样断口呈 [11]Westlake D G.Twinning in zirconium.Acta Metall.1961.9: 327 现为脆性解理断裂方式,退火态试样断口呈现脆性 [12]Cahn R W.Structure and Properties of Nonferrous Alloys. 和韧性断裂混合机制, Ding D Y,translated.Beijing:Science Press.1999 (卡恩R主编,非铁合金的结构与性能.丁道云,译.北京: 参考文献 科学出版社,1999) [1]Mordike B L.Ebert T.Magnesium:properties-applications po- [13]Zhang K F.Yin D L,Han W B.Microstructure evolution in tential.Mater Sci Eng.2001,A302:37 warm deformation of hot rolled AZ31 Mg alloy.Acta Aeronaut [2]Aghion E.Bronfin B.Magnesium alloys development towards the Astronaut Sin.2005.26(4):5 21st century.Mater Sci Forum.2000.350/351:19 (张凯锋,尹德良,韩文波,热轧A231镁合金温变形中的微观 [3]Mehta DS.Masood S H.Song WQ.Investigation of wear prop- 组织演变.航空学报,2005,26(4):5) erties of magnesium and aluminum alloys for automotive applica- [14]Tan J C.Tan M J.Dynamic continuous recrystallization charac tions.J Mater Process Technol,2004.155/156:1526 teristics in two-stage deformation of Mg-3Al-IZn alloy sheet [4]Aghion E.Bronfin B.Eliezer D.The role of the magnesium in- Mater Sci Eng,2003.A339:124 dustry in protecting the environment.J Mater Process Technol. [15]Ha K F.Basics of Fracture Physics.Beijing:Science Press. 2001,117:381 2000 511 IloPTHn K M.Jlecenes AA.Handbook of Magnesium Alloys. (哈宽富·断裂物理基础.北京:科学出版社,2000) Lin P,translated.Beijing:Metallurgical Industry Press,1959图6 喷射沉积 AZ31镁合金拉伸断口形貌.(a) 热轧态;(b) 退火态 (60min200℃) Fig.6 Morphologies of tensile fracture surface of spray formed AZ31magnesium alloy:(a) as-hot rolled;(b) as-annealed (60min200℃) 3 结论 (1) 喷射沉积 AZ31镁合金柱坯为过饱和单相 α(Mg)固溶体组织主要由细小的等轴晶粒组成晶 粒平均尺寸约为20μm.沉积坯中存在两种主要的 疏松或孔隙:凝固缩松和气体卷入疏松. (2) 热轧过程动态再结晶使喷射沉积所得到的 微细组织得到进一步细化晶粒尺寸进一步细化至 约3~5μm.孪生变形积聚的畸变能和非基滑移的 启动是导致 AZ31镁合金动态再结晶形核长大的根 本原因. (3) 随退火时间的延长和退火温度的升高孪 晶消失晶粒长大硬度下降.当退火温度为175~ 200℃保温时间为60~90min 时退火再结晶基本 完成得到平均晶粒尺寸为5~10μm 左右的细小均 匀等轴晶组织. (4) 喷射成形 AZ31镁合金柱坯经热轧和退火 处理后表现出良好的力学性能尤其是屈服强度大 幅度提高而延伸率下降较多.轧制态试样断口呈 现为脆性解理断裂方式退火态试样断口呈现脆性 和韧性断裂混合机制. 参 考 文 献 [1] Mordike B LEbert T.Magnesium:properties-applications-potential.Mater Sci Eng2001A302:37 [2] Aghion EBronfin B.Magnesium alloys development towards the 21st century.Mater Sci Forum2000350/351:19 [3] Mehta D SMasood S HSong W Q.Investigation of wear properties of magnesium and aluminum alloys for automotive applications.J Mater Process Technol2004155/156:1526 [4] Aghion EBronfin BEliezer D.The role of the magnesium industry in protecting the environment.J Mater Process Technol 2001117:381 [5] ПортниКИЛебедевАА.Handbook of Magnesium Alloys. Lin Ptranslated.Beijing:Metallurgical Industry Press1959 (波尔特诺伊КИ列别杰夫 АА.镁合金手册.林裴译.北 京:冶金工业出版社1959) [6] Wang L YHuang G SFan Y Get al.Grain refinement of wrought AZ31magnesium alloy.Chin J Nonferrous Met2003 13(6):594 (汪凌云黄光胜范永革等.变形 AZ31镁合金的晶粒细 化.中国有色金属学报200313(6):594) [7] Yu F XCui J ZRanganathan Set al.Fundamental differences between spray forming and other semisolid processes.Mater Sci Eng2001A304/A306:621 [8] Hehmann FSommer FPredel B.Extension of solid solubility in magnesium by rapid solidification.Mater Sci Eng1990A125: 249 [9] Zhang G QMi G G FLi Zet al.Spray formed nickel based superalloys using argon as atomization gas.Chin J Nonferrous Met19999(Suppl1):90 (张国庆米国发李周等.氩气雾化喷射成形的镍基高温合 金.中国有色金属学报19999(增刊1):90 [10] Cai W DSmugersky JLavernia E J.Low-pressure spray forming of2024aluminum alloy.Mater Sci Eng1998A241: 60 [11] Westlake D G.Twinning in zirconium.Acta Metall19619: 327 [12] Cahn R W. Structure and Properties of Nonferrous Alloys. Ding D Ytranslated.Beijing:Science Press1999 (卡恩 R 主编非铁合金的结构与性能.丁道云译.北京: 科学出版社1999) [13] Zhang K FYin D LHan W B.Microstructure evolution in warm deformation of hot rolled AZ31Mg alloy.Acta Aeronaut Astronaut Sin200526(4):5 (张凯锋尹德良韩文波.热轧 AZ31镁合金温变形中的微观 组织演变.航空学报200526(4):5) [14] Tan J CTan M J.Dynamic continuous recrystallization characteristics in two-stage deformation of Mg—3Al—1Zn alloy sheet. Mater Sci Eng2003A339:124 [15] Ha K F.Basics of Fracture Physics.Beijing:Science Press 2000 (哈宽富.断裂物理基础.北京:科学出版社2000) 第4期 黄进峰等: 喷射沉积 AZ31镁合金微观组织与力学性能 ·413·