T2/QBe_2爆炸复合界面结合层内形变特征的研究
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摘要
本文选用工业纯铜(T2)和铍青铜(QBe2)，采用平板爆炸复合方法制备T2／QBe2复合板。利用金相显微镜、电子背散射衍射技术和透射电镜等实验手段对爆炸复合后，波形复合界面结合层内T2和QBe2金属的塑性变形特征进行了研究。
结果表明：T2和QBe2金属经爆炸复合后，其界面结合层在宏观上表现为连续不断和周而复始的波形，波形复合界面两侧金属的组织不同于各自基体金属的组织；并且在其T2／QBe2波形界面上存在由部分金属的熔化而形成的熔化块／层，同时波形界面形成的过程就是复合界面附近金属塑性变形的过程。在爆炸载荷条件下，QBe2侧产生了大量的平行带状组织，该组织为绝热剪切带(adiabatic shear bands,简写ASBs)和形变孪晶，但在T2侧则没有出现ASBs；在ASBs内分布有十分细小的等轴晶，这些等轴晶晶粒取向差较大，带与带之间基体中的晶粒取向基本相同，而上述两者则存在较大的取向差；ASBs是在爆炸载荷下，QBe2一种特殊的塑性变形方式。爆炸加载后，T2和QBe2中都产生了形变孪晶，形变孪晶是T2／QBe2体系在爆炸载荷作用下非常有利的变形形式。进行再结晶退火后，QBe2内的ASBs消失，并且产生了退火孪晶；T2内晶粒有所长大，而且也出现了退火孪晶。
Pure copper (T2) and beryllium bronze (QBe2) were selected as the material to produce T2/QBe2 composite by flat plate explosive cladding. Modern examination techniques, such as OM, EBSD and TEM were employed to investigate the plastic deformation features of T2 and QBe2 in cladding layer near the composite interface.
The result indicated that the cladding layer at composite interface apperaed like continuous and cyclic waves on a macro scale. Microstructures on both sides of interface were different from those of respective matrix. There were some melted blocks or layer at the waved interface. And plastic deformation occurred concurrently along the formed interface. After explosive loading lots of parallel bands,which were identified as ASBs and deformation twins, apperaed on the side of QBe2. However, there were no ASBs on the side of T2. A number of very fine equix grains were observed in ASBs, and orientation of grains in the ASBs was different, orientatin of grains between adiabatic shear bands was essentially consistent, while there was a large difference in orientation between grains in ASBs and those in matrix. Adiabatic shearing bands would be one of special ways of plastic deformation for QBe2 under explosive loading. Deformation twins are found in the both T2 and QBe2 after explosive loading, which suggested th
at twinning was a favorable deformation mechanism under such condition. After recrystallization annealing, the ASBs in the QBe2 disappeared, and annealing twins occurred. Grains in T2 coarsened and annealing twins appeared.
结果表明：T2和QBe2金属经爆炸复合后，其界面结合层在宏观上表现为连续不断和周而复始的波形，波形复合界面两侧金属的组织不同于各自基体金属的组织；并且在其T2／QBe2波形界面上存在由部分金属的熔化而形成的熔化块／层，同时波形界面形成的过程就是复合界面附近金属塑性变形的过程。在爆炸载荷条件下，QBe2侧产生了大量的平行带状组织，该组织为绝热剪切带(adiabatic shear bands,简写ASBs)和形变孪晶，但在T2侧则没有出现ASBs；在ASBs内分布有十分细小的等轴晶，这些等轴晶晶粒取向差较大，带与带之间基体中的晶粒取向基本相同，而上述两者则存在较大的取向差；ASBs是在爆炸载荷下，QBe2一种特殊的塑性变形方式。爆炸加载后，T2和QBe2中都产生了形变孪晶，形变孪晶是T2／QBe2体系在爆炸载荷作用下非常有利的变形形式。进行再结晶退火后，QBe2内的ASBs消失，并且产生了退火孪晶；T2内晶粒有所长大，而且也出现了退火孪晶。
Pure copper (T2) and beryllium bronze (QBe2) were selected as the material to produce T2/QBe2 composite by flat plate explosive cladding. Modern examination techniques, such as OM, EBSD and TEM were employed to investigate the plastic deformation features of T2 and QBe2 in cladding layer near the composite interface.
The result indicated that the cladding layer at composite interface apperaed like continuous and cyclic waves on a macro scale. Microstructures on both sides of interface were different from those of respective matrix. There were some melted blocks or layer at the waved interface. And plastic deformation occurred concurrently along the formed interface. After explosive loading lots of parallel bands,which were identified as ASBs and deformation twins, apperaed on the side of QBe2. However, there were no ASBs on the side of T2. A number of very fine equix grains were observed in ASBs, and orientation of grains in the ASBs was different, orientatin of grains between adiabatic shear bands was essentially consistent, while there was a large difference in orientation between grains in ASBs and those in matrix. Adiabatic shearing bands would be one of special ways of plastic deformation for QBe2 under explosive loading. Deformation twins are found in the both T2 and QBe2 after explosive loading, which suggested th
at twinning was a favorable deformation mechanism under such condition. After recrystallization annealing, the ASBs in the QBe2 disappeared, and annealing twins occurred. Grains in T2 coarsened and annealing twins appeared.
引文
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[3] Meunier Y, Beatty J H.Shock waves and high strain rate phenomena in metals[M]. New York: Marcel Dekker Inc, 1992: 637-674.
[4] Meyers M.A, Subhash G, Kad B K. Evolution of microstructure and shear band formation in A-hcp titanium[M]. Mechanics of Materials, 1994, 17(2-3): 175-193.
[5] 杨扬，张新明，李正华等．α-钛／低碳钢爆炸复合界面结合层内的绝热剪切现象[J]．中国有色金属学报，1995，5(2)：93-97．
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[7] 魏志刚，李永池，李剑荣等．冲击载荷作用下钨合金材料绝热剪切带形成机理[J]． 金属学报，2000，36(12)：1263-1268．
[8] Kim D S, Sia N N, Isaacs J B, et al. Adiabatic shear band in WHA in high strain rate compression[J]. Mechanics of Materials. 1998, 28: 227-236.
[9] Yang Y, Zhang X M, Li Z H, et al. Effects of stacking fault energy on residual substructure of explosive shock loaded metals[J]. Trans Nonferrous Metals Met Soc, 1994, 4(4): 90-93.
[10] Yang Y, Zhang X M, Li Z H, et al. Adiabatic Shear Band on the Titanium Side in the Ti/Mild Steel Explosive Cladding Interface[J]. Acta Materialia, 1996, 44(2): 561-565.
[11] Sia N N, Wei G G, Vitali F N, et al. Dynamic response of conventional and hot isostatically pressed Ti-6Al-4V alloys: experiments and modeling[J]. Mechanics of Materials, 2001, 33: 425-439.
[12] Magness L.S.et al. Proc First Int Conf on Tungsten and Tungsten Alloys[R]. Arlington: Metal Powder Industries Federation, 1992: 15.
[13] BAI. Y L.Adiabatic shear banding[J]. Res. Mechanics, 1990, 31: 133-203.
[14] 徐天平，王礼立，卢维娴．高应变速率下钛合金Ti-6Al-4V的热粘塑性特性和绝热剪切变形[J]．爆炸与冲击，1987，7(1)：1-7．
[15] 包合胜，王礼立，卢维娴．钛合金在低温下的高速变形特性和绝热剪切[J]．爆炸与冲击，1989，9(2)：109-119．
[16] Pérez-Prado M T, Hines J A, Vecehio K S. Mierostructural evolution in adiabatic shear bands in Ta and Ta-W alloys[J]. Acta Materialia, 2001, 49: 2905-2910.
[17] Andrade U, Meyer M A, Dynamic recrystallization in high-strain, high-strain-rate plastic deformation of copper[J]. Acta Metallurgica et Materialia, 1994, 42(8): 3183-3195.
[18] Chen R W.Microstructural characterization of shear band formation in Al_2Li Alloys[M]. University of California, San Diego, La Jolla, CA. 1993.
[19] Lee S, Cho K M. Mierostruetural study of adiabatic shear band formed by ballistic impact in an HY2100[J]. Metall Trans A, 1993, 24(A): 2217-2224.
[20] 杨卓越，赵家萍．金属材料中绝热剪切带微观结构综述[J]．华北工学院学报，1995，16(4)：327-333．
[21] 杨扬，程信林，绝热剪切的研究现状及发展趋势[J]．中国有色金属学报，2002，12(3)：401-408．
[22] Hines J A.Vecchio K S.Recrystallization kinetics within adiabatic shear bands[J]. Acta Mater, 1997, 45(2): 635-649.
[23] Nemat N S, Isaacs J B, Liu Mingqi.Microstructure of high-strain, high-strain-rate deformed tantalum[J]. Acta Materialia, 1998, 46(4): 1307-1325.
[24] Nseterenko V F, Meyers M A. Shear localization and recrystallization in high-strain, high-strain-rate deformation of tantalum[J]. Materials Science and Engineering A, 1997, 229(A): 23-41.
[25] Meyers M A, Hen Y J.High-strain high-strain-rate behavior of tantalum[J]. Metallurgy and Materials Science Metall, 1995, 26A(10): 2493-2501.
[26] Derep J L.Microstructure transformation induced by adiabatic sheafing in armour steel[J]. Acta Materialia. 1987, 35: 1245-1249.
[27] 唐仁正．物理冶金基础[M]．北京：冶金工业出版社，1997．
[28] Honeycombe R W K．金属塑性变形[M]．重庆：重庆大学出版社，1989．
[29] Sanchez J C, Murr L E, Staudhammer K P.Effect of grain size and pressure on twinning and microbanding in oblique shock loading of copper rods[J]. Acta Materialia, 1997, 45(8): 3223-3235.
[30] J．F．Nye，孟中岩译．晶体的物理性质[M]．西安：西安交通大学社，1994．
[31] 郑哲敏，杨振声等．爆炸加工[M]．北京：国防工业出版社，1981．
[32] 埃兹拉A A，张铁生译．金属爆炸原理与实践[M]．北京：北京机械工业出版社，1981．
[33] 布拉齐恩斯基 T．Z，李富勤．爆炸焊接、成形与压制[M]．北京：北京机械工业出版社，1988．
[34] Carl L R.Metal Progress.1944, 46(1): 102-103.
[35] 邵丙璜，张凯．爆炸焊接原理及其工程应用[M]．大连：大连工学院出版社，1987．
[36] 克劳思兰B．爆炸焊接法[M]．北京：中国建筑工业出版社，1979．
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