第四代粉末高温合金热变形后的“项链”组织
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摘要
利用扫描电镜、透射电镜及电子背散射衍射技术研究新型第四代粉末高温合金等温锻造后的"项链"组织,对其形成机理和消除方法进行了探讨。结果表明,实验合金经过多火次等温锻造后,锻坯大部分区域为再结晶后的等轴细晶组织;然而与模具接触的上下端面得到再结晶不完全的"项链"组织,在非等轴变形晶粒周围分布着大量细小的再结晶晶粒,变形晶粒内含有较高密度的小角度晶界,缠结了大量位错。对存在"项链"组织的试样进行不同温度(1080～1180℃)的退火处理,随着温度的升高,再结晶体积分数和再结晶晶粒尺寸均不断增大。合金锻坯经过1150℃再结晶退火后,可基本消除"项链"组织,获得组织较均匀的细晶盘坯,满足双组织热处理的要求。
The "necklace" structure of an advanced 4 th generation powder metallurgy(PM)superalloy after isothermal forging was investigated by means of scanning electron microscope, transmission electron microscope and electron back scattering diffraction technique. The formation mechanism and elimination method of the "necklace" structure were studied. The results show that after multiple isothermal forging, most region of the forging are fully recrystallized, and equiaxed fine-grained microstructures are obtained. Nevertheless, a typically incomplete recrystallization microstructure, namely the "necklace" structure, is formed nearing the upper and lower end faces of the forging. A great amount of fine recrystallized grains are distributed around the non-equiaxed deformed grains. The deformed grains contain a high density of low angle grain boundaries, so it means plenty of entangled dislocations exist. The samples containing "necklace" structure are annealed over the temperature range from 1080℃ to 1180℃. With the increasing temperature, both the recrystallization volume fraction and recrystallization grain size are increased gradually. The "necklace" structure of the alloy forging is basically eliminated after recrystallization annealing at 1150℃. Therefore, the uniform fine-grained disk can be obtained, which meet the requirements of dual microstructure heat treatment.
The "necklace" structure of an advanced 4 th generation powder metallurgy(PM)superalloy after isothermal forging was investigated by means of scanning electron microscope, transmission electron microscope and electron back scattering diffraction technique. The formation mechanism and elimination method of the "necklace" structure were studied. The results show that after multiple isothermal forging, most region of the forging are fully recrystallized, and equiaxed fine-grained microstructures are obtained. Nevertheless, a typically incomplete recrystallization microstructure, namely the "necklace" structure, is formed nearing the upper and lower end faces of the forging. A great amount of fine recrystallized grains are distributed around the non-equiaxed deformed grains. The deformed grains contain a high density of low angle grain boundaries, so it means plenty of entangled dislocations exist. The samples containing "necklace" structure are annealed over the temperature range from 1080℃ to 1180℃. With the increasing temperature, both the recrystallization volume fraction and recrystallization grain size are increased gradually. The "necklace" structure of the alloy forging is basically eliminated after recrystallization annealing at 1150℃. Therefore, the uniform fine-grained disk can be obtained, which meet the requirements of dual microstructure heat treatment.
引文
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[19] HE G A,LIU F,HUANG L,et al.Microstructure evolutions and nucleation mechanisms of dynamic recrystallization[J].Materials Science and Engineering:A,2016,677:496-504.
[20] KOZAR R W,SUZUKI A,MILLIGAN W W,et al.Strengthening mechanisms in polycrystalline multimodal nickel-base superalloys[J].Metallurgical and Materials Transactions A,2009,40(7):1588-1603.
[21] 赵光普,黄烁,张北江,等.新一代镍基变形高温合金GH4065A的组织控制与力学性能[J].钢铁研究学报,2015,27(2):37-44. ZHAO G P,HUANG S,ZHANG B J,et al.Microstructure control and mechanical properties of the newest nickel-based wrought superalloy GH4065A[J].Journal of Iron and Steel Research,2015,27(2):37-44.
[22] ZHANG B J,ZHAO G P,ZHANG W Y,et al.Deformation mechanisms and microstructural evolution of γ+γ′ duplex aggregates generated during thermo mechanical processing of nickel-base superalloys[C]//Superalloys 2016.Warrendale:TMS,2016:487-496.
[2] 高峻,罗皎,李淼泉.航空发动机双性能盘制造技术与机理的研究进展[J].航空材料学报,2012,32(6):37-43. GAO J,LUO J,LI M Q.Advance in manufacture technology and mechanism of aero-engine dual property disk[J].Journal of Aeronautical Materials,2012,32(6):37-43.
[3] GAYDA J,GABB T P,KANTZOS P T.The effect of dual microstructure heat treatment on an advanced nickel-base disk alloy[C]//Superalloys 2004.Warrendale:TMS,2004:323-329.
[4] 陶宇,张国星,刘建涛.粉末涡轮盘温度梯度热处理工装设计研究[J].钢铁研究学报,2011,23(增刊):486-489. TAO Y,ZHANG G X,LIU J T.Study on design of the device for thermal gradient heat-treatment process of PM superalloy disks[J].Journal of Iron and Steel Research,2011,23(Suppl):486-489.
[5] 陶宇,贾建,刘建涛,等.超细晶镍基粉末高温合金的制备方法:102392147B[P].2012-11-14. TAO Y,JIA J,LIU J T,et al.Preparation method of ultra-fine grain nickel based superalloy:102392147B[P].2012-11-14.
[6] 刘洋,陶宇,贾建.FGH98粉末冶金高温合金热变形过程中组织变化[J].粉末冶金工业,2011,21(2):14-18. LIU Y,TAO Y,JIA J.The microstructure evolution of FGH98 P/M superalloy after hot deformation[J].Powder Metallurgy Industry,2011,21(2):14-18.
[7] WU C J,TAO Y,JIA J.Microstructure and properties of an advanced nickel-base PM superalloy[J].Journal of Iron and Steel Research International,2014,21(12):1152-1157.
[8] REYNOLDS P L.Superalloy compositions,articles and methods of manufacture:US 8147749B2[P].2012-04-03.
[9] POWELL A,BAIN K,WESSMAN A,et al.Advanced supersolovus nickel powder disk alloy DOE:chemistry,properties,phase formations and thermal stability[C]//Superalloys 2016.Warrendale:TMS,2016:189-197.
[10] 宁永权,李辉,姚泽坤,等.FGH96高温合金的再结晶组织特征[J].稀有金属材料与工程,2016,45(5):1225-1229. NING Y Q,LI H,YAO Z K,et al.Recrystallization char-acterization of FGH96 superalloy[J].Rare Metal Materials and Engineering,2016,45(5):1225-1229.
[11] 宁永权,姚泽坤,岳太文,等.FGH4096合金“项链”组织研究[J].稀有金属材料与工程,2009,38(10):1783-1786. NING Y Q,YAO Z K,YUE T W,et al.Link microstructure of FGH4096 alloy[J].Rare Metal Materials and Engineering,2009,38(10):1783-1786.
[12] 谢兴华,姚泽坤,宁永权,等.FGH4096合金的动态再结晶与晶粒细化研究[J].航空材料学报,2011,31(1):20-24. XIE X H,YAO Z K,NING Y Q,et al.Dynamic recrystallization and grain refining of superalloy FGH4096[J].Journal of Aeronautical Materials,2011,31(1):20-24.
[13] PONG D,GOTTSTEIN G.Necklace formation during dynamic recrystallization:mechanisms and impact on flow behavior[J].Acta Metallurgica,1998,46(1):69-80.
[14] BHOWAL P R,BHATHENA N M.Development of a necklace microstructure during isothermal deformation and its properties relative to uniform microstructures[J].Metallurgical Transac-tions A,22(9):1999-2008.
[15] NES E,RYUM N,HUNDERI O.On the zener drag[J].Acta Metallurgica,1985,33(1):11-22.
[16] LI F L,FU R,YIN F J.Impact of γ′(Ni3(Al,Ti)) phase on dynamic recrystallization of a Ni-based disk superalloy during isothermal compression[J].Journal of Alloys and Compounds,2017,693:1076-1082.
[17] HUMPHREYS F J,HATHERLY M.Recrystallization and related anneling phenomena[M].Oxford:Elsevier Ltd,2004:293-306.
[18] LINDSLEY B,PIERRON X.Sub-solves recrystallization mechanisms in UDIMET alloy 720Li[C]//Superalloys 2000.Warrendale:TMS,2000:59-68.
[19] HE G A,LIU F,HUANG L,et al.Microstructure evolutions and nucleation mechanisms of dynamic recrystallization[J].Materials Science and Engineering:A,2016,677:496-504.
[20] KOZAR R W,SUZUKI A,MILLIGAN W W,et al.Strengthening mechanisms in polycrystalline multimodal nickel-base superalloys[J].Metallurgical and Materials Transactions A,2009,40(7):1588-1603.
[21] 赵光普,黄烁,张北江,等.新一代镍基变形高温合金GH4065A的组织控制与力学性能[J].钢铁研究学报,2015,27(2):37-44. ZHAO G P,HUANG S,ZHANG B J,et al.Microstructure control and mechanical properties of the newest nickel-based wrought superalloy GH4065A[J].Journal of Iron and Steel Research,2015,27(2):37-44.
[22] ZHANG B J,ZHAO G P,ZHANG W Y,et al.Deformation mechanisms and microstructural evolution of γ+γ′ duplex aggregates generated during thermo mechanical processing of nickel-base superalloys[C]//Superalloys 2016.Warrendale:TMS,2016:487-496.
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