高Nb-TiAl合金高温变形及组织性能研究
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摘要
高Nb-TiAl合金是发展高温高强TiAl合金的典范，具有高比强度和比模量，良好的高温抗氧化性以及蠕变抗力等优点，使其在航空航天工业以及汽车工业中极具应用前景。高Nb-TiAl合金铸锭制备困难，变形抗力大，限制了其加工和应用。β相凝固被证明可以有效的细化合金的铸造组织，减小元素偏析。本文通过ISM技术、 VAR技术分别制备出了成分为Ti-45Al-9Nb-Y和Ti-44Al-8Nb-0.2W-0.2B-Y的β相凝固高Nb-TiAl合金，并对铸锭制备、热加工技术、热处理工艺，以及组织和性能进行了系统的研究。
采用ISM技术，VAR三次重熔技术分别成功制备了Ti-45Al-9Nb-Y合金以及Ti-44Al-8Nb-0.2W-0.2B-Y合金。Ti-45Al-9Nb-Y合金是典型的近层片组织，相邻片层晶团具有相同的片层取向。γ相遵循(110) β//(111) γ位向关系从晶界上残余的β相内不连续析出，形成混合组织。ISM熔炼可以有效的减少元素偏析，提高组织均匀性。热等静压后大尺寸Ti-44Al-8Nb-0.2W-0.2B-Y合金铸锭元素分布基本均匀。添加的B元素形成的TiB作为异质形核剂提高α相的形核率，导致大量非Burgers位向关系的α相出现，细化了片层组织。铸锭顶部具有最好的性能，室温强度约为680MPa。
对Ti-45Al-9Nb-Y合金进行了高温压缩试验以及包套锻造。高温热压缩过程中，θ=0°的中等强度取向片层晶团发生θ=90°的片层弯曲，并在晶界和片层弯曲处发生动态再结晶。0°＜θ＜90°的软取向片层晶团向θ=90°的取向整体转动同时发生大量的动态再结晶。θ=90°的硬取向片层拉长，晶界上发生动态再结晶。确定最佳变形工艺为：1250℃/0.05s~(-1)。锻态组织是双态组织，残余片层晶团内α_2相板条粗化，并形成垂直于板条取向的花呢状花纹。在1330℃/30min/FC的热处理中,锻态组织中等轴γ相内获得魏氏组织(Widmannst tten)，魏氏组织的出现有利于片层的形成。对锻造组织进行了双态以及全层片组织热处理。全层片组织强度最高，锻态组织延伸率最高。
在1275℃对Ti-44Al-8Nb-0.2W-0.2B-Y合金进行包套锻造，制备出了变形量分别为50%和70%的锻饼，并对70%变形量的锻饼进行了炉冷和空冷处理。变形量越大，室温强度和塑性越高，70%变形量合金的室温强度达到930MPa。空冷组织残余应力大，加工硬化明显，锻饼发生开裂。在70%变形量合金900℃以上高温拉伸组织中，形成白亮的ω相，并且温度越高，应变速率越低，ω相越多。拉伸过程中，ω相的形成可以通过α_2→ω+γ固态相变形成。此外，对锻态Ti-44Al-8Nb-0.2W-0.2B-Y合金在1310℃/20min+1240℃/1h进行了双步热处理，并获得了球状γ等轴晶粒与细小片层的双态组织。1340℃/10min可以获得全层片组织。对双态组织和全片层组织进行了力学性能测试。
详细分析了α板条和γ板条在热加工及冷却过程中的组织演化机制。变形过程中，残余片层内有序γ相首先以亚晶界的转动发生动态再结晶γ_D，而高层错能的无序α相板条仅发生塑性弯曲形成亚结构。γ D再结晶晶粒通过晶界的膨胀在冷却过程中向α_2相板条的生长。随着变形量的增加，α相发生动态再结晶，γ_D对α_2相的吞食作用增加。 γ_D对α_2相的吞食作用与冷却速度有关，冷却速度越快，吞食作用越弱，残余α_2相含量。
包套轧制后Ti-45Al-9Nb-Y合金的组织发生明显变化。轧制组织在RD、ND以及TD三个方向均为动态再结晶等轴晶粒，是典型的近γ组织。随着轧制变形量的增加，发生应力诱发的γ→α相变，形成的α_2+γ混合组织粗化，并完全转变成单相的α_2相。由于变形量较大，65%变形量的板材组织中等轴γ相内形成以层错为核心退火孪晶。轧制变形促进了ω相在β/B2相的形成，轧制变形量的增加，ω相含量增加并改变了ω相的析出形貌。变形量增加到65%，β/B2相内ω相的含量很高。ω相是有害相，1420℃保温20min的全层片热处理可以完全消除ω相。
High Nb containing TiAl based alloy is the typier of high temperature and highstrength TiAl alloy. Due to their attractive propertis, such as high specific strengthand modulus, good high temperature oxidation resistance and creep resistance, etc,high Nb containing TiAl alloys have a high potential application in aerospace andautomobile industry. However, the difficulty in ingot preparation and the largedeformation resistance of high Nb containing TiAl alloy limit their processing andapplication. It is proved that β solidifying can effectively reduce segregation andrefine the structure. Two kinds of β solidifying high Nb containing TiAl alloy withnominal composition of Ti-45Al-9Nb-Y and Ti-44Al-8Nb-0.2W-0.2B-Y areprepared by using ISM and VAR technologies, respectively. The preparation ofingots, hot working technology, heat treatment processing, and microstructure andmechanical properties were investigated systematically in this paper.
Ti-45Al-9Nb-Y and Ti-44Al-8Nb-0.2W-0.2B-Y alloys were prepared by ISMand VAR respectively. Ti-45Al-9Nb-Y alloy shows a typical near lamellar structure,with same orientation in the adjacent lamellar colonies. And γ phase precipitateddiscontinuously in the residual β phase with the relationship of(110) β//(111) γ,forming mixed structure between β/B2and γ phase in the grain boundary. ISMtechnology can effectively reduce segregation and improve the uniformity of theorganization. Elements in Ti-44Al-8Nb-0.2W-0.2B-Y ingot after HIP distributeduniformly. TiB formed during solidifying act as heterogeneous nucleation siteswhich increase the nucleation rate of α phase and refine the lamellar strcutureresulting in the formation of non Burhers relationship α phase. The top of the ingothas the best mechanical properties; room temperature strength is about680MPa.
High temperature compression test and canned forging of Ti-45Al-9Nb-Y alloywere carried out. The θ=0°lamellar colony with medium yield strength bent androtated to the orientation of θ=90°which has highest yield strength, and dynamicrecrystallized at this bent area of lamellar colony and its grain boundary. The0°＜θ＜90°lamellar colony with soft orientation also rotated to the orientation of θ=90°accompanied with numerous dynamic recrystallization, while the θ=90°lamellarcolony was elongated with dynamic recrystallization at grain boundary. Theoptimum deformation process was determined as1250℃/0.05s~(-1). The as-forgedstructure is typically duplex structure, composed of γ phase, β phase and γ/α_2structure. The coarsened α_2phase in the residual lamellar colony containstweed-like pattern perpendicular to the lamellar orientation. Widmannst tten α_2 phase was obtained in equiaxed γ phase after heat treated at1330℃with30min/FC,which promoted the formation of lamellar structure. The full lamellarstructure has the highest strength and the elongation of as-forged structure is thelargest.
Ti-44Al-8Nb-0.2W-0.2B-Y alloy was canned forged at1275℃withdeformation of50%and70%, and pancakes with70%deformation were furnacecooled and air cooled, repectively. And with the increase of deformation, as-forgedstructure has much higher strength and plasticity at room temperture, for example,the strength at room temperature was930MPa of alloy with70%deformation. Theair cooled deformation structure was work hardened obviously which indeedincreased the strength at lower temperature and resulted in the crack of the pancake.After tensiled of the alloy with70%deformations at900℃and above tempertautre,ω phase with white contrast formed, and its content increased with temperatureincreasing or strain rate slowing. Considerating the solid state phase transformationduring the tensile tests, it was believed that ω phase fromed in the transformationα_2→ω+γwhich was promoted by the dynamic recrystallization. Fine duplexmicrostrucutre with globularized γ grain and small lamellar structure formed after atwo steps heat treatment of1310℃/20min+1240℃/1h. Full lamellae structure couldbe obtained at1340℃for10min. The mechanical properties were measured forduplex structure and full lamellar structure.
Microstructure evolution of α laths and γ laths during hot working and thefollowing cooling processss was discussed in detail. During deformation, ordered γphase in remnant lamellae dynamic recrystallized prior (γ_D) in the form ofsubboundary rotaion，while the disordered α lath which has high stacking fault weremerely bended. As deformation increase, dynamic recrystallization occurred in αphase and the grown of γ_Dinto α_2phase by bulging increased. The higher rate ofcooling, the lower rare of swallowing ofγ_D, the more quantity of α_2phase residual.
The microstructure of as-rolled Ti-45Al-9Nb-Y alloy is typically near γstructure with dynamic recrystallized grain in RD, ND and TD directions. As thedeformation increase, the stress induced α phase transformation of γ→αoccurredfrom forming α_2+γ mixed structure into forming single α_2phase. Annealing twinsformed by stacking fault in the sheet with65%deformations. ω phase tranformedfrom β/B2phase was dramatically improved by rolling, the morphology of ω phasechanged, and the number of ω phase increased, as deformation increase. β/B2phasehas high contents of ω phase after rolling with65%deformations. Full lamellae heattreatment at1420℃holding20min could eliminate ω phase completely which isbrittleness and is bad to the properties.
采用ISM技术，VAR三次重熔技术分别成功制备了Ti-45Al-9Nb-Y合金以及Ti-44Al-8Nb-0.2W-0.2B-Y合金。Ti-45Al-9Nb-Y合金是典型的近层片组织，相邻片层晶团具有相同的片层取向。γ相遵循(110) β//(111) γ位向关系从晶界上残余的β相内不连续析出，形成混合组织。ISM熔炼可以有效的减少元素偏析，提高组织均匀性。热等静压后大尺寸Ti-44Al-8Nb-0.2W-0.2B-Y合金铸锭元素分布基本均匀。添加的B元素形成的TiB作为异质形核剂提高α相的形核率，导致大量非Burgers位向关系的α相出现，细化了片层组织。铸锭顶部具有最好的性能，室温强度约为680MPa。
对Ti-45Al-9Nb-Y合金进行了高温压缩试验以及包套锻造。高温热压缩过程中，θ=0°的中等强度取向片层晶团发生θ=90°的片层弯曲，并在晶界和片层弯曲处发生动态再结晶。0°＜θ＜90°的软取向片层晶团向θ=90°的取向整体转动同时发生大量的动态再结晶。θ=90°的硬取向片层拉长，晶界上发生动态再结晶。确定最佳变形工艺为：1250℃/0.05s~(-1)。锻态组织是双态组织，残余片层晶团内α_2相板条粗化，并形成垂直于板条取向的花呢状花纹。在1330℃/30min/FC的热处理中,锻态组织中等轴γ相内获得魏氏组织(Widmannst tten)，魏氏组织的出现有利于片层的形成。对锻造组织进行了双态以及全层片组织热处理。全层片组织强度最高，锻态组织延伸率最高。
在1275℃对Ti-44Al-8Nb-0.2W-0.2B-Y合金进行包套锻造，制备出了变形量分别为50%和70%的锻饼，并对70%变形量的锻饼进行了炉冷和空冷处理。变形量越大，室温强度和塑性越高，70%变形量合金的室温强度达到930MPa。空冷组织残余应力大，加工硬化明显，锻饼发生开裂。在70%变形量合金900℃以上高温拉伸组织中，形成白亮的ω相，并且温度越高，应变速率越低，ω相越多。拉伸过程中，ω相的形成可以通过α_2→ω+γ固态相变形成。此外，对锻态Ti-44Al-8Nb-0.2W-0.2B-Y合金在1310℃/20min+1240℃/1h进行了双步热处理，并获得了球状γ等轴晶粒与细小片层的双态组织。1340℃/10min可以获得全层片组织。对双态组织和全片层组织进行了力学性能测试。
详细分析了α板条和γ板条在热加工及冷却过程中的组织演化机制。变形过程中，残余片层内有序γ相首先以亚晶界的转动发生动态再结晶γ_D，而高层错能的无序α相板条仅发生塑性弯曲形成亚结构。γ D再结晶晶粒通过晶界的膨胀在冷却过程中向α_2相板条的生长。随着变形量的增加，α相发生动态再结晶，γ_D对α_2相的吞食作用增加。 γ_D对α_2相的吞食作用与冷却速度有关，冷却速度越快，吞食作用越弱，残余α_2相含量。
包套轧制后Ti-45Al-9Nb-Y合金的组织发生明显变化。轧制组织在RD、ND以及TD三个方向均为动态再结晶等轴晶粒，是典型的近γ组织。随着轧制变形量的增加，发生应力诱发的γ→α相变，形成的α_2+γ混合组织粗化，并完全转变成单相的α_2相。由于变形量较大，65%变形量的板材组织中等轴γ相内形成以层错为核心退火孪晶。轧制变形促进了ω相在β/B2相的形成，轧制变形量的增加，ω相含量增加并改变了ω相的析出形貌。变形量增加到65%，β/B2相内ω相的含量很高。ω相是有害相，1420℃保温20min的全层片热处理可以完全消除ω相。
High Nb containing TiAl based alloy is the typier of high temperature and highstrength TiAl alloy. Due to their attractive propertis, such as high specific strengthand modulus, good high temperature oxidation resistance and creep resistance, etc,high Nb containing TiAl alloys have a high potential application in aerospace andautomobile industry. However, the difficulty in ingot preparation and the largedeformation resistance of high Nb containing TiAl alloy limit their processing andapplication. It is proved that β solidifying can effectively reduce segregation andrefine the structure. Two kinds of β solidifying high Nb containing TiAl alloy withnominal composition of Ti-45Al-9Nb-Y and Ti-44Al-8Nb-0.2W-0.2B-Y areprepared by using ISM and VAR technologies, respectively. The preparation ofingots, hot working technology, heat treatment processing, and microstructure andmechanical properties were investigated systematically in this paper.
Ti-45Al-9Nb-Y and Ti-44Al-8Nb-0.2W-0.2B-Y alloys were prepared by ISMand VAR respectively. Ti-45Al-9Nb-Y alloy shows a typical near lamellar structure,with same orientation in the adjacent lamellar colonies. And γ phase precipitateddiscontinuously in the residual β phase with the relationship of(110) β//(111) γ,forming mixed structure between β/B2and γ phase in the grain boundary. ISMtechnology can effectively reduce segregation and improve the uniformity of theorganization. Elements in Ti-44Al-8Nb-0.2W-0.2B-Y ingot after HIP distributeduniformly. TiB formed during solidifying act as heterogeneous nucleation siteswhich increase the nucleation rate of α phase and refine the lamellar strcutureresulting in the formation of non Burhers relationship α phase. The top of the ingothas the best mechanical properties; room temperature strength is about680MPa.
High temperature compression test and canned forging of Ti-45Al-9Nb-Y alloywere carried out. The θ=0°lamellar colony with medium yield strength bent androtated to the orientation of θ=90°which has highest yield strength, and dynamicrecrystallized at this bent area of lamellar colony and its grain boundary. The0°＜θ＜90°lamellar colony with soft orientation also rotated to the orientation of θ=90°accompanied with numerous dynamic recrystallization, while the θ=90°lamellarcolony was elongated with dynamic recrystallization at grain boundary. Theoptimum deformation process was determined as1250℃/0.05s~(-1). The as-forgedstructure is typically duplex structure, composed of γ phase, β phase and γ/α_2structure. The coarsened α_2phase in the residual lamellar colony containstweed-like pattern perpendicular to the lamellar orientation. Widmannst tten α_2 phase was obtained in equiaxed γ phase after heat treated at1330℃with30min/FC,which promoted the formation of lamellar structure. The full lamellarstructure has the highest strength and the elongation of as-forged structure is thelargest.
Ti-44Al-8Nb-0.2W-0.2B-Y alloy was canned forged at1275℃withdeformation of50%and70%, and pancakes with70%deformation were furnacecooled and air cooled, repectively. And with the increase of deformation, as-forgedstructure has much higher strength and plasticity at room temperture, for example,the strength at room temperature was930MPa of alloy with70%deformation. Theair cooled deformation structure was work hardened obviously which indeedincreased the strength at lower temperature and resulted in the crack of the pancake.After tensiled of the alloy with70%deformations at900℃and above tempertautre,ω phase with white contrast formed, and its content increased with temperatureincreasing or strain rate slowing. Considerating the solid state phase transformationduring the tensile tests, it was believed that ω phase fromed in the transformationα_2→ω+γwhich was promoted by the dynamic recrystallization. Fine duplexmicrostrucutre with globularized γ grain and small lamellar structure formed after atwo steps heat treatment of1310℃/20min+1240℃/1h. Full lamellae structure couldbe obtained at1340℃for10min. The mechanical properties were measured forduplex structure and full lamellar structure.
Microstructure evolution of α laths and γ laths during hot working and thefollowing cooling processss was discussed in detail. During deformation, ordered γphase in remnant lamellae dynamic recrystallized prior (γ_D) in the form ofsubboundary rotaion，while the disordered α lath which has high stacking fault weremerely bended. As deformation increase, dynamic recrystallization occurred in αphase and the grown of γ_Dinto α_2phase by bulging increased. The higher rate ofcooling, the lower rare of swallowing ofγ_D, the more quantity of α_2phase residual.
The microstructure of as-rolled Ti-45Al-9Nb-Y alloy is typically near γstructure with dynamic recrystallized grain in RD, ND and TD directions. As thedeformation increase, the stress induced α phase transformation of γ→αoccurredfrom forming α_2+γ mixed structure into forming single α_2phase. Annealing twinsformed by stacking fault in the sheet with65%deformations. ω phase tranformedfrom β/B2phase was dramatically improved by rolling, the morphology of ω phasechanged, and the number of ω phase increased, as deformation increase. β/B2phasehas high contents of ω phase after rolling with65%deformations. Full lamellae heattreatment at1420℃holding20min could eliminate ω phase completely which isbrittleness and is bad to the properties.
引文
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