时效及ECAP处理无镍Ti基记忆合金相变与力学行为研究
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摘要
近等原子比Ni-Ti记忆合金由于具有较低的弹性模量，良好的形状记忆效应、超弹性性能，作为生物医用材料已经得到了广泛应用。但Ni-Ti合金中Ni含量高达50at.%，在人体体液环境作用下，Ni原子可能游离出来，对人体健康产生危害。为消除Ni元素可能产生的危害，研制开发无镍Ti基记忆合金已成为当前生物医用材料研究的一个热点，其中，Ti-Mo基、Ti-Nb基记忆合金是Ti基记忆合金研制的两个主要合金系列。
Ti-xMo-4Nb-2V-3Al(x=7.6～11mass%)合金为美国Memry公司研制开发的新型生物医用钛合金，该系列Ti-Mo基合金具有较低的弹性模量，较高的屈服强度，且Mo元素含量约为10mass%的合金固溶处理后呈现出良好的超弹性。本论文研究了时效处理对Ti-9.8Mo-3.9Nb-2V-3.1Al合金组织、变形行为和超弹性的影响规律；对Ti-9.5Mo-4Nb-2V-3Al合金的形状记忆效应进行了分析研究；借助等径弯角挤压(ECAP)技术对Ti-9.8Mo-3.9Nb-2V-3.1Al合金和Ti-25at.%Nb合金进行超细晶及时效处理，研究了超细晶Ti基记忆合金的超弹性行为。
组织分析表明，Ti-9.8Mo-3.9Nb-2V-3.1Al合金固溶后淬火得到β+ω_(ath)两相组织，ωath呈细片层状。经300℃时效30分钟，合金基体上析出弥散椭球状ωiso相，尺寸约10nm。400℃时效30分钟后析出长度约为100nm针状相及椭球状尺寸为20nm的ω_(iso)相。500℃时效30分钟后，大量析出的相均匀弥散分布。600℃时效30分钟相以晶界析出为主，晶粒内有少量相析出，700℃时效30分钟后，相析出数量进一步减少，晶粒内部几乎未有相。
拉伸试验表明，Ti-9.8Mo-3.9Nb-2V-3.1Al合金变形行为可分为三种类型：固溶态及350℃，400℃，450℃时效30分钟的合金属于第Ⅰ类型，其应力-应变曲线呈现较明显加工硬化；250℃、300℃及500℃时效后试样属于第Ⅱ类型，材料屈服后出现平缓应力平台，加工硬化不明显；600℃、700℃时效后的试样属于第Ⅲ类型，其应力-应变曲线表现为双屈服现象，第一屈服强度较低，屈服后加工硬化明显。固溶处理后Ti-9.8Mo-3.9Nb-2V-3.1Al合金呈现出较好的超弹性行为，拉伸4%应变后卸载，恢复应变为2.8%，残余应变为1.2%。经400℃时效处理30分钟后，超弹性进一步提高，恢复应变达3.2%，残余应变为0.8%。300℃或500℃时效处理后，超弹性性能完全消失。Ti-9.8Mo-3.9Nb-2V-3.1Al合金在600℃、700℃时效30分钟，再次表现出良好的超弹性行为，恢复应变达3.3%。由于非热ωath相对基体的强化作用，固溶处理后合金具有较高的屈服强度，弥散均匀分布于基体上的相可极大提高材料的强度。
Ti-9.8Mo-3.9Nb-2V-3.1Al合金马氏体转变温度Ms为-56℃。升温过程中，当温度不高于250℃时，由于ωath相不断溶解，合金的电阻随温度升高而降低。温度范围为250～380℃时，由于不断析出等温ωiso相，电阻随温度升高而增加。温度范围为380～450℃时，ωiso相作为β→α转变的中间过渡相而不断溶解，电阻随温度升高下降。温度范围为450～600℃时，α相从β相析出，电阻随温度升高而增加。温度范围为600～850℃时，发生α→β转变，α相不断溶解到基体中，温度升高到850℃时，α相全部转变为β相。
本研究采用冷坩埚悬浮熔炼炉制备的Ti-9.5Mo-4Nb-2V-3Al(mass%)合金具有良好的形状记忆效应，合金固溶后水冷得到β+ω_(ath)+α"三相组织。拉伸过程中，合金表现出双屈服现象，第一屈服阶段伴随应力诱发马氏体相α"转变(β→α")。变形后的材料经223℃保温5分钟处理，呈现形状记忆效应，呈现完全形状记忆的最大应变量为2.2%。DSC和电阻试验表明，Ti-9.5Mo-4Nb-2V-3Al合金形状记忆的机理在于应力诱发的马氏体α"在加热时逆转变为母相β，其转变温度为92℃。Ti-9.5Mo-4Nb-2V-3Al合金经300～400℃时效30～60分钟后，表现出一定的超弹性。300℃时效60分钟后，合金拉伸4%后卸载，可恢复应变为3.2%，而300℃时效120分钟后，超弹性丧失。
ECAP处理Ti-9.8Mo-3.9Nb-2V-3.1Al合金研究表明，经过400℃处理1道次，得到长条状晶粒，材料强度明显提高。ECAP处理1道次后，合金屈服强度为1296MPa，抗拉强度为1355MPa，模量提高到88.9GPa。处理2道次后，屈服强度高达1500MPa，模量提高到104.9GPa，但塑性急剧下降。700℃快速退火10s，可明显降低ECAP处理后Ti-9.8Mo-3.9Nb-2V-3.1Al合金的模量，此时模量为63GPa。300℃处理1道次得到更为细长的晶粒，屈服强度为1265MPa，极限抗拉强度为1310MPa。经400℃ECAP处理2道次后，材料表面出现明显开裂。
ECAP处理Ti-25at.%Nb合金研究表明，在550℃ECAP处理4道次后，晶粒明显拉长，难以得到细小的等轴晶。400℃进行ECAP处理，晶粒细化明显，其中，处理2道次后，得到的微观组织以拉长晶粒为主，局部区域开始出现尺寸约为500nm的等轴超细晶。4道次ECAP处理后，可以得到等轴细化的超细晶组织，晶粒尺寸在300nm左右。400℃ECAP处理后Ti-25at.%Nb合金的强度、超弹性性能得到提高。ECAP+时效处理可以进一步提高强度和超弹性性能，其中，2道次和4道次处理后时效，合金的完全超弹性应变为1.5%，小应变(1.5%)时超弹性性能稳定。
Ni-Ti shape memory alloys (SMAs) are widely used in biomedical applicationsdue to their superior properties such as low elastic modulus, shape memory effect andsuperelasticity. However, since Ni-Ti alloy contains Ni of about50at.%, the possibilityof Ni-hypersensitivity has been pointed out because of the Ni extricated in the bodyfluid. New practical shape memory alloys consisted of non toxic elements, especiallyNi-free, have been a hotspot in biomedical materials area. Ti-Mo based SMAs andTi-Nb based SMAs are the two kinds of important Ni-free alloys.
Ti-xMo-4Nb-2V-3Al(x=7.6～11mass%) alloys are newly developed Ti-basedbiomedical materials by Memry corporation in USA. These alloys exhibit low Young′smodulus, good superelasticity behavior when Mo element content is about10mass%.In the present study, the effect of aging on the microstructure, deformation behaviorand superelasticity of Ti-9.8Mo-3.9Nb-2V-3.1Al alloy and the shape memory effect(SME) of Ti-9.5Mo-4Nb-2V-3Al alloy were investigated. Ti-9.8Mo-3.9Nb-2V-3.1Alalloy and Ti-25at.%Nb alloy were processed by Equal Channel Angular Pressing(ECAP) and aging treatment to obtain ultra-fine grain (UFG) microstructure, and thesuperelasticity of these alloys with UFG microstructure were investigated.
Microscopic analysis indicates that β+ωathdual phases microstructure wereobtained in solution treated Ti-9.8Mo-3.9Nb-2V-3.1Al alloy, and the shape of ωathphase is lamina. After aging at300℃for30minutes, ellipsoidal shape ωisophase witha size about10nm precipitated in the matrix. As aged at400℃for30minutes,needle-like phase about100nm in length precipitated and ellipsoidal shape ωisophase increased about20nm in size. After aging at500℃for30minutes, lots of phase precipitated and dispersed homogeneously in the matrix. However, as agingtemperature increased to600℃, phase precipitated along grain boundary dominantly, and a few phase precipitated inside grains. When the aging temperaturewas700℃, the amount of phase along the grain boundary decreased and there waslittle phase precipitated inside grains.
Tensile test indicates that deformation behavior of Ti-9.8Mo-3.9Nb-2V-3.1Alalloy can be divided into three groups. For Group I, the stress-strain curves show workhardening after yielding. The specimens aged at350℃,400℃and450℃for30minutes belong to group I, showing a similar deformation behavior to that of STspecimen, with obvious work hardening after yielding. For group II, the stress-straincurves show little work hardening after yielding. Specimens aged at250℃,300℃and500℃for30minutes belong to Group II. For group III, the stress-strain curvesshow two yielding phenomena and a high work-hardening rate after first yielding, butvery small after the second yielding. Specimens aged at600℃and700℃for30minutes belong to group III. The solution treated Ti-9.8Mo-3.9Nb-2V-3.1Al alloyexhibits good superelasticity with a recoverable strain of2.8%and a remained strain of1.2%. After aging at400℃for30minutes, the specimen exhibits excellentsuperelasticity with a recoverable strain of3.2%and a remained strain of0.8%.However, after aging at300℃and500℃, the superelasticity lost completely. Asaging temperature increased to600℃and700℃, the superelasticity was restored witha recoverable strain of3.3%. Because of the strengthening effect of ωathphaseprecipitates, the solution treated specimen exhibits high yielding strength. Dispersed phase homogeneously in the matrix can increase the strength strongly.
The martensitic transformation temperature (Ms) of Ti-9.8Mo-3.9Nb-2V-3.1Alalloy is-56℃.When the temperature is lower than250℃, the resistance ratiodecrease during heating on the resistance (ρ) vs. temperature (T) curves, because ofthe ωathphase dissolving into the matrix. As the temperature is in the range of250～380℃，the resistance ratio increases during heating because of the precipitation of ωisophase. The resistance ratio decreases again during heating from380℃to450℃with the dissolving of ωisoand the precipitation of α phase. When the temperature isin the range of450～600℃, the resistance ratio increases because of the precipitationof α phase from β phase. As the temperature is in the range of600～850℃，resistanceratio decreases because of the dissolving of α phase by α→β transformation. The αphase to β phase transformation completed at850℃.
A multifunctional alloy with a nominal chemical composition ofTi-9.5Mo-4Nb-2V-3Al (mass%) was prepared by cold crucible levitation meltingtechnique, which exhibits shape memory effect. The microstructure of solution treatedTi-9.5Mo-4Nb-2V-3Al alloy is β+ωath+α" three phases. This alloy exhibits doubleyielding stage during tensile deformation. There is a stress induced martensitictransformation (SIM) of β α" during the first yielding stage. Deformed specimensexhibit shape memory effect after heated at223℃for5minutes, and the shaperecoverable strain is2.2%. DSC and ρ-T experiments indicated that α" induced bystress which can transform to parent phase (β) during heating. And the start temperatureof transformation (As) is92℃. After aged at300～400℃for30～60minutes,Ti-9.5Mo-4Nb-2V-3Al alloy exhibites superelastic behavior. The recoverable strain is3.2%for specimen after aged at300℃for60minutes unloading from tensile strain of4%. However, after aging at300℃for120minutes, the superelasticity lostcompletely.
Ti-9.8Mo-3.9Nb-2V-3.1Al alloy was processed by ECAP to obtain the UFGmicrostructure. After one pass ECAP at400℃, the micrograph is lath microstructureand the strength increases obviously. The yielding strength (σ0.2) is1296MPa and thetensile strength1355MPa. The Young′s modulus increases to88.9GPa. After twopasses ECAP, the yielding strength (σ0.2) is more than1500MPa with Young′s modulus104.9GPa, but the plasticity decreases sharply. When materials were flash annealed at700℃for10s after1pass ECAP, the Young′s modulus decreased to63GPa. Afterone pass ECAP at300℃, The yielding strength and ultimate tensile strength are1265MPa and1310MPa, respectively. It is noted that there were cracks on the surface ofspecimen after2pass ECAP.
The microstructure analyses of Ti-25at.%Nb alloy after4passes ECAP at550℃indicates that the grains of Ti-25at.%Nb alloy were elongated, but no obtained UFG.The grains were refined obviously as the process temperature decreased to400℃.After2passed ECAP at400℃, most grains were elongated, and some equiaxed UFGare observed with grain size about500nm. The equiaxed UFG can be obtained after4passes ECAP at400℃with a grain size about300nm. The strength andsuperelasticity can be improved by ECAP+aging treatment. After2,4passes ECAPprocessing and aged at300℃for60minutes, the strain can be restored completely when unloaded from tensile strain of1.5%. The Ti-25at.%Nb alloy after ECAP andaged at300℃for30minutes exhibits good superelastic stability at a tensile strain of1.5%.
Ti-xMo-4Nb-2V-3Al(x=7.6～11mass%)合金为美国Memry公司研制开发的新型生物医用钛合金，该系列Ti-Mo基合金具有较低的弹性模量，较高的屈服强度，且Mo元素含量约为10mass%的合金固溶处理后呈现出良好的超弹性。本论文研究了时效处理对Ti-9.8Mo-3.9Nb-2V-3.1Al合金组织、变形行为和超弹性的影响规律；对Ti-9.5Mo-4Nb-2V-3Al合金的形状记忆效应进行了分析研究；借助等径弯角挤压(ECAP)技术对Ti-9.8Mo-3.9Nb-2V-3.1Al合金和Ti-25at.%Nb合金进行超细晶及时效处理，研究了超细晶Ti基记忆合金的超弹性行为。
组织分析表明，Ti-9.8Mo-3.9Nb-2V-3.1Al合金固溶后淬火得到β+ω_(ath)两相组织，ωath呈细片层状。经300℃时效30分钟，合金基体上析出弥散椭球状ωiso相，尺寸约10nm。400℃时效30分钟后析出长度约为100nm针状相及椭球状尺寸为20nm的ω_(iso)相。500℃时效30分钟后，大量析出的相均匀弥散分布。600℃时效30分钟相以晶界析出为主，晶粒内有少量相析出，700℃时效30分钟后，相析出数量进一步减少，晶粒内部几乎未有相。
拉伸试验表明，Ti-9.8Mo-3.9Nb-2V-3.1Al合金变形行为可分为三种类型：固溶态及350℃，400℃，450℃时效30分钟的合金属于第Ⅰ类型，其应力-应变曲线呈现较明显加工硬化；250℃、300℃及500℃时效后试样属于第Ⅱ类型，材料屈服后出现平缓应力平台，加工硬化不明显；600℃、700℃时效后的试样属于第Ⅲ类型，其应力-应变曲线表现为双屈服现象，第一屈服强度较低，屈服后加工硬化明显。固溶处理后Ti-9.8Mo-3.9Nb-2V-3.1Al合金呈现出较好的超弹性行为，拉伸4%应变后卸载，恢复应变为2.8%，残余应变为1.2%。经400℃时效处理30分钟后，超弹性进一步提高，恢复应变达3.2%，残余应变为0.8%。300℃或500℃时效处理后，超弹性性能完全消失。Ti-9.8Mo-3.9Nb-2V-3.1Al合金在600℃、700℃时效30分钟，再次表现出良好的超弹性行为，恢复应变达3.3%。由于非热ωath相对基体的强化作用，固溶处理后合金具有较高的屈服强度，弥散均匀分布于基体上的相可极大提高材料的强度。
Ti-9.8Mo-3.9Nb-2V-3.1Al合金马氏体转变温度Ms为-56℃。升温过程中，当温度不高于250℃时，由于ωath相不断溶解，合金的电阻随温度升高而降低。温度范围为250～380℃时，由于不断析出等温ωiso相，电阻随温度升高而增加。温度范围为380～450℃时，ωiso相作为β→α转变的中间过渡相而不断溶解，电阻随温度升高下降。温度范围为450～600℃时，α相从β相析出，电阻随温度升高而增加。温度范围为600～850℃时，发生α→β转变，α相不断溶解到基体中，温度升高到850℃时，α相全部转变为β相。
本研究采用冷坩埚悬浮熔炼炉制备的Ti-9.5Mo-4Nb-2V-3Al(mass%)合金具有良好的形状记忆效应，合金固溶后水冷得到β+ω_(ath)+α"三相组织。拉伸过程中，合金表现出双屈服现象，第一屈服阶段伴随应力诱发马氏体相α"转变(β→α")。变形后的材料经223℃保温5分钟处理，呈现形状记忆效应，呈现完全形状记忆的最大应变量为2.2%。DSC和电阻试验表明，Ti-9.5Mo-4Nb-2V-3Al合金形状记忆的机理在于应力诱发的马氏体α"在加热时逆转变为母相β，其转变温度为92℃。Ti-9.5Mo-4Nb-2V-3Al合金经300～400℃时效30～60分钟后，表现出一定的超弹性。300℃时效60分钟后，合金拉伸4%后卸载，可恢复应变为3.2%，而300℃时效120分钟后，超弹性丧失。
ECAP处理Ti-9.8Mo-3.9Nb-2V-3.1Al合金研究表明，经过400℃处理1道次，得到长条状晶粒，材料强度明显提高。ECAP处理1道次后，合金屈服强度为1296MPa，抗拉强度为1355MPa，模量提高到88.9GPa。处理2道次后，屈服强度高达1500MPa，模量提高到104.9GPa，但塑性急剧下降。700℃快速退火10s，可明显降低ECAP处理后Ti-9.8Mo-3.9Nb-2V-3.1Al合金的模量，此时模量为63GPa。300℃处理1道次得到更为细长的晶粒，屈服强度为1265MPa，极限抗拉强度为1310MPa。经400℃ECAP处理2道次后，材料表面出现明显开裂。
ECAP处理Ti-25at.%Nb合金研究表明，在550℃ECAP处理4道次后，晶粒明显拉长，难以得到细小的等轴晶。400℃进行ECAP处理，晶粒细化明显，其中，处理2道次后，得到的微观组织以拉长晶粒为主，局部区域开始出现尺寸约为500nm的等轴超细晶。4道次ECAP处理后，可以得到等轴细化的超细晶组织，晶粒尺寸在300nm左右。400℃ECAP处理后Ti-25at.%Nb合金的强度、超弹性性能得到提高。ECAP+时效处理可以进一步提高强度和超弹性性能，其中，2道次和4道次处理后时效，合金的完全超弹性应变为1.5%，小应变(1.5%)时超弹性性能稳定。
Ni-Ti shape memory alloys (SMAs) are widely used in biomedical applicationsdue to their superior properties such as low elastic modulus, shape memory effect andsuperelasticity. However, since Ni-Ti alloy contains Ni of about50at.%, the possibilityof Ni-hypersensitivity has been pointed out because of the Ni extricated in the bodyfluid. New practical shape memory alloys consisted of non toxic elements, especiallyNi-free, have been a hotspot in biomedical materials area. Ti-Mo based SMAs andTi-Nb based SMAs are the two kinds of important Ni-free alloys.
Ti-xMo-4Nb-2V-3Al(x=7.6～11mass%) alloys are newly developed Ti-basedbiomedical materials by Memry corporation in USA. These alloys exhibit low Young′smodulus, good superelasticity behavior when Mo element content is about10mass%.In the present study, the effect of aging on the microstructure, deformation behaviorand superelasticity of Ti-9.8Mo-3.9Nb-2V-3.1Al alloy and the shape memory effect(SME) of Ti-9.5Mo-4Nb-2V-3Al alloy were investigated. Ti-9.8Mo-3.9Nb-2V-3.1Alalloy and Ti-25at.%Nb alloy were processed by Equal Channel Angular Pressing(ECAP) and aging treatment to obtain ultra-fine grain (UFG) microstructure, and thesuperelasticity of these alloys with UFG microstructure were investigated.
Microscopic analysis indicates that β+ωathdual phases microstructure wereobtained in solution treated Ti-9.8Mo-3.9Nb-2V-3.1Al alloy, and the shape of ωathphase is lamina. After aging at300℃for30minutes, ellipsoidal shape ωisophase witha size about10nm precipitated in the matrix. As aged at400℃for30minutes,needle-like phase about100nm in length precipitated and ellipsoidal shape ωisophase increased about20nm in size. After aging at500℃for30minutes, lots of phase precipitated and dispersed homogeneously in the matrix. However, as agingtemperature increased to600℃, phase precipitated along grain boundary dominantly, and a few phase precipitated inside grains. When the aging temperaturewas700℃, the amount of phase along the grain boundary decreased and there waslittle phase precipitated inside grains.
Tensile test indicates that deformation behavior of Ti-9.8Mo-3.9Nb-2V-3.1Alalloy can be divided into three groups. For Group I, the stress-strain curves show workhardening after yielding. The specimens aged at350℃,400℃and450℃for30minutes belong to group I, showing a similar deformation behavior to that of STspecimen, with obvious work hardening after yielding. For group II, the stress-straincurves show little work hardening after yielding. Specimens aged at250℃,300℃and500℃for30minutes belong to Group II. For group III, the stress-strain curvesshow two yielding phenomena and a high work-hardening rate after first yielding, butvery small after the second yielding. Specimens aged at600℃and700℃for30minutes belong to group III. The solution treated Ti-9.8Mo-3.9Nb-2V-3.1Al alloyexhibits good superelasticity with a recoverable strain of2.8%and a remained strain of1.2%. After aging at400℃for30minutes, the specimen exhibits excellentsuperelasticity with a recoverable strain of3.2%and a remained strain of0.8%.However, after aging at300℃and500℃, the superelasticity lost completely. Asaging temperature increased to600℃and700℃, the superelasticity was restored witha recoverable strain of3.3%. Because of the strengthening effect of ωathphaseprecipitates, the solution treated specimen exhibits high yielding strength. Dispersed phase homogeneously in the matrix can increase the strength strongly.
The martensitic transformation temperature (Ms) of Ti-9.8Mo-3.9Nb-2V-3.1Alalloy is-56℃.When the temperature is lower than250℃, the resistance ratiodecrease during heating on the resistance (ρ) vs. temperature (T) curves, because ofthe ωathphase dissolving into the matrix. As the temperature is in the range of250～380℃，the resistance ratio increases during heating because of the precipitation of ωisophase. The resistance ratio decreases again during heating from380℃to450℃with the dissolving of ωisoand the precipitation of α phase. When the temperature isin the range of450～600℃, the resistance ratio increases because of the precipitationof α phase from β phase. As the temperature is in the range of600～850℃，resistanceratio decreases because of the dissolving of α phase by α→β transformation. The αphase to β phase transformation completed at850℃.
A multifunctional alloy with a nominal chemical composition ofTi-9.5Mo-4Nb-2V-3Al (mass%) was prepared by cold crucible levitation meltingtechnique, which exhibits shape memory effect. The microstructure of solution treatedTi-9.5Mo-4Nb-2V-3Al alloy is β+ωath+α" three phases. This alloy exhibits doubleyielding stage during tensile deformation. There is a stress induced martensitictransformation (SIM) of β α" during the first yielding stage. Deformed specimensexhibit shape memory effect after heated at223℃for5minutes, and the shaperecoverable strain is2.2%. DSC and ρ-T experiments indicated that α" induced bystress which can transform to parent phase (β) during heating. And the start temperatureof transformation (As) is92℃. After aged at300～400℃for30～60minutes,Ti-9.5Mo-4Nb-2V-3Al alloy exhibites superelastic behavior. The recoverable strain is3.2%for specimen after aged at300℃for60minutes unloading from tensile strain of4%. However, after aging at300℃for120minutes, the superelasticity lostcompletely.
Ti-9.8Mo-3.9Nb-2V-3.1Al alloy was processed by ECAP to obtain the UFGmicrostructure. After one pass ECAP at400℃, the micrograph is lath microstructureand the strength increases obviously. The yielding strength (σ0.2) is1296MPa and thetensile strength1355MPa. The Young′s modulus increases to88.9GPa. After twopasses ECAP, the yielding strength (σ0.2) is more than1500MPa with Young′s modulus104.9GPa, but the plasticity decreases sharply. When materials were flash annealed at700℃for10s after1pass ECAP, the Young′s modulus decreased to63GPa. Afterone pass ECAP at300℃, The yielding strength and ultimate tensile strength are1265MPa and1310MPa, respectively. It is noted that there were cracks on the surface ofspecimen after2pass ECAP.
The microstructure analyses of Ti-25at.%Nb alloy after4passes ECAP at550℃indicates that the grains of Ti-25at.%Nb alloy were elongated, but no obtained UFG.The grains were refined obviously as the process temperature decreased to400℃.After2passed ECAP at400℃, most grains were elongated, and some equiaxed UFGare observed with grain size about500nm. The equiaxed UFG can be obtained after4passes ECAP at400℃with a grain size about300nm. The strength andsuperelasticity can be improved by ECAP+aging treatment. After2,4passes ECAPprocessing and aged at300℃for60minutes, the strain can be restored completely when unloaded from tensile strain of1.5%. The Ti-25at.%Nb alloy after ECAP andaged at300℃for30minutes exhibits good superelastic stability at a tensile strain of1.5%.
引文
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[1] H.Y. Kim, J.I. Kim, T. Inamura, H. Hosoda, S. Miyazaki. Effect of thermo-mechanical treatment onmechanical properties and shape memory behavior of Ti–(26–28) at.%Nb alloys. Materials Science andEngineering:A,2006,438-440(25):839-843.
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[10] Tomonari Inamuraa, Yusuke Fukuib, Hideki Hosodaa, Kenji Wakashimaa, Shuichi Miyazaki.Mechanical properties of Ti–Nb biomedical shape memory alloys containing Ge or Ga. MaterialsScience and Engineering C2005,25425-432.
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[13] J. I. Qazi, B. Marquardt, L. F. Allard, H. J. Rack. Phase transformations inTi-35Nb-7Zr-5Ta-(0.06-0.68)O alloys. Materials Science and Engineering: C,2005,25(3):389-397.
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