新型TiAlCrFe系低成本钛合金的组织与性能研究
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摘要
本文采用廉价的Cr-Fe中间合金设计并熔炼制备新型TiAlCrFe系低成本钛合金,该新型钛合金原材料成本仅为TC4合金的75-80%。文中采用光学显微镜(OM)、SEM、TEM和XRD等方法对该新型合金在不同热处理状态下的相组成、组织特征和力学性能进行了研究；并选取两种合金进行Gleeble热模拟实验研究合金的热变形特征,确定合金热加工工艺性能。通过研究得到以下主要结果：
本文对各合金在不同热处理条件下的相组成及组织演变进行研究,结果表明：在Tβ+20℃下进行加热保温0.5h,TCF、TACF、TACF1、TACFB和TACF2合金空冷和炉冷后组织由α相和β相组成；水淬后组织由p相和马氏体相组成,且在TCF和TACF合金的组织中还有ω相。TACF3合金在水淬和空冷后的组织内含有β相、ω相和马氏体相存在；合金在炉冷后的组织由α相和β相组成。在TACFB合金组织中有TiB相存在,TiB相可抑制晶粒长大。在相变点以上进行热处理后,合金晶粒随保温时间和加热温度增加而增大。在相变点以下进行热处理后,合金组织由β相和初生α相组成,随温度升高,组织内初生α相逐渐减少并转变成β相。合金在单相区固溶后再时效的组织除含有α相和β相外,还有TiFe2相；在两相区固溶后再时效与直接时效后的组织均由α相和β相组成。
本文对合金元素含量、冷却方式、加热温度和加热时间等对合金力学性能的影响研究结果表明：不同冷却方式下,由于水淬后TCF和TACF合金中含有ω相,致使水淬后强度最高,但塑性最差；TACF1、TACFB、TACF2和TACF3合金空冷后强度最高,其中TACF3合金空冷后抗拉强度为1260MPa,水淬后弹性模量最低为73.0GPa。在相变点以上进行加热处理,热处理温度和加热时间对合金强度影响不大。
在单相区固溶后再时效的组织内包含有TiFe2相,该相使塑性显著降低,甚至完全脆化。合金在两相区固溶后再时效后的强度和塑性与单相区固溶后再时效相比均有所提高,TACF2合金经860℃/1.0h/WQ+525℃/8.0h/AC热处理后抗拉强度和延伸率分别为1359MPa和4.5%,与单相区固溶后再时效相比分别提高了118MPa和4.0%,延伸率最高可提高19.0%。合金经过退火热处理后,随Cr和Fe元素含量增加,合金强度逐渐增加。随直接时效温度和时间增加,合金强度逐渐降低,TACF3合金在525℃/8.0h/AC时效后强度最高,抗拉强度为1415MPa,延伸率为7.0%。
该系列合金(TACF1和TACFB)是对应变速率和变形温度比较敏感的合金。在不同温度下,随应变速率增加,合金真应力逐渐增大；在不同应变速率下,随形变温度升高,合金真应力逐渐降低。通过Arrhenius双曲正弦本构方程建立TACF1和TACFB合金本构方程,在同等条件下变形,TACF1合金需要激活能比TACFB合金要低,说明TACF1合金高温变形比TACFB合金要容易。在TACF1和TACFB合金变形量为0.7时的加工图中可知,在本实验条件下TACF1合金可加工区域为900℃和950℃下的各应变速率；TACFB合金不可加工区域为870～940℃、应变速为1.0s-1的区域,其余区域均为可加工区域。虽然TACF1合金比TACFB合金变形要容易,但是TACFB合金的加工性更好。随形变温度和应变速率增加,合金组织内岀现动态再结晶的趋势越来越明显,细小的动态再结晶晶粒位于变形晶粒的交叉点和晶界上，所发生的动态再结晶均为不完全动态再结晶。
In this paper, new type of low cost TiAlCrFe alloys were designed and melted by using bargain Cr-Fe alloy as master alloy. The costs of raw materials for these new alloys are three-quarters to eighty percent of TC4. Observation and analysis of the microstructure of alloys under different heat treatment conditions were done by employing OM, SEM, TEM, and XRD. The effects of cooling ways, heating temperature and holding time on mechanical properties of alloys were discussed. Thermal simulation experiments were carried out for some well-selected alloys to explore the processing technology during hot working. The main results are as follows:
Cooling methods, heating temperature and holding time all have certain effect on the microstructure of alloys. The microstructure consists of a phase and β phase when TCF, TACF, TACF1, TACFB and TACF2alloys were heat treated at Tp+20℃and then cooled by air cooling or furnace cooling; β and a martensite when they were heat treated at Tp+20℃and then water quenched except that co also observed in TCF and TACF alloys,β phase,ω phase and a martensite were observed in TACF3alloy after air cooling or quenching in water while a phase and (3phase after furnace-cooled. TiB precipitated in TACFB alloy under different conditions and it could refine ingot microstructure of alloys. The grain size of alloys increased with increasing holding time and heating temperature when the alloys were heat treated above transus temperature and then air cooled. β phase and primary a were observed when the alloys heated below transus temperature, and primary a transformed to β gradually with temperature increasing.
The amounts of alloying elements, cooling methods, heating temperature and holding time have certain effect on tensile properties of alloys. Because of ω phase, TCF and TACF alloys obtained the highest strength when they were water quenched; TACF1, TACFB, TACF2and TACF3alloys obtained the highest strength when they were air cooled, with the highest tensile strength is1260MPa of TACF3alloy. The strength of TACF, TACF2, TACFB and TACF3alloys changed a little with increasing holding time when they were heat treated above transus temperature. The strength of all of six alloys changed a little with increasing heating temperature. The strength of TACF2and TACF3alloys decreased gradually with increasing time and temperature during direct aging, and TACF3alloy directly aged at525℃for8hours obtained the highest strength; with tensile strength and elongation are1415MPa and7.0%respectively.
Strain rates and deformation temperature have a significant influence on true stress-true strain curves for TACF1and TACFB alloys. At the initial stage of hot compression, true stress increased rapidly with increasing true strain, and then decreased after reaching the peak value, and finally reached a constant value. It was found that true stress increased with increasing true strain at different temperature, and decreased with increasing deformation temperature at different strain rates.Constitutive equations were established for TACF1and TACFB alloys based on Arrhenius constitutive equation. When deformed under the same condition, TACF1alloy required less activation energy than TACFB alloy. From the processing map of TACF1and TACFB alloys at the strain of0.7, it could be concluded that TACF1alloy can be processed at various strain rates from900℃to950℃, and TACFB alloy can be processed at every field except at strain rate of1.0s-1from870℃to940℃. The trend of dynamic recrystallization became more and more obviously with increasing deformation temperature and strain rates, and fine recrystallized grains deformed at the intersection of grains and grain boundary. In these experiments, the dynamic recrystallization was incomplete.
本文对各合金在不同热处理条件下的相组成及组织演变进行研究,结果表明：在Tβ+20℃下进行加热保温0.5h,TCF、TACF、TACF1、TACFB和TACF2合金空冷和炉冷后组织由α相和β相组成；水淬后组织由p相和马氏体相组成,且在TCF和TACF合金的组织中还有ω相。TACF3合金在水淬和空冷后的组织内含有β相、ω相和马氏体相存在；合金在炉冷后的组织由α相和β相组成。在TACFB合金组织中有TiB相存在,TiB相可抑制晶粒长大。在相变点以上进行热处理后,合金晶粒随保温时间和加热温度增加而增大。在相变点以下进行热处理后,合金组织由β相和初生α相组成,随温度升高,组织内初生α相逐渐减少并转变成β相。合金在单相区固溶后再时效的组织除含有α相和β相外,还有TiFe2相；在两相区固溶后再时效与直接时效后的组织均由α相和β相组成。
本文对合金元素含量、冷却方式、加热温度和加热时间等对合金力学性能的影响研究结果表明：不同冷却方式下,由于水淬后TCF和TACF合金中含有ω相,致使水淬后强度最高,但塑性最差；TACF1、TACFB、TACF2和TACF3合金空冷后强度最高,其中TACF3合金空冷后抗拉强度为1260MPa,水淬后弹性模量最低为73.0GPa。在相变点以上进行加热处理,热处理温度和加热时间对合金强度影响不大。
在单相区固溶后再时效的组织内包含有TiFe2相,该相使塑性显著降低,甚至完全脆化。合金在两相区固溶后再时效后的强度和塑性与单相区固溶后再时效相比均有所提高,TACF2合金经860℃/1.0h/WQ+525℃/8.0h/AC热处理后抗拉强度和延伸率分别为1359MPa和4.5%,与单相区固溶后再时效相比分别提高了118MPa和4.0%,延伸率最高可提高19.0%。合金经过退火热处理后,随Cr和Fe元素含量增加,合金强度逐渐增加。随直接时效温度和时间增加,合金强度逐渐降低,TACF3合金在525℃/8.0h/AC时效后强度最高,抗拉强度为1415MPa,延伸率为7.0%。
该系列合金(TACF1和TACFB)是对应变速率和变形温度比较敏感的合金。在不同温度下,随应变速率增加,合金真应力逐渐增大；在不同应变速率下,随形变温度升高,合金真应力逐渐降低。通过Arrhenius双曲正弦本构方程建立TACF1和TACFB合金本构方程,在同等条件下变形,TACF1合金需要激活能比TACFB合金要低,说明TACF1合金高温变形比TACFB合金要容易。在TACF1和TACFB合金变形量为0.7时的加工图中可知,在本实验条件下TACF1合金可加工区域为900℃和950℃下的各应变速率；TACFB合金不可加工区域为870～940℃、应变速为1.0s-1的区域,其余区域均为可加工区域。虽然TACF1合金比TACFB合金变形要容易,但是TACFB合金的加工性更好。随形变温度和应变速率增加,合金组织内岀现动态再结晶的趋势越来越明显,细小的动态再结晶晶粒位于变形晶粒的交叉点和晶界上，所发生的动态再结晶均为不完全动态再结晶。
In this paper, new type of low cost TiAlCrFe alloys were designed and melted by using bargain Cr-Fe alloy as master alloy. The costs of raw materials for these new alloys are three-quarters to eighty percent of TC4. Observation and analysis of the microstructure of alloys under different heat treatment conditions were done by employing OM, SEM, TEM, and XRD. The effects of cooling ways, heating temperature and holding time on mechanical properties of alloys were discussed. Thermal simulation experiments were carried out for some well-selected alloys to explore the processing technology during hot working. The main results are as follows:
Cooling methods, heating temperature and holding time all have certain effect on the microstructure of alloys. The microstructure consists of a phase and β phase when TCF, TACF, TACF1, TACFB and TACF2alloys were heat treated at Tp+20℃and then cooled by air cooling or furnace cooling; β and a martensite when they were heat treated at Tp+20℃and then water quenched except that co also observed in TCF and TACF alloys,β phase,ω phase and a martensite were observed in TACF3alloy after air cooling or quenching in water while a phase and (3phase after furnace-cooled. TiB precipitated in TACFB alloy under different conditions and it could refine ingot microstructure of alloys. The grain size of alloys increased with increasing holding time and heating temperature when the alloys were heat treated above transus temperature and then air cooled. β phase and primary a were observed when the alloys heated below transus temperature, and primary a transformed to β gradually with temperature increasing.
The amounts of alloying elements, cooling methods, heating temperature and holding time have certain effect on tensile properties of alloys. Because of ω phase, TCF and TACF alloys obtained the highest strength when they were water quenched; TACF1, TACFB, TACF2and TACF3alloys obtained the highest strength when they were air cooled, with the highest tensile strength is1260MPa of TACF3alloy. The strength of TACF, TACF2, TACFB and TACF3alloys changed a little with increasing holding time when they were heat treated above transus temperature. The strength of all of six alloys changed a little with increasing heating temperature. The strength of TACF2and TACF3alloys decreased gradually with increasing time and temperature during direct aging, and TACF3alloy directly aged at525℃for8hours obtained the highest strength; with tensile strength and elongation are1415MPa and7.0%respectively.
Strain rates and deformation temperature have a significant influence on true stress-true strain curves for TACF1and TACFB alloys. At the initial stage of hot compression, true stress increased rapidly with increasing true strain, and then decreased after reaching the peak value, and finally reached a constant value. It was found that true stress increased with increasing true strain at different temperature, and decreased with increasing deformation temperature at different strain rates.Constitutive equations were established for TACF1and TACFB alloys based on Arrhenius constitutive equation. When deformed under the same condition, TACF1alloy required less activation energy than TACFB alloy. From the processing map of TACF1and TACFB alloys at the strain of0.7, it could be concluded that TACF1alloy can be processed at various strain rates from900℃to950℃, and TACFB alloy can be processed at every field except at strain rate of1.0s-1from870℃to940℃. The trend of dynamic recrystallization became more and more obviously with increasing deformation temperature and strain rates, and fine recrystallized grains deformed at the intersection of grains and grain boundary. In these experiments, the dynamic recrystallization was incomplete.
引文
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