Sc、Sb对Mg-Gd-Y合金组织和性能的影响
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摘要
镁合金较低的高温力学性能严重限制了其广泛应用。本文以Mg-Gd-Y基合金为基础,利用光学显微镜(OM)、X-射线衍射仪(XRD)、带能谱分析(EDS)的扫描电子显微镜(SEM)、透射电子显微镜(TEM)、差动分析仪(DSC)、拉伸实验等检测分析技术,研究Sc、Sb元素对Mg-7Gd-3Y基合金组织和力学性能的影响。
对合金铸态组织研究结果表明:Mg-7Gd-3Y-xSc(x=0,0.5,1)合金的铸态显微组织由等轴α-Mg和主要沿晶界分布的半连续析出相组成;合金组成相为а-Mg、Mg24(Y,Gd)5和Mg5(Gd,Y),在合金中添加Sc后没有生成新相,但合金中的析出相含量有着明显的增多,并在晶界处聚集长大;SEM分析结果表明:Mg-7Gd-3Y-0.5%Sc合金析出相中均含有一定量的Sc,其中,Sc在Mg24(Y,Gd)5相中的含量远大于Sc在Mg5(Gd,Y)相中的含量。在Mg-7Gd-3Y合金加入Sc能提高铸态合金的室温和200℃的抗拉强度和屈服强度,Mg-7Gd-3Y-1Sc合金的室温抗拉强度和屈服强度分别达到了240和180MPa,200℃时的抗拉强度和屈服强度分别为215和149Mpa。在Mg-7Gd-3Y合金中加入Sc会提高析出相熔点和合金的熔化温度;DSC分析表明:低熔点共晶相的溶解温度从411.6℃提高到431.1℃;Mg5(Gd,Y)相向а-Mg中的溶解温度从553.1℃提高到554.1℃,合金的最终熔化温度也从637.5℃提高到639.0℃。
合金的固溶处理结果表明:在525℃进行固溶时发现,合金Mg-7Gd-3Y固溶处理10h后枝晶结构基本消除,但在晶内及晶界上仍有部分未溶解的富RE相,随着时间的延长,这些富RE相会逐渐变小,但很难完全溶解;随着Sc的加入,合金在固溶处理时,未溶解的富RE相明显增多;在540℃进行固溶处理时,Mg-7Gd-3Y-0.5Sc和Mg-7Gd-3Y-1%Sc两种合金的晶粒大小随固溶时间的延长发生了异常变化现象,表现为固溶处理的前2-8h晶粒由大变小,随后晶粒由小变大,这一变化与合金的固溶硬度曲线分析结果一致。Mg-7Gd-3Y-xSc在525℃/10h固溶处理后进行的时效(225℃)处理表明:在时效过程中,合金基体中会有大量的析出相析出,随着时间的延长,析出相的含量也相应地增加,合金中的时效析出相会优先在未固溶相和晶界处析出;而随着Sc含量的增加,这种优先析出倾向更加明显;在合金中添加Sc能够提高提高合金的时效峰值硬度及合金的室温和200℃力学性能; Mg-7Gd-3Y-1Sc合金的时效峰值时的室温抗拉强度和屈服强度分别为254MPa和185MPa,200℃时的抗拉强度和屈服强度分别为228MPa和159Mpa;TEM分析结果表明,合金在时效过程中析出相的长条状Mg24(Y,Gd)5相和颗粒状的Mg5(Gd,Y)相是合金力学性能的到提高的原因。
与金属型铸造对比,挤压铸造获得的组织均匀,且晶粒更加细小。在Mg-7Gd-3Y合金中加入Sb后,合金的晶粒得到了细化,析出相的明显增多并在晶界三角处聚集长大;Mg-7Gd-3Y-xSb(x=0,1)合金合金在525℃固溶处理结果表明:在固溶处理开始后,晶间网状共晶相快速地重新融入基体,取而代之的是在其原来的位置上形成的弥散的点状颗粒相;当固溶时间达到10h,晶间组织完全溶解到基体中,颗粒状析出相变少或消失且合金晶粒都发生了一定的晶粒粗化;在Mg-7Gd-3Y合金中加入Sb后,晶粒的粗化现象降低。在Mg-7Gd-3Y合金中加入Sb能提高合金的室温及200℃的抗拉强度和屈服强度; Mg-7Gd-3Y-1Sb合金时效时效峰值时的室温抗拉强度和屈服强度分别为260MPa和194MPa,200℃时的抗拉强度和屈服强度也达到了244MPa和181MPa。
The poor mechanical properties of magnesium alloys at high temperatures severely limit their applications. In this paper, Sc and Sb elements were introduced into the existing Mg-Gd-Y system alloys to further improve their microstructures and mechanical properties both at room temperatures and elevated temperatures. Optical microscopy (OM), X-ray diffraction(XRD), scanning electron microscopy(SEM), transition electron microscopy(TEM), differential scanning calorimeter(DSC)and tensile test were used to study the microstructures, mechanical properties, fracture behavior, plastic deformation behavior and processing parameters of the Mg-Gd-Y based alloys with different compositions.
The results indicate that the as-cast microstructure of Mg-7Gd-3Y-xSc(x=0,0.5,1) are mainly composed of a lot of semi-continuous network grain eutectics and granular phase ofα-Mg, and the eutectics were made up of Mg5(Gd,Y) and Mg24(Y,Gd)5. With increasing Sc content, the volume fraction of intermetallic phases increased. The SEM result show that all precipitates of Mg-7Gd-Y-0.5Sc alloy contained some Sc, and the Sc content in Mg24(Y,Gd)5 phase was more than its in Mg5(Gd,Y) phase. With increasing Sc content, the tensile properties of the die cast alloys increased. The Mg-7Gd-3Y-0.5Sc alloy exhibited maximum tensile strength and yield strength, and the values were 240MPa and 180MPa at room temperature, and 215MPa and 149MPa at 250℃, respectively. The results of DSC show that the addition of Sc to Mg-7Gd-3Y alloys could improve the solution point of precipitates and the melting temperature of alloys. The solution point of low melting eutectic phase enhanced from 411.6℃to 431.1℃with Sc additions, the solution temperature of Mg5(Gd,Y) intoα-Mg added from 553.1℃to 554.1℃, and the melting point changed from 637.5℃to 639℃.
The result of solution treatmen shows that the dendrite branches of Mg-7Gd-3Y solid solution disappeared after the solution treatmen at 525℃/10h, and the rich RE precipitations became smaller, but hardly cannot disappeared completely, and with the Sc increased, there were more rich RE precipitations retained. The grain size of Mg-7Gd-3Y-0.5Sc and Mg-7Gd-3Y-1Sc behaved abnormally during solution treatments at 540℃. The gain size evolved from large to small during the beginning 2-8 hours and then to the coarse, and the abnormal behavior was in consistent with the outcome of the solution hardness curve.The aging treatment (225℃) after the solution treatmen at 525℃/10h results show that, during the aging process, a large number of precipitates precipitated with the time increased, and the precipitates were mainly distrubted along the gain boundaries and non-solution phase. And with Sc increased, the behavior became more obviously. With increasing Sc content, the age hardening response of the alloys enhanced, tensile properties increased. The Mg–7Gd–3Y-1Sc alloy exhibited maximum tensile strength and yield strength at aged-peak hardness, and the values were 254MPa and 185MPa at room temperature, and 228MPa and 159MPa at 200℃, respectively.
The strong peak age hardening was attributed to the precipitation of the Mg24(Gd,Y)5 and Mg5(Gd,Y). The microstructure of Mg-7Gd-3Y alloys were more regularity and the gains were more fine by the squeeze casting through the contrast experiment of the metal mould casting. The solution treatmen result of Mg-7Gd-3Y-xSb(x=0,1) shows that the continuous network grain boundaries disappeared quikly during the solution treatmen process, and a lot of disperse particle phases remain. After 10h solution treatmen, the grain boundaries disappeared compeletely, and the particle phases became smaller or diappeared, and the grain size coarsened, and with the additions of Sb, the coarsening behavior of Mg-7Gd-3Y weakened. The results show that the addition of Sb to the Mg–7Gd-3Y alloy could reduce the grain size slightly, and increase precipitations along the triangular gain boundry. The Mg-7Gd-3Y-1Sb alloy exhibited notably age-hardening behaviour and the higher mechanical property than that of Mg-7Gd-3Y alloy. The ultimate tensile strength and yield strength of Mg–7Gd–3Y-1Sb alloy in the peak aged hardness are 260 MPa and 194MPa at room temperature, and 244 MPa and 181MPa at 200℃.
对合金铸态组织研究结果表明:Mg-7Gd-3Y-xSc(x=0,0.5,1)合金的铸态显微组织由等轴α-Mg和主要沿晶界分布的半连续析出相组成;合金组成相为а-Mg、Mg24(Y,Gd)5和Mg5(Gd,Y),在合金中添加Sc后没有生成新相,但合金中的析出相含量有着明显的增多,并在晶界处聚集长大;SEM分析结果表明:Mg-7Gd-3Y-0.5%Sc合金析出相中均含有一定量的Sc,其中,Sc在Mg24(Y,Gd)5相中的含量远大于Sc在Mg5(Gd,Y)相中的含量。在Mg-7Gd-3Y合金加入Sc能提高铸态合金的室温和200℃的抗拉强度和屈服强度,Mg-7Gd-3Y-1Sc合金的室温抗拉强度和屈服强度分别达到了240和180MPa,200℃时的抗拉强度和屈服强度分别为215和149Mpa。在Mg-7Gd-3Y合金中加入Sc会提高析出相熔点和合金的熔化温度;DSC分析表明:低熔点共晶相的溶解温度从411.6℃提高到431.1℃;Mg5(Gd,Y)相向а-Mg中的溶解温度从553.1℃提高到554.1℃,合金的最终熔化温度也从637.5℃提高到639.0℃。
合金的固溶处理结果表明:在525℃进行固溶时发现,合金Mg-7Gd-3Y固溶处理10h后枝晶结构基本消除,但在晶内及晶界上仍有部分未溶解的富RE相,随着时间的延长,这些富RE相会逐渐变小,但很难完全溶解;随着Sc的加入,合金在固溶处理时,未溶解的富RE相明显增多;在540℃进行固溶处理时,Mg-7Gd-3Y-0.5Sc和Mg-7Gd-3Y-1%Sc两种合金的晶粒大小随固溶时间的延长发生了异常变化现象,表现为固溶处理的前2-8h晶粒由大变小,随后晶粒由小变大,这一变化与合金的固溶硬度曲线分析结果一致。Mg-7Gd-3Y-xSc在525℃/10h固溶处理后进行的时效(225℃)处理表明:在时效过程中,合金基体中会有大量的析出相析出,随着时间的延长,析出相的含量也相应地增加,合金中的时效析出相会优先在未固溶相和晶界处析出;而随着Sc含量的增加,这种优先析出倾向更加明显;在合金中添加Sc能够提高提高合金的时效峰值硬度及合金的室温和200℃力学性能; Mg-7Gd-3Y-1Sc合金的时效峰值时的室温抗拉强度和屈服强度分别为254MPa和185MPa,200℃时的抗拉强度和屈服强度分别为228MPa和159Mpa;TEM分析结果表明,合金在时效过程中析出相的长条状Mg24(Y,Gd)5相和颗粒状的Mg5(Gd,Y)相是合金力学性能的到提高的原因。
与金属型铸造对比,挤压铸造获得的组织均匀,且晶粒更加细小。在Mg-7Gd-3Y合金中加入Sb后,合金的晶粒得到了细化,析出相的明显增多并在晶界三角处聚集长大;Mg-7Gd-3Y-xSb(x=0,1)合金合金在525℃固溶处理结果表明:在固溶处理开始后,晶间网状共晶相快速地重新融入基体,取而代之的是在其原来的位置上形成的弥散的点状颗粒相;当固溶时间达到10h,晶间组织完全溶解到基体中,颗粒状析出相变少或消失且合金晶粒都发生了一定的晶粒粗化;在Mg-7Gd-3Y合金中加入Sb后,晶粒的粗化现象降低。在Mg-7Gd-3Y合金中加入Sb能提高合金的室温及200℃的抗拉强度和屈服强度; Mg-7Gd-3Y-1Sb合金时效时效峰值时的室温抗拉强度和屈服强度分别为260MPa和194MPa,200℃时的抗拉强度和屈服强度也达到了244MPa和181MPa。
The poor mechanical properties of magnesium alloys at high temperatures severely limit their applications. In this paper, Sc and Sb elements were introduced into the existing Mg-Gd-Y system alloys to further improve their microstructures and mechanical properties both at room temperatures and elevated temperatures. Optical microscopy (OM), X-ray diffraction(XRD), scanning electron microscopy(SEM), transition electron microscopy(TEM), differential scanning calorimeter(DSC)and tensile test were used to study the microstructures, mechanical properties, fracture behavior, plastic deformation behavior and processing parameters of the Mg-Gd-Y based alloys with different compositions.
The results indicate that the as-cast microstructure of Mg-7Gd-3Y-xSc(x=0,0.5,1) are mainly composed of a lot of semi-continuous network grain eutectics and granular phase ofα-Mg, and the eutectics were made up of Mg5(Gd,Y) and Mg24(Y,Gd)5. With increasing Sc content, the volume fraction of intermetallic phases increased. The SEM result show that all precipitates of Mg-7Gd-Y-0.5Sc alloy contained some Sc, and the Sc content in Mg24(Y,Gd)5 phase was more than its in Mg5(Gd,Y) phase. With increasing Sc content, the tensile properties of the die cast alloys increased. The Mg-7Gd-3Y-0.5Sc alloy exhibited maximum tensile strength and yield strength, and the values were 240MPa and 180MPa at room temperature, and 215MPa and 149MPa at 250℃, respectively. The results of DSC show that the addition of Sc to Mg-7Gd-3Y alloys could improve the solution point of precipitates and the melting temperature of alloys. The solution point of low melting eutectic phase enhanced from 411.6℃to 431.1℃with Sc additions, the solution temperature of Mg5(Gd,Y) intoα-Mg added from 553.1℃to 554.1℃, and the melting point changed from 637.5℃to 639℃.
The result of solution treatmen shows that the dendrite branches of Mg-7Gd-3Y solid solution disappeared after the solution treatmen at 525℃/10h, and the rich RE precipitations became smaller, but hardly cannot disappeared completely, and with the Sc increased, there were more rich RE precipitations retained. The grain size of Mg-7Gd-3Y-0.5Sc and Mg-7Gd-3Y-1Sc behaved abnormally during solution treatments at 540℃. The gain size evolved from large to small during the beginning 2-8 hours and then to the coarse, and the abnormal behavior was in consistent with the outcome of the solution hardness curve.The aging treatment (225℃) after the solution treatmen at 525℃/10h results show that, during the aging process, a large number of precipitates precipitated with the time increased, and the precipitates were mainly distrubted along the gain boundaries and non-solution phase. And with Sc increased, the behavior became more obviously. With increasing Sc content, the age hardening response of the alloys enhanced, tensile properties increased. The Mg–7Gd–3Y-1Sc alloy exhibited maximum tensile strength and yield strength at aged-peak hardness, and the values were 254MPa and 185MPa at room temperature, and 228MPa and 159MPa at 200℃, respectively.
The strong peak age hardening was attributed to the precipitation of the Mg24(Gd,Y)5 and Mg5(Gd,Y). The microstructure of Mg-7Gd-3Y alloys were more regularity and the gains were more fine by the squeeze casting through the contrast experiment of the metal mould casting. The solution treatmen result of Mg-7Gd-3Y-xSb(x=0,1) shows that the continuous network grain boundaries disappeared quikly during the solution treatmen process, and a lot of disperse particle phases remain. After 10h solution treatmen, the grain boundaries disappeared compeletely, and the particle phases became smaller or diappeared, and the grain size coarsened, and with the additions of Sb, the coarsening behavior of Mg-7Gd-3Y weakened. The results show that the addition of Sb to the Mg–7Gd-3Y alloy could reduce the grain size slightly, and increase precipitations along the triangular gain boundry. The Mg-7Gd-3Y-1Sb alloy exhibited notably age-hardening behaviour and the higher mechanical property than that of Mg-7Gd-3Y alloy. The ultimate tensile strength and yield strength of Mg–7Gd–3Y-1Sb alloy in the peak aged hardness are 260 MPa and 194MPa at room temperature, and 244 MPa and 181MPa at 200℃.
引文
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