2E12-Zr铝合金的热处理与微观组织及力学性能研究
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摘要
本论文研究了热处理制度对2E12+Zr合金微观组织和性能的影响。通过拉伸性能和疲劳性能测试,利用金相显微镜、透射电镜(TEM)、以及扫描电镜(SEM)观察,得到的主要结论如下:
(1)通过DTA实验,确定合金的过烧温度是503℃。通过SEM观察发现,难溶相主要是AlCu,AlCuMn及AlCuMg粒子。2E12+Zr合金经500℃×40min固溶处理后的抗拉强度、屈服强度及延伸率等达到最佳。
(2)自然时效后,GPB区是合金的主要强化相。T3状态比T4状态具有更高的屈服强度和抗拉强度,而延伸率略有下降。这是由于预变形增加位错,促进GPB区析出的结果。
(3)人工时效后,S'相是合金的主要强化相。T6状态在10h达到峰值,T8状态的峰值时间提前2h,拉伸强度和屈服强度比T6工艺均提高40MPa左右,延伸率降低6个百分点。预变形导致合金中位错密度增高,为S'相形核提供了更多位置,从而促进S'相析出,提高合金强度。
(4)与2E12合金相比,2E12+Zr合金自然时效后,合金的抗拉强度下降了约20～30MPa,屈服强度下降不多,而伸长率提高了4个百分点;人工时效至峰值时,合金的抗拉强度值较2E12合金的强度下降了约40～50MPa,屈服强度下降了约10～30MPa,而伸长率提高了2～5个百分点。这是因为微量Zr的添加,降低了GPB区的形成,减少了亚稳相S'相的析出数量,降低了时效硬化效果。
(5)在应力比R=0.5时,2E12+Zr合金T3状态具有较好的耐损伤疲劳性能,在10~6循环周次下的疲劳强度σ_(max)=280Mpa,高于T4状态σ_(max)=270Mpa。缺口的存在降低了疲劳极限,Kt=3时的疲劳强度不及Kt=1时的一半。
(6)T3和T4两种自然时效状态下,2E12+Zr合金L-T方向的疲劳裂纹扩展可分三个阶段,当R=0.5时,△K在5.5Mpa×m~(1/2)以下时,为裂纹扩展第Ⅰ阶段;△K在5.5Mpa×m~(1/2)～18Mpa×m~(1/2)之间时,为裂纹扩展第Ⅱ阶段;当△K大于18Mpa×m~(1/2)后,为裂纹扩展的第Ⅲ阶段。T3工艺在前两个阶段的曲线比较平缓,且进入瞬间断裂阶段较缓慢,而T4工艺在前两个阶段的曲线倾斜较大,且迅速进入瞬断阶段。
(7)2E12+Zr合金T3状态,R=0.5时的裂纹扩展速率曲线明显位于R=0.1曲线之上,R=0.5时,合金的疲劳裂纹扩展速度更快。R=0.1时,疲劳裂纹扩展的三个阶段分别在△K＜7.3Mpa×m~(1/2)时,为裂纹扩展第Ⅰ阶段;△K在7.3Mpa×m~(1/2)～30Mpa×m~(1/2)之间,为裂纹扩展第Ⅱ阶段;当△K=30Mpa×m~(1/2)时,da/dN为3.2×10~(-3)mm/cycle,△K＞30Mpa×m~(1/2)为裂纹扩展的第Ⅲ阶段。
(8)T3状态,2E12+Zr合金R=0.5和R=0.1时,L-T方向的疲劳裂纹扩展速率都略低于T-L方向,但相差并不大,并且到裂纹扩展后期这种差别进一步缩小。
(9)T3状态,R=0.5和R=0.1时,2E12+Zr合金的裂纹扩展速率在疲劳裂纹的初始阶段快于2E12合金,随着△K的不断增大,两种合金的疲劳裂纹扩展速率的差别也不断减小。
(10)2E12+Zr合金疲劳断口由裂纹源区、裂纹扩展区及瞬断区三部分组成,裂纹萌生一般位于试样表面应力集中处或典型缺陷部位,呈现“鱼骨形”小刻面。裂纹扩展区有明显疲劳辉纹特征,并伴随部分二次裂纹。瞬断区呈现静拉伸断口特征,韧窝多呈现盘形或拉长形。
Effects of heat treatment and microstructures on properties of 2E12+Zr alloy were studied in this paper,including fatigue properties testing and tensile properties testing,Optical microscopy(OM), Transmission electron microscopy(TEM)and Scanning electron microscopy(SEM)observations.The main conclusions are as following:
(1)DTA test were carried out,the overburnt temperature is 503℃.With the SEM obvervations,the insoluble paritles were AlCu, AlCuMn and AlCuMg paticle.The results showed that 2E12+Zr alloy had better tensile properties after 500℃×40min solution treatment.
(2)GPB zone was the comstituent phase after 96h natural aging of 2E12+Zr alloy.The alloy at T3 condition had better strength and lower elongation than T4 condition,because the pre-deformation induced higher dislocation density,promoted the precipitation of GPB zone.
(3)S' phase was the comstituent phase after 190℃artificial aging of 2E12+Zr alloy.At T6 condition 10h the strength arrived at the peak value, at T8 condition was 2h earlier.The Tensile strength and Yield strength at T8 condition increased 40MPa,the elongation decreased 6 percent.The results was that the pre-deformation induced higher dislocation density, promoted the precipitation of S' phase,increased strength of the alloy.
(4)After 96h natural aging,the Tensile strength of 2E12+Zr alloy decreased 20～30MPa,Yield strength was invariant,the elongation increased 4 percent;After 190℃artificial aging,the Tensile strength of 2E12+Zr alloy decreased 40～50MPa,Yield strength decreased 10～30 MPa,the elongation increased 2～5 percent.The results was that the addition of micro Zr reduced the formation of GPB zone,decreased the precipitation of the S' phase,reduced the effect of age harding.
(5)When stress ratio R=0.5,with the same level cycles,the fatigue strength at T3 condition is higher than that at T4 condition,such as the cyclic fatigue strength(σ_(max))at 10~6 cycles is 10MPa higher than that at T4 condition.These notches resulted in reduction of fatigue limit of this alloy.When Kt=3,the fatigue limit is short half of the Kt=1.
(6)The fatigue crack growth of 2E12+Zr alloy contained three stages in L-T direction at T3 and T4 condition.On the condition of R=0.5, AK＜5.5Mpa×m~(1/2),it was the first stage;when△K was between 5.5Mpa×m~(1/2)and 18Mpa×m~(1/2),it was at the second stage;when△K＞18Mpa×m~(1/2),it was at the last stage.With the same level of stress intensity factor△K,the fatigue crack propagation rate(da/dN)at T3 condition is slower than that at T4 condition.
(7)At the T3 condition,with the same level of stress intensity factor△K,the fatigue crack propagation rate(da/dN)on the condition of R=0.1 is slower than that on the condition of R=0.5.When R =0.1, AK＜7.3Mpa×m~(1/2),it was the first stage;when△K was between 7.3Mpa×m~(1/2)and 30Mpa×m~(1/2),it was at the second stage;when△K=30Mpa×m~(1/2),da/dN=3.2×10~(-3)mm/cycle;when△K＞30Mpa×m~(1/2),it was at the last stage.
(8)At the T3 condition,when R=0.5 and R=0.1,with the same level of stress intensity factor△K,the fatigue crack propagation rate(da/dN) on the condition of L-T direction is slower than that on the condition of L-T direction,and the diffenerce was small;at the last stage,the diffenerce turned smaller.
(9)R=0.landR=0.5,with the same level of stress intensity factor△K, the fatigue crack propagation rate(da/dN)of the 2E12 alloy is slower than that of 2E12+Zr alloy until△K=19Mpa×m~(1/2)in the initial stage.As the stress intensity factor△K increased,the diffenerce turned small.
(10)The fracture appearance of 2E12+Zr alloy consisted of fatigue crack intiation zone,fatigue crack zone and final fracture zone.The locations of initial fatigue cracks generally were on the surface stress concentrated or on the different defects in alloy,the appearance of facets had fishbone-like.It was obvious to see fatigue stripe in fatigue crack zone and some secondary cracks.It was just like tensile fracture appearance in the final fracture zone with circular dimples and elongated dimples.
(1)通过DTA实验,确定合金的过烧温度是503℃。通过SEM观察发现,难溶相主要是AlCu,AlCuMn及AlCuMg粒子。2E12+Zr合金经500℃×40min固溶处理后的抗拉强度、屈服强度及延伸率等达到最佳。
(2)自然时效后,GPB区是合金的主要强化相。T3状态比T4状态具有更高的屈服强度和抗拉强度,而延伸率略有下降。这是由于预变形增加位错,促进GPB区析出的结果。
(3)人工时效后,S'相是合金的主要强化相。T6状态在10h达到峰值,T8状态的峰值时间提前2h,拉伸强度和屈服强度比T6工艺均提高40MPa左右,延伸率降低6个百分点。预变形导致合金中位错密度增高,为S'相形核提供了更多位置,从而促进S'相析出,提高合金强度。
(4)与2E12合金相比,2E12+Zr合金自然时效后,合金的抗拉强度下降了约20～30MPa,屈服强度下降不多,而伸长率提高了4个百分点;人工时效至峰值时,合金的抗拉强度值较2E12合金的强度下降了约40～50MPa,屈服强度下降了约10～30MPa,而伸长率提高了2～5个百分点。这是因为微量Zr的添加,降低了GPB区的形成,减少了亚稳相S'相的析出数量,降低了时效硬化效果。
(5)在应力比R=0.5时,2E12+Zr合金T3状态具有较好的耐损伤疲劳性能,在10~6循环周次下的疲劳强度σ_(max)=280Mpa,高于T4状态σ_(max)=270Mpa。缺口的存在降低了疲劳极限,Kt=3时的疲劳强度不及Kt=1时的一半。
(6)T3和T4两种自然时效状态下,2E12+Zr合金L-T方向的疲劳裂纹扩展可分三个阶段,当R=0.5时,△K在5.5Mpa×m~(1/2)以下时,为裂纹扩展第Ⅰ阶段;△K在5.5Mpa×m~(1/2)～18Mpa×m~(1/2)之间时,为裂纹扩展第Ⅱ阶段;当△K大于18Mpa×m~(1/2)后,为裂纹扩展的第Ⅲ阶段。T3工艺在前两个阶段的曲线比较平缓,且进入瞬间断裂阶段较缓慢,而T4工艺在前两个阶段的曲线倾斜较大,且迅速进入瞬断阶段。
(7)2E12+Zr合金T3状态,R=0.5时的裂纹扩展速率曲线明显位于R=0.1曲线之上,R=0.5时,合金的疲劳裂纹扩展速度更快。R=0.1时,疲劳裂纹扩展的三个阶段分别在△K＜7.3Mpa×m~(1/2)时,为裂纹扩展第Ⅰ阶段;△K在7.3Mpa×m~(1/2)～30Mpa×m~(1/2)之间,为裂纹扩展第Ⅱ阶段;当△K=30Mpa×m~(1/2)时,da/dN为3.2×10~(-3)mm/cycle,△K＞30Mpa×m~(1/2)为裂纹扩展的第Ⅲ阶段。
(8)T3状态,2E12+Zr合金R=0.5和R=0.1时,L-T方向的疲劳裂纹扩展速率都略低于T-L方向,但相差并不大,并且到裂纹扩展后期这种差别进一步缩小。
(9)T3状态,R=0.5和R=0.1时,2E12+Zr合金的裂纹扩展速率在疲劳裂纹的初始阶段快于2E12合金,随着△K的不断增大,两种合金的疲劳裂纹扩展速率的差别也不断减小。
(10)2E12+Zr合金疲劳断口由裂纹源区、裂纹扩展区及瞬断区三部分组成,裂纹萌生一般位于试样表面应力集中处或典型缺陷部位,呈现“鱼骨形”小刻面。裂纹扩展区有明显疲劳辉纹特征,并伴随部分二次裂纹。瞬断区呈现静拉伸断口特征,韧窝多呈现盘形或拉长形。
Effects of heat treatment and microstructures on properties of 2E12+Zr alloy were studied in this paper,including fatigue properties testing and tensile properties testing,Optical microscopy(OM), Transmission electron microscopy(TEM)and Scanning electron microscopy(SEM)observations.The main conclusions are as following:
(1)DTA test were carried out,the overburnt temperature is 503℃.With the SEM obvervations,the insoluble paritles were AlCu, AlCuMn and AlCuMg paticle.The results showed that 2E12+Zr alloy had better tensile properties after 500℃×40min solution treatment.
(2)GPB zone was the comstituent phase after 96h natural aging of 2E12+Zr alloy.The alloy at T3 condition had better strength and lower elongation than T4 condition,because the pre-deformation induced higher dislocation density,promoted the precipitation of GPB zone.
(3)S' phase was the comstituent phase after 190℃artificial aging of 2E12+Zr alloy.At T6 condition 10h the strength arrived at the peak value, at T8 condition was 2h earlier.The Tensile strength and Yield strength at T8 condition increased 40MPa,the elongation decreased 6 percent.The results was that the pre-deformation induced higher dislocation density, promoted the precipitation of S' phase,increased strength of the alloy.
(4)After 96h natural aging,the Tensile strength of 2E12+Zr alloy decreased 20～30MPa,Yield strength was invariant,the elongation increased 4 percent;After 190℃artificial aging,the Tensile strength of 2E12+Zr alloy decreased 40～50MPa,Yield strength decreased 10～30 MPa,the elongation increased 2～5 percent.The results was that the addition of micro Zr reduced the formation of GPB zone,decreased the precipitation of the S' phase,reduced the effect of age harding.
(5)When stress ratio R=0.5,with the same level cycles,the fatigue strength at T3 condition is higher than that at T4 condition,such as the cyclic fatigue strength(σ_(max))at 10~6 cycles is 10MPa higher than that at T4 condition.These notches resulted in reduction of fatigue limit of this alloy.When Kt=3,the fatigue limit is short half of the Kt=1.
(6)The fatigue crack growth of 2E12+Zr alloy contained three stages in L-T direction at T3 and T4 condition.On the condition of R=0.5, AK＜5.5Mpa×m~(1/2),it was the first stage;when△K was between 5.5Mpa×m~(1/2)and 18Mpa×m~(1/2),it was at the second stage;when△K＞18Mpa×m~(1/2),it was at the last stage.With the same level of stress intensity factor△K,the fatigue crack propagation rate(da/dN)at T3 condition is slower than that at T4 condition.
(7)At the T3 condition,with the same level of stress intensity factor△K,the fatigue crack propagation rate(da/dN)on the condition of R=0.1 is slower than that on the condition of R=0.5.When R =0.1, AK＜7.3Mpa×m~(1/2),it was the first stage;when△K was between 7.3Mpa×m~(1/2)and 30Mpa×m~(1/2),it was at the second stage;when△K=30Mpa×m~(1/2),da/dN=3.2×10~(-3)mm/cycle;when△K＞30Mpa×m~(1/2),it was at the last stage.
(8)At the T3 condition,when R=0.5 and R=0.1,with the same level of stress intensity factor△K,the fatigue crack propagation rate(da/dN) on the condition of L-T direction is slower than that on the condition of L-T direction,and the diffenerce was small;at the last stage,the diffenerce turned smaller.
(9)R=0.landR=0.5,with the same level of stress intensity factor△K, the fatigue crack propagation rate(da/dN)of the 2E12 alloy is slower than that of 2E12+Zr alloy until△K=19Mpa×m~(1/2)in the initial stage.As the stress intensity factor△K increased,the diffenerce turned small.
(10)The fracture appearance of 2E12+Zr alloy consisted of fatigue crack intiation zone,fatigue crack zone and final fracture zone.The locations of initial fatigue cracks generally were on the surface stress concentrated or on the different defects in alloy,the appearance of facets had fishbone-like.It was obvious to see fatigue stripe in fatigue crack zone and some secondary cracks.It was just like tensile fracture appearance in the final fracture zone with circular dimples and elongated dimples.
引文
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