采用同步辐射小角X射线散射技术研究Al−Mg−Si合金的析出强化行为

研究Al−Mg−Si合金在等温时效过程中的析出强化行为及其对力学性能的影响。利用原位同步辐射小角X射线散射(SAXS)技术和透射电子显微镜(TEM)对纳米析出相及其结构参数(尺寸、体积分数和数密度)进行表征。结果表明,棒状β''析出相优先沿其纵向尺寸生长,但径向尺寸在时效5 h后达到峰值。如预测与测量的屈服强度和硬度结果所示,纳米析出相的尺寸和体积分数的增大与析出强化定量相关。SAXS为Ashby−Orowan模型提供了更可靠的输入参数,这有助于提高模型的预测精度和泛化能力。研究表明,随着时效时间的延长,Al−Mg−Si合金预测力学性能的演变与β''析出相的平均半径和体积分数有关。

Al−Mg−Mn−Er合金双面搅拌摩擦焊接头局部显微组织和强化机制

通过研究Al−Mg−Mn−Er合金双面搅拌摩擦焊接头的局部显微组织和强化机制揭示其软化机制。结果显示:焊核区形成细小等轴晶组织(5.61μm),而热机械影响区(45.32μm)和热影响区(100.73μm)仍为纤维状组织。从基体到焊核区,小角度晶界分数从75.6%降低到15.6%。退火效应导致位错密度从母材的1.8×10^(14)m^(−2)减小到焊核区的4.5×10^(12)m^(−2)。焊核区、热机械影响区和热影响区Al_(3)(Er,Zr)析出相的平均尺寸和体积分数与基体的(13.7 nm,0.13%)均接近。焊核区和热机械影响区的屈服强度最低,约为201 MPa;基体的屈服强度最高,约为295 MPa。位错强化和亚结构强化的损失是从基体到焊核区屈服强度降低的主要原因。

Finite element analysis of temperature and stress fields during selective laser melting process of Al−Mg−Sc−Zr alloy

A 3D finite element model was established to investigate the temperature and stress fields during the selective laser melting process of Al−Mg−Sc−Zr alloy.By considering the powder−solid transformation,temperaturedependent thermal properties,latent heat of phase transformations and molten pool convection,the effects of laser power,point distance and hatch spacing on the temperature distribution,molten pool dimensions and residual stress distribution were investigated.Then,the effects of laser power,point distance and hatch spacing on the microstructure,density and hardness of the alloy were studied by the experimental method.The results show that the molten pool size gradually increases as the laser power increases and the point distance and hatch spacing decrease.The residual stress mainly concentrates in the middle of the first scanning track and the beginning and end of each scanning track.Experimental results demonstrate the accuracy of the model.The density of the samples tends to increase and then decrease with increasing laser power and decreasing point distance and hatch spacing.The optimum process parameters are laser power of 325−375 W,point distance of 80−100μm and hatch spacing of 80μm.

Dynamic recrystallization,texture and mechanical properties of high Mg content Al−Mg alloy deformed by high strain rate rolling

The Al−Mg alloy with high Mg addition(Al−9.2Mg−0.8Mn−0.2Zr-0.15Ti,in wt.%)was subjected to different passes(1,2 and 4)of high strain rate rolling(HSRR),with the total thickness reduction of 72%,the rolling temperature of 400℃and strain rate of 8.6 s^(−1).The microstructure evolution was studied by optical microscope(OM),scanning electron microscope(SEM),electron backscattered diffraction(EBSD)and transmission electron microscope(TEM).The alloy that undergoes 2 passes of HSRR exhibits an obvious bimodal grain structure,in which the average grain sizes of the fine dynamic recrystallization(DRX)grains and the coarse non-DRX regions are 6.4 and 47.7mm,respectively.The high strength((507±9)MPa)and the large ductility((24.9±1.3)%)are obtained in the alloy containing the bimodal grain distribution.The discontinuous dynamic recrystallization(DDRX)mechanism is the prominent grain refinement mechanism in the alloy subjected to 2 passes of HSRR.

Effect of pre-straining on structure and formation mechanism of precipitates in Al−Mg−Si−Cu alloy

The effect of pre-straining on the structure and formation mechanism of precipitates in an Al−Mg−Si−Cu alloy was systematically investigated by atomic resolution high-angle annular dark-field scanning transmission electron microscopy(HAADF-STEM).Elongated and string-like precipitates are formed along the dislocations in the pre-strained Al−Mg−Si−Cu alloy.The precipitates formed along the dislocations exhibit three features:non-periodic atomic arrangement within the precipitate;Cu segregation occurring at the precipitate/α(Al)interface;different orientations presented in one individual precipitate.Four different formation mechanisms of these heterogeneous precipitates were proposed as follows:elongated precipitates are formed independently in the dislocation;string-like precipitates are formed directly along the dislocations;different precipitates encounter to form string-like precipitates;precipitates are connected by other phases or solute enrichment regions.These different formation mechanisms are responsible for forming different atomic structures and morphologies of precipitates.

Relationship among solution heating rate,mechanical properties,microstructure and texture of Al−Mg−Si−Cu alloy

The relationship among heating rate, mechanical properties, microstructure and texture of Al-Mg-Si-Cu alloy during solution treatment was investigated through tensile test, scanning electron microscope, X-ray diffractometer and EBSD technology. The experimental results reveal that there is a non-monotonic relationship among solution heating rate, mechanical properties, microstructure and texture. As the solution heating rate increases, the strength variations are dependent on the tensile direction;work hardening exponent n decreases first, and then increases;plastic strain ratio r increases first, and then decreases, and finally increases. The final microstructure and texture are also affected by heating rate. As heating rate increases, the microstructure transforms from elongated grain structure to equiaxed grain structure, and the average grain size decreases first, and then increases, and decreases finally. Although the texture components including CubeND{001}<310> and P{011}<122> orientations almost have no change with the increase of heating rate, the texture intensity and volume fraction decrease first, and then increase, and finally decrease. Both microstructure and texture evolutions are weakly affected by heating rate. Improving heating rate is not always favorable for the development of fine equiaxed grain structure, weak texture and high average r value, which may be related to the recrystallization behavior.

Microstructure and mechanical properties of Al−Mg−Si alloy U-shaped profile

To get a full understanding of hot extrusion,solid solution treatment and aging process on the Al−0.56Mg−0.63Si alloy,the microstructure and mechanical properties of a U-shaped profile were studied through optical microscopy,scanning electrical microscopy,transmission electrical microscopy,hardness,and tensile tests.The coarse equiaxed grains existed near the profile edge as a result of the dynamic recrystallization nucleation and exceeding growth during hot extrusion.The fibrous deformed and sub-structured grains located between the two coarse grain layers,due to the occurrence of work-hardening and dynamic recovery.Perpendicular needle β′′precipitates were distributed inside the grain,and obvious precipitates-free zone appeared after aging treatment.The tensile strength,yield strength and elongation of the aged Al−Mg−Si alloy U-shaped profile were no less than 279.4 MPa,258.6 MPa,and 21.6%,respectively.The fracture morphology showed dimple rupture characteristics.The precipitates and grain boundaries played key role in the strengthening contribution.

Microstructure and mechanical properties of friction stir processed Al−Mg2Si alloys

The microstructure and mechanical properties of friction stir processed Al−Mg2Si alloys were studied by TEM and EBSD.The results showed that an increase in the tool rotation speed(300−700 r/min)led to a decrease in the defect area(from 10.5 mm2 to zero),whereas the defect area demonstrated the opposite trend(increased to 1.5 mm2 from zero)upon further increasing the rotation speed(700−1200 r/min).The types of defects were transformed from tunnel defects to fusion defects as the rotational speed increased.The coarse Mg2Si dendrites were broken and fine particles(smaller than 10mm)formed in the weld nugget(WN).The amount of low-angle grain boundaries increased significantly from 57.7%to 83.6%,which was caused by an increase in the content of the deformed structure(from 1.7%to 13.6%).The hardness,ultimate tensile strength(UTS)and elongation were all greatly improved for the weld nugget.The hardness values of the WNs had the following order:R300<R1200<R500<R900<R700.The UTS and elongation had the following order:BM(base material)<R300<R1200<R500<R900<R700.The UTS and the elongation for the WN were increased by one and three times,respectively.

Al-Mg系合金中合金化元素作用及其对力学性能的影响

铝镁合金是轻量化材料应用领域中一种重要的金属材料,属于中高强度铝合金,具有较高的塑性、良好的耐蚀性以及优良的焊接性等优势,目前在航空航天、交通运输和军工制造等领域具有广阔的应用前景。笔者综述了铝镁合金力学性能特点以及用途,介绍了Al-Mg系合金中的强化机制,重点阐述了Al-Mg系合金中主合金化元素Mg及其含量对合金微观组织和力学性能的影响规律及机理,详细论述了Mn、Zr、Ti、Sc、Er、Y等微合金化元素的作用以及对Al-Mg系合金微观组织和力学性能的影响规律。最后,结合Al-Mg系合金当前研究现状,提出了今后值得研究的方向。

激光熔化沉积Al-Mg-Sc-Zr合金晶粒尺寸预测及成形工艺优化

通过激光熔化沉积试验分析了工艺条件(送粉速度、扫描速度和激光功率)对Al-Mg-Sc-Zr合金晶粒尺寸的影响,构建了晶粒尺寸预测模型,优化了成形工艺参数,给出了工艺参数最佳区间。结果表明,相较于激光功率和扫描速度,送粉速度对晶粒尺寸的影响最为显著;随着成形能量密度的增加,合金晶粒尺寸呈现出先减小后增大的演变趋势;采用回归方程构建的晶粒尺寸-工艺参数关系模型能准确预测不同工艺条件下激光熔化沉积Al-Mg-Sc-Zr合金的平均晶粒尺寸,相对误差小于2%;通过响应面分析得到工艺参数最佳区间为:送粉速度2.8~3 g·min^(-1)、激光功率1000~1050 W、扫描速度4~5 mm·s^(-1)。

碳纳米管增韧Al-Mg合金复合材料的制备与性能研究

选择碳纳米管为增强相,通过搅拌铸造法制备了碳纳米管增韧Al-Mg合金复合材料,研究了碳纳米管的添加量对复合材料力学性能、微观组织以及韧性的影响,并探究了碳纳米管对Al-Mg合金的增韧机理。结果表明,掺入适量的碳纳米管后细化了Al-Mg合金复合材料的晶粒,晶粒尺寸约为80μm,当碳纳米管的添加量为0.8%(质量分数)时,复合材料的断口形貌最均匀。随着碳纳米管添加量的增大,复合材料的抗拉强度、断裂伸长率、硬度均表现出先增大后降低的趋势,当碳纳米管的添加量为0.8%(质量分数)时,抗拉强度、断裂伸长率和硬度均达到了最大值,分别为208.6 MPa、15.8%和53.1 HB。适量碳纳米管的添加显著改善了Al-Mg合金的韧性,使断裂延伸率逐渐增大,屈服阶段延长,韧性得到提高,这是因为适量的碳纳米管添加后能够与合金发生较好的结合,并贯穿于合金的裂纹中,发挥出了桥联作用,阻碍了裂纹的萌生和扩展,从而改善了Al-Mg合金复合材料的韧性,延缓了合金的失效过程,延长了合金的屈服阶段。综上分析可知,碳纳米管的最佳添加量为0.8%(质量分数)。

高强Al-Zn-Mg-Cu合金静态再结晶模型及组织演变

采用Gleeble 3800热模拟试验机对航空用Al-Zn-Mg-Cu合金的热变形行为进行了测试,对变形后的微观组织进行了表征,系统分析了静态软化行为,建立了静态再结晶动力学模型。结果表明:实验用航空Al-Zn-Mg-Cu合金的静态再结晶激活能为129162 J·mol^(-1),静态再结晶体积分数受变形温度、变形程度、变形速率的影响,且变形温度对静态再结晶影响最明显;变形速率一定时,变形温度越高,道次停留时间的影响越不明显;350℃低温变形后,α-Al基体晶粒内部仍存在大量的位错缠结;400℃中温变形后,位错运动能够充分进行,部分晶粒发生了再结晶;450℃高温变形后,基体晶粒基本全部完成了再结晶,基体晶粒内部发现5~25 nm尺寸范围的Al-Zn-Mg-Cu四元相粒子;对于不同热变形条件,模型预测值的误差在0.008~0.0625范围内,动力学模型的计算结果精确度较高。

基于冷喷涂工艺的Mg-Zn-Al-Sn-Mn合金防腐Al涂层制备

采用冷喷涂技术在Mg-Zn-Al-Sn-Mn合金表面制备Al涂层,以提高其耐腐蚀性能。研究工作气体温度和压力对Al涂层显微组织和腐蚀行为的影响。结果表明,随着气体温度和压力的升高,Al涂层的致密度和厚度均明显增加。高的气体温度能降低颗粒沉积的临界速度,并提高沉积效率。高的气体压力不仅提升机械结合质量,而且对沉积的涂层具有较强的夯实作用。由于孔隙的减少,Al涂层的耐蚀性随着气体温度和压力的升高而提高。Al(OH)_(3)和Al_(2)O_(3)等腐蚀产物可以堵塞涂层中的孔隙,并作为阻碍腐蚀的物理屏障,从而有效保护Mg合金免受腐蚀。

T6态热挤压Al-5Cu-0.8Mg-0.15Zr-0.2Sc-0.5Ag合金的低周疲劳行为

为了揭示经过T6处理的热挤压Al-5Cu-0.8Mg-0.15Zr-0.2Sc-0.5Ag合金在不同温度下的低周疲劳变形与断裂行为,对T6态热挤压合金进行了室温和200℃条件下的低周疲劳实验。结果表明:在室温和200℃下合金塑性应变幅与载荷反向周次之间服从Coffin-Manson公式,而弹性应变幅与载荷反向周次之间服从Basquin公式;合金在室温和200℃下低周疲劳变形时,在较低外加总应变幅下疲劳变形机制主要为平面滑移,而在较高外加总应变幅下疲劳变形机制主要为波状滑移;室温和200℃下合金的疲劳裂纹均萌生于疲劳试样表面并以穿晶方式扩展。

激光选区熔化Al-Mg-Sc-Zr合金各向组织与损伤容限性能

研究激光选区熔化(selective laser melting,SLM)技术成形Al-Mg-Sc-Zr合金材料不同取向的显微组织特征、拉伸和损伤容限性能。结果表明:YZ截面为细小的等轴晶和粗大的柱状晶组成的双峰组织,XY截面由细小的等轴晶组成;0°和90°方向屈服强度、抗拉强度均超过500 MPa,各向异性较小,但堆积层间存在的未熔合缺陷使得90°方向断裂伸长率明显低于0°方向;0°和90°CT试样K_(IC)分别为21.41 MPa·m^(1/2)和20.89 MPa·m^(1/2),在柱状晶区域裂纹扩展阻抗低,导致90°CT试样K_(IC)稍小;显微组织和缺陷是影响裂纹扩展性能各向异性的主要因素,在近门槛区未熔合缺陷起主导作用,当裂纹面平行于水平方向时裂纹扩展速率更快;在稳态扩展区显微组织的影响起主导作用,当裂纹面平行于水平方向时为穿晶断裂,裂纹扩展阻抗较高,裂纹扩展速率较低。

Zr对Al-Si-Mg-Mn合金凝固过程、时效组织和性能的影响

通过模拟计算、组织观察以及力学性能测试,研究了不同Zr含量对铸造Al-Si-Mg-Mn合金凝固过程、时效组织及力学性能的影响。结果表明,随着Zr含量增加,合金凝固路径存在显著差异,晶粒由初期树枝晶逐步演变为等轴晶;175℃时效7 h条件下,Zr的加入显著提高合金硬度。Zr的加入促使析出相在更低时效温度析出,这可能是Zr细化了晶粒从而提高了扩散效率。峰值时效时合金主要析出相为β″相和Q′相。

通过不同热挤压方式制备具有较优强塑性组合的新型Mg-5Sn-2Al-1Zn合金

制备新型Mg-5Sn-2Al-1Zn(TAZ521)合金。为提高合金的强度与塑性,采用正挤压(DE)和挤压-剪切(ES)两种工艺对该合金进行变形处理。通过XRD、SEM、TEM、EBSD和拉伸试验等方法研究均匀态和挤压态合金的显微组织演变、织构演变及强化机制。结果表明,正挤压态合金的力学性能得到改善;然而,合金表现出由粗晶和细小动态再结晶(DRXed)晶粒组成的双峰组织。经过挤压-剪切变形后的合金组织变得更加均匀,并且实现更好的强韧性结合,变形后合金的屈服强度(YS)、极限抗拉强度(UTS)和伸长率(EL)分别达到212 MPa、303 MPa和21.7%。晶粒细化和Mg2Sn析出物的钉扎效应对强度的提高起到重要作用,此外,延展性的提高归因于基面纤维织构的弱化和非基面滑移系的激活。

Cu含量以及Cu/Mg比对Al-Si-Cu-Mg合金组织和力学性能的影响

研究了Cu含量和Cu/Mg比对Al-Si-Cu-Mg合金组织和力学性能的影响。结果表明Al-Si-Cu-Mg合金凝固组织是否形成Mg_(2)Si、Q-Al_(5)Cu_(2)Mg_(8)Si_(6)以及θ-Al_(2)Cu取决于Cu含量以及Cu/Mg比。当Cu/Mg比相对低时形成Mg_(2)Si中间相,而Cu/Mg比高时则倾向于生成Q-Al_(5)Cu_(2)Mg_(8)Si_(6)和θ-Al_(2)Cu相。当Cu/Mg比相同时,高Cu含量和高Mg含量都会促进Q相θ相的形成。通过观察T6热处理后的组织发现Cu含量以及Cu/Mg比控制了初生相的溶解以及析出相的形成,从而影响合金的强度与韧性。通过控制Cu含量及Cu/Mg比使Al-9Si-2Cu-0.5Mg合金中析出较少数量的初生相,再通过热处理析出大量的Q′强化相,使合金具有较高的强度和相对适中的伸长率。

Mn微合金化Al-Si-Cu-Mg合金显微组织及耐蚀性能研究

Al-Si-Cu-Mg系列合金具有优异的强韧性,但其中的含Cu强化相极大地影响了该系合金的耐蚀性能。因此,本文通过对不同Mn含量的Al-7Si-2Cu-0.6Mg合金进行显微组织观察和电化学分析,探究Mn元素的添加对T6热处理状态下合金微观结构和耐蚀性的影响。结果表明,Mn添加量的提高对合金显微硬度几乎没有影响,但在合金基体中可以观察到弥散相。随着Mn含量升高,合金的耐蚀性呈现先升高后降低的趋势。添加0.360%Mn(质量分数)合金具有最佳耐蚀性,腐蚀电流密度比基础合金减少了54%。腐蚀形貌观察结果表明,Mn的添加可以显著减弱合金的点蚀趋势。

基于机器学习的Al-Zn-Mg-Cu合金快速设计

提出一种基于机器学习的合金快速设计系统(ARDS),以定制所需性能的合金制备策略或预测制备策略所对应的合金性能。为此,分别对3种回归算法:线性回归(LR)、支持向量回归(SVR)和人工神经网络(BPNN)进行建模和比较以训练多性能预测模型。其中,应用SVR构建的机器学习模型被证明是最佳的。然后,基于生成对抗网络(GAN)模型原理,构建Al-Zn-Mg-Cu系铝合金快速设计系统(ARDS)。对ARDS的预测可靠性进行验证。结果表明,为了能够获得准确的制备策略,系统中极限抗拉强度(UTS)、屈服强度(YS)和伸长率(EL)的输入上限分别约为790 MPa、730 MPa和28%。此外,基于ARDS预测结果,制备了一种性能优异的新型铝合金材料,其UTS为764 MPa、YS为732 MPa、EL为10.1%,进一步验证了ARDS的可靠性。