7055铝合金厚板的淬透性

通过末端淬火的方法研究7055铝合金厚板的淬透性,采用透射电子显微镜对微观组织进行分析。结果表明:该合金板材的淬透深度可达45 mm,使其淬透的冷却速率需大于230℃/min;随着冷却速率的减小,淬火过程析出平衡相的数量和尺寸增加,时效后析出的η′沉淀强化相的数量减少,晶界无沉淀析出带宽度增加;在所研究的冷却速率范围内,时效后铝合金板材的硬度、晶界无沉淀析出带宽度与冷却速率的对数均呈线性关系。     

时效对7085铝合金厚板淬火引起的不均匀性影响

采用末端淬火试验、光学显微镜、扫描电子显微镜和高分辨透射电子显微镜研究时效对7085铝合金厚板淬火引起的不均匀性影响。结果表明:峰时效和过时效前进行长时间的自然时效提高厚板的均匀性,自然时效、峰时效、过时效、自然时效+峰时效和自然时效+过时效后,两端硬度下降率分别约为3.5%、8.6%、7.8%、5.3%和5.2%,硬度与冷却速率的对数间有较好的线性关系。随淬火速率的减小,冷却过程中平衡相的数量和尺寸随之增加,导致厚板不均匀,峰时效和过时效前的长时自然时效有利于慢速淬火处稳定GP区的形成,最终得到数量更多、分布更均匀弥散和尺寸更细小的强化相,从而减小两端的硬度差值,降低淬火引起的不均匀性。     

淬火速率对含Sc(Zr)高强韧Al-Zn-Mg-Cu合金微观组织和力学性能的影响

通过末端淬火实验(JEQ)、X射线衍射仪(XRD)、扫描电镜(SEM)、透射电子显微镜(TEM)研究一种热挤压Al-Zn-Mg-Cu-Sc-Zr棒材的淬火敏感性。结果表明:随着距离淬火端越远,冷却速率从1800℃/min下降至111℃/min,合金硬度从150 HB下降至133 HB,抗拉强度从430 MPa下降至375 MPa。当冷却速率为131.2℃/min时,合金的硬度为135 HB,合金淬透深度约为93mm。随着冷却速率的降低,端淬时远离淬火端位置,平衡η相先后在晶界、晶内处析出、长大、粗化;时效后,析出的η′强化相的数量减小;时效后,合金内出现无沉淀析出带(PFZ),晶界的PFZ变宽,宽化至160 nm。     

基于末端淬火试验2124铝合金的淬透性

通过Jominy末端淬火实验研究2124铝合金的淬透性。利用温度数据采集、布氏硬度检测、差示量热法(DSC)和透射电子显微镜(TEM)等手段分析淬火冷却速率对时效后第二相析出行为的影响。结果表明:Jominy末端淬火2124铝合金室温水淬硬度下降小于10%的淬透深度大约为50 mm,该位置处合金在222.7～350.0℃温度区间的平均淬火冷却速率大于2.0℃/s;较低的淬火冷却速率致使过饱和的溶质原子和空位损失,导致时效析出相变驱动力不足,显著削弱了时效强化效果。     

淬火介质对7050铝合金板材显微组织和力学性能的影响

采用硬度测试、室温拉伸和透射电子显微镜等手段研究了淬火介质对7050铝合金板材显微组织和力学性能的影响。结果表明,当水淬、油淬和空气淬火时,合金板冷却速率依次减小,合金板时效后的硬度和室温拉伸性能依次降低。当冷却速率减小时,合金中析出了粗大的η平衡相,这不仅没有强化效果,反而减少了后续时效过程沉淀强化相的数量:此外在合金晶界附近形成了很宽的较基体更软的无沉淀析出带。     

7B50铝合金淬透性及其临界平均冷却速率的研究

本研究通过7B50合金改进型Jominy样品表面喷水淬火实验,在获得实测冷却曲线、不同时效状态合金的电导率和硬度的基础上,结合自然时效状态合金的微观组织,对7B50合金的淬透性及其临界平均冷却速率展开研究。结果表明:7B50合金自然时效50 d的淬透深度为70 mm,对应淬火敏感温度区间(420～230℃)内的平均冷却速率为1.55℃×s~(-1);先自然时效50 d再人工峰时效合金的淬透深度减至60 mm,对应的平均冷却速率为1.95℃×s~(-1);与自然时效状态相比,先自然时效再人工峰时效处理后合金的淬透性变差,淬火敏感性增加。表面喷水淬火时,非均匀析出相首先在晶界/亚晶界上析出,然后在基体内的Al_3Zr粒子上析出;晶界/亚晶界上观察到析出相,出现在距淬火表面仅3mm处,对应淬火敏感温度区间内的平均冷却速率高达981℃×s~(-1);基体内零星析出尺寸较小的非均匀析出相,出现在距淬火表面10mm处,对应的平均冷却速率为37.75℃×s~(-1)。喷水淬火后,距淬火表面25 mm处的性能与淬火表面处相比变化不大,该位置对应的平均冷却速率为9.34℃×s~(-1),远小于淬火表面处,控制7B50合金厚板的喷水淬火过程,使厚板内部的平均冷却速率接近但不低于9.34℃×s~(-1),厚板淬火-时效后将获得较好的性能。     

Al-Zn-Mg-Cu合金时效沉淀相应变场研究

利用高分辨透射电子显微镜研究喷射成形Al12Zn2.4Mg1.1Cu合金不同时效时间析出的GPⅡ区和η′亚稳沉淀相,并结合几何相位分析软件计算了GPⅡ区和η′亚稳沉淀相的应变场。研究表明:该合金的时效硬度变化和主要析出相的变化密切相关。GPⅡ区大量弥散析出是造成合金硬度迅速上升的主要原因。η′是峰值时效状态下的主要析出强化相。析出相从GPⅡ区到η′的转变,是应变峰值较小的分散半共格应变场取代了应变峰值较大的集中共格应变场的过程。并对GPⅡ区和η′亚稳沉淀相的演变过程及强化机制进行了讨论。     

四种航空用高强铝合金厚板的淬透性

通过末端淬火方法研究7075合金、7055合金、7150合金和7185合金等四种铝合金厚板的淬透性，采用透射电子显微镜对微观组织进行分析。结果表明：7075合金、7055合金、7150合金和7185合金等四种合金两端的硬度差值分别为30%、14%、12%和8%，淬透层深度分别为25 mm、45 mm、63 mm和100 mm以上。四种合金析出相的尺寸及面积分数均随冷却速率的降低而增加；7185合金总的晶格畸变能最小，析出相的尺寸最小且数量最少，因此淬透性最好；与7185合金相比较，7055合金和7150合金总的晶格畸变能均较高，析出相的尺寸大且数量也较多，合金的淬透性较差；7075合金总的晶格畸变能最大且晶内存在非共格的E(Al₁₈Cr₂Mg₃)相，析出相数量最多且尺寸较7150合金的大，因此淬透性最差。     

2060铝锂合金的淬透性

利用新型的薄板叠层端淬法结合时效后强度变化,评价2060铝锂合金的淬透性,并采用扫描电子显微镜(SEM)、透射电子显微镜(TEM)、场发射透射电子显微镜(STEM)及能谱(EDS)对末端淬火并T8时效后的微观组织进行了分析。结果表明:以抗拉强度下降5%作为淬透深度的判断依据,则2060铝锂合金的淬透深度约为15 mm。随着距淬火端距离的增大,抗拉强度依次降低直至稳定,但在距淬火端12～18 mm的区间内,强度发生较明显变化。端淬过程中析出的富Cu相降低了固溶体过饱和程度,阻碍后续时效过程中同一位置T1相(Al_2CuLi)的析出和长大,导致合金抗拉强度逐渐减小。     

淬火介质对7050铝合金末端淬特性的影响

采用室温水和浓度为20%的PAG水溶液(聚烷撑二醇聚合物)作为淬火介质进行Jominy末端淬火实验,用于评价7050铝合金淬透性;监测合金固溶和淬火过程中的升温速率和冷却速率,测定距淬火端不同距离的合金的淬火态电导率和时效态硬度,观察室温水淬火试样不同位置晶内淬火析出相.结果表明:采用室温水和20%PAG进行末端淬火时,合金的淬透深度分别约为65和40mm;采用PAG淬火可使合金温度快速通过淬火敏感区间,同时在淬火敏感区间外降低合金的冷却速率,使试样淬火端和中间部位合金的温度差减小.随着距淬火端距离的增加,淬火诱发析出的η平衡相的尺寸和体积分数增加,无析出区宽化.     

Effect of step-quenching on microstructure of aluminum alloy 7055

The effect of step-quenching on the microstructure of aluminum alloy 7055 after artificial aging was studied by hardness testing and transmission electron microscopy (TEM). Step-quenching leads to decomposition of solid solution and heterogeneous precipitation of equilibrium phase mainly on dispersoids and at grain boundaries; thus lower hardness after aging. Prolonging isothermal holding at 415 ℃ results in coarser and more spaced η phase particles at grain boundaries with wider precipitates free zone, and lower density of larger η′ hardening precipitates inside grains after aging. Isothermal holding at 355 ℃ results in heterogeneous precipitation of η phase both on dispersoids and at grain boundaries. Isothermal holding at 235 ℃ results in heterogeneous precipitation of η phase first, and then S phase. Precipitates free zones are created around these coarse η and S phase particles after aging. Prolonging isothermal holding at these two temperatures leads to fewer η′ hardening precipitates inside grains, larger and more spaced η phase particles at grain boundaries and wider grain boundary precipitates free zone after aging.     

Mg-4Zn-2Al-0.5Ca合金时效沉淀过程的相演变

利用高分辨透射电镜和扫描电镜分析了Mg-4Zn-2Al-0.5Ca合金时效沉淀过程中的相演变。结果表明:试验合金的时效硬化曲线呈现典型的时效硬化特征。试验合金在160℃时效达到峰值硬度时其沉淀相有:平行于(0001)Mg的圆盘状沉淀相、(梳齿状)块状沉淀相以及大量的亚稳过渡相。随时效时间的延长,生成长条状相,但基体中依然存在很多后析出的细小的弥散分布的粒状沉淀相。120℃×230 h时效处理后的微观组织中存在着蜂窝状组织,宽度为3～4 nm的长条状沉淀相,直径为5～7 nm的球状沉淀相;这些沉淀相的存在大大提高了合金的硬度。     

Influence of interrupted quenching on artificial aging of Al–Mg–Si alloys

In this study the influence of interrupted quenching (IQ) in the temperature range 150–250 °C for periods of 15–1080 s on artificial aging after long-term natural pre-aging was studied for the Al–Mg–Si alloy AA6061 by atom probe tomography, transmission electron microscopy, electrical resistivity and hardness measurements, and differential scanning calorimetry. Compared with a standard quenching procedure, the results showed that hardening kinetics and the age hardening response were enhanced for IQ at low temperatures but reduced at high temperatures. Quenched-in vacancies were shown to be of particular importance for the nucleation of precipitates occurring during IQ at the lower end of the temperature range, finally leading to the formation of a dense distribution of β″ during artificial aging. For standard water quenching and subsequent natural aging, nucleation is hindered by a low concentration of quenched-in vacancies in the matrix. IQ at high temperatures affects subsequent artificial aging via the formation of precipitates which do not contribute to hardening but consume a significant amount of solute.     

Aging precipitation behavior and properties of Al–Zn–Mg–Cu–Zr–Er alloy at different quenching rates

The effect of quenching rate on the aging precipitation behavior and properties of Al–Zn–Mg–Cu–Zr–Er alloy was investigated. The scanning electron microscopy, transmission electron microscopy, and atom probe tomography were used to study the characteristics of clusters and precipitates in the alloy. The quench-induced η phase and a large number of clusters are formed in the air-cooled alloy with the slowest cooling rate, which contributes to an increment of hardness by 24% (HV 26) compared with that of the water-quenched one. However, the aging hardening response speed and peak-aged hardness of the alloy increase with the increase of quenching rate. Meanwhile, the water-quenched alloy after peak aging also has the highest strength, elongation, and corrosion resistance, which is due to the high driving force and increased number density of aging precipitates, and the narrowed precipitate free zones.     

PRECIPITATION HARDENING OF ELINVAR ALLOY

The microstructural evolution and precipitation hardening of an Elinvar alloy doped with Ti and Al during isothermal aging at 700℃ have been investigated by atom probe field ion microscopy and microhardness measurements.The γ′ precipiates are spherical and coherent with the matrix.The chemical composition of the precipitates are(Ni_(0.53)Fe_(0.47)_3 (Ti_(0.(?))Al_(0.4)). During aging,a Lifshitz-Wagner type dissolution and coarsening reaction of the precipitates has been observed,The hardness of the material varies with the aging time and reaches maxi- mum when the average diameter of the precipitates was about 11 nm.     

Microstructure evolution of an Ni-Cr-Co base superalloy heat-treated at 704 and 760℃

Thermodynamic calculation, SEM (scanning electron microscopy), TEM (transmission electron microscopy), XRD (X-ray diffraction), phase extraction, and chemical analysis were employed to study the phase stability and phase precipitation in a new Ni-Cr-Co base superalloy heat-treated at 704 and 760 ℃ for a long time. The results show that the precipitates of this new alloy heat-treated at standard annealing condition and heat-treated at 704 and 760 ℃ for a time up to 2000 h are r', MC, M23C6, and M6C, and η phase forms at grain boundaries and in matrix of samples heat-treated at 760℃ as well. The mass fractions of r' (+η), MC, M23C6, and MgC in all samples have no large changes with an increase in aging time, but r' precipitates grow obviously. The r '-to-r1 transformation in the samples heat-treated at 760℃ took place with increasing aging time. The η precipitates form a Widmanstatten pattern and the y' phases have remelted partly in the samples heat-treated at 760℃. The alloy maintains a better m     

Revisiting the Hierarchical Microstructures of an Al-Zn-Mg Alloy Fabricated by Pre-deformation and Aging

Pre-deformation before aging has been demonstrated to have a positive effect on the mechanical strength of the 7N01 alloy in our previous study, which is rather different from the general negative effects of pre-deformation on high-strength 7XXX aluminum alloys. In order to explain the strengthening mechanism relating to the positive effect, in the present study, the microstructure of the aged 7N01 alloy with different degrees of pre-deformation was investigated in detail using advanced electron microscopy techniques. Our results show that, without pre-deformation, the aged alloy is strengthened mainly by the η′ type of hardening precipitates. In contrast, with pre-deformation, the aged alloy is strengthened by the hierarchical microstructure consisting of the GP-η′ type of precipitates formed inside sub-grains, the η_p type of precipitates formed at small-angle boundaries, and the dislocation introduced by pre-deformation (residual work-hardening effect). By visualizing the distribution of the η_p precipitates through three-dimensional electron tomography, the 3D microstructures of dislocation cells are clearly revealed. Proper combinations of η_p precipitates, GP-η′ precipitates and residual dislocations in the alloy are responsible for the positive effect of pre-deformation on its mechanical properties.     

基于时效曲线和DSC分析的2519A铝合金析出动力学

采用硬度测试和差示扫描量热法研究时效前不同冷轧变形量对2519A铝合金析出动力学的影响。根据DSC曲线,采用单升温速率法计算合金的激活能;采用透射电子显微镜观察冷轧和峰时效状态下合金的微观组织。结果表明：随着冷轧变形量从7%增加至40%,合金的时效硬化能力降低,激活能升高。当冷轧变形量为15%时,在冷轧态合金组织中观察到密度不均匀的位错组织,在峰时效状态合金组织中观察到不均匀分布的θ′相。不均匀分布的θ′相可能是造成合金时效硬化能力降低和激活能升高的原因。     

Microstructure evolution and deformation behavior of ultrafine-grained Al–Zn–Mg alloys with fine η′ precipitates

An aged Al–5Zn–1.6Mg alloy with fine η′ precipitates was grain refined to ～100 nm grain size by means of confined channel die pressing. Microstructure observations and mechanical tests were carried out to characterize the materials before and after various degrees of severe plastic deformation. Deformation processing enhanced the strength of the alloy, but limited its work hardenability. An analysis of deformation mechanisms revealed that plasticity proceeded by dislocation slip through ultrafine-grained cellular and subgrain arrangements. η′ precipitates strengthened the alloy by dispersion hardening, but retarded an increase in the strain rate sensitivity during grain refinement. The influence of η′ precipitates is discussed with respect to their effect on dislocation configurations and deformation mechanisms during processing of the alloy.