GH625合金的热变形行为

采用Gleeble-1500热模拟试验机研究了GH625高温合金在应变速率为0.001～1 s-1、变形温度为1223～1373 K条件下的热变形行为。结果表明:当变形温度一定时,随应变速率的升高,合金的峰值应力σp和稳态流动应力σs及对应的应变εp和εs均升高;当变形速率一定时,随变形温度的升高,σp和σs以及εs均降低,但εp基本保持不变。GH625合金在热压缩变形过程中应变速率的降低和变形温度的升高均有利于动态再结晶的发生;根据应力-应变曲线,通过线性回归获得GH625合金的本构方程。     

热变形参数对GH690合金晶粒细化的影响

采用Gleeble-3500热模拟试验机进行高温等温压缩试验,研究了热变形参数对GH690合金晶粒细化的影响.结果表明:当变形程度较小时,随着真应变的增加,GH690合金动态再结晶的晶粒尺寸逐渐减小,但当真应变达到0.5后,随着真应变继续增加,动态再结晶晶粒尺寸变化不大;动态再结晶晶粒尺寸随变形温度的升高而增大,随应变速率的增大而减小.建立起热变形条件即Z参数与动态再结晶晶粒尺寸的关系.     

Mg-6Zn-1Mn镁合金热压缩流变行为及动态再结晶

采用Gleeble-1500热压缩模拟试验机对Mg-6Zn-1Mn合金进行压缩实验,研究了该合金其在变形温度250 ～400℃、应变速率0.01 ～10 s-1范围内的流变应力及动态再结晶行为.通过计算加工硬化速率θ得到合金发生动态再结晶的临界应力σc和临界应变εc,并且建立临界值与峰值应力σp、峰值应变εp之间的定量关系,用截线法测量合金压缩后的平均晶粒尺寸.结果表明:Mg-6Zn-1Mn镁合金在高温下塑性变形的热本构方程为:ε·exp(22919/T) =2.77·σ8.19;合金发生动态再结晶的临界应变随着应变速率的增加而升高,随变形温度的增加而降低,发生动态再结晶的临界条件为:ε＞εc=6.648×10-3Z0.06149;各特征变量之间存在如下关系:σc=0.7295σp、εc=0.2639εp;动态再结晶的平均晶粒尺寸dave随温度的升高、应变速率的减小而增大,与Zener-Hollomon参数之间的关系为:dave=2.11×103·Z-0.1378.     

GH625合金的动态再结晶行为研究

采用Gleeble-3800热模拟试验机研究了GH625合金在变形温度为950～1150℃,应变速率为0.001～5s-1条件下的热变形特性,并用OM和TEM分析了变形条件对微观结构的影响。结果表明:当应变量很小时,该合金没有发生再结晶,直到应变量达到0.1时才开始有再结晶晶粒析出。随着变形温度的升高,再结晶晶粒尺寸增大,位错密度降低;当温度较低时显微结构中可以观察到孪晶。当变形温度一定时,随应变速率的增大,再结晶的形核率增大且晶粒变小,位错密度变大;而当应变速率较低时,再结晶进行得比较充分,晶粒尺寸较大。根据实测的应力-应变曲线,获得了该合金发生动态再结晶的临界应变εc和峰值应变εp与Z参数之间的关系:εc=2.0×10-3.Z0.12385,lnεp=-6.02285+0.12385lnZ。此外,还采用定量金相法计算出了合金的动态再结晶体积分数,并建立了该合金动态再结晶的动力学模型:Xd=1-exp[-0.5634(ε/εp-0.79)1.313]。     

含Sc超高强Al-Zn-Cu-Mg-Sc-Zr合金的热压缩变形流变应力

采用Gleeblel500热模拟机在应变速率为0.001～10/s、温度为380～470℃、真应变为0～0.7的条件下,研究了实验合金的流变应力行为.结果表明:该合金热压缩变形时存在较明显的稳态流变特征,当ε<1/s时,流变应力开始随应变增加而增加,达到峰值后趋于平稳,呈动态回复特征;当ε≥1/s时,流变应力均出现了明显的峰值应力,为连续动态再结晶特征.带Zener-Hollomon参数的双曲正弦函数可描述合金高温变形时的流变应力,σ解析表达式中A、α和n值分别为5.952×108/s、0.021 MPa-1和5.397:热变形激活能Q为157.9kJ/mol.     

形变参数对GH4169合金热变形行为的影响

利用Gleeble-1500热模拟试验机,研究了GH4169合金在变形温度为900～1100℃、应变速率为0.1 s-1、1 s-1、20 s-1、最大变形量高达70%条件下的高温变形行为,建立了GH4169合金的高温变形流动应力模型,分析了变形工艺参数对合金晶粒再结晶的影响规律。结果表明:随变形温度的降低和应变速率的增加,合金变形抗力显著增加;当变形量超过临界变形量时,随着变形量增加或变形温度的提高,合金的再结晶程度逐渐增加;然而,变形速率的变化,对该合金再结晶影响较为复杂。     

GH4169高温合金热变形力学性能研究

通过热模拟实验对GH4169高温合金热态变形过程中的力学性能进行研究,分析了初始晶粒尺寸、应变速率、变形温度等对GH4169合金热变形时峰值应力的影响。结果表明,该合金的峰值应力随应变速率的增大而增大,随变形温度的增大而减小。该合金的流动应力随初始晶粒尺寸的增大而增大,其原因是该合金在热变形过程中发生了动态再结晶。确定了基于初始晶粒尺寸的峰值应力与热变形参数之间的关系式,确定了GH4169合金的变形激活能。     

GH761合金的热变形行为与动态再结晶模型

采用Gleeble-3500热模拟试验机研究GH761合金在变形温度为900～1150℃,应变速率为0.1～30s-1条件下的热变形行为,建立了GH761合金在热态变形过程中的本构方程.采用Quantiment-500型自动图像分析仪定量测定试样中的动态再结晶晶粒尺寸和再结晶体积分数.根据实验结果,建立了GH761合金动态再结晶过程的物理模型,为科学设计和有效控制GH761合金的锻造工艺提供理论依据.     

Effect of Deformation Conditions on the Dynamic Recrystallization of GH690 Alloy

采用Gleeble-3500热模拟试验机进行高温等温压缩实验,研究了变形条件对GH690合金高温变形动态再结晶的影响。结果表明:GH690合金动态再结晶过程是一个受变形温度和应变速率控制的过程,在应变速率为0.001～1s-1的实验条件下,GH690合金获得完全动态再结晶组织所需的温度随变形速率的增大而升高;动态再结晶晶粒尺寸随变形温度升高而增大。采用力学方法直接从流变曲线确定了GH690合金发生动态再结晶的临界应变量,并回归出临界应变量与Z参数的关系式:εc=1.135×10-3Z0.14233。GH690合金的主要动态再结晶机制是原始晶界凸起形核的不连续动态再结晶机制(DDRX),而新晶粒通过亚晶逐渐转动而形成的连续动态再结晶机制(CDRX)则起辅助作用。     

TA15钛合金热变形参数对组织特征参数影响研究

采用Gleeble-3500热模拟试验机对TA15钛合金进行等温压缩试验。根据试验获得的σ-ε曲线确定合金的再结晶体积分数,并对σ-ε曲线进行加工硬化处理确定再结晶临界应变,研究热变形条件对该合金再结晶临界应变和再结晶体积分数的影响。结果表明,动态再结晶临界应变随着变形温度的升高而减小,随着应变速率的增大而增大;动态再结晶体积分数随着变形温度的升高而增大,随着应变速率的增大而减小。TA15钛合金具有变形温度敏感性和应变速率敏感性,合理选择合金的变形温度和应变速率,可以控制合金性能及细化晶粒。     

Strain rate sensitivity of a high strain rate superplastic TiNp/2014 Al composite

The effects of deformation temperature and strain in hot rolling deformation on strain rate sensitivity of the TiN_p/2014 Al composite were studied by tensile tests conducted out at 773, 798, 818 and 838 K with the strain rates from 1.7 ×10^?3 to 1.7 × 10⁰ s^?1. It is shown that the curves of m value of the TiN_p/2014Al composite deformed at different temperatures can be divided into two stages with the variation of strain rate, and the critical strain rates are 10^?1 s^?1. The optimum deformation temperature of the TiN_p/2014 Al composite is near incipient melting temperature of 816 K and the optimum strain rate is a little higher than the critical strain rate. The effect of deformation temperature on strain rate sensitivity is relative to liquid phase helper accommodation. The effect of strain in hot rolling deformation on strain rate sensitivity attributes to change of microstructure and deformation mechanism.     

Characterization of hot deformation behavior of Haynes230 by using processing maps

The hot deformation characteristics of Haynes230 has been investigated in the temperature range 1050–1250 °C and strain rate range 0.001–10 s^?1 using hot compression tests. Power dissipation map for hot working are developed on the basis of the Dynamic Materials Model. The map exhibits two domains of dynamic recrystallization (DRX): one occurring in the temperature range of 1200–1250 °C and in the strain rate range of 0.001–0.03 s^?1, which associated with grain coarsening; the other occurring in the temperature range of 1100–1200 °C and strain rate range of 0.001–0.01 s^?1, which are the optimum condition for hot working of this material. The average apparent activation energy for hot deformation is calculated to be 449 kJ/mol. The material undergoes flow instabilities at temperatures of 1050–1100 °C and at strain rates of 1–10 s^?1, as predicted by the continuum instability criterion. The manifestations of the instabilities have been observed to be adiabatic shear bands which are confirmed by optical observation.     

35% SiC_p/2024A1复合材料的热变形行为(英文)

采用Gleeble-1500D热模拟试验机,对35%SiCp/2024A1复合材料在温度350~500°C、应变速率0.01~10s-1的条件下进行热压缩试验,研究该复合材料的热变形行为与热加工特征,建立热变形本构方程和加工图。结果表明,35%SiCp/2024A1复合材料的流变应力随着温度的升高而降低,随着应变速率的增大而升高,说明该复合材料是正应变速率敏感材料,其热压缩变形时的流变应力可采用Zener-Hollomon参数的双曲正弦形式来描述;在本实验条件下平均热变形激活能为225.4 kJ/mol。为了证实其潜在的可加工性,对加工图中的稳定区和失稳区进行标识,并通过微观组织得到验证。综合考虑热加工图和显微组织,得到变形温度500°C、应变速率0.1~1 s-1是复合材料适宜的热变形条件。     

Superplastic Behavior of Al-4.5Mg-0.46Mn-0.44Sc Alloy Sheet Produced by a Conventional Rolling Process

This article describes the superplastic behavior of the Al-4.5Mg-0.46Mn-0.44Sc alloy. The investigated alloy was produced by casting and was conventionally processed to form a sheet with a thickness of 1.9 mm and an average grain size of 11 μm. The superplastic properties of the alloy were investigated using a uniaxial tensile testing with a constant cross-head speed and with a constant strain rate in the range 1 × 10⁻⁴ to 5 × 10⁻² s⁻¹ at temperatures from 390 to 550 °C. The investigations included determinations of the true-stress, true-strain characteristics, the maximum elongations to failure, the strain-rate sensitivity index m, and the microstructure of the alloy. The m-values determined with the strain-rate jump test varied from 0.35 to 0.70 in the temperature interval from 390 to 550°C and strain rates up to 2 × 10⁻² s⁻¹. The m-values decreased with increased strain during pulling. The elongations to failure were in accordance with the m-values. They increased with the temperature and were over 1000%, up to 1 × 10⁻³ s⁻¹ at 480 °C and up to 1 × 10⁻² s⁻¹ at 550 °C. A maximum elongation of 1969% was achieved at an initial strain rate of 5 × 10⁻³ s⁻¹ and 550 °C. The results show that the addition of about 0.4 wt.% of Sc to the standard Al-Mg-Mn alloy, fabricated by a conventional manufacturing route, including hot and cold rolling with subsequent recrystallization annealing, results in good superplastic ductility.     

High temperature deformation and processing map of a NiTi intermetallic alloy

The deformation behavior of a 49.8 Ni-50.2 Ti (at pct) alloy was investigated using the hot compression test in the temperature range of 700 °C–1100 °C, and strain rate of 0.001 s^?1 to 1 s^?1. The hot tensile test of the alloy was also considered to assist explaining the related deformation mechanism within the same temperature range and the strain rate of 0.1 s^?1. The processing map of the alloy was developed to evaluate the efficiency of hot deformation and to identify the instability regions of the flow. The peak efficiency of 24–28% was achieved at temperature range of 900 °C–1000 °C, and strain rates higher than 0.01 s^?1 in the processing map. The hot ductility and the deformation efficiency of the alloy exhibit almost similar variation with temperature, showing maximum at temperature range of 900 °C–1000 °C and minimum at 700 °C and 1100 °C. Besides, the minimum hot ductility lies in the instability regions of the processing map. The peak efficiency of 28% and microstructural analysis suggests that dynamic recovery (DRV) can occur during hot working of the alloy. At strain rates higher than 0.1 s^?1, the peak efficiency domain shifts from the temperature range of 850 °C–1000 °C to lower temperature range of 800 °C–950 °C which is desirable for hot working of the NiTi alloy. The regions of flow instability have been observed at high Z values and at low temperature of 700 °C and low strain rate of 0.001 s^?1. Further instability region has been found at temperature of 1000 °C and strain rates higher than 1 s^?1 and at temperature of 1100 °C and all range of strain rates.     

铸态粗晶Ti-5553钛合金高温变形行为与机理研究

本文借助Gleeble-3800热模拟试验机系统地研究了铸态粗晶Ti-5553合金在温度700 ℃~1100 ℃、应变速率为0.001 s_^-1~10 s_^-1条件下的高温变形行为。研究结果表明合金的流变应力对变形温度和速率都有强敏感性,流变软化过程也随变形参数的改变呈现出不同的模式。通过经典的动力学模型,建立了合金高温变形的本构关系和激活能分布图,进一步基于动态材料模型构建了合金的热加工图并实现了对不同加工区间变形机制的识别。合金在低温区(700 ℃)和高速率区( 1 s_^-1)均展现出失稳变形的特征,包括外部开裂、绝热剪切带、局部流变等机制,在实际加工中应对这些加工区域进行规避。合金在800 ℃及中低速率( 0.1 s_^-1)变形下的主导机制为α相的动态析出,在中高温(900 ℃-1100 ℃)及中低速率变形下的主导机制为动态回复与动态再结晶的结合。此外,合金在高温较低应变速率(1100 ℃/0.01 s_^-1)条件的变形中表现出大范围动态再结晶的行为特点并伴随稳定的流变软化,因此此条件附近的参数区间被认定为该合金的最优加工窗口,应在实际加工中给予优先考虑。     

Hot deformation behaviour and microstructure control in AlCrCuNiFeCo high entropy alloy

An AlCrCuNiFeCo high entropy alloy (HEA), which has simple face centered cubic (FCC) and body centered cubic (BCC) solid solution phases as the microstructural constituents, was processed and its high temperature deformation behaviour was examined as a function of temperature (700–1030 °C) and strain rate (10⁻³–10⁻¹ s⁻¹), so as to identify the optimum thermo-mechanical processing (TMP) conditions for hot working of this alloy. For this purpose, power dissipation efficiency and deformation instability maps utilizing that the dynamic materials model pioneered by Prasad and co-workers have been generated and examined. Various deformation mechanisms, which operate in different temperature–strain rate regimes, were identified with the aid of the maps and complementary microstructural analysis of the deformed specimens. Results indicate two distinct deformation domains within the range of experimental conditions examined, with the combination of 1000 °C/10⁻³ s⁻¹ and 1030 °C/10⁻² s⁻¹ being the optimum for hot working. Flow instabilities associated with adiabatic shear banding, or localized plastic flow, and or cracking were found for 700–730 °C/10⁻³–10⁻¹ s⁻¹ and 750–860 °C/10^−1.4–10⁻¹ s⁻¹ combinations. A constitutive equation that describes the flow stress of AlCrCuNiFeCo alloy as a function of strain rate and deformation temperature was also determined.     

Superplastic behaviour of two extruded gamma TiAl(Mo,Si) materials

The superplastic properties of two intermetallic Ti–46.8Al–1.2(Mo,Si) and Ti–46Al–1.5(Mo,Si) (at.%) materials produced by arc melting and processed by hot extrusion in the temperature range between 1200 and 1250 °C were studied. The materials exhibited an equiaxic near γ microstructure with γ grains finer than 1 μm and some band like region of γ grains with a size ranging from 5 to 20 μm. The finer grained zone contained a volume fraction of about 12 vol% in the 46.8Al material and about 25 vol% in the 46Al material of finely dispersed α₂-Ti₃Al particles. Mechanical tests performed on both materials at strain rates ranging from 4.6×10⁻⁴ to 10⁻² s⁻¹ in the temperature range of 975–1050 °C showed strain rate sensitivity exponents of about 0.5 at most strain rates. A maximum elongation to failure of about 300% was obtained for the 46.8Al material while about 900% was recorded for the 46Al material at 1050 °C at a relatively high strain rate of 8×10⁻³ s⁻¹. This difference is attributed to the larger volume fraction of α₂-phase particles in the 46Al material that leads to a decrease of the number and size of band like regions of coarse γ grains. The microstructure in the fine-grained areas of both materials remains essentially constant during deformation. The mechanical behavior at high temperature of these superplastic materials can be explained by considering grain boundary sliding as the dominant deformation mechanism.     

Processing map and microstructure evaluation of AA6061/Al2O3 nanocomposite at different temperatures

Hot compression behavior of Al6061/Al₂O₃ nanocomposite was investigated in the temperature range of 350–500 °C and the strain rate range of 0.0005–0.5 s^?1, in order to determine the optimum conditions for the hot workability of nanocomposite. The activation energy of 285 kJ/mol for the hot compression test is obtained by using hyperbolic sine function. By means of dynamic material model (DMM) and the corresponding processing map, safe zone for the hot workability of AA6061/Al₂O₃ is recognized at temperature of 450 °C and strain rate of 0.0005 s^?1 and at temperature of 500 °C and the strain rate range of 0.0005–0.5 s^?1, with the maximum power dissipation efficiency of 38%. Elongated and kinked grains are observed at 400 °C and strain rate of 0.5 s^?1 due to the severe deformation.     

加工参数对铸态AZ31B镁合金热变形行为及组织演变的影响

借助热压缩实验研究了变形温度、应变速率和变形量对铸态AZ31B镁合金热变形行为及组织演变的影响规律。结果表明:(1)峰值应力随着应变速率的降低和温度的升高而减小,主要的形核机制为晶界弓出形核、亚晶旋转形核、孪生诱发形核,以及连续再结晶;(2)低于400℃变形时,温度的升高有利于再结晶的发生及晶粒细化;高于400℃时,晶粒尺寸开始迅速增大;(3)在小于等于400℃变形时,低速率0.1 s~(-1)更有利于再结晶晶粒细化;当变形温度高于400℃时,中速率1 s~(-1)更有利于再结晶晶粒细化;(4)高温低速率变形时,变形量主要影响晶粒尺寸,而高温高速率变形时,变形量主要影响动态再结晶程度。