热轧带钢连续冷却过程中相变体积分数的计算

基于相变动力学原理 ,在充分考虑变形对相变影响的情况下研究了奥氏体向铁素体、珠光体和贝氏体相变的动力学。探索了热轧带钢连续冷却过程中相变体积分数的计算方法。用此方法进行的计算机模拟与实验结果相当吻合。     

热轧管线钢冷却过程相变预测模型

为能够精确模拟管线钢连续冷却过程中组织演变行为,建立了一种包括相变潜热模型、温度场模型和相变体积分数模型在内的数学耦合模型,深入研究了含碳量和冷却速度对相变潜热的影响,以及相变潜热对冷却过程中温度分布的影响.将耦合模型的计算值与实验数据进行对比,两者吻合较好,且耦合模型的计算结果与普通相变模型计算结果相比更加精确,证明了该耦合模型能够准确预测X80管线钢冷却过程中的组织演变.     

一水硫酸锂非等温动力学参数的确定

利用DTA技术研究了一水硫酸锂脱水及固－固相变的非等温动力学。并运用Kissinger和Ozawa方法计算了脱水及固－固相变过程的表观活化能和反应级数,两种方法的结果一致。     

热轧带钢在冷却过程中的内应力解析

针对热轧带钢的冷却过程,开发了温度、相变的内应力的耦合解析模型,该模型采用有限元法,同时考虑了相变的温度依存性、相变潜热、相变膨胀。通过该数值解析模型,能够模拟热轧带钢在冷却过程中温度一组织内应力的演变过程,计算结果与实测值符合良好。     

基于二元相图精确计算钛合金α＋β/β相变点

基于Ti—X二元相图提出了一种精确计算钛合金α＋β/β相变点的方法,并根据该方法给出了一个计算公式。用该公式对几十个合金的相变点进行了计算,并与实测值进行了对比,除个别合金偏差较大外,其余合金的相变点计算值与测试值相差一般不超过±5℃。这表明该方法和公式涵盖面广、精确度高,适用于绝大多数钛合金的相变点计算。     

基于热膨胀法与相体积计算模型研究连铸坯冷却过程中奥氏体相变行为

采用热膨胀仪测试研究了Q450NQR1钢连铸坯5℃·min-1及20℃·min-1冷却速率下的线性热膨胀(ΔL/L₀)和热膨胀系数随温度的变化规律.在此基础上,建立了一种基于平均原子体积的相体积计算模型,量化研究了奥氏体相变过程中各相体积分数的变化规律,并在将计算结果与显微组织观察结果对比分析基础上,讨论了连铸冷却速率对铸坯奥氏体相变过程的影响.结果表明:该计算模型可以较为准确地描述铸坯的奥氏体相变过程,适用于多相连续析出相变;随着冷却速率的增大,铸坯热膨胀曲线中对应于铁素体和珠光体析出的两个变化峰向低温区移动,峰值明显增大;冷却速率由5℃·min-1上升至20℃·min-1时,铁素体及珠光体起始析出温度分别降低约32℃和37℃,最终体积分数分别由0.894和0.106变为0.945和0.055.      

相变储热材料的研究进展

随着材料科学技术的发展,相变储热材料应用愈来愈广泛,文章基于相变储热材料研究方面的调研,对其进行分类与介绍,并概述了该材料潜在的应用,同时为相变储热材料的研究指出了发展方向.     

热轧带钢FeO共析转变动力学行为分析与预测

热轧后的带钢表面会形成氧化铁皮，其中的FeO在卷取之后的冷却过程中会发生共析相变，形成由Fe与Fe₃O₄共同组成的共析组织。传统对FeO共析相变的研究，多集中在诸如化学成分、相变环境等因素对共析反应的定性分析上，但针对相变的具体进程却少有模型化的分析和计算。同时，由于实际生产中FeO的相变过程多是在连续冷却过程中发生，相变过程受到了不同时刻温度变化的叠加影响，这也加大了研究的困难程度。为此，以常见的普碳钢为例，首先使用同步热分析仪进行了不同温度及时间下氧化铁皮的等温结构转变试验，统计了30个试验节点下的共析组织在FeO中的体积分数，之后基于Johnson-Mehl-Avrami-Kolmogorov(JMAK)方程建立了FeO在等温过程下共析相变的动力学模型，通过试验数据求解其中的关键参数，得到了等温转变条件下FeO中共析组织体积分数与时间的关系，可直接绘制描述FeO共析转变的Time-Temperature-Transformation(TTT)曲线。在此基础上，结合Scheil可加性法则，建立了连续冷却过程中FeO的共析相变模型，通过计算...     

Fe-Mn-C系γ→α相变驱动力计算

本文利用Hillert-Staffanson模型计算了Fe-1.33Mn-0.47C(at％)系Y→α相变驱动力G_v~Y→α。结果表明,ΔG_V~Y→α与温度的关系可以简单地表示为相关系数为0.9992。这一计算结果适用于成分与之相近的C-Mn钢和微合金钢的Y→α相变驱动力估算。     

1000 MPa级冷轧双相钢奥氏体的等时相变动力学

在DIL 805A膨胀仪上测定了1000 MPa级冷轧双相钢在连续加热过程中的热膨胀曲线.根据杠杆定律得到的奥氏体体积分数的计算值与定量金相测量值符合较好.奥氏体的等时相变动力学可以很好地由JMAK形式的方程描述.文中还分析了冷轧压下率和加热速度对奥氏体等时相变动力学的影响,探讨了连续加热奥氏体相变过程中相界面的平衡状态.      

Effect of Niobium on Isothermal Transformation of Austenite to Ferrite in HSLA Low-Carbon Steel

Using thermomechanical simulation experiment,the kinetics of the isothermal transformation of austenite to ferrite in two HSLA low-carbon steels containing different amounts of niobium was investigated under the conditions of both deformation and undeformation.The results of optical microstructure observation and quantitative metallography analysis showed that the kinetics of the isothermal transformation of austenite to ferrite in lower niobium steel with and without deformation suggests a stage mechanism,wherein there exists a linear relationship between the logarithms of holding time and ferrite volume fraction according to Avrami equation,whereas the isothermal transformation of austenite to ferrite in high niobium steel proceeds via a two stage mechanism according to micrographs,wherein,the nucleation rate of ferrite in the initial stage of transformation is low,and in the second stage,the rate of transformation is high and the transformation of residual austenite to ferrite is rapidly complete.Using carbon extraction replica TEM,niobium carbide precipitation for different holding time was investigated and the results suggested that NbC precipitation and the presence of solute niobium would influence the transformation of austenite to ferrite.The mechanism of the effect of niobium on the isothermal transformation was discussed.     

1.6 GPa级中碳高强贝氏体钢残余奥氏体调控机理

 为了研究中碳高强贝氏体钢中的残余奥氏体体积分数在不同等温情况下的变化规律,通过X射线衍射试验、热模拟试验和扫描电子显微镜观察等,分析了等温淬火条件对中碳高强贝氏体钢中残余奥氏体体积分数和组织的影响。结果表明,最终残余奥氏体的体积分数受贝氏体相变和马氏体相变的共同影响。贝氏体相变量决定了未转变奥氏体的体积分数及其化学稳定性,从而影响随后的马氏体相变量及最终残余奥氏体体积分数。此外,随着相变温度的升高,开始由于贝氏体相变量逐渐减少,残余奥氏体体积分数先增加(300~350 ℃),随后由于马氏体相变量增加,残余奥氏体体积分数减少(350~400 ℃)。     

Effect of ausforming on isothermal bainitic transformation and microstructure

Deformation affects the microstructure and morphology of the parent austenite, which affects the subsequent bainite transformation. The effects of ausforming on bainite transformation and microstructure were investigated by means of thermal simulation experiment, TEM and SEM etc. Different deformation temperatures and deformation strains were designed. The amount of bainitic transformation during isothermal holding and the volume fraction of retained austenite at room temperature were analyzed. The results show that the isothermal bainitic transformation is promoted by the deformation at 300?? and 400??. Moreover, the lower deformation temperature leads to larger amount of bainite. In addition, the volume fraction of retained austenite increases with the increase of the deformation strain, and more retained austenite can be obtained by decrease the deformation temperature. It indicates that deformation at lower temperature contributes to the mechanical stabilization of austenite.     

Effect of Warm-Rolled Pearlite Microstructural Features on Austenitic Transformation

The austenite transformation characteristics for various warm-rolled pearlite during rapid heating were investigated. The results indicate that the start temperature (Ts) is sensitive to the microstructural feature of pearlite,whereas the dislocation plays an important role in the transformation rate; at the same time, the uniformity of austenite grains is more or less affected by the amount of spheroidized pearlite. A critical effect on the state of austenite grain is created through the influence of initial microstructures on the start temperature of transformation.     

Modeling of Incubation Time for Austenite to Ferrite Phase Transformation

 The giant stress-impedance (GSI) effect in as-cast and DC current annealed Co71.8Fe4.9Nb0.8Si7.5B15 amorphous glass-covered wires is presented. The SI ratio of the as-cast sample exhibits negative GSI effect. For the sample annealed by 60 mA DC current, the SI ratio first increases with applied tensile stress, then decreases with the applied tensile stress. The maximum ΔZ/Z ratio of 304% is obtained. Frequency dependence in the range from 1 to 110 MHz of the GSI effect is investigated. Experimental results show that the real part R and the imaginary part X of impedance play an important role at high frequency and low frequency, respectively. At 1 MHz, the maximum ΔX/X of 1 448% is obtained. At 110 MHz, the maximum ΔR/R ratio of 648% is obtained.     

Effect of Austenite Deformation on Continuous Cooling Transformation Microstructures for 22CrSH Gear Steel

 The effect of compressive deformation of austenite on continuous cooling transformation microstructures for 22CrSH gear steel has been investigated using a Gleeble 1500 thermal simulator. The experimental results show that the deformation of austenite promotes the formation of proeutectoid ferrite and pearlite, and leads to the increase of critical cooling rate of proeutectoid ferrite plus pearlite microstructure. The grain boundary allotriomorphic ferrite occupies the austenite grain surfaces when the prior deformation takes place or the cooling rate is decreased, which causes a transition from bainite to acicular ferrite. The deformation enhances the stability of transformation from austenite to acicular ferrite, which results in an increase of M/A constituent.     

09MnVTiN钢再结晶奥氏体连续冷却转变的研究

本文利用Formastor-Press压力膨胀仪测试09MnVTiN钢热变形后再结晶奥氏体的连续冷却转变动力学曲线,并用金相法分析不同阶段淬火试样的组织。结果表明,再结晶控轧后,奥氏体区的冷却速度(1000～820℃)对再结晶奥氏体的晶粒尺寸和随后的连续冷却转变动力学都有影响。     

405不锈钢高温组织转变研究

通过热膨胀法以及Thermo-Calc热力学计算软件对SA240-405不锈钢铁素体向奥氏体转变的温度进行了测量和计算。进一步结合淬火与回火热处理,分析了405不锈钢在高温下组织随温度与时间的变化关系。研究结果表明,405不锈钢铁素体向奥氏体开始转变的温度为795~832℃,转变终了温度为910~925℃。温度高于1 050℃,随温度升高,奥氏体逐渐向铁素体转变,淬火后的马氏体含量降低。在950及980℃淬火,得到的组织为马氏体与铁素体的双相组织,淬火时间为30~60 min得到的硬度较高;进一步延长淬火时间,硬度逐渐降低。在730℃回火后得到的组织为铁素体与回火马氏体,无明显残余奥氏体,回火后组织的硬度随时间延长逐渐降低。     

形变诱导铁素体逆相变过程中的组织及取向变化

 通过对普碳钢Q235在Gleeble1500热模拟机上变形后的微观组织分析,研究了组织中形变诱导的铁素体在变形后保温阶段转变为奥氏体的逆相变现象;并利用背散射电子衍射(EBSD)技术分析了晶粒取向变化。结果表明,在变形后的保温过程中,形变诱导的铁素体先逆相变为奥氏体,同时伴随着诱导铁素体晶粒的长大;然后随着变形后保温时间的延长,逆相变后的奥氏体由马氏体相变逐渐过渡到铁素体的平衡转变,相应地铁素体由具有少量亚结构的形变诱导铁素体逐渐转变为具有较多亚结构的先共析铁素体。     

Fe-C-Mn-Al系TRIP钢两相区奥氏体转变模拟

为了研究Fe-C-Mn-A1系TRIP钢两相区奥氏体化过程中合金元素在奥氏体和铁素体中的分布,利用热膨胀仪、金相显微镜、电子探针等仪器,在对TRIP钢两相区奥氏体化过程进行热力学与动力学分析的基础上,建立了两相区奥氏体化过程的扩散模型,采用显式有限体积法对800℃与840℃的奥氏体化过程进行了数值求解.模拟结果表明:奥氏体转变初期受C元素在奥氏体中的扩散控制达到亚平衡,奥氏体转变速率较快;此时A1元素在奥氏体与铁素体界面处的浓度差较显著,Mn元素在奥氏体与铁素体界面处的浓度差不显著.奥氏体转变后期受Mn元素在铁素体内的扩散控制,转变速率较慢;此时A1元素在铁素体内已大量富集,Mn元素在奥氏体与铁索体界面处有较显著的浓度差.