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Modeling of massive transformation in substitutional alloys

机译:替代合金中大量转变的建模

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In a preceding article,[1] a sharp-interface numerical model for diffusional transformation in multicomponent systems has been developed. A finite mobility (friction) of the interface is assumed, and equal jumps in chemical potentials across the migrating interface for all components are predicted. The time-dependent concentration profiles and the position of the interface are obtained by solving the evolution problem. Depending on temperature and chemical composition, the numerical model provides simulations exhibiting features of diffusional transformations or massive transformations. The massive transformation displays the features of a steady-state process. In this article, the steady-state solutions of the problem are presented in order to describe the kinetics of the massive transformation in a more convenient and transparent way. The contact conditions at the moving interface are the same as in the numerical model.[1] The ideal-solution approach is used to describe the diffusion in the spikes occurring in front of the interface. The diffusion in spikes is described by using a diffusivity tensor with nonzero off-diagonal terms or a diagonal tensor corresponding to Manning’s or Fick’s concept of diffusion, respectively. The solutions show that the kinetics of the massive transformation is controlled exclusively by friction in the interface. The steady-state solutions are applied to the γ/α phase transformation in the Fe-Cr-Ni system, and the simulations are compared successfully with the results of the numerical model.[1] For realistic interface mobilities, the computed thicknesses of the spikes in the Fe-Cr-Ni system are, however, much lower than the interatomic distance in a wide range of temperatures. In that case, the spike looses its physical meaning and the numerical model is not applicable. On the other hand, for other systems (e.g., Cu-Zn), the thicknesses of the spikes are estimated to be on the order of the interatomic distances in a wide range of temperatures. In these systems, spike diffusion seems to be a relevant dissipation process, and the numerical model is applicable.
机译:在先前的文章中,[1] 开发了用于多组分系统中扩散转换的尖锐界面数值模型。假定界面具有有限的迁移率(摩擦力),并且可以预测所有组分在迁移界面上化学势的均等跃变。通过解决演化问题获得了随时间变化的浓度分布图和界面位置。取决于温度和化学成分,数值模型提供了具有扩散变换或大规模变换特征的模拟。大规模转换显示了稳态过程的特征。在本文中,提出了问题的稳态解,以便以更方便和透明的方式描述大规模变换的动力学。运动界面处的接触条件与数值模型中的条件相同。[1] 理想解法用于描述界面前部尖峰中的扩散。尖峰的扩散是通过分别使用非零非对角项的扩散张量或对应于Manning或Fick的扩散概念的对角张量来描述的。这些解决方案表明,大量转变的动力学仅受界面摩擦的控制。将稳态解应用于Fe-Cr-Ni体系中的γ/α相变,并将仿真与数值模型的结果成功进行了比较。[1] 对于现实的界面迁移率,然而,在宽温度范围内,Fe-Cr-Ni系统中尖峰的计算厚度远小于原子间距离。在这种情况下,尖峰会失去其物理意义,因此数值模型不适用。另一方面,对于其他系统(例如,Cu-Zn),在宽温度范围内,尖峰的厚度估计为原子间距离的量级。在这些系统中,尖峰扩散似乎是一个相关的耗散过程,并且数值模型是适用的。

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  • 来源
    《Metallurgical and Materials Transactions A》 |2006年第1期|125-132|共8页
  • 作者单位

    the Institute of Physics of Materials Academy of Sciences of the Czech Republic CZ-616 62 Brno Czech Republic;

    the Institute of Mechanics Montanuniversität Leoben A-8700 Leoben Austria;

    Institute of Mechanics Montanuniversität Leoben Austria;

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