On the Thermodynamic Aspect of Interaction Between Dislocations and Highly Mobile Interstitial Solute: With Special Focus on Recent Progress in Pd-H System: A Review

doi:10.1007/s40195-016-0367-4

摘要/Abstract

Abstract:

It is well known that, in kinetics, the interaction between dislocations and interstitial solute normally exerts strong solute drag effect on dislocations, leading to strong solution hardening of the metals. However, due to the low mobility of interstitial solute in many metals, thermodynamic aspect of the interaction between dislocations and interstitial solute is often unobservable and omitted. It will be shown in this article by reviewing the H-induced behaviors in metal-H systems, especially the recent progress in Pd-H system that, when the interstitial solute atoms are highly mobile and able to collect in the vicinity of mobile dislocations easily, the scenario will be remarkably different. The interaction between dislocations and these highly mobile interstitial solute atoms, in thermodynamics, will reduce the line energy of dislocations and will facilitate the generation of dislocations, leading to an increase in dislocation density and an enhanced strain hardening of metals upon plastic deformation.

Key words: Plastic, deformation, Dislocation, Interstitial, solute, Strengthening, mechanism, Thermodynamics

. [J]. 金属学报英文版, 2016, 29(2): 120-128.

Sheng Li, Yu-Zeng Chen, Yu-Ke Cao, Feng Liu. On the Thermodynamic Aspect of Interaction Between Dislocations and Highly Mobile Interstitial Solute: With Special Focus on Recent Progress in Pd-H System: A Review[J]. Acta Metallurgica Sinica (English Letters), 2016, 29(2): 120-128.

图/表 7

Fig. 1 a Measured XRD profiles of the cold-rolled Pd-H alloys with different H/Pd ratios and well-annealed Pd, bWilliamson-Hall plots for the diffraction patterns of cold-rolled alloys and well-annealed Pd [10]

Fig. 2Concentration of the trapped hydrogen c t at lattice defects in cold-rolled Pd versus the chemical potential μH of H in Pd for samples with different H contents during deformation [29]

Fig. 3 Development of the dislocation density of cold-rolled Pd with increasing H content during cold rolling. The measurements were performed by two different methods: interpretation of the diffraction patterns of the samples using the method of Williamson-Hall plots and measurement of the relative dislocation density by evaluating the diffusion time of H through the Pd samples [29]

Fig. 4 a Vickers hardness (Hv) as a function of the initial H/Pd ratio, b linear fit of the measured Hv to square root of the measured dislocation density [28]

Fig. 5 The density of dislocations a and the concentration of deformation-induced vacancies b plotted as a function of the hydrogen concentration in the pre-charged samples [30]

Fig. 6 a True stress-strain curves of Pd and Pd-H alloys with different H concentrations, b linear fitting on ln σ tr-lnε tr curves and the resulting strain-hardening exponent n for Pd and Pd-H alloys [11]

Fig. 7 Stress-strain curves of H-free and H-charged Ni tested at different conditions: a room temperature, strain rate 3.33 × 10-4 s-1, b room temperature, strain rate 8.33 × 10-3 s-1 [35]

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