Interactions between Pre-strain and Dislocation Structures and Its Effect on the Hydrogen Trapping Behaviors

doi:10.1007/s40195-023-01568-x

Abstract

Abstract:

This work investigated the effect of pre-strain and microstructures and their interactions on hydrogen trapping behaviors in case of 1-GPa high-strength martensitic steel Fe-0.05C-0.30Si-1.10Mn-3.50Ni-0.53Cr-0.50Mo-0.03 V (wt%). We found that the trapped reversible and trapped irreversible hydrogen contents increased significantly after applying a pre-strain of 5%, with an increase in the trapped reversible hydrogen content from 0.6 ppm in the original sample to 2.1 ppm. The hydrogen desorption activation energy also showed a slight increase. The microstructural evolution revealed that the concomitant dislocation cell-twin duplex microstructure with high-density tangled dislocations after pre-strain substantially increased the trapped reversible hydrogen contents. Additionally, the tangled dislocations pinned by the nanoprecipitates acted as deep irreversible hydrogen traps, increasing the trapped hydrogen at high temperatures after applying 5% pre-strain. These findings provide an expanded understanding of the hydrogen trapping behaviors of pre-strained microstructures.

Key words: Hydrogen embrittlement, Hydrogen trapping, Pre-strain, Deformed microstructure, High-strength steel

Rongjian Shi, Yanqi Tu, Liang Yang, Saiyu Liu, Shani Yang, Kewei Gao, Xu-Sheng Yang, Xiaolu Pang. Interactions between Pre-strain and Dislocation Structures and Its Effect on the Hydrogen Trapping Behaviors[J]. Acta Metallurgica Sinica (English Letters), 2023, 36(7): 1193-1202.

Figures/Tables 8

Fig. 1 Microstructural characterization in the investigated high-strength martensitic steel before pre-strain. a TEM bright-field micrograph depicting the overall microstructure. b HRTEM image of one typical nanoprecipitate, with the corresponding FFT image in the inset. c IFFT image showing the lattice structure of the FCC nanoprecipitate. d HAADF image. The STEM-EDS mapping of the dotted region with nanoprecipitates in d: (e1) the STEM image, EDS mapping showing (e2) Fe, (e3) Ni, (e4) C, (e5) V, and (e6) Mo

Fig. 2 a Representative engineering stress-engineering strain curves from the normal and interrupted tensile tests. b Hydrogen desorption curves of the steels with and without 5% pre-strain after hydrogen charging. The heating rate was 100 °C/h from room temperature to 500 °C

Fig. 3 Electrochemical hydrogen permeation curve of the original sample. The effective Deff is 4.3 × 10−7 cm2 s−1

Fig. 4 Microstructural characterization of the investigated steel after pre-strain. a Overall TEM bright-field image, with the enlarged view shown in b, indicating the distribution of the dislocation substructure under deformation. c TEM bright-field image of the deformation nano-twins and d dark-field TEM images of NTs; the corresponding selected area electron diffraction patterns are indicated in the inset of c

Fig. 5 Distribution and the morphology of the a deformation twins and the b stacking faults (SF) that nucleated from the grain boundaries

Fig. 6 a Concomitant dislocation cell-twins duplex microstructure of the investigated steel after pre-strain. b Magnified view of the distribution and the morphology of the dislocation cells (indicated by the dotted lines) with the lath boundaries (red arrows)

Fig. 7 a Overall TEM bright-field micrograph indicating the distribution of dislocation cells embedded with the nanoprecipitates (yellow arrows). b Enlarged view of the tangled dislocations (blue arrows) and precipitates (yellow arrows) in the dislocation cell walls. c Enlarged view of the deformed precipitates deviated from the dislocation cell walls

Fig. 8 Details about the morphology of the precipitates with the surrounding dislocations under pre-strain. a TEM bright-field image. b IFFT image of the dislocations adjacent to the precipitate. c Magnified TEM image of the appearance of the deformation close to the precipitate/matrix interface

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