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<p>The deformation behavior of a high-Mn austenitic steel was investigated using in-situ straining transmission electron microscopy (TEM), with emphasis on the dynamic interaction between stacking faults and partial dislocations during plastic deformation. Owing to the low stacking-fault energy of the alloy, plastic deformation is primarily governed by Shockley partial dislocations, leading to extensive stacking-fault formation on multiple {111} planes. As deformation proceeds, stacking faults generated on different slip variants frequently intersect within grain interiors. Real-time observations reveal that these intersections act as strong deformation-induced barriers that impede partial dislocation motion, resulting in dislocation pile-up and localized strain concentration. Such interactions are considered to contribute significantly to strain hardening in low stacking-fault energy austenitic alloys. Despite their strong blocking effect, stacking-fault intersections are not strictly impenetrable. Under conditions of significant dislocation accumulation, the separation distance between leading and trailing partial dislocations can locally decrease, allowing temporary recombination into a perfect dislocation segment. The recombined dislocation adopts screw character, enabling cross-slip onto a secondary {111} slip plane, followed by re-dissociation into Shockley partial dislocations.These findings demonstrate that stacking-fault intersections function as dynamic microstructural features that both impede and mediate dislocation motion. The present in-situ TEM observations provide direct mechanistic insight into stacking-fault intersection-controlled dislocation dynamics and their role in strain hardening and local plastic accommodation in low stacking-fault energy austenitic steels.</p>

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In-situ TEM observation of stacking-fault intersection–controlled partial dislocation dynamics in high-Mn austenitic steel

  • 期刊论文

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  • 发表日期：

    2026年5月7日

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  • Sung-Dae Kim

摘要

The deformation behavior of a high-Mn austenitic steel was investigated using in-situ straining transmission electron microscopy (TEM), with emphasis on the dynamic interaction between stacking faults and partial dislocations during plastic deformation. Owing to the low stacking-fault energy of the alloy, plastic deformation is primarily governed by Shockley partial dislocations, leading to extensive stacking-fault formation on multiple {111} planes. As deformation proceeds, stacking faults generated on different slip variants frequently intersect within grain interiors. Real-time observations reveal that these intersections act as strong deformation-induced barriers that impede partial dislocation motion, resulting in dislocation pile-up and localized strain concentration. Such interactions are considered to contribute significantly to strain hardening in low stacking-fault energy austenitic alloys. Despite their strong blocking effect, stacking-fault intersections are not strictly impenetrable. Under conditions of significant dislocation accumulation, the separation distance between leading and trailing partial dislocations can locally decrease, allowing temporary recombination into a perfect dislocation segment. The recombined dislocation adopts screw character, enabling cross-slip onto a secondary {111} slip plane, followed by re-dissociation into Shockley partial dislocations.These findings demonstrate that stacking-fault intersections function as dynamic microstructural features that both impede and mediate dislocation motion. The present in-situ TEM observations provide direct mechanistic insight into stacking-fault intersection-controlled dislocation dynamics and their role in strain hardening and local plastic accommodation in low stacking-fault energy austenitic steels.