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Understanding the mechanism of martensitic transformation is of greatimportance in developing advanced high strength steels, especiallyTRansformation-Induced Plasticity (TRIP) steels. The TRIP effect leads toenhanced work-hardening rate, postponed onset of necking and excellentformability. In-situ transmission electron microscopy has been performed tosystematically investigate the dynamic interactions between dislocations andalpha martensite at microscale. Local stress concentrations, e.g. from notchesor dislocation pile-ups, render free edges and grain boundaries favorablenucleation sites for alpha martensite. Its growth leads to partial dislocationemission on two independent slip planes from the hetero-interface when theaustenite matrix is initially free of dislocations. The kinematic analysisreveals that activating slip systems on two independent {111} planes ofaustenite are necessary in accommodating the interfacial mismatch strain. Fulldislocation emission is generally observed inside of austenite regions thatcontain high density of dislocations. In both situations, phase boundarypropagation generates large amounts of dislocations entering into the matrix,which renders the total deformation compatible and provide substantial strainhardening of the host phase. These moving dislocation sources enable plasticrelaxation and prevent local damage accumulation by intense slipping on thesofter side of the interfacial region. Thus, finely dispersed martensitedistribution renders plastic deformation more uniform throughout the austeniticmatrix, which explains the exceptional combination of strength and ductility ofTRIP steels.

Dislocation Activities at the Martensite Phase Transformation Interface in Metastable Austenitic Stainless Steel: An In-situ TEM Study