Structure and Texture Evolution of the Metastable Austenitic Steel during Cold Working
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CTURE, PHASE TRANSFORMATIONS, AND DIFFUSION
Structure and Texture Evolution of the Metastable Austenitic Steel during Cold Working M. V. Odnobokovaa, *, A. N. Belyakovb, I. N. Nugmanovc, and R. O. Kaibyshevb a
Institute for Physics of Advanced Materials, Ufa State Aviation Technical University, Ufa, 450008 Russia bBelgorod State University, Belgorod, 308015 Russia c Karimov’ Tashkent State Technical University, Tashkent, 100123 Uzbekistan *e-mail: [email protected] Received December 27, 2019; revised February 11, 2020; accepted March 10, 2020
Abstract—This work studies the structure and texture evolution in the 03Kh19N10 corrosion-resistant metastable austenitic steel (0.05C–18.2Cr–8.8Ni–1.65Mn–0.43Si–0.05P–0.04S wt %, and Fe for balance) during cold rolling, which results in twinning and martensitic transformation. The strain-induced martensite nucleates heterogeneously in the microshear bands and at their intersections. The fraction of strain-induced martensite increases with increasing true strain and approaches 80% at е = 3. The development of deformation twins, microshear bands, and martensitic crystallites results in the formation of a uniform nanocrystalline structure consisting of elongated γ/α' crystallites 100 nm in cross-section size after large deformation (е = 2–3). The austenite texture after cold rolling is characterized by the strong Brass ({110} 112) and Goss ({110}001) texture components, whereas the strain-induced martensite texture is characterized by strong texture component I* ({223}110) and an increased orientation density along γ fiber (111 ∥ ND). The orientation of the γ/α'-phase boundaries depends on the strain value. Keywords: corrosion-resistant austenitic steel, cold rolling, deformation twinning, martensitic transformation, deformation texture DOI: 10.1134/S0031918X20070066
INTRODUCTION Developing the technologies for producing semifinished products from high-strength austenitic chromium–nickel steels [1–3] is an important task. These steels are widely used in various industries because of their corrosion properties. Heat treatment of austenitic chromium–nickel steels traditionally includes heating in the 1000–1100°C temperature range and fast cooling. This treatment fixes γ solid solution with homogeneously-distributed alloying elements and without М23С6 carbides, which provides the best corrosion properties [1, 4]. However, the austenitic chromium–nickel steels have a low strength after the traditional solid-solution treatment, which restricts their application as a structural material. The severe plastic deformation of austenitic steels increases their strength significantly both by producing ultrafinegrained (UFG) and nanocrystalline (NC) structures, as well as by producing strain-induced martensite [4‒6]. The kinetics of the formation of these structures in materials with a fcc lattice is largely dependent on the stacking fault energy (SFE). Materials with low SFE (from 20 to 40 mJ/m2) are characterized by a high rate of structural fragmentation due to deformatio
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