Dynamic Recrystallization and Phase-Specific Corrosion Performance in a Super Duplex Stainless Steel

Mondal, Riya; Bonagani, Sunil Kumar; Raut, P.; Kumar, Saurabh; Sivaprasad, P.V.; Chai, Guocai; Kain, Vivekanand; Samajdar, Indradev

doi:10.1007/s11665-021-06221-1

Cited by 5 publications

(2 citation statements)

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“…Hot deformation of steels is accompanied by softening processes: dynamic recovery and recrystallization [5][6][7][8]. The mechanism of dynamic softening depends on temperature, strain and strain rate, grain size, stacking fault energy, and amount of precipitation [9][10][11].…”

Section: Introductionmentioning

confidence: 99%

Study on the Hot Deformation Behavior of Stainless Steel AISI 321

et al. 2022

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In this study, the hot deformation behavior of austenitic Ti-modified AISI 321 steel with a relatively high content of carbon (0.07 wt.%) and titanium (0.50 wt.%) was studied in the temperature range of 1000–1280 °C and strain rates in the range of 0.01–1 s−1. Hot deformation was carried out with uniaxial compression of cylindrical specimens on a Gleeble 3800 thermomechanical simulator. It is shown that the flow stress increased with a decrease in the deformation temperature and an increase in the strain rate. The shape of the stress-strain curves indicates that, at high temperatures and low strain rates, the hot deformation of AISI 321 steel was accompanied by dynamic recrystallization. The passage of dynamic recrystallization was confirmed by microstructural studies. Hyperbolic sine type of constitutive equation with deformation activation energy Q = 444.2 kJ·mol−1 was established by analyzing the experimental flow stresses. The power-law dependences of the critical strain necessary for the onset of dynamic recrystallization and the size of recrystallized grains on the Zener–Hollomon parameter were established. The value of the parameter Z = 5.6 × 1015 was determined, above which the dynamic recrystallization was abruptly suppressed in the steel under study. It is speculated that the suppression of dynamic recrystallization occurs due to dispersed precipitates of titanium carbonitrides.

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Section: Introductionmentioning

confidence: 99%

Study on the Hot Deformation Behavior of Stainless Steel AISI 321

et al. 2022

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“…2304 grade) are one of the most significant classes of stainless steels. [1][2][3] Their microstructure is made up of ferrite and austenite phases with equal volume fractions (roughly 50% vs. 50%). 1,2 These steels possess superior mechanical properties, such as high strength, proper elastic modulus between 180 and 200 GPa at 300°C, and good fracture toughness as well as excellent corrosion/corrosion-mechanical behavior due to their microstructure.…”

Section: Introductionmentioning

confidence: 99%

Microstructure and tensile-shear behavior of dissimilar resistance spot welds between 2304 duplex stainless steel and Inconel 718 superalloy

Badkoobeh

Mostaan

Rafiei

et al. 2022

Proceedings of the Institution of Mechanical Engineers, Part L:

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Dissimilar joints between duplex stainless steels and nickel-based superalloys are of high significance in some industries. In this research, 2304 duplex stainless steel and Inconel 718 superalloy were welded by the resistance spot welding technique. The studies showed that the fusion zone microstructure was composed of a dendritic structure related to the grains of nickel-based solid solution ( γ-phase) and γ′ islands. The heat-affected zone microstructure of 2304 duplex stainless steel includes the austenite phase with a slight volume fraction and the ferrite phase with a high volume fraction. The austenite phase was formed with two morphologies of Widmanstätten and grain boundary allotriomorphs. The heat-affected zone microstructure of Inconel 718 superalloy also contained γ phase (nickel-based solid solution), annealing twins, and some precipitates. The results of the tensile-shear test revealed that tensile-shear strength (i.e. peak load) and fracture energy were increased by increasing the welding current from 1 to 2 kA and the welding time from 1 to 2 s. However, they were reduced by increasing the welding current from 2 to 4 kA and the welding time from 2 to 4 s. This was caused by the surface splash between the electrodes and the sheets. In the above-mentioned range, an increase in the welding current and time may also intensify the surface splash. It was also found that when the welding time was constant (i.e. 2 s), the spot weld obtained at the welding current of 1 kA failed by interfacial fracture mode. All spot welds obtained at the welding currents of 2, 3, and 4 kA failed by pull-out fracture mode. On the other hand, all spot welds associated with the welding times of 1, 2, 3, and 4 s failed by PF mode when the welding current was constant (i.e. 3 kA).

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