Deformation microstructures and tensile properties of an austenitic stainless steel subjected to multiple warm rolling

Yanushkevich, Zhanna; Lugovskaya, A.; Belyakov, Andrey; Kaibyshev, Rustam

doi:10.1016/j.msea.2016.05.008

Cited by 54 publications

(26 citation statements)

References 31 publications

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“…[24,25] In this case, the mean grain size can be also expressed by a power law function of Z with a much smaller exponent of about À 0.1. [45,46] The present data (the range of warm working in Figure 10) display remarkable deviation from the D DRX~Z À0.1 line as could be expected for CDRX. This discrepancy is caused by insufficient strain for the development of continuous dynamic recrystallization, which requires much larger strain to make a meaningful contribution to the microstructure evolution.…”

Section: A Mechanisms Of Microstructure Evolutionsupporting

confidence: 70%

“…À 0.33, which is an average of those of À 0.27 to À 0.4 reported in other studies on discontinuous dynamic recrystallization (DDRX) in austenite during hot working. [44][45][46][47] On the other hand, the deformation microstructures evolved during warm deformation are generally associated with continuous dynamic recrystallization (CDRX). [24,25] In this case, the mean grain size can be also expressed by a power law function of Z with a much smaller exponent of about À 0.1.…”

Section: A Mechanisms Of Microstructure Evolutionmentioning

confidence: 99%

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Effect of Warm to Hot Rolling on Microstructure, Texture and Mechanical Properties of an Advanced Medium-Mn Steel

Tikhonova

Torganchuk

Brasche

et al. 2019

Metall Mater Trans A

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The deformation microstructures and mechanical properties were studied in a medium-Mn austenitic steel subjected to warm-to-hot rolling. During warm rolling at temperatures of T < 1073 K the structural changes were controlled by dynamic and static recovery leading to a pancaked work-hardened microstructure, during hot rolling at T ‡ 1073 K-by discontinuous dynamic and post-dynamic recrystallization resulting in equiaxed grains. The grain size decreased while the dislocation density increased with a decrease in rolling temperature. A decrease in rolling temperature enhanced the texture development, which consisted of relatively strong Brass, S and P components. The Brass component exhibited the strongest temperature dependence. A decrease in rolling temperature resulted in significant strengthening of the steel. The yield strength increased from 340 to 950 MPa as rolling temperature decreased from 1373 K to 773 K. Both the grain refinement and the work-hardening contributed to the strengthening.

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Section: A Mechanisms Of Microstructure Evolutionsupporting

confidence: 70%

Section: A Mechanisms Of Microstructure Evolutionmentioning

confidence: 99%

Effect of Warm to Hot Rolling on Microstructure, Texture and Mechanical Properties of an Advanced Medium-Mn Steel

Tikhonova

Torganchuk

Brasche

et al. 2019

Metall Mater Trans A

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“…Given the typical grain sizes in similar alloys subjected to similar processing [69,70], it is expected that the grain size of the current samples will be such that the grain size strengthening will follow the Hall-Petch relationship (Equation (6), where σ y is the yield strength, σ 0 is the yield strength attributed to other strengthening mechanisms, i.e., the yield strength of the material in the very large-grained condition, equal to σ P + σ S + σ O in the current study, K g is the Petch coefficient, and d is the grain size and is expected to be between 1 µm and 100 µm) [37][38][39][40][41].…”

Section: Work Hardening and Grain Refinementmentioning

confidence: 99%

“…Approximate values may be calculated from thermokinetic precipitation simulations in Thermo-Calc Prisma (Figure 4). Another approach asserts that the Orowan strengthening can be calculated by using the Bacon-Kocks-Scattergood equation (Equation (11), where A ≈ 0.2 is a coefficient related to the type of dislocations [67][68][69][70][71][72][73], D is a harmonic average that describes the two limit cases of the Orowan strengthening (small, widely spaced particles and relatively large, closely spaced particles), and all other symbols have the meaning defined previously). The harmonic average is given by Equation (12), where D p = 2r p , and L P = L + 2r p is the separation of the precipitate centers [81].…”

Section: Precipitate Strengtheningmentioning

confidence: 99%

Modelling of Strengthening Mechanisms in Wrought Nickel-Based 825 Alloy Subjected to Solution Annealing

Al-Saadi

Sandberg

Jönsson

et al. 2021

Metals

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Wrought nickel-based Alloy 825 is widely used in the oil and gas industries, attributed to its high strength at temperatures up to 540 °C. However, differences in mechanical properties arise in finished components due to variations in both grain size and dislocation density. Numerous experimental studies of the strengthening mechanisms have been reported and many models have been developed to predict strengthening under thermomechanical processing. However, there are debates surrounding some fundamental issues in modeling and the interpretation of experimental observations. Therefore, it is important to understand the evolution of strain within the material during the hot-forging process. In addition, there is a lack of research around the behavior during hot deformation and subsequent stabilization of Alloy 825. This article investigates the origin of this strength and considers a variety of strengthening mechanisms, resulting in a quantitative prediction of the contribution of each mechanism. The alloy is processed with a total forging strain of 0.45, 0.65, or 0.9, and subsequent annealing at a temperature of 950 °C, reflecting commercial practice. The microstructure after annealing is similar to that before annealing, suggesting that static recovery is dominant at this temperature. The maximum yield strength and ultimate tensile strength were 348 MPa and 618 MPa, respectively, obtained after forging to a true strain of 0.9, with a ductility of 40%. The majority of strengthening was attributed to grain refinement, the dislocation densities that arise due to the large forging strain deformation, and solid solution strengthening. Precipitate strengthening was also quantified using the Brown and Ham modification of the Orowan bowing model. The results of yield strength calculations are in excellent agreement with experimental data, with less than 1% difference. The interfacial energy of Ti(C,N) in the face-centered cubic matrix of the current alloy has been assessed for the first time, with a value of 0.8 mJm−2. These results can be used by future researchers and industry to predict the strength of Alloy 825 and similar alloys, especially after hot-forging.

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“…More generally, since austenite and ferrite phases have different elastic and plastic properties in addition to different thermal expansion coefficients, they should act differently during a deformation process. The microstructural and associated hardening evolutions that take place during the hot deformation of single phase austenitic and ferritic stainless steels have been extensively investigated in several research works [7][8][9][10][11][12]. It was already concluded that easy dislocation annihilation and rearrangement, leading to dynamic recovery, occurs in ferrite.…”

Section: Introductionmentioning

confidence: 99%

Microstructure, mechanical behavior, and crystallographic texture in a hot forged dual-phase stainless steel

Badji

Cheniti

Kahloun

et al. 2021

Int J Adv Manuf Technol

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In this work, the hot forging behavior of a dual phase stainless steel in the temperature range of 850 -1250 °C was investigated. The study revealed the occurrence of a significant cracking phenomenon for processing temperatures below 950 °C that was attributed to the combined effect of intermetallic precipitation and severe deformation. EBSD examination highlighted the occurrence of continuous dynamic recrystallization in both ferrite and austenite microstructures for processing temperatures above 1050 °C. Increasing the hot forging temperature to 1250 °C increased the low angle grain boundaries fraction and lowered the one of the high angle grain boundaries. This was accompanied by a gradual change in the crystallographic texture of the material. The mechanical behavior investigation showed that the steel plasticity, sharply dropped after forging at 850°, was gradually recovered after hot forging at temperatures above 1050°C. This was confirmed by nanoindentation measurements that revealed a remarkable increase of the hardness and young modulus of the steel after hot forging at 850°C and 950°C due to the dislocation nucleation and the  phase precipitation at /δ interface. The enhancement of dislocation movement at the vicinity of the grain boundaries due to the absence of  phase as well as the dynamic recovery and recrystallization occurring in the temperature range of 1050°C -1250 °C improved the global mechanical properties of the hot forged steel.

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Deformation microstructures and tensile properties of an austenitic stainless steel subjected to multiple warm rolling

Cited by 54 publications

References 31 publications

Effect of Warm to Hot Rolling on Microstructure, Texture and Mechanical Properties of an Advanced Medium-Mn Steel

Effect of Warm to Hot Rolling on Microstructure, Texture and Mechanical Properties of an Advanced Medium-Mn Steel

Modelling of Strengthening Mechanisms in Wrought Nickel-Based 825 Alloy Subjected to Solution Annealing

Microstructure, mechanical behavior, and crystallographic texture in a hot forged dual-phase stainless steel

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