Exploring the influence of Al content on the hot deformation behavior of Fe-Mn-Al-C steels through 3D processing map

Wu, Zhiqiang; Tang, Yubo; Chen, Wei; Lu, Liwei; Li, Eric; Li, Zhichao; Ding, Hua

doi:10.1016/j.vacuum.2018.10.079

Cited by 50 publications

(21 citation statements)

References 39 publications

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“…In addition, Al can lead to a specific weight reduction, and a 1.3% reduction in density was obtained per 1 wt% addition of Al [17]. Due to the addition of the large amount of Al (~10 wt.%), a new type of steel, namely low-density steel, has been formed [18]. The strength of oxide dispersion strengthened steels (ODSs) also increased with Al addition due to the back stress strengthening combined with Orowan strengthening [19].…”

Section: Of 17mentioning

confidence: 99%

Tensile Properties and Microstructural Evolution of an Al-Bearing Ferritic Stainless Steel at Elevated Temperatures

Han

Sun

et al. 2020

Metals

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The influence of temperature and strain rate on the hot tensile properties of 0Cr18AlSi ferritic stainless steel, a potential structural material in the ultra-supercritical generation industry, was investigated at temperatures ranging from 873 to 1123 K and strain rates of 1.7 × 10−4–1.7 × 10−2 s−1. The microstructural evolution linked to the hot deformation mechanism was characterized by electron backscatter diffraction (EBSD). At the same strain rate, the yield strength and ultimate tensile strength decrease rapidly from 873 K to 1023 K and then gradually to 1123 K. Meanwhile, both yield strength and ultimate tensile strength increase with the increase in strain rate. At high temperatures and low strain rates, the prolonged necking deformation can be observed, which determines the ductility of the steel to some extent. The maximum elongation is obtained at 1023 K for the strain rates of 1.7 × 10−3 and 1.7 × 10−2 s−1, while this temperature is postponed to 1073 K once decreasing the strain rate to 1.7 × 10−4 s−1. Dynamic recovery (DRV) and continuous dynamic recrystallization (CDRX) are found to be the main softening mechanisms during the hot tensile deformation. With the increase of temperature and the decrease of strain rate (i.e., 1123 K and 1.7 × 10−4 s−1), the sub-grain coalescence becomes the main mode of CDRX that evolved from the sub-grain rotation. The gradual decrease in strength above 1023 K is related to the limited increase of dynamic recrystallization and the sufficient DRV. The area around the new small recrystallized grains on the coarse grain boundaries provides the nucleation site for cavity, which generally results in a reduction in ductility. Constitutive analysis shows that the stress exponent and the deformation activation energy are 5.9 and 355 kJ·mol−1 respectively, indicating that the dominant deformation mechanism is the dislocations motion controlled by climb. This work makes a deeply understanding of the hot deformation behavior and its mechanism of the Al-bearing ferritic stainless steel and thus provides a basal design consideration for its extensive application.

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Section: Of 17mentioning

confidence: 99%

Tensile Properties and Microstructural Evolution of an Al-Bearing Ferritic Stainless Steel at Elevated Temperatures

Han

Sun

et al. 2020

Metals

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“…Deformation temperature and strain rate are important factors controlling the hot deformation flow stress. The hyperbolic sinusoidal constitutive equation in the Arrhenius model has been widely used to describe the complex relationships among flow stress, heat distortion temperature, and strain rate [8][9][10][11][12][13][14][15][16][17][18][19]27]. Sellars and McTegart proposed the use of a hyperbolic sine function including the thermal deformation activation energy Q and temperature T to describe the thermal activation behavior of the material.…”

Section: Constitutive Equationsmentioning

confidence: 99%

“…Therefore, the unstable region of the material in hot deformation must be identified in order to determine a suitable processing window [34,35]. On the basis of the principle of irreversible thermodynamics of large plastic deformation proposed by Prasad, the instability criterion is established as follows: (18) = ln + 1 ln + 0 (19) The values of m, η, and ξ were calculated by cubic spline interpolation. The equivalent maps of the dissipated power η and the instability factor ξ are plotted in Figure 6a,b, respectively.…”

Section: Processing Mapmentioning

confidence: 99%

“…In addition, the hot processing map is constructed to predict the plastic deformation mechanism and the unstable deformation domain in various deformation conditions, which provides insights into the optimization of thermo-mechanical processing. This method has been widely used in various alloys, such as Al alloys [8][9][10], Mg alloys [11][12][13], Ti alloys [14][15][16], and steel [17][18][19].…”

Section: Introductionmentioning

confidence: 99%

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Hot Deformation Behavior of a New Al–Mn–Sc Alloy

et al. 2019

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The hot deformation behavior of a new Al–Mn–Sc alloy was investigated by hot compression conducted at temperatures from 330 to 490 °C and strain rates from 0.01 to 10 s−1. The hot deformation behavior and microstructure of the alloy were significantly affected by the deformation temperatures and strain rates. The peak flow stress decreased with increasing deformation temperatures and decreasing strain rates. According to the hot deformation behavior, the constitutive equation was established to describe the steady flow stress, and a hot processing map at 0.4 strain was obtained based on the dynamic material model and the Prasad instability standard, which can be used to evaluate the hot workability of the alloy. The developed hot processing diagram showed that the instability was more likely to occur in the higher Zener–Hollomon parameter region, and the optimal processing range was determined as 420–475 °C and 0.01–0.022 s−1, in which a stable flow and a higher power dissipation were achieved.

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“…Finally, the billets were heated at 1250 • C for 5 h and hot rolled to sheets with 4 mm thickness after 7 passes of hot rolling; the primary rolling temperature was 1150 • C, the final rolling temperature was not lower than 850 • C, and the hot-rolled steel was finally cooled to room temperature at a cooling rate of 15 • C/s. The traditional heat treatment for medium-Mn steels mentioned above requires a long holding time in the intercritical region, and it was proved to be inapplicable to the experimental steels [18][19][20][21][22]. Also, the long annealing time renders the retained austenite too stable.…”

Section: Materials and Experimental Proceduresmentioning

confidence: 99%

Design of an Effective Heat Treatment Involving Intercritical Hardening for High Strength/High Elongation of 0.2C–3Al–(6–8.5)Mn–Fe TRIP Steels: Microstructural Evolution and Deformation Behavior

Mou

Zhang

et al. 2019

Metals

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High strength/high elongation continues to be the primary challenge and focus for medium-Mn steels. It is elucidated herein via critical experimental analysis that the cumulative contribution of transformation-induced plasticity (TRIP) and microstructural constituents governs high strength/high elongation in 0.2C–3Al–(6–8.5)Mn–Fe steels. This was enabled by an effective heat treatment involving a combination of intercritical hardening and tempering to obtain high strength/high ductility. An excellent combination of high ultimate tensile strength of 935–1112 MPa and total elongation of 35–40% was obtained when the steels were subjected to intercritical hardening in the temperature range of 700–750 °C and low tempering at 200 °C. The intercritical hardening impacted the coexistence of austenite, ferrite, and martensite, such that the deformation behavior varied with the Mn content. The excellent obtained properties of the steels are attributed to the cumulative contribution of the enhanced TRIP effect of austenite and the microstructural constituents, ferrite and martensite. The discontinuous TRIP effect during deformation involved stress relaxation, which was responsible for the high ductility. Lamellar austenite, unlike the equiaxed microstructure, is envisaged to induce stress relaxation during martensitic transformation, resulting in the discontinuous TRIP effect.

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Exploring the influence of Al content on the hot deformation behavior of Fe-Mn-Al-C steels through 3D processing map

Cited by 50 publications

References 39 publications

Tensile Properties and Microstructural Evolution of an Al-Bearing Ferritic Stainless Steel at Elevated Temperatures

Tensile Properties and Microstructural Evolution of an Al-Bearing Ferritic Stainless Steel at Elevated Temperatures

Hot Deformation Behavior of a New Al–Mn–Sc Alloy

Design of an Effective Heat Treatment Involving Intercritical Hardening for High Strength/High Elongation of 0.2C–3Al–(6–8.5)Mn–Fe TRIP Steels: Microstructural Evolution and Deformation Behavior

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