Hot workability characteristics of low-density Fe–4Al–1Ni ferritic steel

Xu, Xiangyu; Wang, Xuemin; Li, Jianzhe; Yan, Zepeng; Liú, Dan; Liu, Qiannan; Chen, Shang; Fu, Jianxun; Shen, Ping

doi:10.1016/j.msea.2020.140257

Cited by 19 publications

(6 citation statements)

References 29 publications

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“…To further optimize the hot‐rolling process and improve the stability of the steel during thermal manufacturing, the 3D hot‐processing maps were established based on the dynamic material model (DMM), [ 39–41 ] which can show the trends of strain‐rate sensitivity index ( m ) and efficiency of power dissipation ( η ) for Fe‐31.7Mn‐11.5Al‐0.9C steel at different true strains. The strain‐rate sensitivity index refers to the energy consumed by the plastic deformation and the energy consumed by the microstructure evolution during the TMT of the material.…”

Section: Resultsmentioning

confidence: 99%

“…The higher the value of m , the greater the energy required for microstructure evolution. [ 39–41 ] Figure 5 shows the contour distribution of m at true strains of 0.2, 0.4, and 0.6 in Fe‐31.7Mn‐11.5Al‐0.9C steel, which is given by Equation (19). It is observed that m increases with increasing strain rate and deformation temperature, and higher m is distributed in the region of high strain rate and high deformation temperature combination.

m = {\frac{\partial ln σ}{\partial ln \overset{false.}{ε}} 6extrue|}_{ε, T}

…”

Section: Resultsmentioning

confidence: 99%

“…Higher power dissipation indicates that more energy is consumed by microstructure evolution. [ 39–41 ] For example, stable deformation such as DRV and DRX corresponds to higher η , in addition, adiabatic shear bands, cracks, and other instability defects may occur. [ 39–41 ] The 3D distribution maps of η are shown in Figure 6 with a relationship of

η = 2 m / false(m + 1 false)

.…”

Section: Resultsmentioning

confidence: 99%

“…[ 39–41 ] For example, stable deformation such as DRV and DRX corresponds to higher η , in addition, adiabatic shear bands, cracks, and other instability defects may occur. [ 39–41 ] The 3D distribution maps of η are shown in Figure 6 with a relationship of

η = 2 m / false(m + 1 false)

. An instability criterion ( ξ ) was introduced to reflect the flow instability domain, which was developed by Kumar and Prasad, [ 42–44 ] will be discussed in Section 4.1, and the ξ could be expressed as Equation (20).…”

Section: Resultsmentioning

confidence: 99%

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Thermomechanical Treatment Performance and Flow Stress Model of a Fe–Mn–Al–C Low‐Density Steel

Zhang

Cen

Zhang

et al. 2023

steel research int.

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The flow stress curves of Fe‐31.7Mn‐11.5Al‐0.9C low‐density steel are obtained by a hot‐compression test with a Gleeble‐3500 thermomechanical simulator. It is shown in the results that the dynamic recovery and dynamic recrystallization (DRX) of δ‐ferrite occur preferentially under the same deformation condition, inducing a “yield point‐like” phenomenon in the true stress–strain curves. The Zener–Hollomon parameter is introduced to fit the characteristic parameters used to establish the flow stress model according to Arrhenius hyperbolic sine relationship and Avrami equation, and the DRX activation energy of austenite is 414.12 KJ mol−1. The hot‐processing maps at different true strains are simulated based on the dynamic material model to determine the suitable hot‐rolling process and the optimal hot‐working process selection of high strain rate and high deformation temperature combination, 1100–950 °C/1–0.2 s−1, is recommended.

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Section: Resultsmentioning

confidence: 99%

m = {\frac{\partial ln σ}{\partial ln \overset{false.}{ε}} 6extrue|}_{ε, T}

…”

Section: Resultsmentioning

confidence: 99%

η = 2 m / false(m + 1 false)

.…”

Section: Resultsmentioning

confidence: 99%

η = 2 m / false(m + 1 false)

Section: Resultsmentioning

confidence: 99%

See 2 more Smart Citations

Thermomechanical Treatment Performance and Flow Stress Model of a Fe–Mn–Al–C Low‐Density Steel

Zhang

Cen

Zhang

et al. 2023

steel research int.

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show abstract

“…The size of some subgrains was less than 3 μm, and they got together. Since the morphology and size of these subgrains at Spectrum 1 in Figure 6a were similar to the subgrains formed through dynamic recovery in δ-ferritic steel, [31,32] these fine subgrains were considered formed by dynamic phase transformation. During the holding process, the subgrains of both matrix and the interface suffered static recovery, which will be presented in Section 3.3.3.…”

Section: Body-centered Cubic Phase In the Experimental Steelmentioning

confidence: 99%

Strain‐Associated Alpha‐Ferrite Phase Transformation in a Micro‐Laminated Low‐Density Steel

Liú

Shang

et al. 2022

steel research int.

Self Cite

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Aluminum-alloyed low-density steels have recently received significant attention because of the advantage in strength-todensity ratio [1] and superior corrosion resistance. [2][3][4] Aluminum is a strong ferrite-forming element and expands both α-ferrite and δ-ferrite phase region. Thus, the addition of aluminum in steel can result in δ-ferrite that always exists below solidification temperature, in spite of the addition of austenitic stabilizing elements. Under the action of deformation, the dualphase composed of δ-ferrite and austenite is expected to be elongated and forms micro-laminated microstructure. [5][6][7][8][9][10][11][12][13][14][15][16][17] Except prior δ-ferrite lamellae, through diversified alloy design, hot working process, and heat treatment process, the microstructure transformed from prior austenite can be designed as dual-phase or multiphase constituents, containing austenite, [5][6][7][8][9][10][12][13][14] α-ferrite, [5][6][7][8]12] martensite, [5][6][7][8][9][10][11][12][13] pearlite, [10] and bainite, [10] and the fraction range of each phase is also wide. Accordingly, the mechanical properties also vary among different phases. Hence, micro-laminated low-density steels have a broad application prospect, with extraordinary combinations of mechanical properties. [8,[10][11][12][13] Based on the microstructure, the deformation-induced evolution of the microstructure and the fracture mechanism are also complex. In general, δ-ferrite is a brittle phase, while the complex microstructure transformed from the original austenite has superior plasticity and resistance to crack growth. [17,18] Cracks propagate preferably into δ-ferrite or at the interface l ayer along the δ-ferrite {100} planes. [15,18] The embrittlement of δ-ferrite is because of higher aluminum content. [17][18][19] With the increase of aluminum content, the reduced mobility of dislocations [19,20] and the formation of ordered structure [17][18][19] result in lower ductility and toughness. Given that the retained austenite stability is critical for fracture resistance, [17] previous studies have focused on controlling the content and stability of retained austenite.However, studies on α-ferrite phase transformation on δ-ferrite and corresponding effect on mechanical properties are rare. Li et al. [14] reported that coarse δ-ferrite is harmful to mechanical properties. The grain refinement of ferrite is simultaneously beneficial to both strength and toughness.

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Simultaneous enhancement of strength and ductility in friction stir processed 2205 duplex stainless steel with a bimodal structure: experiments and crystal plasticity modeling

Hu¹,

Fang²,

Peng³

et al. 2021

Sci. China Phys. Mech. Astron.

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Hot workability characteristics of low-density Fe–4Al–1Ni ferritic steel

Cited by 19 publications

References 29 publications

Thermomechanical Treatment Performance and Flow Stress Model of a Fe–Mn–Al–C Low‐Density Steel

Thermomechanical Treatment Performance and Flow Stress Model of a Fe–Mn–Al–C Low‐Density Steel

Strain‐Associated Alpha‐Ferrite Phase Transformation in a Micro‐Laminated Low‐Density Steel

Simultaneous enhancement of strength and ductility in friction stir processed 2205 duplex stainless steel with a bimodal structure: experiments and crystal plasticity modeling

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