J. Mater. Sci. Technol. ›› 2022, Vol. 97: 54-68.DOI: 10.1016/j.jmst.2021.04.035
• Research Article • Previous Articles Next Articles
Pengyu Wena,b, Bin Hua,b, Jiansheng Hana, Haiwen Luoa,b,*()
Received:
2021-02-15
Revised:
2021-04-06
Accepted:
2021-04-16
Published:
2021-06-17
Online:
2021-06-17
Contact:
Haiwen Luo
About author:
* School of Metallurgical and Ecological Engineering, University of Science and Technology Beijing, Xue Yuan Lu 30, Beijing 10 0 083, China. E-mail address: luohaiwen@ustb.edu.cn (H. Luo).Pengyu Wen, Bin Hu, Jiansheng Han, Haiwen Luo. A strong and ductile medium Mn steel manufactured via ultrafast heating process[J]. J. Mater. Sci. Technol., 2022, 97: 54-68.
Fig. 1. Tensile properties in all the specimens to subjected to various annealing processes (a) and the work hardening behaviors during the tensile deformation of UFH-300 and IA-1 h specimens (b).
Fig. 2. EBSD results on HRA (after hot rolling and annealing 700 °C for 2 h) (a-c) and CR (after cold rolling) specimens (d-i). (a, d, g, i) Image quality (IQ) figures overlapped with the grain boundary (GB), phase mapping; (b, e, h) The corresponding normal direction inverse pole figures (ND-IPF) on RD⊥ND section, (c) line scanning results of Mn intensity by Auger electron spectroscopy, and (f) Kernel average misorientation (KAM) map, and (i) the CR samples along the TD-RD section. The thick yellow lines in (a) and (c) represent K-S OR with deviation less than 5°; the dark and red lines high-angle (15-180°) and low-angle (2-15°) grain boundaries respectively; the green is γ phase and the rest bcc phase. High-angle grain boundaries in fcc are revealed by dark lines in (b). (For interpretation of the references to color in this figure legend, the reader is referred to the web version of this article.).
Fig. 3. EBSD results on the specimens after ultrafast heating and the long intercritical annealing. (a, b, b1) UFH-10; (c, d, d1) UFH-100; (e, f, f1) UFH-300; (g, h, h1): IA-1 h. (a-h) Image quality (IQ) figures overlapped with the grain boundary (GB), phase mapping. (b1, d1, f1, h1) Kernel average misorientation (KAM) map overlapped with high-angle grain boundaries (dark lines) in fcc phase. (a, c, e, g) RD⊥TD section; (b-b1, d-d1, f-f1, h-h1) RD⊥ND section. The thick yellow lines in (a-h) represent K-S OR with deviation less than 5°; the dark and red lines high-angle (15-180°) and low-angle (2-15°) grain boundaries respectively; the green is γ phase and the rest bcc phase. (For interpretation of the references to color in this figure legend, the reader is referred to the web version of this article.)
Sample code | fRex | Transformation Temperature | |
---|---|---|---|
bcc | As | Af | |
UFH-10 | 0.34 | 511 | 834 |
UFH-100 | 0.27 | 612 | 883 |
UFH-300 | 0.26 | 618 | 886 |
IA-1h | 0.45 | - | - |
Table 1 Recrystallized fractions (fRex) of ferrite and austenite estimated using the method of GROD, and the reverse transformation start (As) and finish temperatures (Af) measured using dilatometry on the cold-rolled steel specimens.
Sample code | fRex | Transformation Temperature | |
---|---|---|---|
bcc | As | Af | |
UFH-10 | 0.34 | 511 | 834 |
UFH-100 | 0.27 | 612 | 883 |
UFH-300 | 0.26 | 618 | 886 |
IA-1h | 0.45 | - | - |
Sample code | Parameters | |||
---|---|---|---|---|
dθ, nm | fθ | ρRA, × 1015m-2 | ρbcc, × 1015 m-2 | |
UFH-10 | 53.27 ± 19.3 | 0.0099 | 1.99 ± 0.23 | 1.6 ± 0.07 |
UFH-100 | 88.88 ± 37.1 | 0.0076 | 2.05 ± 0.16 | 1.84 ± 0.19 |
UFH-300 | 62.81 ±26.5 | 0.00049 | 2.08 ± 0.21 | 1.92 ± 0.05 |
IA-1h | - | - | 1.13 ± 0.08 | 0.85 ± 0.09 |
Table 2 Volume fractions (fθ) and diameters (dθ) of cementite (θ) particles measured under SEM, and dislocation densities in both RA (ρRA) and bcc phase (ρbcc) estimated from XRD spectra.UFH-300 (c) and IA-1 h (d) specimens.
Sample code | Parameters | |||
---|---|---|---|---|
dθ, nm | fθ | ρRA, × 1015m-2 | ρbcc, × 1015 m-2 | |
UFH-10 | 53.27 ± 19.3 | 0.0099 | 1.99 ± 0.23 | 1.6 ± 0.07 |
UFH-100 | 88.88 ± 37.1 | 0.0076 | 2.05 ± 0.16 | 1.84 ± 0.19 |
UFH-300 | 62.81 ±26.5 | 0.00049 | 2.08 ± 0.21 | 1.92 ± 0.05 |
IA-1h | - | - | 1.13 ± 0.08 | 0.85 ± 0.09 |
Fig. 5. (a) Comparison of RA fractions in all the specimens before and after the tensile deformation, and the corresponding lattice parameters. Note that all the data were calculated from XRD; (b) The measured grain size distribution of RA grains in all the specimens.
Fig. 6. TEM results on the microstructures in the UFH samples. The compositions were measured by EDS. (a-c) UFH-10 sample; (d) UFH-100; and (e, f)) UFH-300.
Sample code | fcc (RA) | bcc | |||||
---|---|---|---|---|---|---|---|
Composition, wt.% | αγ, Å | fγ,% | Composition, wt.% | ||||
C | Mn | Al | Mn | Al | |||
HRA | 0.72 | 9.42 ± 0.34 | 2.2 ± 0.22 | 3.6099 | 30.4 ± 1.6 | 4.00 ± 0.21 | 3.13±0.14 |
Equilibrium | 0.44 | 9.73 | 2.17 | - | 56.6 | 3.88 | 3.16 |
IA-1h | 0.70 | 9.31 ± 0.65 | 2.28 ± 0.16 | 3.6096 | 27.32 ± 3.2 | 4.41 ± 0.45 | 2.93 ± 0.14 |
UFH-10 | 0.71 | 9.3 ± 0.80 | 1.99 ± 0.15 | 3.6082 | 30.92 ± 3.1 | 3.74 ± 0.13 | 3.11 ± 0.16 |
UFH-100 | 0.64 | 9.17±0.70 | 1.99 ± 0.16 | 3.6064 | 34.53 ± 2.8 | 4.21 ± 0.26 | 3.18 ± 0.16 |
UFH-300 | 0.66 | 9.2 ± 0.58 | 2.08 ± 0.06 | 3.6065 | 37.12 ± 4.3 | 4.15 ± 0.52 | 3.07 ± 0.02 |
Table 3 Chemical compositions of bcc and fcc phases, lattice parameters (αγ) and volume fractions of fcc (fγ) in these specimens, measured by STEM-EDS and XRD respectively. The calculated equilibrium phase compositions and fractions at 730 °C are also included.
Sample code | fcc (RA) | bcc | |||||
---|---|---|---|---|---|---|---|
Composition, wt.% | αγ, Å | fγ,% | Composition, wt.% | ||||
C | Mn | Al | Mn | Al | |||
HRA | 0.72 | 9.42 ± 0.34 | 2.2 ± 0.22 | 3.6099 | 30.4 ± 1.6 | 4.00 ± 0.21 | 3.13±0.14 |
Equilibrium | 0.44 | 9.73 | 2.17 | - | 56.6 | 3.88 | 3.16 |
IA-1h | 0.70 | 9.31 ± 0.65 | 2.28 ± 0.16 | 3.6096 | 27.32 ± 3.2 | 4.41 ± 0.45 | 2.93 ± 0.14 |
UFH-10 | 0.71 | 9.3 ± 0.80 | 1.99 ± 0.15 | 3.6082 | 30.92 ± 3.1 | 3.74 ± 0.13 | 3.11 ± 0.16 |
UFH-100 | 0.64 | 9.17±0.70 | 1.99 ± 0.16 | 3.6064 | 34.53 ± 2.8 | 4.21 ± 0.26 | 3.18 ± 0.16 |
UFH-300 | 0.66 | 9.2 ± 0.58 | 2.08 ± 0.06 | 3.6065 | 37.12 ± 4.3 | 4.15 ± 0.52 | 3.07 ± 0.02 |
Fig. 7. Numerical simulation results on the reverse transformation during the heating to 730 °C at 300 °C/s. (a) Configuration for γ nuclei to grow into the neighboring ferrite (α) and SIM (α′) with the assumed initial compositions (in weight percentage); (b) the calculated positions of moving γ/α and γ/α′ interfaces during the heating; and the calculated C (c), Mn (d) and Al (e) concentration profiles developed during the heating.
Fig. 8. Numerical simulation results on the growth kinetics of austenitic nuclei into martensite with the various compositions during the heating at the different rates. (a) The calculated movement of γ/α′ interface during the heating at either 10 or 300 °C/s for the diffusion couple having the assumed compositions and sizes; (b) Dependence of calculated A3 temperature on Mn and C contents; the (c) C and (d) Mn concentration profiles developed during the heating to 730 °C under the condition ‘4′ in (a); (e) C concentration profiles developed during the heating to 730 °C under the condition ‘4′ and ‘5′ in (a).
Fig. 9. Schematic illustration on the microstructural changes when the cold rolled 7Mn steel was subjected to the UFHs at 10, 100/300 °C/s to 730 °C or IA at 730 °C for 1 h.
Fig. 10. The reverse transformation temperature, ${{T}_{0}}$, is calculated for the compositional ranges of 0.6-0.8% C, 4-12% Mn and 2% Al, and the additional driving force of 500 J and 1000 J/mol are assumed for calculating $T_{0}^{\prime }$. The austenitization temperatures (As) during the heating at the rates of 10, 100 and 300 °C/s were measured using dilatometer and included for comparison.
Sample code | Quantifying contribution of each strengthening, MPa | Measured increment of YS, △YS, MPa | Estimated boundary strengthening, MPa △σb=△YS-△σρ-△σP | |||||
---|---|---|---|---|---|---|---|---|
Dislocation | Precipitation | Sum | ||||||
RA | bcc | Sum | △σρ | △σP | △σρ+△σP | |||
IA-1h | 403.6 | 396.7 | 398.6 | 0 | 0 | 0 | 0 | 0 |
UFH-10 | 535.6 | 544.2 | 541.5 | 142.9 | 67.2 | 210.1 | 327 | 116.9 |
UFH-100 | 543.5 | 583.7 | 569.8 | 171.7 | 41 | 212.7 | 283 | 70.3 |
UFH-300 | 547.1 | 596.2 | 578 | 179.4 | 11.9 | 191.3 | 273 | 81.7 |
Table 4 Quantifying the contributions of dislocation, boundary and precipitation strengthening in the UFH specimens. Dislocation and precipitation strengthening are quantified using the method described in the supplementary materials and added by the rule of mixtures; the contribution of boundary strengthening is estimated by the difference in the measured YS increments and the sum of dislocation and precipitation hardening.
Sample code | Quantifying contribution of each strengthening, MPa | Measured increment of YS, △YS, MPa | Estimated boundary strengthening, MPa △σb=△YS-△σρ-△σP | |||||
---|---|---|---|---|---|---|---|---|
Dislocation | Precipitation | Sum | ||||||
RA | bcc | Sum | △σρ | △σP | △σρ+△σP | |||
IA-1h | 403.6 | 396.7 | 398.6 | 0 | 0 | 0 | 0 | 0 |
UFH-10 | 535.6 | 544.2 | 541.5 | 142.9 | 67.2 | 210.1 | 327 | 116.9 |
UFH-100 | 543.5 | 583.7 | 569.8 | 171.7 | 41 | 212.7 | 283 | 70.3 |
UFH-300 | 547.1 | 596.2 | 578 | 179.4 | 11.9 | 191.3 | 273 | 81.7 |
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