Hot Deformation Behavior of an Ultra-High-Strength Fe-Ni-Co-Based Maraging Steel

doi:10.1007/s40195-019-00913-3

Abstract

Abstract:

Hot processing behavior of an ultra-high-strength Fe-Ni-Co-based maraging steel was studied in temperature range of 900-1200 °C and strain rate range of 0.001-10 s^-1. Deformation processing parameters and optimum hot working window were characterized via flow stress analysis, constitutive equation construction, hot processing map calculation and microstructure evolution, respectively. Critical strain value for dynamic recrystallization was determined through theoretical mathematical differential method: the inflection point of θ-σ and -??θ/?σ?-?σ curves. It was found that the flow stress increased with the decrease in deformation temperature and increase in the strain rate. The power dissipation maps in the strain range of 0.1-0.6 were entirely similar with the tendency of contour lines which implied that strain had no strong effect on the dissipation maps. Nevertheless, the instability maps showed obvious strain sensitivity with increasing strain, which was ascribed to the flow localization and instability. The optimized hot processing window of the experimental steel was obtained as 1100-1200 °C/0.001-1 s^-1 and 1000-1100 °C/0.001-0.1 s^-1, with the efficiency range of 20-40%. Owing to high Mo content in the experimental steel, high dynamic activation energy, Q?=?439.311 kJ mol^-1, was achieved, indicating that dynamic recrystallization was difficult to occur in the hot deformation process, which was proved via microstructure analysis under different hot deformation conditions.

Key words: Maraging steel, Hot working, Dynamic recrystallization, Constitutive equation, Hot processing map

Le Zhang, Wei Wang, M. Babar Shahzad, Yi-Yin Shan, Ke Yang. Hot Deformation Behavior of an Ultra-High-Strength Fe-Ni-Co-Based Maraging Steel[J]. Acta Metallurgica Sinica (English Letters), 2019, 32(9): 1161-1172.

Figures/Tables 13

Fig. 1 Microstructure of the experimental MAS at the initial state

Fig. 2 Schematic diagram of hot compression test

Fig. 3 True stress-strain curves of the experimental steel at different strain rates and temperatures of a 900 °C, b 1000 °C, c 1050 °C, d 1100 °C, e 1200 °C, f flow stress curves at different temperatures with strain rate of 0.01 s-1

Fig. 4 Variation of work-hardening rate with flow stress under different deformation conditions

Fig. 5 Variation of -??θ/?σ as a function of flow stress under different conditions

Fig. 6 Relationship among flow stress, strain rate and deformation temperature: a lnσ?-?ln$\dot{\varepsilon }$, bσ?-?ln$\dot{\varepsilon }$, c ln[sinh(ασ)]?-?ln$\dot{\varepsilon }$, d ln[sinh(ασ)]?-?1000/T, e ln[sinh(ασ)]?-?InZ

Fig. 7 Power dissipation maps at true strains of a 0.1, b 0.2, c 0.3, d 0.4, e 0.5, f 0.6

Fig. 8 Hot processing maps at true strains of a 0.1, b 0.2, c 0.3, d 0.4, e 0.5, f 0.6

Fig. 9 Distribution maps of inverse pole figure-Z at 1200 °C under different strain rates at true strain of 0.6: a 0.001 s-1, b 0.01 s-1, c 0.1 s-1, d 1 s-1, e 10 s-1

Fig. 10 Distribution maps of different microstructures at 1200 °C under different strain rates: a 0.001 s-1, b 0.01 s-1, c 0.1 s-1, d 1 s-1, e 10 s-1

Fig. 11 Statistical results of the microstructures in Fig. 10

Fig. 12 Distribution maps of local misorientation at 1200 °C under different strain rates: a 0.001 s-1, b 0.01 s-1, c 0.1 s-1, d 1 s-1, e 10 s-1

Fig. 13 SEM micrographs of the specimens deformed in the instability region at true st of 0.6: a 900/10 s-1 °C, b 1000/10 s-1 °C

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