Heterogeneous lamella design to tune the mechanical behaviour of a new cost-effective compositionally complicated alloy

doi:10.1016/j.jmst.2021.03.083

Abstract

Abstract:

A heterogeneous lamella (HL) design strategy was applied to manipulate mechanical properties of a new cost-effective Fe₃₅Ni₃₅Cr₂₅Mo₅ compositionally complicated alloy (CCA). The HL structure was produced by single-step heat treatment (800 °C for 1 h) after cold rolling. This HL structure consists of alternative lamellae regions of coarse-grained FCC matrix (5‒20 μm), and regions containing ultra-fine grains or subgrains (200‒500 nm) together with nanoprecipitates (20‒500 nm) and annealing twins. As compared with other cost-effective CCAs, the 800 °C annealed sample with HL structure demonstrated a comparable tensile property, with yield strength over 1.0 GPa and total elongation of ~13%. Formation of the annealing twins and nanoprecipitates decorated HL structure was a result of the concurrent partial recrystallization and precipitation of σ phase at the shear bands with a high density of lattice defects (e.g. high-density dislocation walls and deformation twins). The latter restricted the growth of recrystallized grains, leading to the formation of ultrafine subgrains within the HL structure. The high yield strength resulted from the multistage hetero-deformation induced (HDI) strengthening and precipitation strengthening associated with heterogeneous lamella structures containing nanoprecipitates. The ductility was originated from the coexistence of multiple deformation mechanisms, which started with dislocation slip and formation of stacking faults at the initial stage, followed by nano-twinning at the higher strain level. This HL design strategy, comprising composition and thermomechanical process designs, and the resultant microstructure tuning, open a broader window for the development of cost-effective CCAs with enhanced performance.

Key words: High entropy alloys, Compositionally complicated alloys, Heterogeneous lamella structure, Nanoprecipitates, Recrystallization, Mechanical properties

Yu Yin, Qiyang Tan, Qiang Sun, Wangrui Ren, Jingqi Zhang, Shiyang Liu, Yingang Liu, Michael Bermingham, Houwen Chen, Ming-Xing Zhang. Heterogeneous lamella design to tune the mechanical behaviour of a new cost-effective compositionally complicated alloy[J]. J. Mater. Sci. Technol., 2022, 96: 113-125.

Figures/Tables 13

Table 1 Calculated parameters of Fe35Ni35Cr25Mo5 CCA for phase prediction.

ΔH_mix (kJ/mol)	ΔS_mix (J/(K mol))	T_m (K)	Ω	δ (%)	VEC
-4.41	10.24	1926.55	4.47	0.83	8.10

Fig. 1. (a) XRD spectra of the Fe35Ni35Cr25Mo5 CCA before and after thermomechanical processing; (b) enlarged sections of the spectra.

Fig. 2. Low-magnification (a?f) and high-magnification (a1?f1) BSE images of the as-cast, as-rolled and rolled Fe35Ni35Cr25Mo5 samples annealed at different temperatures for 1 h: (a, a1) as-cast, (b, b1) as-rolled, (c, c1) 500 °C annealing, (d, d1) 700 °C annealing, (e, e1) 800 °C annealing, (f, f1) 900 °C annealing.

Fig. 3. EBSD mapping showing the concurrent occurrence of recrystallization/partial recrystallization of FCC matrix and precipitation of σ phase in the as-cast (a), as-rolled (b) and annealed (c?e) Fe35Ni35Cr25Mo5 samples: band contrast maps (a1?e1); inverse pole figure (IPF) maps (a2-e2); phase maps (a3?e3), red corresponds to FCC phase and yellow corresponds to σ phase.

Fig. 4. (a) A typical SEM image of the Fe35Ni35Cr25Mo5 sample annealed at 800 °C after etching; (b) a STEM bright-field image of the thin-foil sample cut from the marked region in (a) using FIB. The dash lines in (b) mark the boundaries of the coarser grain and fine grain area. The yellow arrows indicate the σ precipitates.

Fig. 5. TKD mapping showing the recrystallized grains and σ precipitates in the vicinity of shear bands in the Fe35Ni35Cr25Mo5 samples after rolling (a) and annealing under different temperatures for 1 h (b): band contrast maps (a1, b1); inverse pole figure (IPF) maps (a2, b2); phase maps (a3, b3), red corresponds to FCC phase and yellow colour corresponds to σ phase. The dash lines in (b1) indicate the boundaries of the coarser grain and fine grain area.

Fig. 6. TEM characterization showing the microstructure of the Fe35Ni35Cr25Mo5 CCA at as-rolled (a?c) and as-annealed at 800 °C (d?f): TEM-BF image (a, d), STEM-BF image (b, e), EDS mapping (c, f). The yellow arrows in (e) indicate the nano-sized precipitates.

Fig. 7. (a) HRTEM image obtained along the [011]FCC ([010]σ) zone axis, showing the interface between the FCC matrix and a σ precipitate, with the inset as the corresponding FFT pattern; (b) magnified HRTEM image of the σ precipitates in (a), with the inset schematically showing the atoms column; (c) simulated crystal structure of the Cr5.5Mo1.5Fe6.5Ni1.5-type intermetallic phase; (d) TEM HAADF image and corresponding EDS line scan of a σ precipitate.

Fig. 8. (a) Typical engineering tensile stress-strain curves of the Fe35Ni35Cr25Mo5 CCA at different states; (b) comparison of the present Fe35Ni35Cr25Mo5 CCA with previously reported Co-free and other low-cost HEAs/CCAs [13, 41, [64], [65], [66], [67], [68], [69], [70], [71], [72], [73], [74], [75], [76]] in terms of yield strength and fracture strain. Here, low-cost HEAs/CCAs are those that contain less than total 5 at.% of expensive metals (e.g. Mo, W, Co, Nb, Ta, V, Hf); (c) fractography of the Fe35Ni35Cr25Mo5 CCAs after tensile tests.

Table 2 . Room-temperature tensile properties of the Fe35Ni35Cr25Mo5 CCA at different states.

Condition	σ_0.2 (MPa)	σ_u (MPa)	ε (%)
As-cast	251	592	37
CR	1269	1398	8
CR + 500 °C, 1 h	1435	1510	5
CR + 700 °C, 1 h	1286	1396	9
CR + 800 °C, 1 h	1049	1192	13
CR + 900 °C, 1 h	523	843	35

Fig. 9. (a) TEM-BF image of the 800 °C annealed sample after tensile test; (b) magnified TEM-DF image of the marked area in (a), with inset of corresponding diffraction patterns; (c) HRTEM image of the deformation twins in (b); (d, e) TEM-BF images of the 800 °C annealed sample after tensile test show the interaction of deformation twins and low-angle boundaries. The red, green, orange and white arrows indicate the HAGBs, LAGBs, dislocations network and DTs, respectively.

Fig. 10. (a) TEM-BF image of the 800 °C annealed sample after tensile test shows high density of dislocations, deformation twins and stacking faults near the precipitates; (b) HRTEM image showing the stacking faults near the precipitates in (a); (c, d) HRTEM images showing the stacking faults near the precipitate in (b). The yellow, orange, white and blue arrows indicate the precipitates, dislocations network, DTs and SFs, respectively.

Fig. 11. Schematic illustration of the HL microstructure with nanoprecipitates and twins (a), GND pile-up near the HL interface and phase boundaries (b), and interaction of dislocations, SFs, DTs, LAGBs and precipitates (c).

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