J. Mater. Sci. Technol. ›› 2021, Vol. 72: 52-60.DOI: 10.1016/j.jmst.2020.09.021
• Research Article • Previous Articles Next Articles
Feng Hea,b, Bin Hana,c, Zhongsheng Yangb, Da Chena,d, Guma Yelia, Yang Tonge, Daixiu Weif, Junjie Lib, Zhijun Wangb,*(), Jincheng Wangb,*(), Ji-jung Kaia,d,**()
Received:
2020-07-29
Revised:
2020-09-10
Accepted:
2020-09-12
Published:
2021-05-10
Online:
2021-05-10
Contact:
Zhijun Wang,Jincheng Wang,Ji-jung Kai
About author:
** Centre for Advanced Nuclear Safety and SustainableDevelopment, City University of Hong Kong, Hong Kong, China. E-mail addresses: jijkai@cityu.edu.hk (J.-j. Kai).Feng He, Bin Han, Zhongsheng Yang, Da Chen, Guma Yeli, Yang Tong, Daixiu Wei, Junjie Li, Zhijun Wang, Jincheng Wang, Ji-jung Kai. Elemental partitioning as a route to design precipitation-hardened high entropy alloys[J]. J. Mater. Sci. Technol., 2021, 72: 52-60.
Fig. 1. Schematic of the current design route (b) compared with traditional design strategy (a). The APT quantified elemental partitioning coefficients were used as an intermediate link to quantify the chemical compositions of the matrix-precipitate HEAs and thus the key features (e.g. volume fraction f, anti-phase boundary energy γAPB, lattice misfit ε) that determine their mechanical responses.
HEAs | Phase | Co | Ni | Cr | Fe | Ti | Al | Ref. | |
---|---|---|---|---|---|---|---|---|---|
1 | NiCoCrFeTi0.2 800 °C/1 h | γ′ | 16.0 | 55.4 | 0.9 | 2.0 | 25.7 | - | [ |
γ | 25.1 | 18.9 | 26.3 | 28.1 | 1.6 | - | - | ||
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.64 | 2.93 | 0.03 | 0.07 | 16.06 | - | - | ||
2 | Ni30Co30Fe13Cr15Al6Ti6 | γ′ | 19.78 | 50.79 | 2.53 | 3.36 | 13.37 | 10.17 | [ |
780 °C/4 h | γ | 34.25 | 17.86 | 23.14 | 19.69 | 1.43 | 3.63 | - | |
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.58 | 2.84 | 0.11 | 0.17 | 9.35 | 2.80 | - | ||
3 | (NiFeCo)86Ti7Al7 | γ′ | 23.69 | 43.23 | - | 10.06 | 14.41 | 8.61 | [ |
780 °C/4 h | γ | 31.84 | 18.69 | - | 41.13 | 2.66 | 5.69 | - | |
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.74 | 2.31 | - | 0.24 | 5.42 | 1.51 | - | ||
4 | (NiCoCr)94Ti3Al3 | γ′ | 11.30 | 60.45 | 3.44 | - | 15.88 | 8.92 | [ |
800 °C/1 h | γ | 33.70 | 28.25 | 34.42 | - | 1.75 | 1.89 | - | |
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.34 | 2.14 | 0.10 | - | 9.07 | 4.72 | - | ||
5 | Ni56Co19Cr15Al5Ti5 | γ′ | 5.264 | 69.37 | 2.00 | - | 12.10 | 11.27 | [ |
800 °C/1000 h | γ | 26.1 | 46.75 | 24.99 | - | 0.73 | 1.41 | ||
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.202 | 1.484 | 0.080 | - | 16.6 | 8.0 | |||
6 | Ni47Co28Cr15Al5Ti5 | γ′ | 9.6 | 64.8 | 2.05 | - | 12.22 | 11.31 | [ |
800 °C/1000 h | γ | 36.89 | 36.6 | 23.82 | - | 0.91 | 1.74 | ||
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.260 | 1.770 | 0.086 | - | 13.49 | 6.5 | |||
7 | Ni37Co38Cr15Al5Ti5 | γ′ | 16.1 | 57.5 | 2.45 | - | 12.8 | 11.12 | [ |
800 °C/1000 h | γ | 46.8 | 25.2 | 24.9 | 0.95 | 2.07 | |||
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.344 | 2.28 | 0.098 | - | 13.5 | 5.4 | |||
8 | Ni28Co47Cr15Al5Ti5 | γ′ | 28.4 | 46.0 | 3.75 | - | 11.7 | 10.26 | [ |
800 °C/1000 h | γ | 53.9 | 19.8 | 21.7 | - | 1.6 | 3.09 | ||
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.527 | 2.32 | 0.173 | - | 7.3 | 3.3 | |||
9 | Ni19Co56Cr15Al5Ti5 | γ′ | 42.79 | 30.28 | 6.53 | - | 12.0 | 8.43 | [ |
800 °C/1000 h | γ | 59.2 | 13.9 | 21.2 | - | 2.04 | 3.72 | ||
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.723 | 2.18 | 0.308 | - | 5.9 | 2.27 | |||
10 | NiCoCrFeTi0.1Al0.1 | γ′ | 12.6 | 56.2 | 2.3 | 4.3 | 16.8 | 7.9 | [ |
800 °C/1 h | γ | 24.3 | 20.7 | 26.4 | 25.4 | 1.3 | 1.9 | - | |
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.52 | 2.71 | 0.09 | 0.17 | 12.92 | 4.16 | - |
Table 1 Chemical compositions (at.%) of γ and γ′ phases from APT measurements and the partition coefficients of component elements of HEAs in literatures.
HEAs | Phase | Co | Ni | Cr | Fe | Ti | Al | Ref. | |
---|---|---|---|---|---|---|---|---|---|
1 | NiCoCrFeTi0.2 800 °C/1 h | γ′ | 16.0 | 55.4 | 0.9 | 2.0 | 25.7 | - | [ |
γ | 25.1 | 18.9 | 26.3 | 28.1 | 1.6 | - | - | ||
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.64 | 2.93 | 0.03 | 0.07 | 16.06 | - | - | ||
2 | Ni30Co30Fe13Cr15Al6Ti6 | γ′ | 19.78 | 50.79 | 2.53 | 3.36 | 13.37 | 10.17 | [ |
780 °C/4 h | γ | 34.25 | 17.86 | 23.14 | 19.69 | 1.43 | 3.63 | - | |
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.58 | 2.84 | 0.11 | 0.17 | 9.35 | 2.80 | - | ||
3 | (NiFeCo)86Ti7Al7 | γ′ | 23.69 | 43.23 | - | 10.06 | 14.41 | 8.61 | [ |
780 °C/4 h | γ | 31.84 | 18.69 | - | 41.13 | 2.66 | 5.69 | - | |
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.74 | 2.31 | - | 0.24 | 5.42 | 1.51 | - | ||
4 | (NiCoCr)94Ti3Al3 | γ′ | 11.30 | 60.45 | 3.44 | - | 15.88 | 8.92 | [ |
800 °C/1 h | γ | 33.70 | 28.25 | 34.42 | - | 1.75 | 1.89 | - | |
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.34 | 2.14 | 0.10 | - | 9.07 | 4.72 | - | ||
5 | Ni56Co19Cr15Al5Ti5 | γ′ | 5.264 | 69.37 | 2.00 | - | 12.10 | 11.27 | [ |
800 °C/1000 h | γ | 26.1 | 46.75 | 24.99 | - | 0.73 | 1.41 | ||
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.202 | 1.484 | 0.080 | - | 16.6 | 8.0 | |||
6 | Ni47Co28Cr15Al5Ti5 | γ′ | 9.6 | 64.8 | 2.05 | - | 12.22 | 11.31 | [ |
800 °C/1000 h | γ | 36.89 | 36.6 | 23.82 | - | 0.91 | 1.74 | ||
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.260 | 1.770 | 0.086 | - | 13.49 | 6.5 | |||
7 | Ni37Co38Cr15Al5Ti5 | γ′ | 16.1 | 57.5 | 2.45 | - | 12.8 | 11.12 | [ |
800 °C/1000 h | γ | 46.8 | 25.2 | 24.9 | 0.95 | 2.07 | |||
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.344 | 2.28 | 0.098 | - | 13.5 | 5.4 | |||
8 | Ni28Co47Cr15Al5Ti5 | γ′ | 28.4 | 46.0 | 3.75 | - | 11.7 | 10.26 | [ |
800 °C/1000 h | γ | 53.9 | 19.8 | 21.7 | - | 1.6 | 3.09 | ||
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.527 | 2.32 | 0.173 | - | 7.3 | 3.3 | |||
9 | Ni19Co56Cr15Al5Ti5 | γ′ | 42.79 | 30.28 | 6.53 | - | 12.0 | 8.43 | [ |
800 °C/1000 h | γ | 59.2 | 13.9 | 21.2 | - | 2.04 | 3.72 | ||
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.723 | 2.18 | 0.308 | - | 5.9 | 2.27 | |||
10 | NiCoCrFeTi0.1Al0.1 | γ′ | 12.6 | 56.2 | 2.3 | 4.3 | 16.8 | 7.9 | [ |
800 °C/1 h | γ | 24.3 | 20.7 | 26.4 | 25.4 | 1.3 | 1.9 | - | |
Ki=$K_i^{\gamma '}/K_i^{\gamma}$ | 0.52 | 2.71 | 0.09 | 0.17 | 12.92 | 4.16 | - |
Fig. 3. Separated demonstration of the elemental partitioning coefficient matrix. The larger the absolute value of the regression coefficient is, the stronger the influence on the partitioning behavior is. Ti and Al showed vital importance in the elemental partitioning behavior of the Ni-Co-Cr-Fe-Ti-Al system.
Fig. 4. Plot of anti-phase boundary energy of γ′ phase in HEAs vs (a) Ti/Al ratio of the γ′ phase and (b) the current defined parameter $\Psi = \frac{{C_{{\text{Ni}}}^{\gamma '}C_{{\text{Al}}}^{\gamma '}}}{{C_{{\text{Co}}}^{\gamma '}C_{{\text{Ti}}}^{\gamma '}}}$.
Fig. 5. TEM-DF images, DP images, and HRTEM images of the Ni2CoCrFeTixAly HEAs aged at 800 °C for 1 h: (a-c) Ni2CoCrFeTi0.1Al0.2 HEA, (d-f) Ni2CoCrFeTi0.15Al0.15 HEA, (g-i) Ni2CoCrFeTi0.2Al0.1 HEA. All three HEAs are composed of spherical γ? and γ matrix.
HEAs | Phase | Co | Cr | Fe | Ni | Ti | Al | f | γAPB | σor |
---|---|---|---|---|---|---|---|---|---|---|
Ni2CoCrFeTi0.1Al0.2 | γ′ | 6.37 | 1.23 | 3.07 | 64.67 | 9.42 | 15.13 | 0.138 | 128 | 253 |
γ | 20.87 | 21.69 | 21.4 | 33.43 | 0.68 | 1.93 | - | - | ||
Ki=$C_i^{\gamma '}/C_i^{\gamma}$ | 0.31 | 0.06 | 0.14 | 1.93 | 13.85 | 7.84 | - | - | ||
Ni2CoCrFeTi0.15Al0.15 | γ′ | 7.45 | 0.91 | 2.36 | 66.61 | 13.19 | 9.50 | 0.162 | 179 | 382 |
γ | 21.07 | 22.34 | 22.06 | 32.16 | 0.85 | 1.52 | - | - | ||
Ki=$C_i^{\gamma '}/C_i^{\gamma}$ | 0.35 | 0.04 | 0.11 | 2.07 | 15.52 | 6.25 | - | - | ||
Ni2CoCrFeTi0.2Al0.1 | γ′ | 8.53 | 0.57 | 1.60 | 67.96 | 16.16 | 5.22 | 0.187 | 199 | 457 |
γ | 21.25 | 23.07 | 22.84 | 30.78 | 0.94 | 1.12 | - | - | ||
Ki=$C_i^{\gamma '}/C_i^{\gamma}$ | 0.40 | 0.02 | 0.07 | 2.20 | 17.19 | 4.66 | - | - |
Table 2 Predicted chemical compositions (at.%) of γ and γ′ phases, partitioning coefficients of component elements, volume fractions and anti-phase boundary energies (mJ m-2) of γ′ phase, and ordering strengthening (MPa) of HEAs with different Ti/Al ratios.
HEAs | Phase | Co | Cr | Fe | Ni | Ti | Al | f | γAPB | σor |
---|---|---|---|---|---|---|---|---|---|---|
Ni2CoCrFeTi0.1Al0.2 | γ′ | 6.37 | 1.23 | 3.07 | 64.67 | 9.42 | 15.13 | 0.138 | 128 | 253 |
γ | 20.87 | 21.69 | 21.4 | 33.43 | 0.68 | 1.93 | - | - | ||
Ki=$C_i^{\gamma '}/C_i^{\gamma}$ | 0.31 | 0.06 | 0.14 | 1.93 | 13.85 | 7.84 | - | - | ||
Ni2CoCrFeTi0.15Al0.15 | γ′ | 7.45 | 0.91 | 2.36 | 66.61 | 13.19 | 9.50 | 0.162 | 179 | 382 |
γ | 21.07 | 22.34 | 22.06 | 32.16 | 0.85 | 1.52 | - | - | ||
Ki=$C_i^{\gamma '}/C_i^{\gamma}$ | 0.35 | 0.04 | 0.11 | 2.07 | 15.52 | 6.25 | - | - | ||
Ni2CoCrFeTi0.2Al0.1 | γ′ | 8.53 | 0.57 | 1.60 | 67.96 | 16.16 | 5.22 | 0.187 | 199 | 457 |
γ | 21.25 | 23.07 | 22.84 | 30.78 | 0.94 | 1.12 | - | - | ||
Ki=$C_i^{\gamma '}/C_i^{\gamma}$ | 0.40 | 0.02 | 0.07 | 2.20 | 17.19 | 4.66 | - | - |
Fig. 6. APT characterization of the Ni2CoCrFeTi0.1Al0.2 HEA aged at 800 °C for 1 h: (a) atom maps of different elements, (b) proximity histogram constructed across the interface between the matrix and precipitates showing the partitioning of different elements and a 3D construction with the 50 at.% Ni iso-concentration surface. The particle is evidently rich in Ni, Ti, and Al while depleted in Co, Fe, and Cr.
HEAs | Phase | Co | Cr | Fe | Ni | Ti | Al | f | σor | γAPB |
---|---|---|---|---|---|---|---|---|---|---|
Ni2CoCrFeTi0.1Al0.2 | γ′ | 6.56 | 1.75 | 3.04 | 64.97 | 11.36 | 12.31 | 0.129 | 248 | 129 |
γ | 19.68 | 21.37 | 19.21 | 35.20 | 1.22 | 3.32 | - | - | - | |
Ki=$C_i^{\gamma '}/C_i^{\gamma}$ | 0.33 | 0.08 | 0.16 | 1.85 | 9.31 | 3.71 | - | - | - | |
Ni2CoCrFeTi0.15Al0.15 | γ′ | 7.23 | 1.19 | 2.37 | 64.78 | 15.25 | 9.19 | 0.151 | 365 | 176 |
γ | 20.66 | 22.89 | 20.47 | 32.85 | 1.07 | 2.06 | - | - | - | |
Ki=$C_i^{\gamma '}/C_i^{\gamma}$ | 0.35 | 0.05 | 0.12 | 1.97 | 14.25 | 4.46 | - | - | - | |
Ni2CoCrFeTi0.2Al0.1 | γ′ | 6.92 | 1.82 | 1.54 | 65.81 | 17.40 | 6.51 | 0.186 | 433 | 188 |
γ | 20.86 | 24.74 | 21.31 | 31.07 | 0.96 | 1.05 | - | - | - | |
Ki=$C_i^{\gamma '}/C_i^{\gamma}$ | 0.33 | 0.077 | 0.07 | 2.12 | 18.13 | 6.2 | - | - | - |
Table 3 Experimental chemical compositions (at.%) of γ and γ′ phases, partitioning coefficients of component elements, volume fractions and anti-phase boundary energies (mJ m-2) of γ′ phase, and ordering strengthening (MPa) of HEAs with different Ti/Al ratios.
HEAs | Phase | Co | Cr | Fe | Ni | Ti | Al | f | σor | γAPB |
---|---|---|---|---|---|---|---|---|---|---|
Ni2CoCrFeTi0.1Al0.2 | γ′ | 6.56 | 1.75 | 3.04 | 64.97 | 11.36 | 12.31 | 0.129 | 248 | 129 |
γ | 19.68 | 21.37 | 19.21 | 35.20 | 1.22 | 3.32 | - | - | - | |
Ki=$C_i^{\gamma '}/C_i^{\gamma}$ | 0.33 | 0.08 | 0.16 | 1.85 | 9.31 | 3.71 | - | - | - | |
Ni2CoCrFeTi0.15Al0.15 | γ′ | 7.23 | 1.19 | 2.37 | 64.78 | 15.25 | 9.19 | 0.151 | 365 | 176 |
γ | 20.66 | 22.89 | 20.47 | 32.85 | 1.07 | 2.06 | - | - | - | |
Ki=$C_i^{\gamma '}/C_i^{\gamma}$ | 0.35 | 0.05 | 0.12 | 1.97 | 14.25 | 4.46 | - | - | - | |
Ni2CoCrFeTi0.2Al0.1 | γ′ | 6.92 | 1.82 | 1.54 | 65.81 | 17.40 | 6.51 | 0.186 | 433 | 188 |
γ | 20.86 | 24.74 | 21.31 | 31.07 | 0.96 | 1.05 | - | - | - | |
Ki=$C_i^{\gamma '}/C_i^{\gamma}$ | 0.33 | 0.077 | 0.07 | 2.12 | 18.13 | 6.2 | - | - | - |
Fig. 7. Comparison between the predicted and experimental elemental partitioning coefficients of Ni2CoCrFeTixAly HEAs. The alloy number 1, 2, and 3 represent Ni2CoCrFeTi0.1Al0.2 HEA, Ni2CoCrFeTi0.15Al0.15 HEA, and Ni2CoCrFeTi0.2Al0.1 HEA, respectively.
Fig. 8. (a) Predicted and experimental volume fraction of γ′ phase in the Ni2CoCrFeTixAly HEAs, (b) tensile stress-strain curves of the Ni2CoCrFeTixAly HEAs aged for 1 h at 800 °C, (c) predicted and experimental precipitation strengthening effects of γ′ phase in the Ni2CoCrFeTixAly HEAs. The alloy number 1, 2, and 3 represent Ni2CoCrFeTi0.1Al0.2 HEA, Ni2CoCrFeTi0.15Al0.15 HEA, and Ni2CoCrFeTi0.2Al0.1 HEA, respectively.
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