TCHEA1

TCHEA1 - TCS High entropy alloy Database, Version 1.0

Thermo-Calc Software is pleased to announce the release of TCHEA1.0, a thermodynamic database for high entropy alloys (HEA) [2003Yeh, 2006Yeh], which are also known as multi-principal element alloys (MPEA) [2013Wan, 2015Sen]. TCHEA1.0 has been developed in a CALPHAD spirit based on the critical evaluation of all the binary systems and many ternary systems. A hybrid approach of experiments, first-principals calculations and CALPHAD modeling had been used to obtain reliable thermodynamic descriptions of the BCC and FCC solutions. That enables predictions to be made for multi-component alloy systems, especially for HEAs. The database has been developed in a 15-element framework:

Al Co Cr Cu Fe Hf Mn Mo Nb Ni Ta Ti V W Zr

All the 105 binary systems in this 15-element framework have been assessed to their full range of composition and temperature and can be calculated with the BINARY Module in Thermo-Calc. In total, 200 ternaries have been assessed, and 104 of them to their full range of composition and temperature. They can be calculated with the TERNARY Module in Thermo-Calc.

TCHEA1.0 contains nearly all stable phases in all assessed binary systems and most ternary systems. In total, 163 solution and intermetallic phases are modelled. The complete list of phases is given at the end of this document. First there is a list of all phases and then a detailed description of their models, e.g. number of sublattices and constituents on each sublattice.

The database can be used to calculate various phase diagrams and property diagrams in the assessed systems and higher-order systems. The extrapolation to higher-order systems helps to understand the phase equilibria in HEAs, so as to predict the phase formation, phase fractions and phase compositions or to calculate the driving force of forming a phase. The database can also be used for predicting solidification behaviour of HEAs with the SCHEIL_GULLIVER module in Thermo-Calc. All necessary molar volume data and thermal expansion data have been assessed or estimated for most of the phases.

The ordered B2 and L12 phases, together with bcc_A2 and fcc_A1, respectively, have been modeled with the so-called partitioning model, which describes an ordered phase and its disordered counterpart using a single Gibbs energy curve. This type of description is of particular importance to be able to predict second order transformations between a disordered phase and its ordered structures. Also note that there may be several possible composition sets for the phases named FCC_L12 and BCC_B2 designated by #1, #2, and so on (e.g. FCC_L12#1 and FCC_L12#2), due to the co-existence of disordered and ordered structures or the presence of miscibility gap. The #n suffix (where n is an integer) is generated dynamically by Thermo-Calc when using global minimization and therefore the identification of the phases should be determined from their site occupations. It can be found by LIST_EQUILIBRIUM with the VXNS option in the Console mode or showing the site fraction in moles of the constituent elements in the Graphic mode. When the site occupancies of the first and second sublattices are equal the phase is disordered.

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All the 105 binary systems have been assessed in full range of composition and temperature:

104 assessed ternary systems, in full range of composition and temperature: Al-Co-Cr Al-Co-Fe Al-Co-Hf Al-Co-Mo Al-Co-Ni Al-Co-Ta Al-Co-Ti Al-Co-W Al-Co-Zr Al-Cr-Hf Al-Cr-Ni Al-Cr-Pt Al-Cr-Ta Al-Cr-Ti Al-Cr-Zr Al-Cu-Fe Al-Cu-Mn Al-Cu-Ni Al-Fe-Mn Al-Fe-Mo Al-Fe-Ti Al-Hf-Mo Al-Hf-Ni Al-Hf-Ta Al-Hf-Ti Al-Hf-W Al-Hf-Zr Al-Mn-Ni Al-Mn-Ti Al-Mo-Ni Al-Nb-Ni Al-Ni-Pd Al-Ni-Pt Al-Ni-Ru Al-Ni-Ta Al-Ni-Ti Al-Ni-V Al-Ni-W Al-Ni-Zr Al-Ta-Ti Co-Cr-Cu Co-Cr-Mo Co-Cr-Nb Co-Cr-Ni Co-Cr-Ti Co-Cr-W Co-Cu-Fe Co-Cu-Mn Co-Cu-Nb Co-Cu-Ni Co-Cu-Ti Co-Fe-Nb Co-Fe-Ti Co-Hf-W Co-Mo-Ta Co-Mo-W Co-Ni-Ta Co-Ni-W Co-Ta-W Co-Ti-W Co-Ti-Zr Co-W-Zr Cr-Cu-Fe Cr-Cu-Nb Cr-Cu-Ni Cr-Fe-Mo Cr-Fe-Ni Cr-Fe-W Cr-Hf-Nb Cr-Mo-Ni Cr-Nb-Ni Cr-Ni-Ta Cr-Ni-Ti Cr-Ni-W Cr-Ni-Zr Cr-W-Zr Cu-Fe-Mn Cu-Fe-Mo Cu-Fe-Nb Cu-Fe-Ni Cu-Fe-Ti Cu-Fe-V Cu-Mn-Ni Cu-Mo-Ni Cu-Ni-Ti Cu-Ti-Zr Fe-Mn-Ni Fe-Mo-Ni Fe-Mo-W Fe-Nb-Ni Fe-Nb-Zr Fe-Ni-W Hf-Mo-Ni Hf-Ni-Ta Mo-Nb-Ni Mo-Ni-Ta Mo-Ni-Ti Mo-Ni-W Nb-Ni-Ti Nb-Ni-W Ni-Ta-W Ni-W-Zr Ta-W-Zr Ti-W-Zr

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96 tentatively assessed ternary systems: AL-CO-NB AL-CR-FE AL-CR-MO AL-CR-NB AL-FE-HF AL-FE-NB AL-FE-NI AL-FE-TA AL-FE-W AL-FE-ZR AL-HF-NB AL-MO-NB AL-MO-TA AL-MO-TI AL-NB-TA AL-NB-TI AL-NB-W AL-NB-ZR CO-CR-FE CO-CR-HF CO-FE-HF CO-FE-MO CO-FE-NI CO-FE-TA CO-FE-W CO-FE-ZR CO-HF-NB CO-HF-NI CO-MO-NB CO-MO-NI CO-NB-NI CO-NB-TA CO-NB-TI CO-NB-W CO-NB-ZR CO-NI-TI CO-NI-V CO-NI-ZR CO-TA-TI CR-FE-HF CR-FE-NB CR-FE-TA CR-FE-TI CR-FE-ZR CR-HF-NI CR-MO-NB CR-NB-TA CR-NB-TI CR-NB-W CR-NB-ZR FE-HF-MO FE-HF-NB FE-HF-NI FE-HF-TA FE-HF-TI FE-HF-W FE-HF-ZR FE-MO-NB FE-MO-TA FE-MO-TI FE-MO-ZR FE-NB-TA FE-NB-TI FE-NB-W FE-NI-TA FE-NI-TI FE-NI-V FE-NI-ZR FE-TA-TI FE-TA-W FE-TA-ZR FE-TI-W FE-TI-ZR FE-W-ZR HF-MO-NB HF-NB-NI HF-NB-TA HF-NB-TI HF-NB-W HF-NB-ZR HF-NI-TI HF-NI-W HF-NI-ZR MO-NB-TA MO-NB-TI MO-NB-W MO-NB-ZR MO-NI-ZR NB-NI-TA NB-NI-ZR NB-TA-TI NB-TA-W NB-TA-ZR NB-TI-W NB-TI-ZR NB-W-ZR NI-TA-TI NI-TA-ZR NI-TI-W NI-TI-ZR TA-TI-V

Examples of calculations

FCC forming ternary systems

Fig.1: Calculated Co-Cr-Ni isothermal section at 1200 °C

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Fig.2: Calculated Co-Cu-Ni isothermal section at 1000 °C

BCC forming ternary systems

Fig.3: Calculated Cr-Mo-Nb isothermal section at 1500 °C

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Fig.4: Calculated Mo-Nb-Ti isothermal section at 800 °C

FCC/FCC+BCC forming ternary systems

Fig.5: Calculated Cr-Fe-Ni isothermal section at 1000 °C

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Fig.6: Calculated Cr-Fe-Ni isothermal section at 1300 °C

FCC+BCC forming ternary systems

Fig.7: Calculated Co-Cr-Fe isothermal section at 1200 °C

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Fig.8: Calculated Co-Cr-Fe isothermal section at 1300 °C

Multi-component alloy systems Figure 9 shows the effect of the Al addition on the phase formation in the CoCrFeNi-bases high entropy alloy. With a small amount of Al addition (<10 at.% Al), only FCC forms in as-cast alloys. The region roughly from 10 to 18 at.% Al is near the eutectic reaction, where both FCC and BCC can form in as-cast alloys. With an Al addition above 18 at.%, only BCC forms. It should be noted, however, that the phase formation also depends on the actual experimental conditions, especially the cooling rate and the heat treatment. The data from [2012Wan] indicate the compositions of the investigated as-cast alloys and the observed phases. The data from [2011Kao] are the composition limits for forming BCC, FCC and BCC+FCC in as-cast alloys or alloys homogenized at 1000 °C. Figures 10 and 11 show the phase formation in the Co-Cr-Fe-Mn-Ni equiatomic alloy from the equilibrium calculation and the Scheil calculation, respectively. They indicate that a single FCC solid solution can be obtained during solidification at different cooling rates (from equilibrium solidification to extremely non-equilibrium solidification). The single FCC state remains during a wide temperature ranged down to 600 °C. [2004Can] and [2013Ott] observed only FCC in as-cast alloys. The single phase state remained after the alloy had been annealed at 1000 °C or 850 °C for three days [2013Ott].

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Fig.9: Calculated phase diagram along the composition line of CoCrFeNi-Al.

Fig.10: Equilibrium calculation of the phase formation in the Co-Cr-Fe-Mn-Ni equiatomic alloy.

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Fig.11: Scheil calculation of the phase formation in the Co-Cr-Fe-Mn-Ni equiatomic alloy.

[2004Can] had investigated as-cast alloys prepared by melting spinning and reported that adding Cu into the Co-Cr-Fe-Mn-Ni alloy destabilized FCC dendrites and caused an interdendritic segregation with no second phase. According to the present calculation, as shown in Fig. 12, however, the interdendritic region actually corresponds to a Cu-rich secondary FCC phase. In other words, there is a miscibility gap of FCC. Note that the conclusion of no second phase by [2004Can] had been drawn merely based on the poor XRD pattern, which was not sufficient to identify two sets of FCC phases. Figure 12 suggested a peritectic type transformation from the primary FCC and liquid to the secondary FCC, but the amount of liquid involved in the transition is much more than that of the pimary FCC. Considering the high cooling rate, the peritectic reaction would be suspended and a direct solidification of the secondary FCC from liquid can be considered, as illustrated by segments 3 and 4 on the curve of Scheil simulation (Fig. 13). The phase formation was dramatically affected by the composition segregation during the fast cooling: the amount of secondary FCC was predicted to be up to 28 % compared to about 20 % from the equilibrium calculation (Fig. 12); the accumulation of Cr in the residual liquid caused the BCC phase to form at and below 1019 °C. The amount of BCC was calculated to be less than 1 %, so it might be overlooked during the microstructure examination. Moreover, the formation of BCC might be suspended during melting spinning, due to insufficient diffusion in both liquid and FCC and/or inefficient nucleation of BCC.

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Fig.12: Equilibrium calculation of the phase formation in the Co-Cr-Cu-Fe-Mn-Ni equiatomic alloy.

Fig.13: Scheil calculation of the phase formation in the Co-Cr-Cu-Fe-Mn-Ni equiatomic alloy.

Figure 14 shows that single BCC_A2 solid solution can be obtained in as-cast equiatomic Al-Cr-Mn-Ti-V alloys. The BCC single phase remains in a wide temperature range down to 629 °C, where it starts to order to form the B2 phase.

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Fig.14: Equilibrium calculation of the phase formation in the Al-Cr-Mn-Ti-V equiatomic alloy.

References [2004Can] B. Cantor, I.T.H. Chang, P. Knight, A.J.B. Vincent, Microstructural development in equiatomic multicomponent alloys. Mat. Sci. Eng. A 375-377 (2004) 213-218.

[2004Yeh] Yeh JW, Chen SK, Lin SJ, Gan JY, Chin TS, Shun TT, Tsau CH, Chang SY. Nanostructured high-entropy alloys with multiple principal elements: novel alloy design concepts and outcomes. Adv Eng Mater. 2004;6:299–303.

[2004Yeh1] J.W. Yeh, S.K. Chen, S.J. Lin, J.Y. Gan, T.S. Chin, T.T. Shun, C.H. Tsau, S.Y. Chang: Adv. Eng. Mater., 6 (2004) 299-303.

[2004Yeh2] J.W. Yeh, S.K. Chen, J.Y. Gan, S.J. Lin, T.S. Chin, T.T. Shun, C.H. Tsau, S.Y. Chang: Metall. Mater. Trans. A, 35 (2004) 2533-2536.

[2005Ton1] C.J. Tong, Y.L. Chen, S.K. Chen, J.W. Yeh, T.T. Shun, C.H. Tsau, S.J. Lin, S.Y. Chang: Metall. Mater. Trans. A, 36A (2005) 881-893.

[2005Ton2] C. Tong, M. Chen, S. Chen, J. Yeh, T. Shun, S. Lin,S. Chang, Mechanical performance of the AlxCoCrCuFeNi high-entropy alloy system with multiprinciple elements, Metallurgical And Materials Transactions A-Physical Metallurgy And Materials Science, 36 (2005) 1263-1271.

[2006Yeh] Yeh JW. Recent progress in high-entropy alloys. Ann Chim-Sci Mat. 2006;31:633–648.

[2011Kao] Yih-Farn Kao, Swe-Kai Chen, Ting-Jie Chen, Po-Chou Chu, Jien-Wei Yeh, Su-Jien Lin, Electrical, magnetic, and Hall properties of AlxCoCrFeNi high-entropy alloys. J Alloy Compd, 509 (2011) 1607-1614.

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[2012Wan] Woei-Ren Wang, Wei-Lin Wang, Shang-Chih Wang, Yi-Chia Tsai, Chun-Hui Lai, Jien-Wei Yeh, Effects of Al addition on the microstructure and mechanical property of AlxCoCrFeNi high-entropy alloys. Intermetallics, 26 (2012) 44-51.

[2013Ott] F. Otto, Y. Yang, H. Bei, E. P. George, Relative effects of enthalpy and entropy on the phase stability of equiatomic high-entropy alloys. Acta mater. 61 (2013) 2628-2638.

[2013Wan] S. Wang, Atomic structure modeling of multi-principal-element alloys by the prcinciple of maximum entropy, Entropy, 2013, 15:5536-5548.

[2014Tsa] M. Tsai,J. Yeh, High-entropy alloys: A critical review, Materials Research Letters, 2 (2014) 107-123.

[2015Sen] O. N. Senkov, J. D. Miller, D. B. Miracle,C. Woodward, Accelerated exploration of multi-principal element alloys with solid solution phases, Nature, 2015, 6: 6529:1-17.

List of all phases included in TCHEA1.0 One can list phases and constituents in the Database module and the GES module. For some phases, supplementary information has been included in their definitions. In order to show the information, it is recommended to use “List-System” or “List-Database” with the option of “Constituents” in the Database module.

LIQUID:L FCC_A1 FCC_L12 BCC_A2 BCC_B2 HCP_A3 DIS_FCC_A1 CBCC_A12 CUB_A13 D019_HCP AL10CU10FE AL10FEMN2 AL10V AL11CR2 AL11CU5MN3 AL11MN4_HT AL11MN4_LT AL11TI5 AL12MN AL12W AL13CO4 AL13CR2 AL13FE2MN2 AL13FE4 AL16FEMN3 AL23CUFE4

AL23V4 AL28CU4MN7 AL2FE AL2TI AL2W AL2ZR3 AL31MN6NI2 AL3CO AL3NI1 AL3NI2 AL3NI5 AL3ZR AL3ZR2 AL3ZR4 AL3ZR5 AL4CR AL4MN_R AL4MN_U AL4W AL4ZR5 AL5CO2_D811 AL5FE2 AL5FE4 AL5W AL62CU25FE13 AL63MO37

AL6MN AL77W23 AL7CU2FE AL7CU4NI AL7V AL7W3 AL8CR5_H AL8CR5_L AL8MN5 AL8MO3 AL8V5 AL9CO2 AL9CR4_H AL9CR4_L ALCR2 ALCU_DEL ALCU_EPS ALCU_ETA ALCU_PRIME ALCU_ZETA ALCU3MN2 ALMO ALPHA_B19 ALTI_L10 ALTI3_DO19 ALZR

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ALZR2 B11 BCT_D022 C14_LAVES C15_LAVES C16_THETA C36_LAVES CFC2_FENBZR CHI_A12 CO10CU57TI33 CO11ZR2 CO3VV CO7HF CO7M2 CR3MN5 CR3SI_A15 CRNI2_OP6 CU10HF7 CU10ZR7 CU2TI CU2TIZR CU3TI2 CU4TI1 CU4TI3 CU51HF14 CU51ZR14 CU8HF3 CU8ZR3 CUTI3

DIS_MU DIS_SIG FCC_L10 G_PHASE GAMMA_D83 GAMMA_H H_L21 HF3NI7 HF8NI21 HFMN HFNI_ALPHA HFNI3_ALPHA HFNI3_BETA HIGH_SIGMA MN3TI MN4TI MNNI2 MNTA MNTI_HT MNTI_LT MONI_DELTA MONI4_BETA MOSI2_C11B MU_PHASE MZR3_E1A NB13NI75TI12 NB15NI56TI29 NB15NI80TI5 NB5NI75TI20

NB8NI9TI3 NI10ZR7 NI11ZR9 NI2TA NI2V NI3TA_D0A NI3TI_D024 NI5ZR NI7ZR2 NI8TA NITI2 NIZR P_PHASE R_PHASE SIGMA T1_CU2TI T1CUNITI T2_CU3TI2 T2CUNITI T3_CU4TI3 T4CUFETI T4CUNITI T5CUFETI T6CUNITI TAAL TAAL2 ALMNTI_L12

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List of models for all the phases included in TCHEA1.0

LIQUID:L :AL CO CR CU FE HF MN MO NB NI TA TI V W ZR: > LIQUID mixture.

FCC_A1 2 SUBL, 1 1 :AL CO CR CU FE HF MN MO NB NI TA TI V W ZR:VA: > If FCC_L12 is defined, this phase will be combined to it.

FCC_L12 3 SUBL, 0.75 0.25 1 :AL CO CR CU FE HF MN MO NB NI TA TI V W ZR:AL CO CR CU FE HF MN MO NB NI TA TI V W ZR:VA: > This phase has some contribution from FCC_A1.

BCC_A2 2 SUBL, 1 3 :AL CO CR CU FE HF MN MO NB NI TA TI V W ZR VA:VA: > If BCC_B2 is defined, this phase will be combined to it.

BCC_B2 3 SUBL, 0.5 0.5 3 :AL CO CR CU FE HF MN MO NB NI TA TI V W ZR VA:AL CO CR CU FE HF MN MO NB NI TA TI V W ZR VA:VA: > This phase has some contribution from BCC_A2.

HCP_A3 2 SUBL, 1 0.5 :AL CO CR CU FE HF MN MO NB NI TA TI V W ZR:VA:

DIS_FCC_A1 2 SUBL, 1 1 :AL CO CR CU FE HF MN MO NB NI TA TI V W ZR:VA:

CBCC_A12 2 SUBL, 1 1 :AL CO CR CU FE MN MO NB NI TA TI V W ZR:VA:

CUB_A13 2 SUBL, 1 1 :AL CO CR CU FE HF MN MO NB NI TA TI V W ZR:VA:

D019_HCP 3 SUBL, 0.75 0.25 1 :AL CO CR FE HF MO NB NI TA TI W ZR:AL CO CR FE HF MO NB NI TA TI W ZR:VA:

NI3TI_D024 2 SUBL, 0.75 0.25 :AL CO CR CU FE HF NI TA TI W ZR:AL CR CU HF MO NB NI TA TI W ZR: > also AlNi6Ta

NI3TA_D0A 2 SUBL, 3 1 :AL CO CR FE NI NB:AL FE MO NB NI TA TI V W: > also Ni3Mo, Ni3Nb

BCT_D022 2 SUBL, 3 1 :AL CR FE MO NB NI TI V:AL CR MO NB NI TA TI V: > gamma double prime

C14_LAVES 2 SUBL, 2 1 :AL CO CR CU FE HF MN MO NB NI TA TI W ZR:AL CO CR CU FE HF MN MO NB NI TA TI W ZR: > prototype CuZn2

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DIS_MU :AL CO CR CU FE MN MO NB NI TA TI W: > Part of the description of MU_PHASE.

MU_PHASE 4 SUBL, 1 2 6 4 :AL CO CR CU FE MN MO NB NI TA TI W:AL CO CR CU FE MN MO NB NI TA TI W:AL CO CR CU FE MN MO NB NI TA TI W:AL CO CR CU FE MN MO NB NI TA TI W: DIS_MU contribution is introduced in the description of this phase

DIS_SIG :AL CO CR FE MN MO NB NI TA TI V W: > Part of the description of SIGMA phase.

SIGMA 3 SUBL, 10 4 16 :AL CO CR FE MN MO NB NI TA TI V W:AL CO CR FE MN MO NB NI TA TI V W:AL CO CR FE MN MO NB NI TA TI V W: > DIS_SIG contribution is introduced in the description of this phase

R_PHASE 3 SUBL, 27 14 12 :CO CR FE NI:MO W:CO CR FE MO NI W: > Prototype : Co5Cr2Mo3

P_PHASE 3 SUBL, 24 20 12 :CR FE NI:CR FE MO NI:MO: > Prototype : Cr9Mo21Ni20

CHI_A12 3 SUBL, 24 10 24 :CR FE NI:AL CR HF MO NB TA TI W ZR:CR FE MO NB NI TA W:

MONI_DELTA 3 SUBL, 24 20 12 :CO CR FE NI:CO CR FE MO NI W:CU MO W:

ALTI_L10 2 SUBL, 1 1 :AL CR MN MO TA TI W:AL CR MN MO TA TI W:

NIZR 2 SUBL, 1 1 :NI:TI ZR:

ALZR 2 SUBL, 1 1 :AL:HF ZR: >also AlHf

ALPHA_B19 2 SUBL, 1 1 :MO NB TI V ZR:MO NB TI V ZR:

B11 2 SUBL, 1 1 :CO CU NI TI:CU NI TA TI:

HFMN 2 SUBL, 0.5 0.5 :HF:MN:

FCC_L10 2 SUBL, 0.5 0.5 :CU MN NI:CU MN NI:

MNTA 2 SUBL, 1 1 :MN:TA:

C15_LAVES 2 SUBL, 2 1

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:AL CO CR CU FE HF MN MO NB NI TA TI V W ZR:AL CO CR CU FE HF MO NB NI TA TI V W ZR:

C36_LAVES 2 SUBL, 2 1 :AL CO CR CU FE HF MO NB NI TA TI W ZR:AL CO CR CU FE HF MO NB NI TA TI W ZR:

CRNI2_OP6 2 SUBL, 1 2 :CR MO W:MO NI W:

NI2TA 2 SUBL, 2 1 :CO NI:TA TI:

NI2V 2 SUBL, 2 1 :MO NI:MO NB TA V: > Ni2V

C16_THETA 2 SUBL, 2 1 :AL HF MO NB TA TI W ZR:AL CO CR CU FE NI: > Al2Cu, Hf2Al, Zr2Co, Ta2Co, Hf2Ni, Ta2Ni, Zr2Ni

CU2TI 2 SUBL, 2 1 :CO CU NI:TI:

MNNI2 2 SUBL, 1 2 :MN NI:NI:

NITI2 2 SUBL, 1 2 :CO CR CU FE NI TI:AL CR CU HF NI TA TI ZR:

ALTI3_DO19 2 SUBL, 3 1 :AL CO CR MN MO NI TA TI W:AL CR MO NB NI TA TI W:

AL3ZR 2 SUBL, 3 1 :AL:HF ZR: > also Al3Hf

CUTI3 2 SUBL, 1 3 :CU TI:TI:

MZR3_E1A 2 SUBL, 1 3 :CO FE NI:ZR: > COZR3, FEZR3,

H_L21 3 SUBL, 0.5 0.5 1 :AL NI TI:AL HF NB NI TA TI ZR:CO NI VA:

G_PHASE 3 SUBL, 16 6 7 :AL CO FE MN NI TI:HF NB TI ZR:CO FE MN NI: > Th6Mn23 prototype

ALCU_DEL 2 SUBL, 2 3 :AL:CU FE:

ALCU_EPS 2 SUBL, 1 1 :AL CU NI:CU FE:

ALCU_ETA 2 SUBL, 1 1

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:AL CU:CU FE NI:

ALCU_PRIME 2 SUBL, 2 1 :AL:CU:

ALCU_ZETA 2 SUBL, 9 11 :AL:CU FE:

GAMMA_D83 3 SUBL, 4 1 8 :AL NI:AL CU NI:CU FE MN NI: > Al5Cu8 (rt)

GAMMA_H 3 SUBL, 4 1 8 :AL:AL CU:CU FE MN NI: > Cu5Zn8-type Al8Cu5 (ht) phase

AL23CUFE4 3 SUBL, 23 1 4 :AL:CU:FE:

AL62CU25FE13 3 SUBL, 0.125 0.255 0.62 :FE:AL CU:AL:

AL7CU2FE 3 SUBL, 1 2 7 :FE NI:CU:AL: > Solution phase of the ternary compound Al7Cu2Fe

AL10CU10FE 3 SUBL, 1 10 10 :FE:AL CU:AL:

AL7CU4NI 2 SUBL, 1 1 :AL:FE CU NI VA:

AL12MN 2 SUBL, 12 1 :AL:MN:

AL4MN_R 2 SUBL, 461 107 :AL:MN FE:

AL4MN_U 2 SUBL, 4 1 :AL:MN:

AL11MN4_LT 2 SUBL, 11 4 :AL:MN FE:

AL11MN4_HT 2 SUBL, 29 10 :AL MN:MN:

AL8MN5 3 SUBL, 12 5 9 :AL TI:MN:AL CU MN TI:

ALMNTI_L12 3 SUBL, 0.25 8E-2 0.67 :AL MN TI:AL MN:AL MN TI:

AL28CU4MN7 3 SUBL, 28 7 4 :AL:MN:CU:

AL11CU5MN3 3 SUBL, 11 3 5 :AL:MN:CU:

ALCU3MN2 3 SUBL, 1 2 3

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:AL:MN:CU:

AL16FEMN3 2 SUBL, 4 1 :AL:FE MN:

AL13FE2MN2 2 SUBL, 4 13 :FE MN:AL:

AL10FEMN2 2 SUBL, 3 10 :FE MN:AL:

AL6MN 2 SUBL, 6 1 :AL:FE MN:

ALZR2 2 SUBL, 1 2 :AL:ZR:

AL2ZR3 2 SUBL, 2 3 :AL:HF ZR: > also Al2Hf3

AL3ZR4 2 SUBL, 3 4 :AL:HF ZR: > also Al3Hf4

AL3ZR2 2 SUBL, 3 2 :AL:HF ZR: > also Al3Hf2

AL3NI2 3 SUBL, 3 2 1 :AL:AL CU NI:NI VA:

AL12W 2 SUBL, 12 1 :AL:MO W: > also AL12MO

AL4W 2 SUBL, 4 1 :AL:MO W: > also Al4Mo

MONI4_BETA 2 SUBL, 1 4 :MO W:NI: > also WNi4

AL5W 2 SUBL, 5 1 :AL:MO W: > also AL5MO

CO10CU57TI33 3 SUBL, 0.1 0.57 0.33 :CO:CU:TI:

CU51HF14 2 SUBL, 51 14 :CU:HF:

CU8HF3 2 SUBL, 8 3 :CU:HF:

CU10HF7 2 SUBL, 10 7

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:CU:HF:

T1_CU2TI 2 SUBL, 2 1 :CU FE:TI: > the Cu-Fe-Ti ternary phase, Tau1

T2_CU3TI2 2 SUBL, 3 2 :CU FE:TI: > the Cu-Fe-Ti ternary phase, Tau2

T3_CU4TI3 2 SUBL, 4 3 :CU FE:TI: > the Cu-Fe-Ti ternary phase, Tau3

T4CUFETI 2 SUBL, 0.63 0.37 :CU FE:TI: > the Cu-Fe-Ti ternary phase, Tau4

T5CUFETI 2 SUBL, 0.55 0.45 :CU FE:TI: > the Cu-Fe-Ti ternary phase, Tau5

T1CUNITI 2 SUBL, 2 1 :CU NI:TI: > the Cu-Ni-Ti ternary phase, Tau1

T2CUNITI 3 SUBL, 0.175 2.825 2 :CU:NI:TI: > the Cu-Ni-Ti ternary phase, Tau2

T4CUNITI 3 SUBL, 5E-2 0.7 0.25 :CU:NI:TI: > the Cu-Ni-Ti ternary phase, Tau4

T6CUNITI 3 SUBL, 0.25 0.5 0.25 :CU:NI:TI: > the Cu-Ni-Ti ternary phase, Tau6

CU3TI2 2 SUBL, 3 2 :CU NI FE:CO TI:

CU4TI1 2 SUBL, 4 1 :CU TI:CU TI:

CU4TI3 2 SUBL, 4 3 :CO CU NI:TI:

CU2TIZR 3 SUBL, 0.5 0.25 0.25 :CU:TI:ZR: CU10ZR7 2 SUBL, 10 7 :CU:ZR:

CU51ZR14 2 SUBL, 51 14 :CU:ZR:

CU8ZR3 2 SUBL, 8 3 :CU:ZR:

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NI7ZR2 2 SUBL, 7 2 :AL CO CR NI:HF ZR: > also NI7HF2, NI7Y2, CO7Y2 and CO7HF2

NI11ZR9 2 SUBL, 11 9 :NI:HF ZR:

NI10ZR7 2 SUBL, 23 17 :NI:HF ZR:

NI5ZR 2 SUBL, 5 1 :CU NI:HF ZR: > also Ni5Y, Ni5Hf, Cu5Hf and Cu5Zr

HF8NI21 2 SUBL, 8 21 :HF ZR:NI: > also ZR8NI21

AL13FE4 3 SUBL, 0.6275 0.235 0.1375 :AL CU:FE MN:AL VA:

NI8TA 2 SUBL, 8 1 :NI:NB TA:

CO7M2 2 SUBL, 7 2 :CO:NB TA:

CR3SI_A15 3 SUBL, 3 1 3 :CR FE MO NB NI TA TI V:AL CO CR MO NB NI TA TI V:VA: > Mo3Al, Nb3Al, V3Co, V3Ni

MOSI2_C11B 2 SUBL, 1 2 :CO CU FE MO NI W:AL HF TI ZR: > also CuHf2, CuTi2, CuZr2, Prototype MoSi2

AL13CO4 2 SUBL, 13 4 :AL:CO:

AL3CO 2 SUBL, 3 1 :AL:CO:

AL5CO2_D811 2 SUBL, 5 2 :AL:CO: > D811

AL9CO2 2 SUBL, 9 2 :AL:CO:

AL11CR2 3 SUBL, 10 1 2 :AL:AL:CR:

AL13CR2 2 SUBL, 13 2 :AL:CR:

AL4CR 2 SUBL, 4 1 :AL:CR:

AL8CR5_H 2 SUBL, 8 5

TCHEA1

:AL:CR:

AL8CR5_L 2 SUBL, 8 5 :AL:CR:

AL9CR4_H 2 SUBL, 9 4 :AL:CR:

AL9CR4_L 2 SUBL, 9 4 :AL:CR:

ALCR2 2 SUBL, 1 2 :AL:CR:

AL2FE 2 SUBL, 2 1 :AL CU:FE MN:

AL5FE2 2 SUBL, 5 2 :AL CU:FE MN:

AL5FE4 :AL CU FE:

AL63MO37 2 SUBL, 63 37 :AL:MO:

AL8MO3 2 SUBL, 8 3 :AL:MO:

ALMO 2 SUBL, 1 1 :AL MO:AL MO: > A2 badly described

AL3NI1 2 SUBL, 0.75 0.25 :AL:NI:

AL3NI5 2 SUBL, 0.375 0.625 :AL:NI:

TAAL 2 SUBL, 0.51515 0.48485 :TA:AL:

TAAL2 2 SUBL, 0.35 0.65 :TA:AL:

AL11TI5 2 SUBL, 17 8 :AL:TI:

AL2TI 2 SUBL, 2 1 :AL:TI:

AL10V 2 SUBL, 10 1 :AL:V:

AL7V 2 SUBL, 7 1 :AL:V:

AL23V4 2 SUBL, 23 4 :AL:V:

TCHEA1

AL8V5 2 SUBL, 8 5 :AL:V:

AL77W23 2 SUBL, 77 23 :AL:W:

AL7W3 2 SUBL, 7 3 :AL:W:

AL2W 2 SUBL, 2 1 :AL:W:

AL3ZR5 2 SUBL, 3 5 :AL:ZR:

AL4ZR5 2 SUBL, 4 5 :AL:ZR:

CO7HF 2 SUBL, 7 1 :CO:HF:

CO3VV 2 SUBL, 3 1 :CO V:CO V:

CO11ZR2 2 SUBL, 11 2 :CO:ZR:

CR3MN5 2 SUBL, 3 5 :CR:MN:

HIGH_SIGMA 3 SUBL, 8 4 18 :MN:CR:CR MN:

HFNI3_ALPHA 2 SUBL, 0.25 0.75 :HF:NI:

HFNI3_BETA 2 SUBL, 0.25 0.75 :HF:NI:

HF3NI7 2 SUBL, 0.3 0.7 :HF:NI:

HFNI_ALPHA 2 SUBL, 0.5 0.5 :HF:NI:

MNTI_LT 2 SUBL, 1 1 :MN:TI:

MNTI_HT 2 SUBL, 0.515 0.485 :MN:TI:

MN3TI 2 SUBL, 3 1 :MN:TI:

MN4TI 2 SUBL, 0.815 0.185 :MN:TI:

AL31MN6NI2 3 SUBL, 31 6 2 :AL:MN:NI: > Orthorhombic, ternary Al-Mn-Ni phase

TCHEA1

CFC2_FENBZR 3 SUBL, 2 1 3 :FE NB ZR:NB ZR:NB ZR:

NB15NI56TI29 3 SUBL, 0.15 0.56 0.29 :NB:NI:TI:

NB8NI9TI3 3 SUBL, 0.4 0.45 0.15 :NB:NI:TI:

NB5NI75TI20 3 SUBL, 5E-2 0.75 0.2 :NB:NI:TI:

NB13NI75TI12 3 SUBL, 0.13 0.75 0.12 :NB:NI:TI:

NB15NI80TI5 3 SUBL, 0.15 0.8 5E-2 :NB:NI:TI:

TCHEA1

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