Physical Factors Controlling Large Shape Memory Effect in FCC ↔ HCP Martensitic Transformation in CrMnFeCoNi High-Entropy-Alloy Single Crystals
Abstract
:1. Introduction
2. Materials and Methods
2.1. Preparation of Single Crystals and Samples for Testing
2.2. Optical and Microstructural Studies
2.3. Thermal Transformation Studies
2.4. Mechanical Studies
3. Results
3.1. Thermal Transformation Behavior
3.2. Temperature Dependence of Yield Stress
3.3. Shape Memory Effect under External Tensile Stress
3.4. Shape Memory Effect under Tensile Strain at Different Temperatures
4. Discussion
4.1. The Main Parameters for the Implementation of a Reversible FCC–HCP MT
4.1.1. The Role of the Yield Stress σ0.1 of the Initial FCC Phase
4.1.2. The Role of Difference between the Critical Shear Stresses for Slip and HCP Martensite at the Ms Temperature
4.1.3. The Role of Short-Range Order
4.1.4. The Role of the Splitting of the a/2<110> Dislocation into the a/6<112> Partial Shockley Dislocations under External Stresses
4.2. Orientation Dependence of SME in Cr20Mn20Fe20Co34.5Ni5.5 HEA Single Crystals
5. Conclusions
- In [011]- and -oriented Cr20Mn20Fe20Co34.5Ni5.5 HEA single crystals, FCC–HCP transformation develops upon cooling and heating in a free state and under stress. The start temperature of the forward FCC–HCP transformation upon a cooling Ms temperature is 195–200 K. The FCC–HCP transformation during cooling/heating in a free state and under stress is characterized by wide temperature hysteresis: ΔTh = Af − Ms = 180–195 K in a free state and ΔTh = 150–185 K at σex = 150–170 MPa.
- The temperature dependence of the yield stress, σ0.1(T), has the form characteristic of alloys experiencing a martensitic transformation under stress and consists of three stages. The first stage at T < Ms is associated with the thermally activated motion of the interphase boundaries and introduction of thermally induced HCP martensite. The second one in the temperature range Ms < T < Md, on which a linear increase in stresses with increasing temperature is observed, is associated with the development of stress-induced HCP martensite and is described via the Clapeyron–Clausius relation. This stage in [011]- and -oriented crystals develops in a narrow temperature range, ΔTSIM = 105 K, and α = dσcr/dT at this stage weakly depends on the crystal orientation. The orientation dependence, α = dσcr/dT, is described via the orientation dependence of the theoretical value of the transformation strain, ε0Theory, for the FCC–HCP transition under tension in accordance with the Clausius–Clapeyron relation. The third stage, associated with the deformation of the FCC phase, takes place at a temperature above the Md temperature.
- For the first time, in [011]- and -oriented Cr20Mn20Fe20Co34.5Ni5.5 HEA crystals oriented for the development of HCP martensite in one system, the SME is realized under tension, which depends on the crystal orientation and external stresses, σex, in the “cooling-heating” cycle. The maximum SME is 13.6 ± 0.2% in [011]-oriented crystals at an external stress of 150 MPa, and 8.4 ± 0.2% in -oriented crystals at an external stress of 170 MPa. In the “stress-strain” cycle under tension, the maximum SME has the value of 14 ± 0.2% in -oriented crystals at the Ms temperature and of 13 ± 0.2% in [011]-oriented crystals at Ms and 77 K. The following physical factors are identified that contribute to the reversible movement of a/6<211> partial Shockley dislocations that are “exactly backward” when the stress is removed and lead to large SME: the stress level of the FCC phase, short-range order, and an increase in the splitting of a/2<110> perfect dislocations into a/6<211> partial Shockley dislocations in the external stress field.
Author Contributions
Funding
Institutional Review Board Statement
Informed Consent Statement
Data Availability Statement
Conflicts of Interest
References
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Orientation | Schmid Factor for Slip, msl | Schmid Factor for FCC–HCP Transition, mFCC–HCP | Theoretical Value ε0Theory, % |
---|---|---|---|
0.45 | 0.45 | 15.7 | |
[011] | 0.41 | 0.47 | 16.4 |
FCC Alloys | ΔV, % | TNe, K | σ0.1(Md), MPa | σ0.1(Ms), MPa | , MPa | SRO | , %, for Different Orientations |
---|---|---|---|---|---|---|---|
Fe–Mn–Si alloys [1,30] | 1.26–1.42, [13] | TNe ≈ Ms | 160 | 45 | 30 | no or weakly expressed | |
0.5–1.2, [001] | |||||||
Cr20Mn20Fe20Co34.5Ni5.5 HEA in the present paper | 1.15, [13] | TNe = 23 K << Ms | 205 | 115–125 | 65 | Yes SRO | 13.6, [011] |
, [18] | |||||||
3.6, [001], [20] |
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Kireeva, I.V.; Chumlyakov, Y.I.; Saraeva, A.A.; Vyrodova, A.V. Physical Factors Controlling Large Shape Memory Effect in FCC ↔ HCP Martensitic Transformation in CrMnFeCoNi High-Entropy-Alloy Single Crystals. Metals 2023, 13, 1755. https://doi.org/10.3390/met13101755
Kireeva IV, Chumlyakov YI, Saraeva AA, Vyrodova AV. Physical Factors Controlling Large Shape Memory Effect in FCC ↔ HCP Martensitic Transformation in CrMnFeCoNi High-Entropy-Alloy Single Crystals. Metals. 2023; 13(10):1755. https://doi.org/10.3390/met13101755
Chicago/Turabian StyleKireeva, Irina V., Yuriy I. Chumlyakov, Anastasia A. Saraeva, and Anna V. Vyrodova. 2023. "Physical Factors Controlling Large Shape Memory Effect in FCC ↔ HCP Martensitic Transformation in CrMnFeCoNi High-Entropy-Alloy Single Crystals" Metals 13, no. 10: 1755. https://doi.org/10.3390/met13101755