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Article

Ni-Mn-Sn-Cu Alloys after Thermal Cycling: Thermal and Magnetic Response

by
Asma Wederni
1,
Mihail Ipatov
2,
Julián-María González
2,
Mohamed Khitouni
3 and
Joan-Josep Suñol
1,*
1
Department of Physics, P2, EPS, University of Girona, 17003 Girona, Spain
2
Department of Applied Physics, University of the Basque Country, 20018 Donostia, Spain
3
Laboratory of Inorganic Chemistry, University of Sfax, B.P. 1171, Sfax 3000, Tunisia
*
Author to whom correspondence should be addressed.
Materials 2021, 14(22), 6851; https://doi.org/10.3390/ma14226851
Submission received: 14 October 2021 / Revised: 2 November 2021 / Accepted: 10 November 2021 / Published: 13 November 2021
(This article belongs to the Section Metals and Alloys)
Browse Figures
Versions Notes

Abstract

:
Heusler Ni-Mn-Sn-based alloys are good candidates for magnetic refrigeration. This application is based on cycling processes. In this work, thermal cycles (100) have been performed in three ribbons produced by melt-spinning to check the thermal stability and the magnetic response. After cycling, the temperatures were slowly shifted and the thermodynamic properties were reduced, the entropy changed at about 3–5%. Likewise, the thermomagnetic response remains similar. Thus, these candidates maintain enough thermal stability and magnetic response after cycling. Likewise, Cu addition shifts the structural transformation to higher temperatures, whereas the Curie temperature is always near 310 K. Regarding magnetic shape memory applications, the best candidate is the Ni49Mn36 Sn14Cu1 alloy.

1. Introduction

Ni-Mn-Sn-based Heusler ferromagnetic alloys are multifunctional materials due to the coupling of a reversible solid-state first order transformation (austenite to martensite) and a second order magnetic transformation (ferromagnetic to paramagnetic). In these alloys, the transformations can be induced by mechanical stress, temperature and/or external magnetic field. Functional effects of these materials are: magnetic shape memory [1], magnetocaloric [2], magneto-resistance [3], exchange-bias [4], barocaloric [5] or elastocaloric [6].
Addition of small quantities of a fourth element in the ternary off-stoichiometry Heusler alloys has been proposed as a way to improve the functional response and to tailor the transition temperatures [7]. The shift of the transition temperatures is due to the sensitivity to interatomic distances and hybridization [8]. This trend opens the possibility of deliberate changes in the transition temperatures and benefits while forcing phase transitions by a temperature and magnetic field [9]. The improvement of the magnetic response could be favored by the addition of a magnetic element as Fe [10] or Co [11]. Gd-based and Ni-Mn-In alloys are good candidates for magnetic refrigeration devices. Thus, Gd [12] or In [13] addition has been also analyzed. A minor amount of other metallic elements, such as Zn [14], Al [15] or Pd [16], or metalloids, such as B [17] have been also checked. In these compounds, the main effect is the shift of the transition temperatures. Obviously, the addition of two elements to combine their effect has been done, such as Pt and Co [18]. In our work, Cu addition has been performed.
Likewise, for the magnetic refrigeration or shape memory applications it is necessary to check the stability of the functional response after cycling. The mechanical cycling from Ni-Mn-based alloys shows that the mechanical stability is linked to the good geometrical compatibility at the interphase between austenite and martensite [19].
In our study, we produce three Ni-Mn-Sn-(Cu) Heusler alloys. In a previous work [20], we analyzed the microstructure of the as produced ribbons as well as the thermal and magnetic behavior. These ribbon flakes have been now subjected to controlled thermal cycling (100 cycles). The main objective is to analyze the thermal and magnetic response to check its thermal and magnetic stability after cycling.

2. Materials and Methods

Three alloys with nominal composition (at.%) Ni50−xMn36Sn14Cux (x = 0, 1, and 2) were produced by melt-spinning (melt-spinner MSP 10, Edmund Bühler GmbH, Bodelshausen, Germany) as ribbon flakes (1 mm thick, 2–3 cm long, 20 μm width). The X-ray diffraction (XRD, D500 S equipment, Bruker, Billerica, MA, USA) patterns at room temperature were made to verify the crystallographic structure of the spun-ribbons. The refinement of crystalline structures were made by applying the Maud software, which is founded on the Rietveld method [11]. Austenite to martensite direct and inverse temperatures were determined by differential scanning calorimetry (DSC) in a DSC822 Mettler-Toledo calorimeter, at a heating/cooling rate of 10 K/min. Thermal cycling (100 cycles) experiments were performed with liquid nitrogen between nitrogen liquidus temperature and room temperature. Thermomagnetic measurements were done on a PPMS 6000 device (Quantum Design, San Diego, CA, USA). Zero-field-cooling (ZFC), field-cooling (FC) and field-heating (FH) protocols, in a temperature range from low temperature up to 400 K and an applied magnetic field up to 50 kOe; whereas magnetic hysteresis loops were recorded at 50 K and 300 K.

3. Results and Discussion

The results include the crystallographic analysis of the as-quenched ribbon flakes and the analysis of the thermal and magnetic behavior after cycling. These results were discussed by comparison with those of ribbons before thermal cycling.

3.1. Crystallographic Analysis

The analysis of the three diffraction patters collected by XRD of the ribbons shows that at room temperature all the samples have a cubic L21 Heusler structure. This crystallographic structure is found in ternary alloys and the stoichiometry is 2:1:1 (X2YZ). Thus, we produce of stoichiometry alloys, and the excess od Mn atoms will be in Z sites. The Rietveld analysis has been performed, as shown in the Figure 1.
The L21 orders have been determined by taking into account Equation (1):
(I111∕I220) exp = [ SL21 (3 − SB2∕2)]2 (I111∕I220) th,
where the I (hkl) refers to the Bragg peak’s intensity, Miller indices (hkl) and the suffixes ‘exp’ represent experimentally obtained intensity values and “th” represents theoretically simulated and “S” represents the order parameter. This order parameter before cycling ranged between 85–88% [20], whereas between 73–75% after cycling. The produced alloys were off-stoichiometry. Thus, this reduction indicates that the alloys evolve to the lower expected L21 order.
The crystallographic parameters derived from Rietveld analysis of the specimens before and after thermal cycling are given in Table 1.
The lattice parameters change slightly with the thermal cycling and/or the Cu addition. Meanwhile, the microstrain decreases after cycling and the crystalline size increases. Probably the local atomic displacements during cycling and the accommodation of the martensite favors this behavior.

3.2. Thermal Analysis

As the crystallographic phase is cubic at room temperature, in all samples only the austenite phase is detected. In order to determine the temperatures of the reversible austenite to martensite structural transformation continuous cooling-heating was performed. Figure 2, Figure 3 and Figure 4 show the DSC scans before and after thermal cycling of alloys Ni50−x Mn36 Sn14 Cux (x = 0, 1, and 2), respectively.
The scans show that the addition of a minor amount of Cu shifts the transition temperatures to higher values. Thus, by controlling composition it is possible to design the production of alloys with transformation temperatures close to room temperature. A characteristic temperature is the equilibrium Gibbs temperature of the martensite structural transformation, To, that is calculated from DSC scan analysis following the procedure described in reference [21]. The To values obtained before and after thermal cycling are provided in Table 2. Thermal cycling slightly increases the transformation temperatures.
The enthalpy and entropy values of the structural transformation (ΔH and ΔS respectively) are also given in Table 1. The enthalpy decreases with thermal cycling, the same effect is found in the entropy. These trends need to be confirmed for long term cycles and should be taken into account in the design of magnetocaloric devices.

3.3. Magnetic Analysis

Further, we will consider the magnetic properties of the alloys. Zero-field-cooling (ZFC), field-heating (FH), and field-cooling (FC) experiments have been performed at two different external magnetic fields to check the magnetic response at low (50 Oe) and high (50 KOe) magnetic fields. The thermomagnetic curves are represented in Figure 5, Figure 6 and Figure 7 for thermally cycled alloys Ni50−x Mn36 Sn14 Cux (x = 0, 1, and 2), respectively.
As expected, through the process of the structural transition at 50 Oe, both FC and ZFC curves exhibit an irreversible behavior due to the obvious hysteresis between FC and ZFC curves, leading to the direct and inverse martensite transformation. It is known that this transformation requires overheating (martensite to austenite) and undercooling (austenite to martensite). This behavior was presented in such a thermal hysteresis between the FH and FC curves. Furthermore, the separation between the ZFC and FC scans below this ferromagnetic transition usually caused by spin glass state and/or the coexistence of antiferromagnetic and ferromagnetic states [22,23].
Regarding the influence of the Cu addition, it is clear that the Cu favors the increase of the temperatures of the structural transformation, confirming DSC data, whereas the Curie temperature remains early constant at around 310 K. Thus, this temperature was slightly increased (3–5 K) after thermal cycling [20]. The first effect was also detected in the samples before thermal cycling, whereas a slight decrease (up to 13 K) was found in the Curie temperature. From the results after cycling, we can remark that Cu addition could be a way to shift the structural transformation close to the magnetic transformation in order to favor the interplay between both transformations at low magnetic fields. It is well known that the total entropy change, ΔS, linked to the martensite transformation represents a limit to the attainable magnetic entropy change, and it has been phenomenologically established that it decreases exponentially with the increment of the generalized order parameter defined as the temperature interval between the Curie temperature of the austenite and the Gibbs equilibrium temperature of the structural transformation, TC − To [10]. From such relation, it can be deduced that the closest the Curie temperature of the austenite to the equilibrium temperature, the largest the magnetic entropy change values can be achieved. Likewise, at 50 Oe the magnetization has a minor growth as Cu content increases. This tendency is not followed at 50 kOe, 1 at.% Cu addition increases magnetization, but 2 at.% Cu addition does not.
Furthermore, one can note that the martensite is more stable when increasing the applied magnetic field because in the alloy without Cu, it takes more energy to transform the austenite into martensite. The important shift in the temperatures of the structural transformation by the Cu addition detected in DSC scans is reduced in the thermomagnetic scans at 50 kOe. Thus, for the possible applications of these alloys it is important to analyse their magnetic response at the expected working magnetic field.
It is known that the increase of the magnetization shift between the martensitic and the austenite phases benefits the field induced phase transformation, especially close to temperatures close the austenite start formation [7]. In our study, an increase of the magnetization change was found as increasing Cu content, it is a signal that the energy difference between the austenite L21 structure and the martensite structure increases by Cu doping [24]. Likewise, the calculated values of the temperature change due to an applied magnetic field of 1 T were 1.10, 1.30 and 1.16 K/T for the alloys with x = 0, 1, and 2 at.% of Cu, respectively. These values are slightly different than the calculated for the same specimens before thermal cycling: 1.28, 1.29, and 1.11 K/T. As there are close compositions, it is expected that the martensite phase was modulated 10M, as previously found in reference [20].
It can be concluded that the best alloy for applications linked to the magnetic shape memory and magnetocaloric effects is Ni49Mn36Sn14Cu1, as the elastocaloric behavior [25]. The non-continuous variation (as a function of Cu content) may be caused by hybridization or the non-entirely ferromagnetic band splitting [24].
Complementary magnetic analysis has been performed by performing magnetic hysteresis loops (50 K and 300 K). The results are shown in the Figure 8.
All the hysteresis loops at 50 K are clearly ferromagnetic. The measurements at 300 K show the decrease of the magnetization of saturation and the coercivity. The Cu addition provokes an increase in the coercivity and minor changes in the magnetization of saturation. The results are given in Table 3 and are similar to those obtained before thermal cycling. The increase on the coercivity with the increase of the Cu content can be provoked by the higher microstrain (Table 1 data).

4. Conclusions

Three alloys with nominal composition (at.%) Ni50−xMn36Sn14Cux (x = 0, 1, and 2) were produced by melt-pinning as ribbon flakes. At room temperature all the samples have the austenite L21 cubic Heusler structure. The L21 order parameter decreases after cycling to values ranged between 73–75%. Thermal analysis detects the reversible structural transformation, Cu addition shifts this transformation to higher temperature. After thermal cycling (100 cycles) it was found a slight increase of the Gibbs equilibrium temperature of the structural transformation, this shift is reduced in the thermomagnetic scans at 50 kOe. Whereas the Curie temperature remains close to 310 K. The calculated magnetization/entropy change ratios were 1.10, 1.30 and 1.16 K/T for the alloys with x = 0, 1, and 2 at.% of Cu, respectively. Results show the interest to check the thermal stability and the magnetic response of these alloys due to the cycling working conditions linked to some of their specific applications and also the interest of Cu addition to shift the transition temperatures.

Author Contributions

Conceptualization, J.-J.S. and M.K.; methodology, J.-M.G. and M.I.; formal analysis, A.W.; investigation, A.W. and M.I.; data curation, J.-M.G. and M.K.; writing—original draft preparation, J.-J.S. and M.I. All authors have read and agreed to the published version of the manuscript.

Funding

This study was funded by University of Girona PONT2020-01 and Spanish Mineco MAT2016-75967-P projects.

Data Availability Statement

Data can be requested from the authors.

Acknowledgments

The authors would like to thank the members of the Research Services (STR) of the University of Girona and the SGIker laboratory of the University of the Basque Country for their assistance and support in the analysis of the composites.

Conflicts of Interest

The authors declare no conflict of interest.

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Materials 14 06851 g001 550
Figure 1. X-ray diffraction patterns of the Ni-Mn-Sn-(Cu) ribbons.
Figure 1. X-ray diffraction patterns of the Ni-Mn-Sn-(Cu) ribbons.
Materials 14 06851 g001
Materials 14 06851 g002 550
Figure 2. DSC reversible scans of alloy Ni50 Mn36 Sn14 before and after 100 thermal cycles.
Figure 2. DSC reversible scans of alloy Ni50 Mn36 Sn14 before and after 100 thermal cycles.
Materials 14 06851 g002
Materials 14 06851 g003 550
Figure 3. DSC reversible scans of alloy Ni49 Mn36 Sn14 Cu1 before and after 100 thermal cycles.
Figure 3. DSC reversible scans of alloy Ni49 Mn36 Sn14 Cu1 before and after 100 thermal cycles.
Materials 14 06851 g003
Materials 14 06851 g004 550
Figure 4. DSC reversible scans of alloy Ni48 Mn36 Sn14 Cu2 before and after 100 thermal cycles.
Figure 4. DSC reversible scans of alloy Ni48 Mn36 Sn14 Cu2 before and after 100 thermal cycles.
Materials 14 06851 g004
Materials 14 06851 g005 550
Figure 5. ZFC, FH, and FC thermomagnetic measurements of alloy Ni50Mn36Sn14. (a) 50 Oe and (b) 50 KOe.
Figure 5. ZFC, FH, and FC thermomagnetic measurements of alloy Ni50Mn36Sn14. (a) 50 Oe and (b) 50 KOe.
Materials 14 06851 g005
Materials 14 06851 g006 550
Figure 6. ZFC, FH and FC thermomagnetic measurements of alloy Ni49Mn36Sn14Cu1. (a) 50 Oe and (b) 50 KOe.
Figure 6. ZFC, FH and FC thermomagnetic measurements of alloy Ni49Mn36Sn14Cu1. (a) 50 Oe and (b) 50 KOe.
Materials 14 06851 g006
Materials 14 06851 g007 550
Figure 7. ZFC, FH, and FC thermomagnetic measurements of alloy Ni48Mn36Sn14Cu2. (a) 50 Oe and (b) 50 KOe.
Figure 7. ZFC, FH, and FC thermomagnetic measurements of alloy Ni48Mn36Sn14Cu2. (a) 50 Oe and (b) 50 KOe.
Materials 14 06851 g007
Materials 14 06851 g008 550
Figure 8. Magnetic hysteresis loops at room temperature of alloys: (a) Ni50Mn36Sn14, (b) Ni49Mn36Sn14Cua and (c) Ni48Mn36 Sn14Cu2.
Figure 8. Magnetic hysteresis loops at room temperature of alloys: (a) Ni50Mn36Sn14, (b) Ni49Mn36Sn14Cua and (c) Ni48Mn36 Sn14Cu2.
Materials 14 06851 g008
Table
Table 1. Crystallographic parameters obtained from XRD analysis of specimens before and after thermal cycling.
Table 1. Crystallographic parameters obtained from XRD analysis of specimens before and after thermal cycling.
AlloyLattice
Parameter/nm		Microstrain/%Crystallite Size/nm
Ni50 Mn36 Sn14 (before)a = 0.59830.650114
Ni50 Mn36 Sn14 (after)a = 0.59810.583127
Ni49 Mn36 Sn14 Cu1 (before)a = 0.59800.643103
Ni49 Mn36 Sn14 Cu1 (after)a = 0.59870.536125
Ni48 Mn36 Sn14 Cu2 (before)a = 0.59820.92882
Ni48 Mn36 Sn14 Cu2 (after)a = 0.59920.85394
Table
Table 2. Equilibrium Gibbs temperature, To, and thermodynamic parameters (enthalpy ΔH, entropy, ΔS) of the structural transformation before and after thermal cycling (before values are calculated following the procedure and data provided in reference [21]). To is one half of Ms + Af.
Table 2. Equilibrium Gibbs temperature, To, and thermodynamic parameters (enthalpy ΔH, entropy, ΔS) of the structural transformation before and after thermal cycling (before values are calculated following the procedure and data provided in reference [21]). To is one half of Ms + Af.
AlloyTo/KΔH/J g−1ΔS/J g−1 K−1
Ni50 Mn36 Sn14 (before)203.21.540.0077
Ni50 Mn36 Sn14 (after)204.41.440.0073
Ni49 Mn36 Sn14 Cu1 (before)211.51.610.0079
Ni49 Mn36 Sn14 Cu1 (after)212.41.600.0077
Ni48 Mn36 Sn14 Cu2 (before)237.02.530.0100
Ni48 Mn36 Sn14 Cu2 (after)238.22.270.0096
Table
Table 3. Magnetic parameters derived from Figure 8 hysteresis loops.
Table 3. Magnetic parameters derived from Figure 8 hysteresis loops.
AlloySaturation
Magnetization (emu/g) at 50 K		Saturation
Magnetization (emu/g) at 300 K		Coercivity (Oe) at 50 KCoercivity (Oe) at 300 K
Ni50 Mn36 Sn1438.519.526610.2
Ni49Mn36Sn14Cu140.021.527510.0
Ni48Mn36Sn14Cu238.618.840011.6
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Wederni, A.; Ipatov, M.; González, J.-M.; Khitouni, M.; Suñol, J.-J. Ni-Mn-Sn-Cu Alloys after Thermal Cycling: Thermal and Magnetic Response. Materials 2021, 14, 6851. https://doi.org/10.3390/ma14226851

AMA Style

Wederni A, Ipatov M, González J-M, Khitouni M, Suñol J-J. Ni-Mn-Sn-Cu Alloys after Thermal Cycling: Thermal and Magnetic Response. Materials. 2021; 14(22):6851. https://doi.org/10.3390/ma14226851

Chicago/Turabian Style

Wederni, Asma, Mihail Ipatov, Julián-María González, Mohamed Khitouni, and Joan-Josep Suñol. 2021. "Ni-Mn-Sn-Cu Alloys after Thermal Cycling: Thermal and Magnetic Response" Materials 14, no. 22: 6851. https://doi.org/10.3390/ma14226851

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