Mater Eng Res

Received: March 26, 2018; Accepted: April 20, 2018; Published: April 28, 2018

Correspondence to: Saleem Yousuf, Condensed Matter Theory Group, School of Studies in Physics, Jiwaji University, Gwalior 474011, India; Email:nengroosaleem17@gmail.com

Citation: Yousuf S and Gupta DC. Chemical stability and thermodynamics of new Zr2-based heusler alloys. Mater Eng Res, 2018, 1(1):1-6

Copyright: © 2018 Saleem Yousuf and Dinesh C. Gupta. This is an open access article distributed under the terms of the Creative Commons Attribution License which permits unrestricted use, dis- tribution, and reproduction in any medium, provided the original author and source are credited.

### 1 Introduction

The history of the Heusler alloys began in 1903. Friedrich Heusler discovered Cu2MnAl to be ferromagnetic, although its elements are all non-ferromagnetic.[ 1 ] The search initiated for other Heusler alloys with similar unit cells, only after when in 1929, scientists understood the microstructure completely. The theoretical prediction of 100% spin polarization of some Heusler alloys[ 2 ] especially Co2MnSi[ 3 ] makes them interesting for spin-electronic applications as an alternative for conventional 3d Ferro-magnets, such as Fe, Co or Ni and their alloys, exhibiting only 51% spin polarization at low temperatures.[ 4 ] The two Co sub-lattices are positioned at (0, 0, 0) and (1/2, 1/2, 1/2), where the Mn sub-lattice is at (1/4, 1/4, 1/4) and the Sb sub-lattice at (3/4, 3/4, 3/4) in the unit cell. Thus, eight cobalt atoms surround silicon and manganese atoms. Each cobalt atom has four silicon and four manganese atoms as next neighbors.

In present scenario efforts are focussed on the search of the new materials mainly focussed to use for spin technology to fulfil the basic demands of present technological era such as the powerful new generation of computing devices, shape memory devices etc.[ 5–7 ] Spintronics and magneto electronics which are the backbone in these fields desire for the search of novel material which possibly will revolutionise these fields.[ 8, 9 ] The advancement in spintronic devices have proven from the efficient and desirable 100% spin-polarized currents obtained at the Fermi level. These properties are proven by the eminent materials like half metallic materials that have electrons of unique spin polarization, around the Fermi level.[ 10–14 ] They are proving to be the promising candidate for use as spin injectors.[ 15 ]

The Zirconium based Heusler alloys have rarely been studied so far and hence, the present study is aimed to investigate the electronic structure, magnetism and transport properties of Zr2NiX Heusler compounds. The less toxic nature of zirconium has attracted the search of novel spintronic materials with unusual properties at the room temperature.

### 2 Computational methods

The calculations were carried out using the First-principles full-potential linearized augmented plane wave method (FP-LAPW).[ 16 ] The generalised gradient approximation (GGA)[ 17 ] is taken for the exchange-correlation potential. Inside the non-overlapping spheres of muffin-tin radius (RMT ), the linear combination of radial solution of the Schrdinger equation times the spherical harmonics is used, whereas the plane basis set is chosen in the interstitial region. The muffin tin radii for Zr, Ni were set to 2.3 a.u. and 2.35 a.u., respectively while as 1.8 a.u and 1.9 a.u for Al and Ga, respectively. RMT is chosen in such a way that there is no charge leakage from the core and the total energy convergence is ensured. Further, for the energy Eigen-value convergence, the wave function in the interstitial region is expanded in terms of plane waves with a cut-off parameter KMAX RMT = 9.00. The maximum value of the angular momentum lMAX =10 is taken for the wave function expansion inside the atomic spheres. In the interstitial region the charge density and the potential were expanded as a Fourier series with the wave vector up to GMAX =12 a.u 1. The k integration mesh was set to a size of (17 17 17) during the self-consistent cycles and a doubled k- mesh for calculation of the density of states. The self-consistent calculations are considered to converge only when the calculated total energy of the crystal converges to less than 10 4 Ry.

In order to study thermal effects, quasi-harmonic Debye model. The model is sufficiently flexible in giving all thermo-dynamical quantities by incorporating the obtained results of energy and volume. In this model, nonequilibrium Gibbs function G*(V; P, T) is defined as follows

$$G^*(V;P,T)=E(V)+PV+A_{vib}(\theta(V),T)$$ (1)

where E(V) represents the total energy/formula unit, PV is the constant hydrostatic pressure condition, (V), is the Debye temperature and Avib is the lattice vibration expressed as

$$A_{vib}(\theta,T)=nk_BT \left[\frac{9\theta}{8T}+3ln(1-e^\frac{\theta}{T})-D(\theta/T)\right]$$ (2)

where n represents the number of atoms/formula unit, D( /T) reperesents the Debye integral, where for the anisotropic solid, is expressed by the following expression:

$$\theta=\frac{h}{k}\left[ 6\pi^2 V^{1/2} n\right] ^{1/3}f(\nu)\sqrt{\frac{B_s}{M}}$$ (3)

here M is the molecular mass, and Bs the adiabatic bulk modulus, and f(ν) is defined as

$$f(\nu)=\left\lbrace 3\left[ 2\left( \dfrac{21+\sigma}{31-2\sigma}\right)^{3/2}+\left( \frac{11+\sigma}{31-\sigma}\right) ^{3/2} \right] ^{-1} \right\rbrace ^{1/3}$$ (4)

And σ is the Poisson ratio in the above relation. In order to get minimized value of the non-equilibrium Gibb’s function with respect to volume at constant pressure and temperature mathematically is obtained as

$$\left( \frac{\partial G^*(V;P,T)}{\partial V}\right) _{P,T}=0$$ (5)

After solving above equation, one can obtain a relation for V(P,T), i.e., thermal equation of state (EOS). Using Eq. (5) for different thermal properties, i.e., isothermal bulk modulus (BT ), specific heat capacity values at constant volume (CV ) and at constant pressure (CP ) and thermal expansion coefficient can be evaluated using the following formulas:

$$B_T (P,T)=V\left( \frac{\partial^2 G^* (V;P,T)}{\partial V^2}\right)$$ (6)
$$C_V=3nk_B \left[ 4D\left( \theta/T\right) -\frac{3\theta/T}{e^{\theta/T}-1}\right]$$ (7)
$$C_P=C_V (1+\alpha \gamma T)$$ (8)
$$\alpha=\frac{\gamma C_V}{B_TV }$$ (9)

Where γ is the Gruneisen parameter and is calculated from the following expression:

$$\gamma=-\frac{dln\theta(V)}{dlnV}$$ (10)

### 3 Results and discussion

#### 3.1 Structural properties and chemical stability

Highly magnetic materials mainly having either the L21 and or C1b[ 18 ] crystallographic phases have been of interest for both theorists and experimentalists since their discovery. The interest is mainly focused due to their strong ferromagnetic character, subsequently their usage as the testing grounds for the development of new magnetic systems. These novel class families share simultaneously the property of an energy gap between valence and conduction bands for electrons of one spin polarization and the property of continuous band for other spin polarization. This asymmetric character reflects the character of L21 structure itself. In general, experimental preparation and interpretation of true half-metallic compounds are still scarce, therefore from the beginning, structural optimization is needed to estimate the magnetically and structurally stable phase by means of the total energy minimization. In the present series of new Zr2NiX (Z=Al, Ga) alloys we have investigated the stable ground state phase among the structures possible. Mostly the zirconium based Heusler alloys crystallize in the cubic ordered Full-Heusler (L21) structure of Hg2CuTi-type, with space group F-43m at ambient conditions. For the present compounds, Hg2CuTi (space group 216) is found to be the stable ground state as shown in Figure 1.

Firstly, in order to assure their chemical stability and existence, we have calculated the formation energy of these alloys defined by the following equation:

$$E_{f}=E_{Zr_{2}NiZ}-2E_{Zr}-E_{Ni}-E_{Z}$$ (11)

where EZr2NiZ are the calculated equilibrium total energies of alloys per formula unit, EZr, ENi and EZ are the chemical potential of these atoms in their stable bulk phases. Results showed that the Eformation of the Zr2NiZ (Z= Al, Ga) alloys are 2.33 eV, 2.63 eV, respectively. The calculated formation energy turns out to be negative and comparable for the same kind of compounds.[ 19 ] Negative formation energy indicates that the alloys are thermodynamically stable. In addition, we also calculate the cohesive energy to evaluate the strength of bonding of studied alloys. The cohesive energy is obtained from the following relation:[ 20 ]

$$E_{coh}=2E^{Zr}_{atom}+E^{Ni}_{atom}+E^{Z}_{atom}+E^{Zr_{2}NiZ}_{total}$$ (12)
where EtZort2aNliZ is the total energies of alloys at equilibrium per formula unit, and EaZtrom, EaNtiom, EaZtom are the total energies of the pure atomic components. It is evident that the cohesive energy is the energy required to break the crystal into isolated atoms, which is not only an indicator of the bonds strength but also an indicator of the mobility of atoms in crystal. In Figure 2, we show the cohesive energy of alloys, it is observed that Zr2NiAl has the strongest bonding in comparison to the Zr2NiGa due to its larger cohesive energy, implying that it is difficult to deform in comparison to the latter.

#### 3.2 Magnetic Properties

Magnetic materials are now-a-days regarded as the potential candidates for spintronics. Mostly in case of Heusler alloys, the Y sites contributes greater to the total magnetic moment in comparison to the atoms at X site. In case of Heusler alloys the total magnetic moment is characterized by their total valence electron count defined through the Slater-Pauling rule. Here in our group of compounds the total valence electron count is 21. They satisfy the ZT -18 rule,[ 21, 22 ] according to which they present a magnetic moment of 3 B per unit cell. The total magnetic moment with contributions from various components is given in Table 1. The magnetic alignment is ferromagnetic with maximum contribution from Zr atoms per unit cell in both compounds. Further it is the different occupation of the d-bands for the majority and minority spins that leads to the magnetization in these compounds.

#### 3.3 Thermodynamic properties

In order to calculate the pressure and temperature dependence of the thermodynamic properties, we used quasiharmonic (QH) approximation.[ 23, 24 ] Specialty is that the values of thermodynamic parameters are computed at the level of the quasi-harmonic Debye model[25, 26] approach for full-Heusler Zr2NiAl and Zr2NiGa alloys. Several properties are calculated which include the specific heats at constant volume (CV ) and constant pressure (CP ), Debye temperature ( D), thermal expansion coefficient ( ), and Gruneisen parameter ( ) in temperature range of 0 K to 800 K in steps of 100 K and at pressure ranging from 0 GPa to 70 GPa (Zr2NiAl) and 0 GPa to 30 GPa (Zr2NiGa) in steps of 5 GPa.

The graphical variations of various properties are shown in Figure 3, 4 (a, b), our calculated results for CV and CP each as a function of temperature are illustrated for Zr2NiAl and Zr2NiGa respectively. The important thermodynamic property viz, specific heat capacity is strictly related to the temperature dependence of ultimate thermodynamic functions, and it is utmost central constraint for associating thermodynamics with dynamics and microscopic structure. From the graphical variation, we can see that when the temperature is below 650 K, CV and CP variations are very close together demonstrating strong dependence on temperature owing to the anharmonic approximation used in this scheme of calculations. Further, we can also argue that at high temperatures, CV approaches to a constant value of (97 Jmol 1K 1), obeying Dulong and Petit’s rule, which is followed by all solids at high temperatures, owing to the suppression of the anharmonic effect.[27] The concluding statement which is quite interesting is that the specific heat capacity at constant pressure CP increases monotonically with the increase of temperature.

The thermodynamic properties with other physical properties of solids are closely related to the Debye temperature (θD) and Gruneisen parameter (γ). The variations of both the properties are respectively shown in Figure 3, 4 (c, d) with their numerical variation enlisted in Table 2. From the analysis of the properties, we can see that Debye temperature increases with increasing pressure whereas the Gruneisen parameter decreases when the temperature is kept constant. Here the concluding statement is that, at constant pressure, the Debye temperature decreases and the Gruneisen parameter increase as the temperature increases.

The mathematical formula reflecting the variation of volume thermal expansion coefficient ( ) with volume at constant pressure is given as:

$$\alpha=\frac{1}{V}\left( \frac{\partial V}{\partial T}\right)_{P}$$ (13)

P The variation of parameter is shown in Figure 3, 4 (e) with temperature at different pressures for the two compounds. The variation shows that the thermal expansion increases sharply with temperature up to 300 K after then slowly for temperature higher than 300 K, and gradually turns into a linear increase. Furthermore, we can also see that, at a fixed temperature, higher the pressure, smaller the thermal expansion coefficient, indicating that high pressure suppresses thermal expansion. At zero pressure and 300 K, the values of the thermal expansion for Zr2NiAl and Zr2NiGA are 1.48×10-5K-1and 1.43×10-5K-1, respectively.

### 4 Conclusion

First principle spin-polarised calculations for new inverse Heusler alloys within the GGA approach show the F4-3m as the ground state of Zr2NiZ alloys with L21 ordered structure. Magnetic moment of 3 B is characterised with the help of generalised Slater-Pauling rule of ZT-18 rule. Formation energy analysis show that these alloys are chemically stable and can be synthesised experimentally. Finally, the thermodynamic properties including volume variation, heat capacity, Debye temperature, and thermal expansion coefficients of the full-Heusler Zr2NiAl and Zr2NiGa compounds are investigated. The observed variations are well according with the results of the Debye theory, which is regularly applied to several materials.

### References

[1] Heusler F. F. Heusler, Verh. Dtsch. Phys. Ges. 5, 219 (1903). Verh. Dtsch. Phys. Ges., 1903, 5: 219.

[2] De Groot RA, Mueller FM, Van Engen PG, et al. New class of materials: half-metallic ferromagnets. Physical Review Letters, 1983, 50(25): 2024. https://doi.org/10.1103/PhysRevLett.50.2024

[3] Ishida S, Masaki T, Fujii S, et al. Theoretical search for half-metalliic films of Co2 MnZ (ZSi, Ge). Physica B: Con- densed Matter, 1998, 245(1): 1-8. https://doi.org/10.1016/S0921-4526(97)00495-X

[4] Moodera JS, Mathon G. Spin polarized tunneling in fer- romagnetic junctions. Journal of magnetism and magnetic materials, 1999, 200(1-3): 248-273. https://doi.org/10.1016/S0304-8853(99)00515-6

[5] Datta S, Das B. Electronic analog of the electro-optic mod- ulator. Applied Physics Letters, 1990, 56(7): 665-667. https://doi.org/10.1063/1.102730

[6] Kilian KA, Victora RH. Electronic structure of NiCo2 MnIn for use in spin injection. Journal of Applied Physics, 2000, 87(9): 7064-7066. https://doi.org/10.1063/1.372932

[7] Tanaka CT, Nowak J, Moodera JS. Spin-polarized tunneling in a half-metallic ferromagnet. Journal of applied physics, 1999, 86(11): 6239-6242. https://doi.org/10.1063/1.371678

[8] Park JH, Vescovo E, Kim HJ, et al. Direct evidence for a half-metallic ferromagnet. Nature, 1998, 392(6678): 794. doi:10.1038/33883

[9] Hirohata A, Takanashi K. Future perspectives for spin- tronic devices. Journal of Physics D: Applied Physics, 2014, 47(19): 193001.

[10] Ishida S, Akazawa S, Kubo Y, et al. Band theory of CoCo2 MnSn, CoCo2 TiSn and CoCo2 TiAl. Journal of Physics F: Metal Physics, 1982, 12(6): 1111.

[11] Ishida S, Fujii S, Kashiwagi S, et al. Search for half-metallic compounds in CoCo2 MnZ (Z= IIIb, IVb, Vb element). Journal of the Physical Society of Japan, 1995,64(6): 2152- 2157. https://doi.org/10.1143/JPSJ.64.2152

[12] Gupta DC, Bhat IH. Investigation of high spin-polarization, magnetic, electronic and half-metallic properties in RuMnCo2Ge and RuMnCo2Sb Heusler alloys. Materials Science and Engineering: B, 2015, 193: 70-75. https://doi.org/10.1016/j.mseb.2014.11.009

[13] Fujii S, Sugimura S, Asano S. Hyperfine fields and elec- tronic structures of the Heusler alloys Co2 MnX (X= Al, Ga, Si, Ge, Sn). Journal of Physics: Condensed Matter, 1990, 2(43): 8583.

[14] Bhat IH, Yousuf S, Bhat TM, et al. Investigation of elec- tronic structure, magnetic and transport properties of half- metallic MnCo2 CuSi and MnCo2 ZnSi Heusler alloys. Journal of Magnetism and Magnetic Materials, 2015, 395: 81-88. https://doi.org/10.1016/j.jmmm.2015.07.022

[15] De Boeck J, Van Roy W, Das J, et al. Technology and ma- terials issues in semiconductor-based magnetoelectronics. Semiconductor Science and Technology, 2002, 17(4): 342. https://doi.org/10.1088/0268-1242/17/4/307

[16] Blaha P, Schwarz K, Madsen GKH, et al. wien2k. An aug- mented plane wave+ local orbitals program for calculating crystal properties, 2001.

[17] Schwarz K, Blaha P, Madsen GKH. Electronic structure cal- culations of solids using the WIEN2k package for material sciences. Computer Physics Communications, 2002, 147(1- 2): 71-76. https://doi.org/10.1016/S0010-4655(02)00206-0

[18] Ouardi S, Fecher GH, Felser C, et al. Realization of spin gapless semiconductors: the Heusler compound MnCo2 CoAl. Physical review letters, 2013, 110(10): 100401. https://doi.org/10.1103/PhysRevLett.110.100401

[19] Wang XT, Cui YT, Liu XF, et al. Electronic structures and magnetism in the LiCo2 AgSb-type Heusler alloys, ZrCo2 CoZ (Z= Al, Ga, In, Si, Ge, Sn, Pb, Sb): A first-principles study. Journal of Magnetism and Magnetic Materials, 2015, 394: 50-59. https://doi.org/10.1016/j.jmmm.2015.06.035

[20] Pugaczowa-Michalska M. Theoretical prediction of ferri- magnetism in MnCo2 FeB, MnCo2 CoB and MnCo2 NiB. Intermetallics, 2012, 24: 128-134. https://doi.org/10.1016/j.intermet.2012.01.004

[21] Slater JC. The ferromagnetism of nickel. Physical Review, 1936, 49(7): 537. https://doi.org/10.1103/PhysRev.49.537

[22] Pauling L. The nature of the interatomic forces in metals. Physical Review, 1938, 54(11): 899. https://doi.org/10.1103/PhysRev.54.899

[23] Otero-de-la-Roza A, Abbasi-Pe´rez D, Luan˜a V. Gibbs2: A new version of the quasiharmonic model code. II. Models for solid-state thermodynamics, features and implementa- tion. Computer Physics Communications, 2011, 182(10): 2232-2248. https://doi.org/10.1016/j.cpc.2011.05.009

[24] Blanco MA, Francisco E, Luana V. GIBBS: isothermal- isobaric thermodynamics of solids from energy curves using a quasi-harmonic Debye model. Computer Physics Commu- nications, 2004, 158(1): 57-72. https://doi.org/10.1016/j.comphy.2003.12.001

[25] Marx D, Hutter J. Ab initio molecular dynamics. Parallel computing, 2009, 309(309): 327.

[26] Allen MP, Tildesley DJ. Computer Simulation of Liquids Oxford Univ. Press. 1987.

[27] Peng F, Fu H, Yang X. Ab initio study of phase transition and thermodynamic properties of PtN. Physica B: Con- densed Matter, 2008, 403(17): 2851-2855. https://doi.org/10.1016/j.physb.2008.02.022