Structural, Electronic, Magnetic, Mechanic and Thermodynamic Properties of the Inverse Heusler Alloy Ti₂NiIn Under Pressure

Abstract

Structural, electronic, magnetic and mechanic properties of the inverse Heusler alloy Ti₂NiIn under different pressure are systematically studied with density functional theory (DFT). The equilibrium lattice constant and electronic band structure at null pressure are obtained to be consistent with previous work. Under currently applied static pressure from 0 GPa to 50 GPa, it is found that the half-metallicity of the material is maintained and the total magnetic moment (M_t) is kept at 3 µ_B, which obeys the Slater–Pauling rule, M_t = Z_t − 18, where Z_t is the total number of valence electrons. Besides, the effect of the tetragonal distortion was studied and it is found that the magnetic property of Ti₂NiIn is almost unchanged. Several mechanical parameters are calculated including three elastic constants, bulk modulus B, Young’s modulus E, and shear modulus S and the mechanical stability is examined accordingly. Furthermore, the thermodynamic properties, such as the heat capacity C_V, the thermal expansion coefficient α, the Grüneisen constant γ and the Debye temperature Θ_D, are computed by using the quasi-harmonic Debye model within the same pressure range at a series of temperature from 0 to 1500 K. This theoretical study provides detailed information about the inverse Heusler compound Ti₂NiIn from different aspects and can further lead some insight on the application of this material.

1. Introduction

During the last decade, half-metallic materials (HMMs) have attracted tremendous attention and become of great interest because they can provide novel functionalities for spintronic [1] and magneto-electronic materials [2,3]. The electronic structure of HMMs shows metallic behavior with no band gap for one channel and semiconducting behavior with band gap in the other channel, leading to a possible 100% spin polarization of electrons near the Fermi energy level [4,5]. Among these materials, the Heusler alloy family stands out because of its high Curie temperature and tunable physical properties [6,7,8]. Besides, the Heusler materials have comparable crystal structure with zinc-blende-type and rock-salt-type semiconductors [9,10,11], making them suitable for the spin injection source of semiconductors. The first-principles calculations have been successfully and extensively applied to study the physical properties of Heusler alloys, including electronic property, magnetic property, mechanical property, etc. Many Heusler compounds have been predicted theoretically to be half-metal and many experiments also have been carried out to establish this half-metallicity [12,13,14].

Heusler alloys are commonly represented by a generic formula X₂YZ [15,16,17], in which X and Y stand for transition metal elements and Z for s-p element. Normally, the Heusler compounds crystallize in a highly ordered cubic structure either in Cu₂MnAl-type or Hg₂CuTi-type, and there is half metallic behavior found in both types. We should point out here that Hg₂CuTi-type full Heusler alloys have been widely studied and a number of this type alloys exhibit half-metallic properties [18,19,20], and also, many of Hg₂CuTi alloys obey the well-known Slater–Pauling rule [21,22,23]. More important, some Hg₂CuTi-type Ti₂-based full Heusler alloys have been predicted to be spin-gapless semiconductors [18,24] or magnetic Weyl semimetal [25]. Thus, Ti₂-based Heusler becomes of great interest nowadays.

Several Ti₂Ni-based full Heusler alloys have been theoretically studied, such as Feng et al. [26,27] demonstrated Ti₂NiAl and Ti₂NiIn being half-metal with complete spin polarization around the Fermi level; Wei et al. [19] and Boudali et al. [28] performed a series of studies on the half-metallic, structural, mechanical properties of Ti₂NiZ (Z = Al, Ga, In); Wei et al. [29] and Feng et al. [27] made detailed analysis of the electronic and magnetic properties of defects in Ti₂NiIn and also examined the stability and thermodynamic properties on Ti₂NiIn; Wen et al. concentrated on the mechanical and acoustic properties of Ti₂NiZ (Z = Al, Ga, In) Heusler alloys. In this work, we focus on Ti₂NiIn compound and carry out a systematic study on its strain condition in terms of the pressure and temperature dependence of its structural, electronic, magnetic and mechanical properties based on first-principles calculation and the quasi-harmonic Debye model. Different from previous studies, we further enlarge the applied static pressure to 50 GPa and elevate the temperature limit to 1500 K and also correlated the different lattice constants with pressure by geometry optimization. Thus, we can reveal the effect of external pressure to better understand the real condition. Besides, we also discuss the tetragonal distortion and its impact on the half-metallic, electronic and magnetic properties of Ti₂NiIn.

2. Computational Details

2.1. Crystal Structure and Equilibrium Lattice

The cubic Heusler compounds X₂YZ commonly have Cu₂MnAl-type structure or Hg₂CuTi-type structure. The former one is also known as L₂₁ structure and the latter on as XA structure or inverse structure. In either one, the basic crystal structure is based on four interpenetrating face-centered-cubic (FCC) sublattices defined by Wyckoff coordinates as A (0, 0, 0), B (0.25, 0.25, 0.25), C (0.5, 0.5, 0.5) and D (0.75, 0.75, 0.75). For the currently studied Ti₂NiIn alloy, we adopt the inverse structure and the position sites A, B, C and D are occupied by Ti, Ti, Ni and In atoms, accordingly, see the inset crystal structure in Figure 1. We have performed first-principles calculations using the pseudo-potential plane-wave methods based on density functional theory (DFT) [30] as implemented in the CASTEP codes [31]. The exchange-correlation functional scheme is selected as the Perdew–Burke–Ernzerhof (PBE) functional within the generalized gradient approximation (GGA) [32]. The ultrasoft pseudopotential is applied to describe the interaction between ions and electrons. After the convergence test, the following parameters are set: 500 eV plane-wave cutoff energy, 5 × 10⁻⁶ eV self-consistent field tolerance and 12 × 12 × 12 k-point mesh.

To determine the equilibrium lattice constant of Ti₂NiIn, we first compute the total energy at different lattice constants and the result is shown in Figure 1. By polynomial fitting and total energy minimization, we successfully obtain the equilibrium lattice constant, 6.42 Å, which is in very good agreement with other studies [27,28,29,33,34].

2.2. Electronic and Magnetic Properties

Based on the obtained equilibrium lattice, we can calculate the electronic structure and magnetic properties of Ti₂NiIn with PBE-GGA and ultrasoft pseudopotential to describe the exchange-correlation functional and the interaction between ions and electrons. Furthermore, for the application of external pressure, we performed structural optimization with the Broyden-Fletcher-Goldfarb-Shanno (BFGS) minimization [35]. The converge parameters for this structure optimization are set as follows: the energy change per atom is less than 5 × 10⁻⁶ eV; the forces on atoms are less than 0.01 eV/Å and all the stress components are less than 0.02 GPa. Figure 2 shows the lattice constants and total energies under different pressure. With pressure increase, the lattice decreases yet the total energy increases. After the structure optimization under different pressure, the electronic and magnetic behaviors at different pressure were calculated accordingly.

2.3. Mechanical Properties

For the mechanical properties of Ti₂NiIn, we first study its elastic constants and they are obtained by the stress-strain method [36]. For a cubic structure, there are three independent elastic constants, namely, C₁₁, C₁₂ and C₁₄, in which C₁₁ represents the elasticity in length and the other two characterize the elasticity in shape. In addition, the mechanical stability for cubic structure crystal can be judged by the following generalized Born-Huang elastic stability criteria [37,38]:

$${\mathrm{C}}_{11}+2{\mathrm{C}}_{12}>0,{\mathrm{C}}_{11}-{\mathrm{C}}_{12}>0,{\mathrm{C}}_{44}>0$$

(1)

With these three elastic constants we can further calculated other mechanical properties by the Voigt-Reuss-Hill (VRH) approximation [39]. The bulk modulus B and the shear modulus G generally describe the resistance to volume and shape variation and can be given by

$$\mathrm{B}=\frac{{\mathrm{B}}_{\mathrm{R}}+{\mathrm{B}}_{\mathrm{V}}}{2},\mathrm{G}=\frac{{\mathrm{G}}_{\mathrm{R}}+{\mathrm{G}}_{\mathrm{V}}}{2}$$

(2)

where B_R (B_V) and G_R (G_V) represent the lower (upper) limit for polycrystalline crystal at the Reuss (Voigt) boundary. For a cubic crystal, they have the following relations with the elastic constants [40]:

$${\mathrm{B}}_{\mathrm{R}}={\mathrm{B}}_{\mathrm{V}}=\frac{{\mathrm{C}}_{11}+2{\mathrm{C}}_{12}}{3},{\mathrm{G}}_{\mathrm{V}}=\frac{{\mathrm{C}}_{11}-{\mathrm{C}}_{12}+3{\mathrm{C}}_{44}}{5},{\mathrm{G}}_{\mathrm{R}}=\frac{5{\mathrm{C}}_{44}({\mathrm{C}}_{11}-{\mathrm{C}}_{11})}{4{\mathrm{C}}_{44}+3({\mathrm{C}}_{11}-{\mathrm{C}}_{12})}$$

(3)

Then, the Young’s modulus E and Poisson’s ratio ν can be determined from B and G by the following formula [41]:

$$\mathrm{E}=\frac{9\mathrm{GB}}{3\mathrm{B}+\mathrm{G}},\mathsf{\nu }=\frac{3\mathrm{B}-2\mathrm{G}}{2(3\mathrm{B}+\mathrm{G})}$$

(4)

2.4. Thermodynamic Properties

In order to understand the specific behavior of Ti₂NiIn compound under severe constraints, we further studied its thermodynamic properties and their dependencies on temperature and pressure by the quasi-harmonic Debye model [42,43,44]. The studied temperature range is from 0 to 1500 K and pressure range from 0 to 50 GPa. In the quasi-harmonic Debye model, the non-equilibrium Gibbs free energy is expressed by

$${\mathrm{G}}^{*}(\mathrm{V};\mathrm{P},\mathrm{T})=\mathrm{E}\left(\mathrm{V}\right)+\mathrm{PV}+{\mathrm{A}}_{\mathrm{vib}}({\mathsf{\Theta }}_{\mathrm{D}}\left(\mathrm{V}\right);\mathrm{T})$$

(5)

where E(V) is the total energy per unit cell of Ti₂NiIn, PV represents the constant hydrostatic pressure condition, Θ_D(V) corresponds the Debye temperature and A_vib stands for the vibrational Helmholtz free energy, which can be expressed as follow using the Debye model of the phonon density:

$${\mathrm{A}}_{\mathrm{vib}}({\mathsf{\Theta }}_{\mathrm{D}};\mathrm{T})={\mathrm{nk}}_{\mathrm{B}}\mathrm{T}\left[\frac{9}{8}\frac{{\mathsf{\Theta }}_{\mathrm{D}}}{\mathrm{T}}+\frac{1}{3}\ln (1-{\mathrm{e}}^{-{\mathsf{\Theta }}_{\mathrm{D}}/\mathrm{T}})-\mathrm{D}({\mathsf{\Theta }}_{\mathrm{D}}/\mathrm{T})\right]$$

(6)

where k_B is the Boltzmann constant, n is the number of atoms per formula unit, D(Θ_D/T) is the Debye integral defined as

$$\mathrm{D}(\mathrm{x})=\frac{3}{{\mathrm{x}}^3}{\int }_0^{\mathrm{x}}\frac{{\mathrm{y}}^3}{{\mathrm{e}}^{\mathrm{y}}-1}\mathrm{dy}$$

(7)

For an isotropic solid, the Debye temperature Θ_D can be written as:

$${\mathsf{\Theta }}_{\mathrm{D}}=\frac{\hslash }{{\mathrm{k}}_{\mathrm{B}}}{\left(6{\mathsf{\pi }}^2{\mathrm{V}}^{1/2}\mathrm{n}\right)}^{1/3}\mathrm{f}\left(\mathsf{\nu }\right)\sqrt{\frac{{\mathrm{B}}_{\mathrm{S}}}{\mathrm{M}}}$$

(8)

where M is the molecular mass per formula unit and B_S the static bulk modulus, which can be approximated by the static compressibility:

$${\mathrm{B}}_{\mathrm{S}}={\mathrm{B}}_{\mathrm{static}}\left(\mathrm{V}\right)=\mathrm{V}\left[\frac{{\mathrm{d}}^2\mathrm{E}\left(\mathrm{V}\right)}{{\mathrm{dV}}^2}\right]$$

(9)

and ν is the Poisson’s ratio and f(ν) is given as:

$$\mathrm{f}\left(\mathsf{\nu }\right)={\left\{3{\left[2{\left(\frac{2}{3}\frac{1+\mathsf{\nu }}{1-2\mathsf{\nu }}\right)}^{3/2}+{\left(\frac{1}{3}\frac{1+\mathsf{\nu }}{1-\mathsf{\nu }}\right)}^{3/2}\right]}^{-1}\right\}}^{1/3}$$

(10)

As a result, the non-equilibrium Gibbs functions can be minimized with respect to volume V as follow:

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

(11)

Then, the thermal equation of state (EOS) can be obtained by solving the above equation and the isothermal bulk modulus B_T, the heat capacity C_V at constant volume and C_P at constant pressure are given by the following equations:

$${\mathrm{B}}_{\mathrm{T}}(\mathrm{P},\mathrm{T})=\mathrm{V}{\left[\frac{{\partial }^2{\mathrm{G}}^{*}(\mathrm{V};\mathrm{P},\mathrm{T})}{\partial {\mathrm{V}}^2}\right]}_{\mathrm{P},\mathrm{T}}$$

(12)

$${\mathrm{C}}_{\mathrm{V}}=3{\mathrm{nk}}_{\mathrm{B}}\left[4\mathrm{D}({\mathsf{\Theta }}_{\mathrm{D}}/\mathrm{T})-\frac{3{\mathsf{\Theta }}_{\mathrm{D}}/\mathrm{T}}{{\mathrm{e}}^{{\mathsf{\Theta }}_{\mathrm{D}}/\mathrm{T}}-1}\right]$$

(13)

$${\mathrm{C}}_{\mathrm{P}}={\mathrm{C}}_{\mathrm{V}}(1+\mathsf{\alpha }\mathsf{\gamma }\mathrm{T})$$

(14)

where the thermal expansion coefficient α and the Grüneisen constant γ are

$$\mathsf{\alpha }=\frac{\mathsf{\gamma }{\mathrm{C}}_{\mathrm{V}}}{{\mathrm{B}}_{\mathrm{T}}\mathrm{V}},\mathsf{\gamma }=\frac{\mathrm{d}\ln {\mathsf{\Theta }}_{\mathrm{D}}\left(\mathrm{V}\right)}{\mathrm{d}\mathrm{lnV}}$$

(15)

3. Results and Discussion

3.1. Electronic, Magnetic and Half-Metallic Behaviors

Based on the obtained equilibrium lattice constant at null pressure and the optimized structure at different pressures, the electronic band structure of Ti₂NiIn compound has been calculated and displayed in Figure 3. The Fermi energy level is represented by the zero energy in the figure. It can be seen clearly that this material exhibits half-metallic behavior because there is no band gap in the majority spin, but a band gap exists in the minority spin. Through the currently applied pressure from 0 to 50 GPa, there is always a band gap in the minority spin and the Fermi level is kept inside this gap, meaning the half-metallicity of Ti₂NiIn compound is maintained even to the high pressure of 50 GPa. A closer look at the band structure, especially for the band gap in the minority spin channel, we found that as the Ti₂NiIn is compressed with increased pressure, the valence band maximum (VBM) in the minority spin is continuously shifted downwards while the conduction band minimum (CBM) is almost unchanged, leading to the increase of the band gap in the minority spin, as shown in Figure 4, which is also confirmed by the total density of state in the figure. For the majority spin, there is only a very small variation of the band structure, especially at the G point.

The total magnetic moment (TMM) and the atom-resolved spin magnetic moment (AMM) of atom Ti, Ni and In under pressure from 0 to 50 GPa are calculated and plotted in Figure 5. The magnetic moments of Ni and In atoms are always negative and also very small. With pressure increase, their magnetic moments only show a very tiny increase. Therefore, the total magnetic moment is mainly from Ti atoms from both two sites. The two sites of Ti atoms both have positive magnetic moments: for site I, the AMM of Ti does not change with pressure; whereas, for site II, there is a slight decrease along pressure increase. From the different variation effects of AMMs of all atoms, the TMM is always equal to an integer value of 3 µ_B through the whole pressure range. This integral behavior of the TMM is a typical characteristic of the Heusler compound. The Ti₂NiIn material has 21 valence electrons (Z_t) and the total magnetic moment (M_t) obeys the Slater–Pauling rule [19,29], M_t = Z_t − 18. All these magnetic behaviors show a good stability again pressure variation to the applied pressure limit of 50 GPa.

During film growth, this tetragonal distortion often occurs and, then, the physical properties of material may vary greatly. Consequently, we further study the effects of tetragonal distortion on the electronic and magnetic properties of the Ti₂NiIn compound. By keeping the unit cell volume constantly at the equilibrium condition and varying the ratio of c/a from 0.9 to 1.1, we realize different tetragonal structures as shown in the left panel of Figure 6 and calculate the electronic and magnetic properties of Ti₂NiIn accordingly. The results are shown in Figure 6 and Figure 7 for the electronic and magnetic behaviors, respectively.

It can be seen that with the ratio of c/a changing from 1 (no distortion) to either smaller or larger values, the valence band maximum always increases, yet, the conduction band minimum decreases. However, the variation amplitude of the conduction band minimum is larger than that of the valence band maximum, which leads to the band gap decrease at c/a ratio different from 1. Moreover, we found the effect of c/a ration is a little stronger when it is smaller than one. For the magnetic moment of each atom, the effect of c/a ratio is shown in Figure 7 and there are very small changes only for Ti(I) and Ni atoms by the tetragonal distortion. The total magnetic moment keeps the same value of 3 µ_B, meaning that the magnetic behavior of Ti₂NiIn compound shows some resistance to tetragonal distortion.

3.2. Mechanic Properties

The mechanical property of material plays a critical role for its application. For the studied cubic Ti₂NiIn compound, three independent elastic constants together with the bulk modulus B, shear modulus G, Young’s modulus E and Pugh’s ratio B/G are calculated as described in Section 2.3 under the pressure range from 0 to 50 GPa. The results are listed in

Table 1. The elastic constants C_ij, bulk modulus B, shear modulus G, Young’s modulus E and Pugh’s ratio B/G of Ti₂NiIn compound under different pressure.

P	C11	C12	C44	B	G	E	B/G
(GPa)	(GPa)	(GPa)	(GPa)	(GPa)	(GPa)	(GPa)
0	145.06	101.66	88.24	116.13	50.63	132.61	2.29
10	200.41	143.84	108.47	162.70	63.61	168.83	2.56
20	246.02	177.93	126.21	200.63	74.97	199.99	2.68
30	286.15	207.09	142.41	233.44	85.52	228.64	2.73
40	330.37	241.47	157.26	271.10	95.09	255.40	2.85
50	372.05	273.39	163.73	306.28	101.45	274.09	3.02

and also plotted in Figure 8. The obtained results at low pressure range from 0 to 10 GPa, and match other studies very well [27,28,29,33,34]. From the three elastic constants and bulk modulus, the mechanical stability of Ti₂NiIn compound is examined with the generalized Born-Huang elastic stability criteria [37,38], see Equation (1). It is found that through the whole pressure range from 0 to 50 GPa, the Ti₂NiIn compound satisfies this criteria and thus is mechanically stable. From Figure 8, one can see that all the three elastic constants C_ij show a moderate increase with pressure. But, C₁₁ and C₁₂ have much larger change with pressure than C₄₄. Obviously, the increases of elastic constants and moduli with pressure make the material stronger and more difficult to compress. The Pugh’s ratio can be used to predict whether the material is brittle or ductile and it is equal to 2.29 at null pressure, larger than 1.75, indicating that this compound is ductile. With pressure increase, the Pugh’s ratio shows a upward trend, meaning the Ti₂NiIn compound becomes more and more ductile at higher pressure. From Figure 8 it can also be observed that the bulk modulus B, shear modulus G and Young’s modulus E increase monotonically with pressure increase from 0 to 50 GPa. However, the variation of G is smaller than that of B and E.

3.3. Thermodynamic Properties

The thermodynamic properties can provide us much more information about the material’s specific behaviors under severe constraints, such as high temperature or high pressure conditions. Thus, we further investigate the influence of temperature and temperature on the thermodynamic parameters, e.g., thermal expansion coefficient α, heat capacity C_V, Grüneisen constant γ and Debye temperature Θ_D, by applying the quasi-harmonic Debye model [42,43,44]. The thermodynamic properties are studied in the temperature range from 0 to 1500 K under a series of pressure values from 0 to 50 GPa.

Figure 9 shows the variation of the normalized unit cell volume V/V₀ under different pressure and temperature values for Ti₂NiIn, where V is the volume at pressure P and temperature T and V₀ is the equilibrium volume at null pressure and 0 K. It clearly shows that the relative volume increases with increasing temperature for all the pressure series, see the left panel of Figure 9. This result is apparently expected because commonly material expands at higher temperature. Besides, the volume variation with temperature at lower pressure is stronger than at higher pressure. With pressure increase, the relative volume simply decreases for all different temperature series because material is compressed at higher pressure. Moreover, the volume at higher temperature shows larger variation with pressure than that at lower temperature. Furthermore, we found that the volume is more sensitive to pressure than temperature, i.e., the volume variation with pressure is more important than that of temperature.

The thermal expansion coefficient α has both theoretical and practical significances and also it is essential to predicate the thermodynamic equation of state. The variation of α with temperature and pressure is displayed in Figure 10. It can be seen that the thermal expansion α increases markedly with temperature from 0 to 1500 K; also, the increasing rate is much larger at initial temperature increase from 0 to 300 K. This is because the anharmonic effect of the Debye model at lower temperature is strongly depressed at high temperature. The variation of α with temperature is stronger at lower pressure. From the right panel of Figure 10, we found the α decreases continuously with pressure increase and also the variation trend is stronger at the initial pressure change from 0 to 10 GPa, especially for the higher temperature series. At null pressure and 300 K, the thermal expansion α for the studied Ti₂NiIn compound is 4.34 × 10⁻⁵ K⁻¹.

Next, we examine the heat capacity C_V and C_P of Ti₂NiIn dependence on temperature and pressure. Commonly, heat capacity is a critical parameter for the material physical properties and it can provide significant information about the lattice vibration and transition of phase. The result is plotted in Figure 11. It is found that the temperature has a very strong effect at the low temperature from 0 to 300 K because of the sharp increase of C_V and C_P. This is because of the anharmonic approximation of the Debye model at lower temperature. Further increasing temperature, this anharmonic part is suppressed and C_V saturates quickly to the Dulong-Petit limit, which indicates that thermal energy excites all the possible phonon mode at higher temperature and is common to all solids. While for C_P, it continues to increase slowly with temperature and this different behaviors can be easily understood by Equation 14. Besides, the pressure has reverse impact, i.e., both C_V and C_P decrease with pressure increase. The changing rate is reduced with temperature increase. At zero pressure and 300 K, the C_V and C_P for the studied Ti₂NiIn compound is equal to 91.3 JMol⁻¹ K⁻¹ and 93.7 JMol⁻¹ K⁻¹.

The Grüneisen constant γ is of great interest because it appears in some important thermodynamic relations. The dependence of γ on temperature and pressure is calculated and plotted in Figure 12. With increasing temperature, Grüneisen constant γ continuously increases and its amplitude of variation from 0 to 1500 K is strongly suppressed by higher pressure. Moreover, the increasing rate of γ with temperature is bigger at higher temperature; though, there is very small change between 0 and 300 K. For a given temperature, γ decreases with pressure increase. The calculated γ of Ti₂NiIn compound at zero pressure and 300 K is 2.085.

Finally, we investigate the effect of temperature and pressure on the Debye temperature Θ_D and the result is shown in Figure 13. When the temperature of the material is below its Debye temperature, the lattice vibration is mainly excited from acoustic vibration and the quantum mechanical effect plays a critical role in the thermodynamic properties. However, these can be negligible when the temperature is above the Debye temperature. It can be seen in Figure 13, that Θ_D smoothly decreases with increasing temperature and the variation trend is larger at lower pressure. Furthermore, the decreasing rate of Θ_D with temperature becomes stronger at higher temperature and there is a very small variation at low temperature from 0 to 300 K. However, with pressure increase, Θ_D continuously increases. The calculated Θ_D of the studied Ti₂NiIn compound at zero pressure and 300 K is 403.88 K.

4. Conclusions

In this work, we employ first-principles calculations based on density functional theory and systematically study the structural, electronic, magnetic and mechanical properties of the inverse Heusler compound Ti₂NiIn under a series of external pressure. The obtained equilibrium lattice constant and electronic band structure at null pressure are consistent with previous studies. By applying static pressure from 0 to 50 GPa, this material maintains its half-metallicity and also its total magnetic moment is kept the same as 3 µ_B, which obeys the Slater–Pauling rule. This means the Ti₂NiIn is robust against pressure changes. Along the pressure increase, all the elastic constants and moduli monotonically increase. With the generalized elastic stability criteria, Ti₂NiIn is mechanically stable through the studied pressure range. The Pugh’s ratio of Ti₂NiIn at null pressure is 2.29 and increases with increasing pressure, reflecting its stronger ductility. Furthermore, we examine the thermodynamic properties of this material by applying the quasi-harmonic Debye model and obtain the dependence on temperature and pressure of several parameters including the normalized volume V/V₀, thermal expansion coefficient α, heat capacity C_V, Grüneisen constant γ and Debye temperature Θ_D. It is found that α, γ and C_V increase with increasing temperature and decrease with increasing pressure, while an opposite effect of temperature and pressure on Θ_D is seen. For different parameters, the amplitude of variation from temperature and pressure show different trends. This theoretical study can provide detailed information and valuable reference for further experimental work.