The structural, elastic, electronic, thermal, and optical properties of superconducting nanolaminates Ti_{2}InX (X = C, N) are investigated by density functional theory (DFT). The results obtained from the least studied nitride phase are discussed in comparison with those of carbide phase having Tc value half as that of the former. The carbide phase is found to be brittle in nature, while the nitride phase is less brittle. Elastic anisotropy demonstrates that the c-axis is stiffer in Ti_{2}InN than in Ti_{2}InC. The band structure and density of states show that these phases are conductors, with contribution predominantly from the Ti 3d states. The bulk modulus, Debye temperature, specific heats, and thermal expansion coefficient are obtained as a function of temperature and pressure for the first time through the quasiharmonic Debye model with phononic effects. The estimated values of electron-phonon coupling constants imply that Ti_{2}InC and Ti_{2}InN are moderately coupled superconductors. The calculated thermal expansion coefficient is in fair agreement with the only available measured value for Ti_{2}InC. Further the first time calculated optical functions reveal that the reflectivity is high in the IR-visible-UV region up to ~10 eV and 12.8 eV for Ti_{2}InC and Ti_{2}InN, respectively, showing these to be promising coating materials.
1. Introduction
The so-called nanolaminates (or MAX) phases since their discovery by Nowotny [1] have attracted a lot of interest among the research community due to their remarkable properties having attributes of both ceramic and metal [2–24]. Ceramic attributes include lightweight, elastically rigid, and high temperatures strength, whereas metallic attributes show the phases to be thermally and electrically conductive, quasiductile, and damage tolerant. Currently there are about 60 synthesized MAX phases [3]. Out of these only seven low-Tc superconductors have so far been identified. These are Mo_{2}GaC [4], Nb_{2}SC [5], Nb_{2}SnC [6], Nb_{2}AsC [7], Ti_{2}InC [8], Nb_{2}InC [9], and Ti_{2}InN [10].
The X-ray diffraction, magnetic, and resistivity measurements discovered that Ti_{2}InX (X = C, N) are superconductors [8, 10] with superconducting temperatures of 3.1 and 7.3 K, respectively. In fact Bortolozo et al. [10] in 2010 showed unambiguously that Ti_{2}InN is the first nitride superconductor belonging to the Mn+1AXn family. Among the ternary phases almost all the studies are concerned with carbide properties, but a very limited work on nitrides which was discovered in 1963 by Jeitschko et al. [12]. This nitride crystallizes in the same prototype structure as carbides (Cr_{2}AlC), where the basic structural component is an octahedron of six Ti atoms with an N atom instead of C [16]. It has also been shown that the interactions in the Ti_{6}N octahedra are stronger than those in TiN octahedra in agreement with the general trend known for binary carbides and nitrides [16]. Further calculations show that the nitride phase has higher density of states at Fermi level than that of carbide phase. All these point to the role of N atom in changing the electronic structure and the possible transport properties which were the motivation of Bortolozo et al. [10] to seek superconductivity in nitride phase. These motivate us to revisit the system Ti_{2}InX (X = C, N) and investigate further the influence of the substitution of N for C on the M2AX nanolaminates.
Some works on elastic and electronic structures of Ti_{2}InC have been carried out by several groups of workers [15–20, 22, 23] using several different methodologies. A theoretical study of the elastic properties for six of the seven known superconducting MAX phases: Nb_{2}SC, Nb_{2}SnC, Nb_{2}AsC, Nb_{2}InC, Mo_{2}GaC, and Ti_{2}InC has been presented by Shein and Ivanovskii [20]. Long before this Ivanovskii et al. [16] calculated the electronic structure of the H-phases Ti_{2}MC and Ti_{2}MN (M = Al, Ga, In) by the self-consistent linearized muffin-tin-orbital method in the atomic-sphere approximation and the MO LCAO method using RMH parameterization. The band structure and bonding configuration of the H-phases are compared with those of other Ti-M-C and Ti-M-N phases. The energy band structure of the Ti_{2}InC along with some other MAX phases has been calculated in the framework of the full-potential augmented-plane-wave method under GGA [17]. Medkour et al. [18] reported on the electronic properties of only M_{2}InC phases by employing the pseudo potential plane wave (PP-PW) method using CASTEP. He et al. [19] have performed ab initio calculations for the structural, elastic, and electronic properties of only M_{2}InC. Benayad et al. [22] very recently included Ti_{2}InN along with Ti_{2}InC to investigate the structural, elastic, and electronic properties by using the full-potential linear muffin-tin orbital (FP-LMTO) method. The exchange and correlation potential is treated by the local density approximation (LDA).
Despite all the above efforts, it is clear that T_{2}InN has been subjected to limited study. Moreover full optical as well as finite-temperature and finite-pressure thermodynamical studies are absent for both the superconducting phases. Therefore there is a need to highlight those areas where little or no work has been carried out. We are thus inclined to address these areas of the two nanolaminates as well as revisit the existing theoretical works so as to provide elastic, electronic properties of the nitride phase in comparison with carbide phase. The optical properties such as dielectric function, absorption spectrum, conductivity, energy-loss spectrum and reflectivity for both the phases will be calculated and discussed.
2. Computational Techniques
The ab initio calculations were performed using the plane-wave pseudopotential method within the framework of the density functional theory [25] implemented in the CASTEP code [26]. The ultrasoft pseudopotentials were used in the calculations, and the plane-wave cutoff energy was 500 eV. The exchange-correlation terms used are of the Perdew-Berke-Ernzerhof form of the generalized gradient approximation [27]. We have used a 10×10×2 Monkhorst-pack [28] grid to sample the Brillouin zone. All the structures were relaxed by BFGS methods [29]. Geometry optimization was performed using convergence thresholds of 1×10-5 eV/atom for the total energy, 0.03 eV/Å for the maximum force, 0.05 GPa for maximum stress, and 1×10-3 Å for the maximum displacements. The elastic constants Cij, bulk modulus B, and electronic properties were directly calculated by the CASTEP code.
The quasiharmonic Debye model [30] has been employed to investigate the finite-temperature and finite-pressure thermodynamic properties. Here the thermodynamic parameters can be calculated at any temperature and pressure using the DFT calculated E-V data at T = 0 K, P = 0 GPa, and the Birch-Murnaghan third order EOS [31].
3. Results and Discussion3.1. Structural and Elastic Properties
The superconducting MAX phases Ti_{2}InC and Ti_{2}InN possess the hexagonal structure with space group P6_{3}/mmc (no. 194) as shown in Figure 1. The unit cell contains two formula units, and the atoms occupy the following Wyckoff positions: the Ti atoms in the position 4f[(1/3,2/3,zM),(2/3,1/3,zM+1/2),(2/3,1/3,-zM),(1/3,2/3,-zM+1/2)}, the In atoms in the position 2d {(1/3,2/3,3/4),(2/3,1/3,1/4)], and the C atoms (or, N atoms) in the position 2a[(0,0,0),(0,0,1/2)], where zM is the internal parameter [2, 32].
Crystal structure of layered MAX phases Ti_{2}InX (X = C, N).
The calculated fully relaxed equilibrium values of the structural parameters of the two superconducting phases are presented in Table 1 together with other available data on both theoretical [15, 19, 20, 22, 23] and experimental [11, 13, 14] results. The comparison shows that the calculated values are in good agreement with the available experimental as well as theoretical results.
Calculated lattice parameters (a and c in Å), ratio c/a and internal parameters zM for the superconducting MAX phases Ti_{2}InC and Ti_{2}InN.
Phase
a
c
c/a
zM
Reference
Ti_{2}InC
3.1453
14.215
4.519
0.0780
Present
3.1373
14.1812
4.520
0.0783
[15]
3.14
14.17
4.51
0.0779
[19]
3.1485
14.2071
4.512
0.0780
[20]
3.084
13.906
4.508
0.0788
[22]
3.135
14.182
4.524
[23]
3.134
14.077
4.492
[11] ^{Experimental data}
3.133
14.10
4.5
[14] ^{Experimental data}
Ti_{2}InN
3.0956
14.063
4.543
0.07855
Present
3.033
13.727
4.525
0.07908
[22]
3.07
13.97
4.54
[13] ^{Experimental data}
The elastic constant tensors of the superconducting MAX phases Ti_{2}InC and Ti_{2}InN are reported in Table 2 along with available computed elastic constants [15, 20, 22, 23]. For Ti_{2}InC the agreement with available theoretical results is quite good. But for Ti_{2}InN, the only set of data due to Benayad et al. [22] deviate much from our calculations and also from the trend for similar phase (Table 2). The reason may be the use of FP-LMTO method treated with LDA with P-W parameterization.
Calculated elastic constants (Cij, in GPa), bulk moduli (B, in GPa), shear moduli (G, in GPa), Young’s moduli (Y, in GPa), Poisson’s ratio (ν), A and kc/ka for superconducting Ti_{2}InC and Ti_{2}InN.
Phase
C11
C12
C13
C33
C44
B
G
Y
ν
A
kc/ka
Reference
Ti_{2}InC
284.2
58.7
52.3
246.1
90.0
126.4
100.4
240
0.184
0.798
1.230
Present
273.4
62.9
50.3
232.3
87.2
120
96
228
0.184
0.829
1.293
[15]
282.6
70.2
54.9
232.9
57.6
124.7
81.7
201.1
0.232
0.542
1.365
[20]
281.0
57.7
44.5
226.6
85.8
98.6
0.768
1.371
[22]
287.0
65
53
244
85
128
99
0.766
1.288
[23]
Ti_{2}InN
213.7
36.8
105.6
231.7
98
125.5
81
200
0.234
1.11
0.312
Present
102.9
60.9
62.7
106.1
46.1
41.8^{a}
32.9
86.3
0.31
2.19
0.884
[22]
^{
a}Calculated based on data from [22].
Using the second-order elastic constants, the bulk modulus B, shear modulus G (all in GPa), Young’s modulus Y, and Poisson’s ratio ν at zero pressure are calculated and presented in Table 2. The pressure dependence of the elastic constants is a very important characterization of the crystals with varying pressure and/or temperature, but we defer it till in a later section. The ductility of a material can be roughly estimated by the ability of performing shear deformation, such as the value of shear-modulus-to-bulk-modulus ratios. Thus a ductile plastic solid would show low G/B ratio (<0.5); otherwise, the material is brittle. As is evident from Table 2, the calculated G/B ratios are 0.8 and 0.65 for carbide and nitride phases, respectively, indicating that first compound is brittle in nature and the second one will be more on the brittle/ductile border line. The same can be inferred from an additional argument that the variation in the brittle/ductile behavior follows from the calculated Poisson’s ratio. For brittle material the value is small enough, whereas for ductile metallic materials ν is typically 0.33 [24].
The elastic anisotropy of the shear of hexagonal crystals, defined by A=2C44/(C11-C12), may be responsible for the development of microcracks in the material [36]. This factor is unity for an ideally isotropic crystal. The calculated value of A increases from 0.798 to 1.11 as C atom is replaced by N. We can also examine a second anisotropy parameter which is the ratio between the uniaxial compression values along the c- and a-axis for a hexagonal crystal: kc/ka=(C11+C12-2C13)/(C33-C13). We find that the compressibility of Ti_{2}InC along the c-axis is larger than along the a-axis (kc/ka=1.23) in agreement with other calculations [15, 20, 22, 23], but for Ti_{2}InN the situation is reversed, as c is stiffer for this material.
3.2. Electronic Bonding Properties
The energy bands of the two nanolaminates along the high symmetry directions in the first Brillouin zone are shown in Figures 2(a) and 2(b) in the energy range from −15 to +5 eV. The band structures of both the superconducting phases reveal 2D-like behaviour with smaller energy dispersion along the c-axis and in the K-H and L-M directions. The 2D behaviour does not differ much from one superconductor to the other, except that the bands of the nitride phase are shifted more towards the Fermi level. The occupied valence bands of Ti_{2}InC and Ti_{2}InN lie in the energy range from -8.8 eV to Fermi level and −9.5 eV to Fermi level, respectively. Further, the valence and conduction bands are seen to overlap, thus indicating metallic-like behaviour of both the phases. This conductivity increases as C is replaced by N. The In 4d and C 2s-type quasicore bands with a small dispersion can be seen in the energy intervals ~−13.7 to −14.4 eV and from −11 to −10 eV, respectively below the Fermi level. The corresponding energy intervals are about −14 to −15 eV for In 4d and N 2s-type quasicore bands. As seen in [15] the multiband character of the systems can be inferred from three near Fermi bands which intersect the Fermi level.
Calculated band structures of (a) Ti_{2}InC and (b) Ti_{2}InN.
The total and partial densities of states for the two superconducting phases are illustrated in Figures 3(a) and 3(b). The values of DOS at the Fermi level are 2.78 and 4.98 states/eV which predominantly contain contributions from the Ti 3d states of 2.22 and 4.06 states/eV of the two phases Ti_{2}InC and Ti_{2}InN, respectively. The diffuse character of both s and p states of In atoms causes larger dispersion of In bands than those due to C and N. A covalent interaction occurs (−9 eV to Fermi level) between the constituting elements as a result of the degeneracy of the states with respect to both angular momentum and lattice site. C p, N p, and Ti d as well as In p and Ti d states are all hybridized. Such hybridization peak of Ti d−C p in Ti_{2}InC and Ti d−N p in Ti_{2}InN lies lower in energy (−5 to −2 eV) and (−7 to −4 eV) than that of Ti d−In p (−3 eV to Fermi level). All these indicate that Ti–In bond is weaker than either Ti–C or Ti–N bond. The population analysis shows that bond lengths in Å for Ti_{2}InC and Ti_{2}InN in increasing order are as Ti–C (2.1277), Ti–Ti (2.8661), Ti–In (3.0456), In–C (3.9908) and Ti–N (2.1010), Ti–Ti (2.8416), Ti–In (3.0013), and In–N (3.9439). The bands associated with N atoms are narrower and lower in energy. This is attributed to the large electronegativity of N compared to that of C.
Total and partial DOSs of (a) Ti_{2}InC and (b) Ti_{2}InN.
Ivanovskii et al. [16] from their band structure calculations for the phases suggest that the transition metal does not play role in the superconducting mechanism suggesting that the transport behaviour of this material is of 2D nature. The C atom is less electronegative than N, and the chemical bond between Ti–C is less polarized than Ti–N. It is thus hypothesized [16] that the electrons of the basal plane rather than the d-electrons of Ti may be responsible for the superconducting behaviour in nanolaminates. One also notes that Tc value is more than doubled when C atoms are replaced by N atoms in the Ti_{2}InX compound.
3.3. Thermodynamic Properties at Elevated Temperature and Pressure
The elastic parameters and associated physical quantities like Debye temperature, allow a deeper understanding of the relationship between the mechanical properties and the electronic and phonon structure of materials. We investigated the thermodynamic properties of Ti_{2}InC and Ti_{2}InN by using the quasiharmonic Debye model, the detailed description of which can be found in literature [30]. For this we need E-V data obtained from Birch-Murnaghan third-order EOS [31] using zero temperature and zero pressure equilibrium values, E0,V0, and B0, based on DFT method. Then the thermodynamic properties at finite-temperature and finite-pressure can be obtained using the model. The nonequilibrium Gibbs function G*(V;P,T) can be written in the form [30]:
(1)G*(V;P,T)=E(V)+PV+Avib[Θ(V);T],
where E(V) is the total energy per unit cell, PV corresponds to the constant hydrostatic pressure condition, Θ(V) is the Debye temperature, and Avib is the vibrational term, which can be written using the Debye model of the phonon density of states as [30]:
(2)Avib(Θ,T)=nkT[9Θ8T+3ln(1-exp(-ΘT))-D(ΘT)],
where n is the number of atoms per formula unit, D(Θ/T) represents the Debye integral.
A minimization of G*(V;P,T) with respect to volume V can now be made to obtain the thermal equation of state V(P,T) and the chemical potential G(P,T) of the corresponding phase. Other macroscopic properties can also be derived as a function of P and T from standard thermodynamic relations [30]. Here we computed the bulk modulus, Debye temperature specific heats, and volume thermal expansion coefficient at different temperatures and pressures.
The temperature variation of isothermal bulk modulus B of Ti_{2}InC and Ti_{2}InN is shown in Figure 4(a) and the inset of which shows B as a function of pressure. We see that there is hardly any difference in the values of B for the two phases and these vary almost identically as a function of temperature. This means that for the same compressive stress applied to both carbide and nitride phases at a particular temperature results in the same volume strain in both of these. Further the B values, signifying the average strength of the coupling between the neighboring atoms, of 126.4 and 125.5 GPa for Ti_{2}InC and Ti_{2}InN, respectively, at 0 K are the smallest among all the superconducting MAX phases [20]. Moreover, it is found that the bulk modulus increases with pressure at a given temperature and decreases with temperature at a given pressure, which is consistent with the trend of volume of the nanolaminates.
Temperature dependence of (a) Bulk modulus and (b) Debye temperature of Ti_{2}InC and Ti_{2}InN. Inset shows pressure variation.
Figure 4(b) displays temperature dependence of Debye temperature ΘD at zero pressure of Ti_{2}InC and Ti_{2}InN. One observes that ΘD, smaller for nitride phase, decrease nonlinearly with temperature for both the phases. Further ΘD presented as inset of Figure 4(b) at T = 300 K shows a nonlinear increase. The variation of ΘD with pressure and temperature reveals that the thermal vibration frequency of atoms in the nanolaminates changes with pressure and temperature. From knowledge of the calculated Debye temperature the value of the electron-phonon coupling constant (λ) can be estimated from McMillan’s relation [37]:
(3)λ=1.04+μ*ln(ΘD/1.45Tc)(1-0.62μ*)ln(ΘD/1.45Tc)-1.04,
where μ* is a Coulomb repulsion constant (typical value, μ*=0.13). Utilizing the measured Tc values and the calculated Debye temperatures, we find λ~0.49 and 0.62, for Ti_{2}InC and Ti_{2}InN, respectively. The values imply that both of these are moderately coupled superconductors.
Figures 5(a) and 5(b) show the temperature dependence of constant-volume and constant-pressure specific heat capacities CV,CP of Ti_{2}InC and Ti_{2}InN. We know that phonon thermal softening occurs when the temperature increases and hence the heat capacities increase with increasing temperature. It should be noted that the heat capacity anomaly close to Tc value (3.1 and 7.3 K, for the two superconductors) is so small (about 0.1%) that it has no effect on the analysis being made here. The only measured CP data for Ti_{2}InC due to Barsoum et al. [11] show complex behaviour as shown on the theoretical graph. Even the authors themselves remark that such a complex behaviour is not expected from a single-phase solid that does not go through phase transitions. The drop in CP must be related to loss of In atoms from the sample. This type of loss would be endothermic and thus exhibits a trough as observed. Barsoum et al. [11] acknowledged that the heat capacity measurements should be repeated with larger samples where the surface to volume ratio is reduced. The increase at higher temperatures is most likely due to oxidation.
Temperature dependence of specific heat at constant (a) volume and (b) pressure of Ti_{2}InC and Ti_{2}InN.
The volume thermal expansion coefficient, αV as a function of both temperature and pressure is displayed in Figure 6. The expansion coefficient is seen to increase rapidly especially at temperature below 300 K, whereas it gradually tends to a slow increase at higher temperatures. On the other hand at a constant temperature, the expansion coefficient decreases strongly with pressure. It is well-known that the thermal expansion coefficient is inversely related to the bulk modulus of a material. The calculated values of αV at 300 K for Ti_{2}InC and Ti_{2}InN are 3.04×10-5 and 3.3×10-5 K^{−1}, respectively. The measured value of linear thermal expansion coefficient of Ti_{2}InC is 9.5×10-6 K^{−1} [11]. Assuming, linear thermal expansion coefficient =αV/3, the calculated value of 10.1×10-6 K^{−1} for Ti_{2}InC is in fair agreement with experiment.
Temperature dependent thermal expansion coefficient of Ti_{2}InC and Ti_{2}InN. Inset shows pressure variation.
3.4. Optical Properties
The study of the optical functions of solids provides a better understanding of the electronic structure. The imaginary part of complex dielectric function, ε(ω)=ε1(ω)+iε2(ω), is obtained from the momentum matrix elements between the occupied and the unoccupied electronic states. This is calculated directly using [38]
(4)ε2(ω)=2e2πΩε0∑k,v,c|ψkc|u·r|ψkv|2δ(Ekc-Ekv-E),
where ψkc and ψkv are the conduction and valence band wave functions at k, respectively, u is the vector defining the polarization of the incident electric field, ω is the light frequency, and e is the electronic charge. The Kramers-Kronig transform of the imaginary part ε2(ω) provides the real part. Equations (49) to (54) in [38] define all other optical constants, such as refractive index, absorption spectrum, loss-function, reflectivity, and conductivity (real part).
The calculated optical functions of Ti_{2}InC and Ti_{2}InN for photon energies up to 20 eV for polarization vectors [100] and [001] (only spectra for [100] shown) along with measured spectra of TiC and TiN (where available) are shown in Figure 7. We have used a 0.5 eV Gaussian smearing for all calculations. The calculations only include interband exciatations. In metal and metal-like systems there are intraband contributions from the conduction electrons mainly in the low-energy infrared part of the spectra. It is thus necessary to include this via an empirical Drude term to the dielectric function [39, 40]. A Drude term with plasma frequency 3 eV and damping (relaxation energy) 0.05 eV was used.
Energy dependent (a) real part of dielectric function, (b) imaginary part of dielectric function, (c) refractive index, (d) extinction coefficient, (e) absorption, (f) loss function, (g) reflectivity, and (h) real part of conductivity of Ti_{2}InC and Ti_{2}InN along [100] direction. Experimental data shown for TiC and TiN are from [33–35], respectively.
Despite some variation in heights and positions of peaks, the overall features of our calculated optical spectra of Ti_{2}InC and Ti_{2}InN are roughly similar. In the energy range for which ε1(ω)<0, Ti_{2}InC, and Ti_{2}InN exhibit the metallic characteristics (Figure 7(a)). The result of Ti_{2}InC is somewhat different as regards the energy range for negativity of ε1(ω). The dielectric function of Ti_{2}InC is compared with that of TiC_{0.9} [33]. We see that the double peak structure centred at 1.7 eV for TiC_{0.9} is replaced with a sharp peak at around 0.7 eV for Ti_{2}InC. The spectra differ at low energy due to the electronic structure change near the Fermi level, induced by the addition of In layer in TiC. The same inference can be made when one compares low-energy spectra of Ti_{2}InN and TiN [34]. On the other hand no maxima are seen in ε2 for the two MAX phases, although the values are large in the low-energy region (Figure 7(b)). The corresponding spectra for TiC_{0.9} [33] and TiN [34] are shown for comparison. The refractive index and extinction coefficients of the nanolaminates are displayed in Figures 7(c) and 7(d).
The absorption coefficient provides data about optimum solar energy conversion efficiency and it indicates how far light of a specific energy (wavelength) can penetrate into the material before being absorbed. Figure 7(e) shows the absorption coefficients of both the phases which begin at 0 eV due to their metallic nature. Ti_{2}InC has two peaks, one at ~4.3 eV (same for Ti_{2}InN) and the other at 6.3 eV (8 eV for Ti_{2}InN), besides having a shoulder at lower energy. Both the nanolaminates show rather good absorption coefficient in the 4–10 eV region. The energy loss L(ω) of a fast electron traversing in the material is depicted in Figure 7(f). The bulk plasma frequency ωP is at the peak position which occurs at ε2<1 and ε1=0. In the energy-loss spectrum, we see that ωP of the two phases Ti_{2}InC and Ti_{2}InN are ~13.2 eV and ~12.8 eV, respectively. When the incident photon frequency is higher than ωP, the material becomes transparent.
Figure 7(g) presents the reflectivity spectra as a function of photon energy in comparison with measured spectra of TiC_{0.97} [33] and TiN [35]. The reflectance for TiC_{0.97} is nearly constant over the energy range considered. With addition of In to TiC the reflectivity is much higher in the infrared region, it then decreases sharply to 0.55 which becomes almost steady till 5 eV. After an increase with photon energy up to ~10 eV, the reflectivity falls again. On the other hand we find that the reflectivity in Ti_{2}InN is high in IR-visible-UV up to ~12.8 eV region (reaching maximum between 10 and 12.8 eV). Compared to this the reflectivity of TiN starts with a higher value in the infrared and there is a sharp drop between 2 and 3 eV, which is the characteristics of high conductance [35]. The low reflectivity in the region of visible blue and violet light (2.8–3.5 eV) increases to a value of 0.36 at 6 eV (ultraviolet). The analysis shows that the nitride phase would be a comparatively better material as promising candidate for use as coating material.
Figure 7(h) shows that the photoconductivity starts with zero photon energy due to the reason that the materials have no band gap which is evident from band structure. Moreover, the photoconductivity and hence electrical conductivity of a material increases as a result of absorbing photons.
4. Conclusion
We have performed a first-principles calculations based on DFT to compare the structural, elastic, thermodynamic, electronic, and optical properties of the two superconducting MAX phases Ti_{2}InC and Ti_{2}InN. The obtained elastic constants are compared with available calculations and elastic anisotropy discussed. The carbide phase is found to be brittle in nature, while the nitride phase is less brittle (near the border line).
The energy band structure and total densities of states reveal that both the materials exhibit metallic conductivity. This conductivity increases as X is changed from C atom to N in Ti_{2}InX. Hybridization of Ti-atom d states with C (N)-atom p states is responsible for the bonding. The Ti–In bond is weaker and the order of the bond strength: Ti–N > Ti–C > Ti–In. The bands associated with N atoms are lower in energy and narrower that can be attributed to the large electronegativity of N compared to that of C.
The temperature and pressure dependence of bulk modulus, specific heats, thermal expansion coefficient, and Debye temperature are all obtained through the quasiharmonic Debye model, and the results are analyzed. We find the electron-phonon coupling strengths λ ~ 0.49 and 0.62 for Ti_{2}InC and Ti_{2}InN, respectively, which implies that both are moderately coupled superconductors. The heat capacities increase with increasing temperature, which shows that phonon thermal softening occurs when the temperature increases. The thermal expansion coefficients for Ti_{2}InC and Ti_{2}InN are evaluated, and the calculation is in fair agreement with the only measured value available for Ti_{2}InC.
The optical features such as the real and imaginary parts of the dielectric function and positive dielectric constant do show to support the potential applications of the compounds in future. The reflectivity is high in the IR-visible-UV region up to ~10 eV and 12.8 eV for Ti_{2}InC and Ti_{2}InN, respectively, showing promise as good coating materials.
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