Prediction of fully compensated ferrimagnetic spin-gapless semiconducting FeMnGa/Al/In half Heusler alloys

First-principles calculations suggest that C1b-ordered FeMnZ (Z = Al, Ga, In and Al0.5Ga0.5) alloys are half-metallic fully compensated ferrimagnets with a spin-gapless semiconducting nature. In such materials, full spin polarization, spin-gapless properties and absence of external stray fields, thus exhibiting minimal energy losses, are expected.


Introduction
Cubic Heusler alloys are a rich family of materials that were first discovered by Heusler in 1903(Heusler, 1903. These alloys have attracted much attention because of their wide range of extraordinary multi-functional properties including half-metallic ferromagnetism (de Groot et al., 1983), thermoelectric materials (Uher et al., 1999), magnetic shape memory effects (Webster et al., 1984;Liu et al., 2003;Zhu et al., 2009) and tunable topological insulators (Lin et al., 2010). Halfmetallic ferromagnets (HMFs), which exhibit a complete spin polarization at the Fermi energy (E F ), are a natural source of spin-polarized current and are thus considered useful for spintronic applications (de Groot et al., 1983;Wolf et al., 2001). A nominally infinite magnetoresistance can be achieved if the two magnetic layers of magnetic tunnel junctions (MTJs) are replaced by HMFs (de Groot et al., 1983;Katsnelson et al., 2008). For example, giant tunnel magnetoresistance ratios of up to 1995% were obtained for epitaxial Co 2 MnSi/MgO/ Co 2 MnSi MTJs, where Co 2 MnSi is an HMF (Liu et al., 2012). However, most of the ferromagnets have a major drawback: the intrinsic net dipolar moment hinders the performance of the nearby device arrays or the multilayer bits in spintronic chips (Hu, 2012). Materials with no net magnetization but high spin polarization are therefore in high demand (Hu, 2012). Obviously, this is impossible for conventional antiferromagnets (AFMs) because of the symmetry of spin rotation, which leads to no spin polarization (de Groot, 1991). Breaking the symmetry of spin rotation is then a requirement for spintronic materials in AFMs (Venkateswara et al., 2018). Half-metallic antiferromagnets (HM-AFMs), which show 100% spin polarization while having zero net magnetization, are one of the most promising candidates (van Leuken & de Groot, 1995;Akai & Ogura, 2006). HM-AFMs were thought to be a special case of ferrimagnets because of the fact that they have no inversion symmetry in magnetic structure (Wurmehl et al., 2006). Because of this they were later renamed half-metallic fully compensated ferrimagnets (HM-FCFs) (Wurmehl et al., 2006).
In L2 1 ordered X 2 YZ Heusler alloys, when X and Y atoms carry a moment and the X-Y coupling is antiparallel, the alloys are ferrimagnets. In a carefully selected material the total magnetic moment (M) can be zero (Galanakis et al., 2007). This is based on the famous Slater-Pauling rule, which for X 2 YZ Heusler alloys is M = N v À 24, where N v is the number of valence electrons per formula (Galanakis et al., 2002b). The ordered L2 1 structure has four formula units per cubic unit cell, with X in A (0, 0, 0) and C (0.5, 0.5, 0.5) sites, Y in B (0.25, 0.25, 0.25) sites and Z in D (0.75, 0.75, 0.75) sites of the Wyckoff coordinates (Cu 2 MnAl-type structure). When the valence of Y is larger than that of X, the atomic sequence is then X-X-Y-Z and the prototype is Hg 2 TiCu, which is known as an inverse Heusler alloy (Ö zdog an & Galanakis, 2009). A well known example is Mn 2 CoAl (M = 2 B ) (Liu et al., 2008). There are three different variants, i.e. M = N v À 18, M = N v À 24 and M = N v À 28, of the Slater-Pauling rule for the inverse Heusler alloys depending on the chemical type of the constituent transition-metal atoms (Skaftouros et al., 2013a). For C1 b -ordered XYZ half Heusler alloys, the form of the Slater-Pauling rule is then M = N v À 18. The original example of an HMF was NiMnSb (M = 4 B ) (de Groot et al., 1983). Quaternary Heusler alloys XX 0 YZ also obey the Slater-Pauling rule (Ö zdog an et al., 2013). Therefore, a generalized version of the Slater-Pauling rule can be extracted for the Heusler alloys, and half-metallic Heusler alloys with N v = 18, 24 or 28 should be the likeliest candidates for HM-FCFs (Wurmehl et al., 2006).
It should be noted that in all HM-FCFs, transport is mediated by electrons having only one kind of spin, since the band structure is metallic in one spin channel. In a recently proposed new class of materials named spin-gapless semiconductors (SGSs), the realization of band gaps in both spin directions, i.e. an open band gap in one spin channel and a closed gap in the other, seems possible (Wang, 2008;Ouardi et al., 2013). An SGS has 100% spin-polarized carriers with tunable capabilities and the speed of the fully polarized spin electrons in the SGS could be much faster than in diluted magnetic semiconductors (Wang et al., 2009). As shown in Fig. 1, the SGS band structure and zero net magnetic moment are realized in the same material suggesting the discovery of a novel class of materials with both the features of HM-FCFs and SGSs. These were named fully compensated ferrimagnetic spin-gapless semiconductors (FCF-SGSs) (Jia et al., 2014;Zhang et al., 2015b). Because of their unique properties, full spin polarization, higher mobility of carriers and absence of stray fields generation are expected, thus leading to minimal energy losses using FCF-SGSs as electrode materials in spintronics devices (Han & Gao, 2018;Baltz et al., 2018).
To date, FCF-SGS-like properties have been observed in several Heusler ferrimagnets (Jia et al., 2014), including Ti 2and Cr 2 -based inverse Heusler (Skaftouros et al., 2013b), Mnbased half Heusler (Zhang et al., 2015b), and quaternary Heusler CrVTiAl (Venkateswara et al., 2018). So far few of them have been experimentally realized because generally they turned out to be unstable, or crystallized with a different structure (Feng et al., 2015;Venkateswara et al., 2018). The growth of the Heusler ferrimagnet Ti 2 MnAl on an Si (001) substrate has been attempted using magnetron sputtering but the samples obtained were of poor crystallinity (Feng et al., 2015). The higher energy configuration CrVTiAl has a spingapless semiconducting nature but the corresponding configuration is not a ground state (Venkateswara et al., 2018). We recently found several new FCF-SGS candidates based on the Slater-Pauling rule (Zhang et al., 2015b). But these candidates are not easy to realize in experiments. For example, C1 b -type Mn 2 Si was predicted to be an FCF-SGS. However, Mn 2 Si alloy actually crystallized with a different structure. Therefore, the search for FCF-SGSs with a high possibility of experimental realization is still under the spotlight in spintronics.
In this study, we report that an equiatomic FeMnGa alloy with C1 b -ordered structure can show both zero net moment and SGS properties at the same time and have a fair chance of realization. FeMnGa alloys were originally proposed as magnetic shape memory materials (Zhu et al., 2009;Omori et al., 2009;Liu et al., 2018). Stoichiometric Fe 2 MnGa has an L2 1ordered full Heusler structure (Xin et al., 2016). Although the crystal structure of stoichiometric FeMnGa has not been confirmed experimentally yet, the C1 b -ordered structure is likely to be realized in this alloy because of two considerations. First, FeMnGa alloys crystallize to an L2 1 -ordered cubic phase in quite a large composition range (Omori et al., 2009). Second, stoichiometric Ni 2 MnGa (Webster et al., 1984) and Co 2 MnGa (Hames, 1960) are L2 1 -ordered full Heusler alloys, and their equiatomic forms of NiMnGa (Ding et al., 2017)   CoMnGa  were all confirmed to be C1 bordered structures by experiment. In addition, competing magnetic behaviour was recently observed in Fe 41 Mn 28 Ga 31 (Sun et al., 2018). Therefore, experimental realization of C1 bordered FeMnGa with zero net magnetization seems feasible. In the present work, we performed a detailed first-principles calculations study on the structural, electronic and magnetic properties of a C1 b -ordered stoichiometric FeMnGa alloy. The results show that C1 b -ordered FeMnGa is a potential FCF-SGS. Similar band dispersions and magnetic properties were also found in FeMnAl 0.5 In 0.5 by first-principles calculations. Details are provided in the following sections.

Computation details and methods
Calculations were performed using the Vienna ab initio simulation package (VASP) (Hafner, 2008). The electronic exchange and correlation used a spin-polarized generalizedgradient approximation (GGA) of density functional theory (DFT) and the electron-ion interaction was described within the framework of projector augmented-wave formalism. The wave kinetic energy cutoff was set to 500 eV and a 15 Â 15 Â 15 mesh for the reciprocal-space integration with a Monkhorst-Pack scheme was used for good convergence.
According to the literature, the influence of spin-orbit coupling (SOC) on the band gap of Heusler alloys is insignificant for the 3d series elements (Mavropoulos et al., 2004). Therefore, SOC of the alloys was not employed in the calculations. For magnetism, the orbital moments originated from SOC are expected to be very small in FeMn-based alloys (Galanakis, 2005), thus the spin and orbital moments were not separated here.
The SGS properties were further confirmed by the self-consistent fullpotential linearized augmented planewave method (Wimmer et al., 1981;Weinert et al., 1982). It should be pointed out that the modified Beche-Johnson (MBJ) exchange potential + local density approximation (LDA) correlation, which allows the calculation of band gaps with an accuracy similar to GW calculations, was also employed. The electronic and magnetic properties of disordered systems were calculated using the Korringa-Kohn-Rostoker (KKR) Green's function method combined with the coherent potential approximation (CPA) (Katayama et al., 1979;Blü gel et al., 1987;Kaprzyk & Bansil, 1990). This is a powerful method for disordered systems.

Crystal structure and compensated ferrimagnetism
Half Heusler alloys with a general formula XYZ, where X and Y are transition metals, and Z is a main group element, crystallize in a non-centrosymmetric C1 b structure. The most well known one is NiMnSb, which was found to be an HMF by de Groot et al. (1983). It is a ternary ordered variant of the CaF 2 structure and can be derived from the tetrahedral ZnStype structure by filling the octahedral lattice sites. The C1 btype FeMnGa alloy considered here consists of three interpenetrating f.c.c. sublattices, each of which are occupied by Fe, Mn and Ga atoms. Fig. 2 and Table 1 show the three possible inequivalent atomic arrangements and the corresponding occupied Wyckoff positions by fixing Ga at the D site.
We first performed structural optimization calculations to determine the lattice parameters and the ground state of C1 bordered FeMnGa. Three possible arrangements of atoms are summarized in Table 1 and three kinds of magnetic orders, i.e. paramagnetic, ferromagnetic and antiferromagnetic states, are considered in the calculations. The paramagnetic (or nonmagnetic) state means that the constituent atoms of FeMnGa have no spin polarization. The ferromagnetic (or antiferromagnetic) state means the parallel (or antiparallel) alignment of the magnetic moments of the Fe and Mn atoms.
Although the more precise term to describe them was thought to be compensated ferrimagnets as used in the literature (Galanakis et al., 2014), the term we use here is still AFMs, which is a more general term. The moments of the Z atoms are usually ignored since most of them are close to zero. Fig. 3(a) shows the calculated total energy as functions of lattice constant for FeMnGa. It can be seen that a ferromagnetic state of Type I or II configuration appears only when the lattice constants of the crystal go beyond 5.8-6.0 Å , because the ferromagneric state of FeMn cannot be stabilized in a selfconsistent process below a critical distance between Fe and Mn atoms. This can be explained by the Bethe-Slater curve  Crystal structures in conventional unit cells for three different types of Wyckoff coordinate, i.e. (a) Type I, (b) Type II and (c) Type III, for atoms in C1 b -ordered FeMnGa alloy with 1:1:1 composition. Table 1 Inequivalent site occupancies within the C1 b -type structure.
Void means that no atoms occupy the site.  which shows that MnMn or MnFe atoms tend to couple antiferromagnetically when they are first nearest neighbours or the distance between them is less than a certain value (Khovaylo et al., 2009). Similar situations also occur in many other Heusler alloys, such as NiMnGa, Fe 2 MnGa, Mn 2 FeGa, MnCrZ (Z = Al, Si and Sb) and FeCrZ (Z = Ga, Ge and As) (Fujii et al., 2010;Zhang et al., 2018). For Type III configuration [ Fig. 2(c)], Fe and Mn atoms have a larger distance which results in a possible ferromagnetic coupling. Among all these calculated states, the Type I antiferromagnetic state is the most stable one since it has the lowest energy. This structure type agrees with the already observed half Heusler alloys (de Groot et al., 1983;Galanakis et al., 2002a). The optimized equilibrium lattice constant is a = 5.50 Å . Fig. 3(b) shows the atomic resolved and total magnetic moments of the unit cell as a function of the lattice constants. For the equilibrium lattice constant, the calculation reveals nearly full compensation of the magnetic moments. A change in the lattice parameter by up to À1.8 to 3.6% (5.4-5.7 Å ) with respect to the equilibrium one only alters the local magnetic moments of the Mn and Fe atoms. An overall increase in the lattice parameter slightly increases the magnetic moment of the Mn atoms and decreases the magnetic moment of the Fe atoms. The total magnetic moment of zero, as a sum of those of each atom, remains unaffected. This result indicates the fully compensated ferrimagnetism and the half-metallic character of FeMnGa. The magnetic moment of the half-metallic C1 b Heusler alloys follows the simple rule: M = N v À 18. The robustness of the fully compensated ferrimagnetism originates from the large half-metallic gap of the minority channel that is induced by the hybridization of transition-metal atoms, as observed in many other Heusler type compounds (Galanakis et al., 2002b). The hybridization and details of the electronic structure of FeMnGa were analysed and are discussed below.

Electronic structure of FeMnGa
Detailed analyses of atomic hybridization and the origin of the half-metallic band gap in studies of Heusler-based HMFs have been performed by Galanakis et al. They found that, for most of the Heusler alloys, the band gap mainly arises from the hybridization of d states of the transition-metal atoms (Galanakis et al., 2002a,b). The possible hybridization orbitals for C1 b FeMnGa from low energy to high energy according to the literature are 1 Â s, 3 Â p, 2 Â e g , 3 Â t 2g, , 2 Â e g and 3 Â t 2g as shown in Fig. 4(a) (Galanakis et al., 2002a).   Structural optimization and fully compensated ferrimagnetism for FeMnGa. The optimized lattice constant (a) and the magnetic moment (b) are shown as functions of the lattice parameter. TX-P, TX-A and TX-F represent the Type-X paramagnetic state, the Type-X antiferromagnetic state, and the Type-X ferromagnetic state, respectively, where X is I, II or III.
Figs. 4(b)-4(d) display the spin-resolved band structure and density of states (DOS) of FeMnGa at the equilibrium lattice constant. The relative band structure shows that the spindown state has a real gap between the [t 2g ]À point and the [e g ]À point with the valence band maximum (VBM) at the À point and the conduction band minimum (CBM) at the X point. Hence the gap of the spin-down state is an indirect one, which agrees with many of the C1 b -type Heusler compounds (Zhang et al., 2015a,b). There is also a considerable gap between the [t 2g ]À point and the [e g ]À point in the spin-up channel, but the VBM and CBM are not located at the À point. Instead, they are located at the L and X points, respectively. In addition, the valence band and conduction band overlap at the X point resulting in a pseudo-gap at the Fermi level. The obtained spin-down DOS clearly shows a gap at the Fermi energy (E F ), while the spin-up DOS exhibits a valley shape with the minimum value being close to zero and located at E F . This shape follows the idealized DOS for SGS (Wang, 2008). Similar electronic structure was observed in many other Heusler alloys, such as Mn 2 CoAl (Ouardi et al., 2013). However, most of them have a considerable magnetic moment. FeMnGa is a very special case in which the total spin moment is exactly 0 B . Compared with the widely studied SGS material Mn 2 CoAl, whose magnetization is 2 B , FeMnGa will offer a superior advantage owing to its ideally compensated magnetic moment.
Note that the closed gap of the spin-down channel is not a real zero width gap. The Fermi level cuts a little of the valence band. Uniform strain, simulated by changing the lattice constants, has often been used to open a real band gap in many Heusler alloys . Fig. 5(a) shows the DOS of FeMnGa for different lattice constants. Either expansion or contraction of the lattice results in a practically rigid shift of the bands with small rearrangements of the shape of the peaks to account for the charge neutrality (Galanakis et al., 2002a). It is clearly seen that expansion by less than 1% (5.55 Å ) opens a real narrow gap in the spin-up channel.  Table 2, contraction results in a small net magnetic moment because of the destroyed spin-down gap, while expansion retains the zero net magnetic moment. This indicates that FeMnGa has the potential for the realization of FCF-SGS.
From the discussion above, we can see that the fully compensated ferrimagnets with spin-gapless semiconducting nature can arise with net spin N s = 0 as the number of up and down electrons are equal. Such materials have the advantage of being able to generate fully spin-polarized current while exhibiting zero net magnetization. This is very different from a  Electronic structure under uniform strain simulated by changing the lattice constants. (a) The total DOS for the FeMnGa alloy as a function of the lattice constant. As the lattice constant was expanded less than 1% (5.55 Å ), a real closed gap was obtained. (b) The corresponding band structure of FeMnGa for a = 5.55 Å based on both the GGA and the LDA + MBJ.

Table 2
Total and atom-resolved spin magnetic moments in B for the FeMnZ alloys, where Z = Al, Ga, In or In 0.5 Al 0.5 , as a function of the lattice constants.
PCLC represents the percentage change of lattice constant with respect to those at equilibrium. Negative (or positive) signs of PCLC means the uniform strain is a contraction (or expansion). conventional AFM, in which the vanishing of the net magnetic moment originates from a symmetry relation between sites of opposite spin. It causes the electronic structure of the two spin directions to be identical, which results in no polarization of the conduction electrons (de Groot, 1991). In the magnetic structure of FeMnGa, as shown in Table 2, the cancellation of the magnetic moment is not caused by a symmetry relation between sites with up and down spins, instead the moments of Fe are cancelled by the moments of Mn at different crystallographic sites. It can be seen that the magnetic moments of Fe atoms are not equal to those of Mn atoms. Ga atoms also carry a small spin magnetic moment indicating the breaking of magnetic inversion symmetry. This is one of the features of fully compensated ferrimagnetism (Venkateswara et al., 2018). Another important feature of FeMnGa that differs from conventional AFMs is that the electronic structures for the two spin directions are completely asymmetrical with respect to the spin direction, as shown in the DOS of Fig. 4(c). This is because the distributions of electronic states of Fe and Mn atoms in FeMnGa as a function of energy are totally different from each other. Fig. 6 shows the atom-resolved DOS, which demonstrates that the local DOS of Fe and Mn have a totally different distribution and do not completely compensate each other resulting in a spin polarization.
From the atom-resolved DOS of FeMnGa as shown in Fig. 6, it can be seen that the contribution of Ga is not dominant in forming the total DOS of the alloy. However, Ga plays a very important role in forming the SGS property in FeMnGa, as observed in many other alloys (Galanakis et al., 2002a). This is because the Ga atom has three valence electrons, and in FeMnGa each Ga atom introduces a deep lying s band, and three p bands below the centre of the d bands. These bands accommodate a total of eight electrons per unit cell, so that formally Ga acts as a five-charged Ga 5À ion. Analogously, an Sb atom behaves in NiMnSb as an Sb 3À ion. This does not mean that locally such a large charge transfer exists. In fact, the s and p states strongly hybridize with the transition-metal d states, and the charge in these bands is delocalized and locally Ga loses only about one electron, if one counts the charge in the Wigner-Seitz cells. What does count is that the s and p bands accommodate eight electrons per unit cell, thus effectively reducing the d charge of the transition-metal atoms. This will have a crucial effect on the distribution of the density state of each magnetic atom, hence affecting the total DOS of the alloy. Fig. 7 shows the atom-resolved DOS of Fe, Mn and Ga atoms for C1 b FeMnGa (blue curve) and for FeMn (red curve) with the Ga atom removed from the crystal. Since the Ga atom is removed from the crystal, Fig. 7(c) only gives the DOS of Ga for C1 b FeMnGa. In the FeMn crystal hypothetical alloy (red curve), there is a gap in the spin-down channel for DOS of both Fe and Mn, and E F is located at the gap in the spin-down bands and crosses a peak in the spin-up bands. As Ga atoms are added to the structure, the DOS of Fe and Mn have a totally different distribution which shows a large overlap in energy with the DOS of Ga atoms. This indicates a strong hybridization between the d states of the transition metals Fe and Mn, and the p states of the main group element Ga. The interaction of FeMn-d and Ga-p leads to the redistribution of electrons in the FeMn alloy, hence producing the spin-gapless semiconducting property in C1 b -ordered FeMnGa alloy.
The C1 b structure has high atomic order, while atomic disorder is sometimes inevitable in Heusler alloys. Such structural details were treated by applying the CPA. Three atomic disorders, i.e. Fe-Ga, Mn-Ga and Fe-Mn were considered in the present work. The results are given in Fig. 8. It can be seen that the DOS exhibits SGS properties when x = 0. With the increase in the degree of disorder of Fe-Ga, Fe-Mn or Mn-Ga, the SGS properties gradually disappear. The    SGS properties were totally destroyed when x = 0.5, especially for MnGa and FeGa disorder. This indicates that the distribution of DOS is very sensitive to atomic disorder, which reduces hybridization between the d states of the transitionmetal atoms resulting in smaller exchange splitting of the d band (Ö zdog an & Galanakis, 2011). It should be noted that the DOS of ordered FeMnGa (x = 0) based on the KKR-CPA has a smaller energy gap with respect to the results based on the DFT-GGA (as shown in Fig. 6). Similar cases also exist in the well known SGS Mn 2 CoAl (Liu et al., 2008;Xu et al., 2014). The important conclusion, however, is that the atomic disorder has a crucial influence on electronic structure. Therefore, highly ordered C1 b structure is important for obtaining SGS properties.
FeMnGa alloys can crystallize in different structural phases when treated under different conditions. The B2 phase can be obtained with annealing at 1073-1373 K (Zhu et al., 2009;Yang et al., 2016). The highly ordered C1 b (or L2 1 ) phase is usually obtained from the B2 phase by ordering treatment (Ishikawa et al., 2008). An Ni 3 In type hexagonal phase was recently observed with annealing at 873-923 K (Okumura et al., 2014;Liu et al., 2018). The order-disorder transition temperature from the B2 to C1 b (or L2 1 ) phase in Heusler alloys is always between 773 and 973 K (Ishikawa et al., 2008). Therefore, it is necessary to carefully avoid the hexagonal phase when obtaining the C1 b phase in experiment.

Isoelectronic substitution
Since FeMnZ (Z = Al, In) have the same valence electrons as FeMnGa, they meet the requirement of fully compensated ferrimagnetism according to the Slater-Pauling rule. Therefore, we also performed calculations on these alloys. The optimized equilibrium lattice constants for FeMnAl and FeMnIn are 5.44 and 5.98 Å , respectively. Table 2 gathers their corresponding atomic and total spin magnetic moments. The moments of the Al and In atoms are negligible. The Fe and Mn atoms contribute the main local magnetic moments and are arranged antiparallel to each other. This leads to a small nonzero net spin magnetic moment deviating from the Slater-Pauling rule, which indicates the loss of SGS properties. The corresponding band structures for FeMnAl and FeMnIn are present in Fig. 9. The band structures represented in Figs. 9(a) and 9(c) are with equilibrium lattice constants. No SGS properties are observed. Both the magnetic moment and band structures indicate that FeMnAl and FeMnIn in the ground state are not FCF-SGSs. However, by correcting the lattice constants of FeMnAl and FeMnIn, the Fermi energy would again move into the gap. As shown in Figs. 9(b) and 9(d), expansion and contraction of the lattice constants can induce SGS electronic structures in FeMnAl and FeMnIn, respectively, and we can see that both FeMnAl and FeMnIn present FCF-SGS for the specific lattice constant of 5.70 Å . This means that the lattice constant of 5.70 Å is a key point for Band structures for FeMnAl with lattice parameters at 5.44 Å (a) and 5.70 Å (b), for FeMnIn at 5.98 Å (c) and 5.70 Å (d), and for FeMnAl 0.5 In 0.5 at 5.70 Å (e) based on the GGA.  realising FCF-SGS. The problem is that expansion of 4.78% for FeMnAl and contraction of 4.68% for FeMnIn are too large to realize in practice. A more feasible way to modulate the lattice constant experimentally is to isoelectronically replace the sp element with an element in the same main group. This will effectively change the lattice constant because of the different atomic radii, thereby adjusting the energy gap without altering the number of valence electrons. Based on the calculations, we found that the optimized equilibrium lattice constant of FeMnAl 0.5 In 0.5 is exactly 5.70 Å , and the band structure exhibits the idealized SGS behaviour as shown in Fig. 9(e), the magnetic moment of which is 0 B as shown in Table 2. Therefore, substituting 0.5In for Al may realize FCF-SGS properties in its ground state in FeMnAl (In).

Conclusions
In this work, we employed first-principles calculations to investigate the crystal structure, electronic and magnetic properties of C1 b -ordered stoichiometric half Heusler FeMnAl/Ga/In alloys. Our calculations show that the band structure of FeMnGa exhibits a considerable gap in one of the spin channels and a zero gap in the other thus allowing for higher mobility of fully spin-polarized carriers. The band gap originates from the strong hybridization between the d states of the transition-metal atoms. The interaction of FeMn-d and Ga-p leads to the redistribution of the electronic states of the Fe and Mn atoms, which is very important for the formation of SGS properties. The localized magnetic moments of the Fe and Mn atoms have an antiparallel arrangement leading to a fully compensated ferrimagnetism. The exact cancellation of the magnetic moment originates from the antiparallel arrangement of inequivalent magnetic ions (Fe and Mn) being totally different from that of conventional antiferromagnets. One of the most important features is that the electronic structure for the two spin directions is completely asymmetrical with respect to the spin direction, which comes from the asymmetrical distributions of the electronic states of the Fe and Mn atoms. These results indicate that the C1 b -ordered stoichiometric FeMnGa is an HM-FCF with a spin-gapless semiconducting nature. The highly ordered C1 b structure is very necessary because the SGS properties are very sensitive to atomic disorder. Similar band dispersion and compensated moments were found in C1 b -ordered half Heusler FeMnAl 0.5 In 0.5 alloys. This work is expected to enrich the diversity of spin-polarized antiferromagnetic materials and boost the development of spintronics.