Prediction of superconductivity of 3d transition-metal based antiperovskites via magnetic phase diagram

Prediction of superconductivity of transition-metal based antiperovskites via magnetic phase diagram

D. F. Shao Key Laboratory of Materials Physics, Institute of Solid State Physics, Chinese Academy of Sciences, Hefei 230031, P. R. China    W. J. Lu wjlu@issp.ac.cn    P. Tong Key Laboratory of Materials Physics, Institute of Solid State Physics, Chinese Academy of Sciences, Hefei 230031, P. R. China    S. Lin Key Laboratory of Materials Physics, Institute of Solid State Physics, Chinese Academy of Sciences, Hefei 230031, P. R. China    J. C. Lin Key Laboratory of Materials Physics, Institute of Solid State Physics, Chinese Academy of Sciences, Hefei 230031, P. R. China    Y. P. Sun ypsun@issp.ac.cn Key Laboratory of Materials Physics, Institute of Solid State Physics, Chinese Academy of Sciences, Hefei 230031, P. R. China High Magnetic Field Laboratory, Chinese Academy of Sciences, Hefei 230031, P. R. China University of Science and Technology of China, Hefei 230026, P. R. China
Abstract

We theoretically studied the electronic structure, magnetic properties, and lattice dynamics of a series of transition-metal antiperovskite compounds AXM by density function theory. Based on the Stoner criterion, we drew the magnetic phase diagram of carbon-based antiperovskites ACM. In the phase diagram, compounds with non-magnetic ground state but locating near the ferromagnetic boundary are suggested to yield sizeable electron-phonon coupling and behave superconductivity. To approve this deduction, we systematically calculated the phonon spectra and electron-phonon coupling of a series of Cr-based antiperovskites ACCr and ANCr. The results show that AlCCr, GaCCr, and ZnNCr could be moderate coupling BCS superconductors. The influence of spin fluctuation on superconductivity are discussed. Furthermore, other potential superconducting AXM including some new Co-base and Fe-based antiperovskite superconductors are predicted from the magnetic phase diagram.

pacs:
74.70.Ad, 74.25.Ha, 74.25.Kc, 74.20.Pq

I Introduction

Since superconductivity (SC) was found by Onnes onnes_resistance_1911 (), researchers have made a lot of efforts to figure out its mechanism. The BCS theory BCS1 (); BCS2 (); BCS3 () pointed out two electrons with opposite spins can pair with each other via electron-phonon coupling (EPC). Therefore, magnetism or spin fluctuation (SF) may break the pair and be harmful to SC. The discovery of unconventional superconductors such as cuprate oxide superconductors bednorz_possible_1986 (); wu_superconductivity_1987 (), iron based superconductors HCP-iron-nature (); kamihara_iron-based_2008 (), SrRuOmaeno_superconductivity_1994 (), NaCoOHO NaCoO2-SC-found (), etc., challenges the EPC mechanism. For the unconventional superconductors, SF may play an important role in the superconducting mechanism, which makes researchers reconsider the relation between magnetism and SC.

Superconducting MgCNi he_superconductivity_2001 (), containing a high concentration of magnetic element Ni, attracted a lot of attentions on the role of SF. MgCNi has a so-called antiperovskite structure, in which Mg atom locates at the corner, and six Ni atoms at the face-center together with one C atom at the body center form the C-Ni octahedron. A van Hove singularity locates just below Fermi level (), leading to large density of states (DOS) at () rosner_prl_2001 (); Singh-Mazin (); Shim (). It makes the compound strongly exchange-enhanced and unstable toward to ferromagnetism (FM) upon hole doping rosner_prl_2001 (); Singh-Mazin (). Experimentally speaking, due to the high volatility of Mg and the relatively poor reactivity of C, it is extremely difficult to synthesize stoichiometric MgCNi Mollah (); Lee-AM (); Gordon-singlecrystal (). The atomic deficiencies in the antiperovskite system may strongly affect the properties Sieber-PRB2007 (); Shao-jap2013 () and lead to some contradictory results in the reported polycrystalline samples Mollah (). Recently, the single crystal samples have been prepared Lee-AM (); Gordon-singlecrystal (); Lee-jpcm (); Pribulova (); Diener (); Jang (); Hong-phonon-singlecrystal (). The physical property measurements demonstrate the conventional EPC mechanism, but the reported EPC strengths of these samples are contradicted Gordon-singlecrystal (); Lee-jpcm (); Pribulova (); Diener (); Jha-mgcni3phonon (); tong (). Moreover, it has not been successful so far to induce FM instability by preparing hole-doped compounds such as MgNaCNi and MgLiCNi. The interplay between SC and SF in MgCNi is still unclear and in debate Loison-RBPd3 ().

Nowadays, lots of transition-metal based antiperovskite AXM (A usually is main group element; X = B, C, and N; M = transition-metal elements) have been experimentally synthesized Fruchart (). However, the reported physical property measurements are mainly focused on the Ni- and Mn-based antiperovskites. In Ni-based antiperovskites, CdCNi and ZnNNi were reported to show SC behavior CdCNi3 (); ZnNNi3 (). Abundant magnetism appears in Mn-based antiperovskites (see recent review article Ref. Tong-AXMn3-review, ). Moreover, superconducting trace has been found in InBSc Wiendlocha-InBSc3 (). Some theoretical predictions suggest that SC may exist in some Sc-based and Cr-based antiperovskites Wiendlocha-ABSc3 (); Wiendlocha-ANCr3 (); RhNCr3 (); GaNCr3-sc (). Indeed, due to the high concentration of transition-metal atoms, one can imagine that more interesting properties exist in other antiperovskite AXM. The investigation of them will be very important, both in the search for new superconductors and in the pursuit of a better understanding of the interplay between SC and magnetism Loison-RBPd3 ().

In the present work, we offer an approach to explore new transition-metal based antiperovskite superconductors. In order to have an overall understanding of the magnetism in AXM, we calculated the electronic structures of a series of transition-metal based antiperovskites AXM and concluded the doping effects of each atom. From the analysis of these doping effects, we can evaluate the variation of of different AXM. We drew a magnetic phase diagram of ACM based on the Stoner criterion . From the phase diagram, we predict that the materials locating near FM boundary may have sizeable EPC and could show SC. To confirm this deduction, we systematically investigated the formation energies, electronic structures, lattice dynamic properties, and EPC of a series of Cr-based AXCr. For comparison, such properties of MgCNi are also calculated. Our results confirm the strong EPC for MgCNi and suggest that AlCCr, GaCCr, and ZnNCr are moderate coupling BCS superconductors. The depairing effects from SF are aslo discussed. Furthermore, some potential superconducting antiperovskites such as new Co- and Fe-based superconductors are suggested.

Ii Methods

The structural relaxation and electronic structure calculations were performed using projected augmented-wave (PAW) blochl1994projector (); torrent2008implementation () method as implemented in the ABINIT code gonze2002firstprinciples (); gonze2009abinitfirstprinciples (); gonze_brief_2005 (). Electronic wavefunctions are expanded with plane waves up to an energy cutoff () of 1200 eV. Brillouin zone sampling is performed on a Monkhorst-Pack (MP) mesh monkhorst1976special () of The self-consistent calculations were considered to be converged when the total energy of the system was stable within Ha. Non-magnetic (NM) and FM states were tested in the study.

The calculations of phonon spectra and EPC were based on the frame work of the self consistent density functional perturbation theory (DFPT) DFPT () using planewaves and ultrasoft pseudopotentials US () with QUANTUM-ESPRESSO QE (). We use an grid for zone integration in the self-consistent calculations, while a denser grid was used in the EPC calculations. We have calculated dynamical matrices at a uniform grid of -points.

To ensure our calculation reliability, we cross-checked the results given by the above two DFT codes and found them to be in close agreement. And for consistency, we used the same GGA-PBE perdew1996generalized () exchange-correlation potential in both cases.

Iii Results and Discussions

iii.1 Doping effects of AXM

As Rosner et al. rosner_prl_2001 () mentioned, the A-site atom only plays the role as an effective valent electrons supplier. The most common A-site atoms of the antiperoveskite compounds can be divided into four groups according to the effective valence electrons: Cu and Ag (A); Mg, Zn, and Cd (A); Al, Ga, and In (A); Ge and Sn (A). Clearly, the effective valence electrons of A-site atoms are usually in the range from 1 to 4. For simplification, we chose Na, Mg, Al, and Si atoms as the A-site atoms of the antiperovskites we investigated.

Figure 1: Lattice parameters and magnetic moments of ACM (A = Na, Mg, Al, and Si, M = transition metal elements).

Figure 1 shows the lattice parameters and magnetic moment of a series of carbon-based ACM. As expected, the lattice parameter varies with the same trend of variation of the atom radius. The ground states of these compounds are determined by comparing the total energies of the NM and FM states. The ACMn and most ACFe show FM state, which coincides with the experimental results. Surprisingly, SiCFe and AlCCo show NM state. Comparing the magnetic moments with the (table 1), one can see that all the compounds with FM ground state have quite large in NM state. It is corresponding to the Stoner’s itinerant magnetism: the higher in NM state, the easier a system becomes spin-polarized. The magnetism of these compounds will be discussed below.

M Sc Ti V Cr Mn Fe Co Ni Cu
A
Na 3.66/0.26 3.19/0.22 1.51/0.50 4.17/0.32 7.84/0.37 7.61/0.30 3.83/0.41 7.45/0.33 0.44/0.74
Mg 5.30/0.30 1.64/0.40 4.28/0.23 2.86/0.34 5.47/0.35 6.20/0.32 3.69/0.41 2.57/0.28 0.41/0.79
Al 0.26/0.29 1.491/0.05 4.31/0.32 2.22/0.32 4.87/0.45 5.53/0.39 0.77/0.74 1.13 /0.58 1.04/0.20
Si 1.26/0.42 2.23/0.25 6.38/0.21 3.06/0.27 6.20/0.47 1.35/0.31 3.87/0.42 1.68/0.19 0.75/0.72
Table 1: The (states/eV/spin) in NM ground state (above “/”) and Stoner parameter (under “/”) of ACM (A = Na, Mg, Al, and Si, M = transition metal elements).

In order to have an overall understanding of the transition-metal based antiperovskites AXM, the doping/substitution effects of each atom on the electronic structure must be investigated. We start from reviewing the electronic structure of MgCNi. Figure 2 shows the calculated DOS of MgCNi. It can be seen that the total DOS near are mainly contributed by Ni- electrons. From -7 eV to -4 eV and near , C- electrons hybridize strongly with Ni- electrons. The anti-bonding state locates just below , which leads to the van Hove singularity, yielding the high states/eV/spin. We calculated the Stoner parameter using the methods mentioned by Rosner et al. rosner_prl_2001 (). The result shows that , and Stoner enhancement factor , indicating the strong SF exists in MgCNi. Our results are very close to the previous theoretical reports rosner_prl_2001 (); Singh-Mazin (); Shim (); Mollah (), which proves the validity of present calculations.

Figure 2: Total and atom-orbital-projected DOS of MgCNi.
Figure 3: DOS of (a) NaCNi, (b) MgCNi, (c) MgAlCNi, (d) AlCNi, and (e) SiCNi.

We firstly studied the A-site doping effect by investigating the electronic structures of NaCNi, MgCNi, AlCNi, and SiCNi. Using a doubled supercell, we also calculated the electronic structure of MgAlCNi. As shown in figure 3, the doping of A-site atoms does not change the overall shape of DOS of ACNi near . The main change is the moving with the variation of the amount of electrons. Thus the doping effect of A-site atom of AXM can be evaluated by the rigid band approximation. For NaCNi, it can be seen as doped MgCNi by a hole, which causes decreasing. The just locates at the DOS peak, leading to very large , which makes NaCNi satisfied with the Stoner criteria . Therefore, spin polarization appears in NaCNi.

Next we consider the X-site doping effect. Figure 4 shows the DOS of MgBNi, MgCNi and MgNNi. Since the X- electrons strongly hybridize with Ni- electrons, the change of X-site atoms is expected to strongly influence the shape of DOS. The evaluation of X-site doping effect needs to investigate the X-M hybridization besides the moving. For instance, replacing the carbon atom in MgCNi by boron atom, moves to the DOS peak. On the other hand, the B-Ni hybridization makes the peak smeared, which does not lead to very large . Therefore MgBNi is still in the NM ground state. The calculated of MgBNi is 2.58 states/eV/spin, which can be comparable to that of MgCNi. For MgNNi, the DOS peak is smeared, too. Meanwhile moves away from the DOS peak, leading to small states/eV/spin.

Figure 4: DOS of (a) MgBNi, (b) MgCNi, and (c) MgNNi.
Figure 5: DOS of (a) AlCCr and (b) AlNCr.

According to our calculation, except for Ni- and Cu-based AXM, all the other compounds have similar character that the bonding and anti-bonding states are far from . That means for most AXM compounds, there exists weak X-M hybridizations at . Figure 5 shows the DOS of AlCCr and AlNCr. The shapes of DOS near are very similar. The only difference is the location of decided by total electrons. Thus for most AXM (except for Ni- and Cu-based ones) the influence of electronic structure by changing X-site atom can be approximately evaluated as hole or electron doping.

Now we study the M-site doping effect on the electron structure. Figure 6 shows the DOS of MgCM. The shape of the DOS of MgCZn is quite different from those of other MgCM. It is possibly due to that all the orbitals of Zn are fulfilled, which makes electrons of Zn atom localized. From MgCSc to MgCCu, moves towards to high energy as total electrons increase, and the shapes of DOS keep similar feature. Can we just deduce the M-site doping effect using rigid band approximation? The answer is negative.

Figure 6: DOS of MgCM (M = transition metal elements).
Figure 7: DOS in NM state of (a) MgCCo, (b) MgCCoNi, (c) MgCCoNi, (d) MgCNi and (e) DOS in FM state of MgCCoNi.

We further investigated the electronic structure of doped MgCNi by Co (i.e. MgC(Ni,Co)). The calculated DOS in NM state of the doped MgCNi by one, two, and three cobalt atoms are shown in figures 7 (a)-(d). of MgCCo locates at a DOS peak, which makes MgCCo be in FM ground state. For MgCCoNi and MgCCoNi, the DOS near can be seen as the sum of the DOS of Ni- electrons and Co- electrons. The small of MgCCoNi and MgCCoNi lead them to show NM ground state. The DOS peak (van Hove singularity) splits into two peaks contributed by anti-bonding states of C-Ni and C-Co, respectively. The Co doping decreases the total electrons, which reduces and makes the anti-bonding state of C-Ni unoccupied. On the other hand, the Co doping weakens the DOS peak of Ni- electrons and enhances the DOS peak of Co- electrons. From the above discussion, one can deduce that as MgCNi is doped by a small Co content, the DOS peak of Ni- electrons can still has considerable strength. Meanwhile moves through the peak, which will lead to very large . According to Stoner criteria , the system will become FM state. The calculation of MgCCoNi proves the deduction (figure 7 (e)). However such a FM state has not been observed in experiments Mollah (), might due to a high doping content or an inaccurate stoichiometry. Similarly, the variations of and magnetic properties of M-site doping in other AXM can be evaluated, too.

Additionally, the doping effect of some isovalent A-site atoms was also investigated. As shown in figure 8, changing Mg to the isovalent atoms Zn and Cd, the electronic structure near rarely changes. It supports the A-site atoms only give the effective valence electrons as Rosner et al. proposed rosner_prl_2001 (). Thus the doping effects of A-, X-, and M-sites we concluded above can be generally applied to most transition-metal based antiperovskites.

Figure 8: DOS of (a) MgCNi, (b) CdCNi, (c) ZnCNi, (d) MgNNi, and (e) ZnNNi.

iii.2 Magnetic phase diagram of ACM

We calculated the Stoner parameters of a series of carbon-based ACM (see table 1). According to the doping effects we concluded above, the variation of of different AXM can be evaluated. Using the factor , we drew the magnetic phase diagram of carbon-based ACM in figure 9.

The ACM locating in the areas with the colors green to red are satisfied with the Stoner criteria and therefore show FM ground state. All the Mn-based antiperovskites and most Fe-based antiperovskites show FM. Here we must point out that we only consider the NM and FM states. In reality, abundant magnetisms, e.g. antiferromagnetism and non-collinear magnetism, are observed experimentally in the Mn-based antiperovskites Tong-AXMn3-review (). In this sense, our phase diagram can not present the real magnetism of such compounds. But in principle, if an itinerant system has very high in NM state, this system is unstable and prefers to be spin-polarized. Accordingly, the magnetic ordering must occur to lower to stabilize the system. Therefore, if a compound locates in the FM area of our phase diagram, it means that the NM state does not favor the energy minimum and the magnetic ordering will emerge. Such phase diagram can help to explore new magnetic antiperovskites. Furthermore one can also predict the magnetic state of most boron- and nitrogen-based antiperovskites based on the magnetic phase diagram after considering the X-site doping effect as concluded above.

Figure 9: Magnetic phase diagram of ACM. The black line is the NM-FM boundary. MgCNi is highlighted using the red star.

We highlighted MgCNi using a red star in the phase diagram. Obviously, MgCNi is very close to the FM state. One can imagine that there must be some interplay between FM and SC in MgCNi. As mentioned above, in order to figure out such interplay, exploring more MgCNi-like superconducting antiperovskites is necessary. We assume SC may appear in the area near the NM-FM boundary, since in such area the compounds have sizeable that can lead to a strong EPC.

iii.3 Superconductivity in MgCNi and AXCr

In the magnetic phase diagram, one can notice that some Cr-based antiperovskites locate in a small interval between two FM areas, which makes AXCr as a good system to prove our deduction above. In this part, we investigated the potential SC in AXCr. For comparison, the lattice dynamics and EPC property of MgCNi were also calculated.

Previously, we calculated the formation energies and electronic structures of a series of Cr-based antiperovskite carbides ACCr Shao-ACCr3 (). Only AlCCr and GaCCr have negative formation energies and may be synthesized experimentally. Both the two compounds show the NM ground state. Because of the isovalent A-site atoms, the electronic structures near of the two compounds are almost the same. Similar to MgCNi, of the two compounds locates at a slope of a DOS peak, which leads to large and may generate sizeable EPC.

In present work, we also investigated a series of Cr-based antiperovskite nitrides ANCr. The lattice parameters and the formation energies of NM and FM states are listed in table 2. It can be seen that the magnetic state of ANCr is almost the same as that of ACCr, which accords with the X-site doping effect we concluded above. The calculated results show that ZnNCr, AlNCr, GaNCr, and SnNCr have negative formation energies and therefore may be synthesized under normal condition in experiments.

A Zn Ga Al Ag Cd Sn Mg In
() 3.861 3.868 3.878 3.861 3.91 3.944 3.956 3.918
(eV/atom) -0.1027 -0.2195 -0.2448 0.0972 0.0619 -0.0813 0.0173 0.0187
(eV/atom) -0.1027 -0.2206 -0.2455 0.0969 0.0626 -0.0831 0.0173 0.0186
(/Cr) 0 0.23 0.22 0.06 0 0.69 0.03 0.4
Table 2: Lattice parameter , formation energies , and magnetic moments per Cr atom of ANCr.

The overall shapes of DOS near of ZnNCr, AlNCr, GaNCr, and SnNCr are very similar (see figures 10 (a)-(d)). The calculated and Stoner criteria are listed in table 3. It was previously suggested that GaNCr may be a potential superconductor Wiendlocha-ANCr3 (); GaNCr3-sc (). According to our calculations, it can be seen that for AlNCr and GaNCr, which means the two compounds just locate at the FM quantum critical point. They show weak FM with small exchange splitting energies (figures 10 (e) and (f)). Therefore we did not consider the possibility of SC in AlNCr and GaNCr. It is worth noting that of ZnNCr locates very close to a DOS peak, which leads to large and suggests a sizeable EPC.

ZnNCr AlNCr GaNCr SnNCr
2.81 3.53 3.08 3.01
0.76 1.09 1.01 1.29
Table 3: Calculated (states/eV/spin) and Stoner criteria of ZnNCr, AlNCr, GaNCr, and SnNCr.
Figure 10: Left panel: DOS of (a) ZnNCr, (b) AlNCr, (c) GaNCr, and (d) SnNCr in NM state. Right panel: DOS of (e) AlNCr, (f) GaNCr, and (g) SnNCr in FM state.

We calculated the lattice dynamics and EPC properties of MgCNi, AlCCr, GaCCr, and ZnNCr. For reliability, we tested different exchange-correlation potentials and calculation parameters. The results are coincide with each other. The calculated phonon dispersion curves and the corresponding atom-projected phonon DOS are shown in figure 11. The ideal antiperovskite in cubic structure (Pmm) with five atoms per unit cell presents fifteen phonon modes including three acoustic and twelve optical modes. The highest three optical branches resulting mainly from the lighter C/N atom vibrations are well separated from the other phonon branches. The phonon modes in low-frequency region come mainly from the vibrations of Cr/Ni atoms with partial contribution of A and C/N vibrations.

Figure 11: Phonon dispersions and phonon DOS of (a) MgCNi, (b) AlCCr, (c) GaCCr, (d) ZnNCr. The phonon dispersions are decorated with symbols, proportional to the partial EPC strength .
Figure 12: Schematic eigen displacements of zone-centre optical phonon modes in AXM. All phonon modes are infrared active.

Earlier calculations suggested lattice instabilities existing in MgCNi Ignatov (); Heid (); Jha-PRB (); HMTUTU (), which seem to be ruled out by the recent experimental and theoretical reports Hong-phonon-singlecrystal (); Jha-mgcni3phonon (). According to our calculation, no imaginary frequency was found in MgCNi, and the result is similar to the experimental one Hong-phonon-singlecrystal (). Soft longitudinal acoustic (LA) modes at M and R points are reproduced. Between X and R point, transverse acoustic (TA) mode of MgCNi is significantly softened and very close to instability. In previous calculation by Tütüncü et al. HMTUTU (), imaginary frequency exists just in the same -space path. Unfortunately, there are no existing experimental data about the phonon properties in such place. Additionally, in many previous calculations Heid (); HMTUTU (); Ignatov (), strong softening or imaginary frequency is shown between and R points. Our calculation reproduces such softening. However, experimental result only shows very small hints of the softening of TA mode between and R points Hong-phonon-singlecrystal (). The differences between theoretical and experimental results may be due to the sample quality. As Heid et al. Heid () pointed out, the lattice defects may play an important role in stabilizing the real structure. Indeed, the stoichiometry of the reported single crystals are deficient (MgCNi and MgCNi), which may be the reason of the absence of such soft-phonon anomaly in the experimental result. Such phonon mode softening is considered as the key role in the SC mechanism of MgCNi Ignatov (); walte-rosner (); Dolgov (). In experiments, single crystals with better quality are needed to figure out such puzzling anomalies.

) )
MgCNi 4.26 5.21 17.01 8.28 1.34 115.77
AlCCr 4.87 8.57 21.84 5.48 0.60 291.51
GaCCr 4.19 5.62 21.63 4.44 0.78 253.91
ZnNCr 2.45 5.92 18.98 4.82 0.67 260.27
Table 4: Optical phonon frequencies (THz) at point, the calculated EPC strengths , and the logarithmically averaged phonon frequency (K).

For AlCCr, GaCCr, and ZnNCr, the absence of imaginary frequency suggests the dynamic stability of the considered crystal structures of the three compounds. The acoustic modes are harder than those of MgCNi, and no modes are close to instability. The optical phonons at point belong to the following irreducible representations: (see figure 12), which are infrared (IR) active (table 4). The C/N related mode and mode of ZnNCr are softer than those of AlCCr and GaCCr maybe due to the larger atomic mass of nitrogen. We did not observe the significant softening of mode that reported by Tütüncü et al. in RhNCr and GaNCr RhNCr3 (); GaNCr3-sc ().

The calculated Eliashberg functions of MgCNi, AlCCr, GaCCr, and ZnNCr are plotted in figure 13 according to the below formula:

(1)

where are phonon frequencies, electronic energies, and matrix elements. The total EPC strength is

(2)

The calculated are visualized as red circles in figure 11. For MgCNi, the absence of imaginary frequency allows the direct calculation of the quantitative EPC contribution details from the lowest acoustic mode. Obviously for MgCNi the EPC originates mainly from acoustic phonon modes softening. For AlCCr, GaCCr, and ZnNCr, optical modes are playing an important role. The EPC distributes throughout some low-frequency phonon modes. One can note that a larger always exists at the frequencies at which large Cr-phonon DOS present. At the zone center, the and modes mainly contribute to EPC. For the two modes, Cr atoms vibrate strongly against each other (figure 12). Such vibrations can make large change in the overlap of orbitals between neighbouring Cr atoms, leading to strong coupling. Comparing the EPC strength from different phonon modes of GaCCr and ZnNCr, it can be found that the softening of mode can strongly enhance .

Figure 13: Eliashberg functions (left) and frequency-dependent EPC strength (right) of (a) MgCNi, (b) AlCCr, (c) GaCCr, and (d) ZnNCr.

The integrated EPC strengths are calculated using equation (2), and are plotted in figure 13. The EPC comes mainly from the peaks at low frequencies, which are mostly related to the vibrations of Ni/Cr atoms. For the peaks at high frequencies related to the vibrations of C/N atoms, their contributions to are less than 6%.

The calculated of MgCNi is 1.34, implying very strong EPC. However, the calculated of AlCCr, GaCCr, and ZnNCr are less than 1.0 and about (table 4), implying moderate EPC. The difference of for AXCr can be described qualitatively using Hopfield expression

(3)

where is mean square EPC matrix element averaged over Fermi surface, is the ion mass, and is the average squared phonon frequency. The higher and the lower phonon frequency make GaCCr has the larger .

Figure 14: (a) Variation of with (purely static pair breaking); (b) Variation of with (electron-paramagnon coupling).

To calculate , we used the Allen-Dynes equation mcmillan1968transition (); Dynes (); Allen-dynes ()

(4)

where is Coulomb pseudopotential and the logarithmically averaged characteristic phonon frequency is defined as

(5)

At the absence of SF, using a typical , we can get with the values of 11.82, 6.67, 11.29, and 8.23 K for MgCNi, AlCCr, GaCCr, and ZnNCr, respectively. According to the experimental results of MgCNi single crystals Lee-AM (); Lee-jpcm (); Pribulova (); Diener (); Jang (); Gordon-singlecrystal (); Hong-phonon-singlecrystal (), the observed is around 7 K. It seems that our calculation overestimates of MgCNi. Therefore we need to consider the influence of SF in the system.

We firstly considered the purely static pair breaking due to SF by varying . In figure 14 (a), one can note that the increasing significantly depresses . As around 7 K, we can get . Such a value is smaller than the previous derivations of Ignatov () and walte-rosner (), but still larger than the typical values for the absence of SF.

It is better to discuss the influence of SF in terms of electron-paramagnon coupling strength Ignatov (). In that case, the effective coupling strength should be . The effective mass of the carriers should be enhanced by the factor . And equation (4) shound be changed as Dolgov (); Oritenzi-Boeri ()

(6)

Figure 14 (b) shows the calculated using equation (6) with different (here the Coulomb pseudopotential is fixed to the typical value ). When is around 7 K, we can get . Although the obtained parameter is small, it still implies that SC in the system is partially suppressed by depairing effect from SF walte-rosner (); Dolgov (). The influence of SF on of AlCCr, GaCCr, and ZnNCr is also present in figure 14. If we consider the same SF influence as in MgCNi, using equation (4) with and , we can get , 3.11, and 1.40 K for AlCCr, GaCCr, and ZnNCr, respectively; using equation (6) with and , we can get , 3.52, and 1.69 K for AlCCr, GaCCr, and ZnNCr, respectively.

Let us look back at the electronic structures of AlCCr, GaCCr, and ZnNCr. The locates between two DOS peaks, which suggests in the system both hole and electron doping can enhance the SF and lead to a transition from SC to magnetic instability. Considering it has not been successful so far to investigate such transition in doped antiperovskites such as Mg(A)CNi due to the difficulty in experimental preparation of samples, AXCr may be good candidates to figure out the relation between SC and magnetism in antiperovskites.

iii.4 Other potential superconducting AXM

Since the discovery of SC in MgCNi, researchers have made great efforts to explore other transition-metal based antipervoskite superconductor Wiendlocha-InBSc3 (); Wiendlocha-ABSc3 (); Wiendlocha-ANCr3 (); RhNCr3 (); GaNCr3-sc (); Schaak (). The observed superconducting trace at 4.5 K found in InBSc is encouraging Wiendlocha-InBSc3 (). Theoretically, InBSc is close to weak FM and with an EPC superconducting mechanism Wiendlocha-InBSc3 (); Wiendlocha-ABSc3 (). One should believe the Ni-based antiperovskite superconductor are not alone and other superconducting antiperovskites may be hidden behind them.

Figure 15: DOS near of (a) SiCFe and (b) AlCCo.

Indeed, our magnetic phase diagram shows that some AXSc should be very close to FM, which may potentially be superconducting. There are also some other antiperovskite compounds close to FM, such as AXV, for which the cubic phase has not been successfully prepared so far. Here we present two potential superconducting parent materials ACFe (A = Si, Ge, etc.) and ACCo (A = Al, Ga, etc.). The DOS near of SiCFe and AlCCo are plotted in figure 15. One can notice that the of the two compounds just locates at a DOS valley. Thus both electron and hole doping can move to the DOS peaks nearby, and largely enhance to yield strong EPC. Therefore, doped ACCo may be new Co-based superconductors besides NaCoOHO NaCoO2-SC-found (). And doped ACFe may be new Fe-based superconductors.

As we know, the role of EPC in the Fe-based superconductors is still puzzling. For instance, EPC mechanism can get a reasonable of the hcp iron under pressure, but can not explain the rapid disappearance of SC above 30 GPa HCP-iron-nature (); mazin-hcpiron (); Bose-hcpiron (). For the iron pnictide superconductors kamihara_iron-based_2008 (), Boeri et al. Boeri-PRL2008 (); Boeri-Physica C2009 () and Mazin et al. Mazin-PRL2008 () pointed out that the EPC in the system is intrinsically weak, but can be enhanced strongly by magnetism Boeri-Mazin-PRB2008 (). Although EPC is still not enough to explain the high critical temperature, it is strong enough to have a non-negligible effect on SC. On the other hand, in the similar system of nickel pnictide superconductors, it seems the EPC plays the main role Boeri-Physica C2009 (). One may connect nickel pnictide superconductors with MgCNi by the similar EPC mechanism. The potential supeconductivity in doped ACFe may also help to figure out the superconducting mechanism, which needs to be futher confirmed in experimental and theoretical works.

Iv Conclutions

In this work, we theoretically investigated the electronic structure, magnetic properties, and lattice dynamics of the transition-metal based antiperovskite compounds AXM. Based on the analysis of the doping effect in AXM, we drew the magnetic phase diagram of ACM. We suggested that superconducting antiperovskites can be found in the NM area but very close to FM boundary. In order to prove the deduction, we investigated a series of Cr-based antiperovskite AXCr (X=C, N). The results indicate that AlCCr, GaCCr, and ZnNCr are of NM ground state but very close to FM instability. Due to the large , these compounds have sizeable EPC. We calculated the phonon spectra and EPC of MgCNi, AlCCr, GaCCr, and ZnNCr. Our results confirm the strong EPC in MgCNi, and show that AlCCr, GaCCr, and ZnNCr are moderate coupling BCS superconductors. Such compounds may be good candidates to figure out the role of SF. Moreover, some potential new antiperovskite Co-based and Fe-based superconductors are suggested.

Up to date, there is no definite evidence of SF in MgCNi single crystals Lee-jpcm (). Since such single crystals are not stoichiometric, the interplay between SC and magnetism are still puzzling. Our phase diagram and predictions could offer new route to figure out the issue. In experiments one can try to prepare such potential antiperovskite superconductors we predicted. Furthermore, by doping we can control the physical properties and may observe the magnetic-superconducting transition through quantum critical point. We hope our phase diagram and predictions can help to explore more transition-metal based antiperovskite superconductors and figure out the relation between SC and magnetism in the system.

Acknowledgements.
This work was supported by the National Key Basic Research under Contract No. 2011CBA00111, and the National Nature Science Foundation of China under Contract Nos. 51171177, 11304320, 11274311, 11174295, and U1232139. The calculations were partially performed at the Center for Computational Science, CASHIPS.

References

  • (1) Onnes H K 1911 Comm. Phys. Lab. Univ. Leiden 122 124
  • (2) Cooper L N 1956 Phys. Rev. 104 1189
  • (3) Bardeen J, Cooper L N, and Schrieffer J R 1957 Phys. Rev. 106 162
  • (4) Bardeen J, Cooper L N, and Schrieffer J R 1957 Phys. Rev. 108 1175
  • (5) Bednorz J G and Müller K A 1986 Z. Phys. B: Condens. Matter 64 189
  • (6) Wu M K, Ashburn J R, Torng C J, Hor P H, and Meng R L 1987 Phys. Rev. Lett. 58 908
  • (7) Shimizu K, Kimura T, Furomoto S, Takeda K, Kontani K, Onuki Y, and Amaya K 2001 Nature 412 316
  • (8) Kamihara Y, Watanabe T, Hirano M, and Hosono H 2008 J. Am. Chem. Soc. 130 3296
  • (9) Maeno Y, Hashimoto H, Yoshida K, Nishizaki S, Fujita T, Bednorz J G, and Lichtenberg F 1994 Nature 372 532
  • (10) Takada K, Sakurai H, Takayama-Muromachi E, Izumi F, Dilanian R A, and Sasaki T 2003 Nature 422 53
  • (11) He T, Huang Q, Ramirez A P, Wang Y, Regan K A, Rogado N, Hayward M A, Haas M K, Slusky J S, Inumara K, Zandbergen H W, Ong N P, and Cava R J 2001 Nature 411 54
  • (12) Rosner H, Weht R, Johannes M D, Pickett W E, and Tosatti E 2001 Phys. Rev. Lett. 88, 027001
  • (13) Singh D J and Mazin I I 2001 Phys. Rev. B 64 140507(R)
  • (14) Shim J H, Kwon S K, and Min B I 2001 Phys. Rev. B 64 180510(R)
  • (15) Mollah S 2004 J. Phys.: Condens. Matter 16 R1237
  • (16) Lee H S, Jang D J, Lee H G, Lee S I, Choi S M, and Kim C J 2007 Adv. Mater. 19 1807
  • (17) Gordon R T, Zhigadlo N D, Weyeneth S, Katrych S, and Prozorov R 2013 Phys. Rev. B 87 094520
  • (18) Sieberer M, Mohn P, and Redinger J 2007 Phys. Rev. B 75 024431
  • (19) Shao D F, Lu W J, Lin J C, Tong P, Jian H B, and Sun Y P 2013 J. Appl. Phys. 113 023905
  • (20) Lee H S, Jang D J, Lee H G, Kang W, Cho M H, and Lee S I 2008 J. Phys.: Condens. Matter 20, 255222
  • (21) Pribulová Z, Kačmarčík J, Marcenat C, Szabó P, Klein T, Demuer A, Rodiere P, Jang D J, Lee H S, Lee S I, and Samuely P 2011 Phys. Rev. B 83 104511
  • (22) Diener P, Rodière P, Klein T, Marcenat C, Kacmarck J, Pribulova Z, Jang D J, Lee H S, Lee H G, and Lee S I 2009 Phys. Rev. B 79 220508(R)
  • (23) Jang D J, Lee H S, Lee H G, Cho M H, and Lee S I 2009 Phys. Rev. Lett. 103 047003
  • (24) Hong H, Upton M, Said A H, Lee H S, Jang D J, Lee S I, Xu R, and Chiang T C 2010 Phys. Rev. B 82 134535 (2010).
  • (25) Jha P K, Gupta S D, and Gupta S K 2012 AIP Advances 2 022120
  • (26) Tong P and Sun Y P 2012 Adv. Cond. Matter Phys. 2012 903239
  • (27) Loison C, Leithe-Jasper A, and Rosner H 2007 Phys. Rev. B 75 205135
  • (28) Fruchart D, Fruchart R, L’heritier P, Kanematsu K, Madar R, Misawa S, Nakamura Y, Webster P J, and Ziebeck K R A 1988 Alloys and Compounds of D-Elements With Main Group Elements (Berlin: Springer)
  • (29) Uehara M, Yamazaki T, Kôri T, Kashida T, Kimishima Y, and Hase I 2007 J. Phys. Soc. Jpn. 76 034714
  • (30) Uehara M, Uehara A, Kozawa K, Yamazaki T, and Kimishima Y 2010 Physica C 470S688
  • (31) Tong P, Wang B S, and Sun Y P 2013 Chin. Phys. B 22 067501
  • (32) Wiendlocha B, Tobola J, Kaprzyk S, Fruchart D, and Marcus J 2006 Phys. Status Solidi B 243 351
  • (33) Wiendlocha B, Tobola J, and Kaprzyk S 2006 Phys. Rev. B 73 134522
  • (34) Wiendlocha B, Tobola J, Kaprzyk S, and Fruchart D 2007 J. Alloys Compd. 442 289
  • (35) Tütüncü H M and Srivastava G P 2012 J. Appl. Phys. 112 093914
  • (36) Tütüncü H M and Srivastava G P 2013 J. Appl. Phys. 114 053905
  • (37) Blöchl P E 1994 Phys. Rev. B 50 17953
  • (38) Torrent M, Jollet F, Bottin F, Zérah G, and Gonze X 2008 Comp. Mater. Sci. 42 337
  • (39) Gonze X, Beuken J M, Caracas R, Detraux F, Fuchs M, Rignanese G M, Sindic L, Verstraete M, Zerah G, Jollet F, et al. 2002 Comp. Mater. Sci. 25 478
  • (40) Gonze X, Amadon B, Anglade P M, Beuken J M, Bottin F, Boulanger P, Bruneval F, Caliste D, Caracas R, Cote M, et al. 2009 Comput. Phys. Comm. 180 2582
  • (41) Gonze X, Rignanese G M, Verstraete M, Beuken J M, Pouillon Y, Caracas R, Jollet F, Torrent M, Zerah G, Mikami M, et al. 2005 Z. Kristallogr. 220 558
  • (42) Monkhorst H J and Pack J D 1976 Phys. Rev. B 13 5188
  • (43) Baroni S, de Gironcoli S, Dal Corso A, and Giannozzi P 2001 Rev. Mod. Phys. 73 515
  • (44) Vanderbilt D 1990 Phys. Rev. B 41 7892
  • (45) Giannozzi P, et al. 2009 J. Phys.: Condens. Matter 21 395502
  • (46) Perdew J P, Burke K, and Ernzerhof M 1996 Phys. Rev. Lett. 77 3865
  • (47) Shao D F, Lu W J, Lin S, Tong P, and Sun Y P 2013 Adv. Condens. Matter. Phys. 2013 136274
  • (48) Ignatov A Y, Savrasov S Y, and Tyson T A 2003 Phys. Rev. B 68 220504(R)
  • (49) Heid R, Renker B, Schober H, Adelmann P, Ernst D, and Bohnen K P 2004 Phys. Rev. B 69 092511
  • (50) Jha P K 2005 Phys. Rev. B 72 214502
  • (51) Tütüncü H M and Srivastava G P 2006 J. Phys.: Condens. Matter 18 11089
  • (52) Wälte A, Fuchs G, Müller K H, Handstein A, Nenkov K, Narozhnyi V N, Drechsler S L, Shulga S, Schultz L, and Rosner H 2004 Phys. Rev. B 70 174503
  • (53) Dolgov O V, Golubov A A, Mazin I I and Maksimov E G 2008 J. Phys.: Condens. Matter 20 434226
  • (54) McMillan W L 1968 Phys. Rev. 167 331
  • (55) Dynes R 1972 Solid State Commun. 10 615
  • (56) Allen P B and Dynes R C 1975 Phys. Rev. B 12 905
  • (57) Ortenzi L, Biermann S, Andersen O K, Mazin I I , and Boeri L 2011 Phys. Rev. B 83 100505(R)
  • (58) Schaak R E, Avdeev M, Lee W L, Lawes G, Zandbergen H W, Jorgensen J D, Ong N P, Ramirez A P, Cava R J 2004 J. Solid State Chem. 177 1244
  • (59) Mazin I I, Papaconstantopoulos D A, and Mehl M J 2002 Phys. Rev. B 65 100511(R)
  • (60) Bose S K, Dolgov O V, Kortus J, Jepsen O, and Andersen O K 2003 Phys. Rev. B 67 214518
  • (61) Boeri L, Dolgov O V, and Golubov A A 2008 Phys. Rev. Lett. 101 026403
  • (62) Boeri L, Dolgov O V, and Golubov A A 2009 Physica C 469 628
  • (63) Mazin I I, Singh D J, Johannes M D, and Du M H 2008 Phys. Rev. Lett. 101 057003
  • (64) Boeri L, Calandra M, Mazin I I, Dolgov O V, and Mauri F 2010 Phys. Rev. B 82 020506(R)
Comments 0
Request Comment
You are adding the first comment!
How to quickly get a good reply:
  • Give credit where it’s due by listing out the positive aspects of a paper before getting into which changes should be made.
  • Be specific in your critique, and provide supporting evidence with appropriate references to substantiate general statements.
  • Your comment should inspire ideas to flow and help the author improves the paper.

The better we are at sharing our knowledge with each other, the faster we move forward.
""
The feedback must be of minimum 40 characters and the title a minimum of 5 characters
   
Add comment
Cancel
Loading ...
169176
This is a comment super asjknd jkasnjk adsnkj
Upvote
Downvote
""
The feedback must be of minumum 40 characters
The feedback must be of minumum 40 characters
Submit
Cancel

You are asking your first question!
How to quickly get a good answer:
  • Keep your question short and to the point
  • Check for grammar or spelling errors.
  • Phrase it like a question
Test
Test description