Composition-dependent magnetic response properties of Mn{}_{1-x}Fe{}_{x}Ge alloys

Composition-dependent magnetic response properties of MnFeGe alloys

S. Mankovsky, S. Wimmer, S. Polesya, and H. Ebert Dept. Chemie/Phys. Chemie, LMU Munich, Butenandtstrasse 11, D-81377 Munich, Germany
July 30, 2019

The composition-dependent behavior of the Dzyaloshinskii-Moriya interaction (DMI), the spin-orbit torque (SOT), as well as anomalous and spin Hall conductivities of MnFeGe alloys have been investigated by first-principles calculations using the relativistic multiple scattering Korringa-Kohn-Rostoker (KKR) formalism. The component of the DMI exhibits a strong dependence on the Fe concentration, changing sign at in line with previous theoretical calculations as well as with experimental results demonstrating the change of spin helicity at . A corresponding behavior with a sign change at is predicted also for the Fermi sea contribution to the SOT, as this is closely related to the DMI. In the case of anomalous and spin Hall effects it is shown that the calculated Fermi sea contributions are rather small and the composition-dependent behavior of these effects are determined mainly by the electronic states at the Fermi level. The spin-orbit-induced scattering mechanisms responsible for both these effects suggest a common origin of the minimum of the AHE and the sign change of the SHE conductivities.

71.15.-m,71.55.Ak, 75.30.Ds
preprint: APS/123-QED

I Introduction

During the last decade Skyrmionic magnetic materials have moved into the focus of scientific interest because their unique properties hold promises for various applications in magnetic storage and spintronic devices Kanazawa et al. (2017). The key role for the formation of a Skyrmion magnetic texture is played by the Dzyaloshinskii-Morirya interaction (DMI) Dzyaloshinsky (1958); Moriya (1960). Its competition with the isotropic exchange interaction, magnetic anisotropy, and the Zeeman interaction in the presence of an external magnetic field determines the size of Skyrmions and the region of stability in the corresponding phase diagram. Another important characteristic feature of Skyrmions is their helicity (i.e., the spin spiraling direction), which is determined by the orientation of the involved Dzyaloshinskii-Morirya interaction vectors and can be exploited as an additional degree of freedom for the manipulation of Skyrmions Díaz and Troncoso (2016); Taguchi et al. (2001); Bruno et al. (2004). The correlation between the Skyrmion helicity and crystal chirality has been already discussed in the literature Ishida et al. (1985); Dyadkin et al. (2011). Recent experiments have demonstrated in addition a change of the Skyrmion helicity with the chemical composition in the case of B20 alloys Shibata et al. (2013); Grigoriev et al. (2014) while the crystal chirality was unaltered. This finding opens an alternative possibility for DMI engineering in order to manipulate the Skyrmion helicity.

This holds particularly true for the MnFeGe alloy system which is in the center of interest for the present investigation. Experimentally, it was found Shibata et al. (2013); Grigoriev et al. (2013) that the size of Skyrmions in this material can be tuned by changing the Fe concentration, reaching a maximum at  Grigoriev et al. (2013), i.e., at the concentration when the Skyrmion helicity changes sign without a change of the crystal chirality. This behavior was investigated theoretically Gayles et al. (2015); Koretsune et al. (2015) via first-principles calculations of the DMI and analyzing the details of the electronic structure that may have an influence on it. Gayles et al. Gayles et al. (2015) have demonstrated that the sign of the DMI in MnFeGe can be explained by the relative positions in energy of the - and -states of Fe which change when the Fe concentration increases above . As a consequence a flip of the chirality of the magnetic texture occurs. Similar conclusions have been drawn by Koretsune et al. Koretsune et al. (2015). While these calculations have been done treating chemical disorder within the virtual crystal approximation (Ref. Gayles et al., 2015) or even employing the rigid band approximation (Ref. Koretsune et al., 2015), the present work is based on the coherent potential approximation (CPA) alloy theory, which should give more reliable results for the electronic structure of disordered alloys.

In addition we investigate the concentration dependence of response properties connected to spin-orbit coupling (SOC) in the presence of an applied electric field, i.e., the spin-orbit torque (SOT), the anomalous Hall effect (AHE) and the spin Hall effect (SHE), as these are important for practical applications. Especially, we focus on the SOT, expecting common features with the DMI according to recent findings by Freimuth et al. Freimuth et al. (2014).

The article is organised as follows. We start with theoretical details on the formalisms employed to calculate DMI parameters and linear response coefficients from first principles in section II. Results for the MnFeGe alloy system are presented and discussed in section III, subdivided into Dzyaloshinskii-Morirya interaction (III.1), spin-orbit torque (III.2), anomalous and spin Hall conductivity (III.3), and symmetry considerations (III.4). We conclude with a brief summary in (IV). Additional derivations connected to the expressions in II are given in the Appendix V.

Ii Theoretical details

All calculations were performed using the fully relativistic Korringa–Kohn–Rostoker (KKR) Green function method SPR (2017); Ebert et al. (2011) within the framework of local spin density approximation (LSDA) to density functional theory (DFT) and the parametrization scheme for the exchange and correlation potential as given by Vosko et al. Vosko et al. (1980). A cutoff was used for the angular momentum expansion of the Green function. The chemical disorder was treated within the coherent potential approximation (CPA) alloy theory Soven (1967); Velický (1969).

In order to investigate the composition dependent behavior of the Skyrmion size and helicity observed in experiment, we have calculated the element of the micromagnetic DMI tensor as a function of Fe concentration . As it was demonstrated previously Mankovsky and Ebert (2017), this quantity can be calculated in two different ways. Either by performing a direct evaluation of the expression


with the overlap integrals and the matrix elements of the torque operator Ebert and Mankovsky (2009)


or by using the interatomic interactions


that are calculated in an analogous way Mankovsky and Ebert (2017).

The current-induced torkance Wimmer et al. (2016) and the anomalous Lowitzer et al. (2010) and spin Lowitzer et al. (2011) Hall conductivities were calculated within the Kubo linear response formalism using the expression


where and are Fermi surface and Fermi sea contributions, respectively. The operator representing in all three cases the perturbation is the electric current density operator . For the calculations of the anomalous Hall conductivity one has for the response , for the spin Hall conductivity with the relativistic spin-polarization operator Bargmann and Wigner (1948); Vernes et al. (2007), while for the calculations of the spin-orbit torkances the torque operator has to be used. Additional calculations for the Fermi sea torkance have been performed following the relationship between this quantity and the DMI parameters as suggested by Freimuth et al. Freimuth et al. (2014). In line with Eq. (1), these calculations were based on the expression


which obviously differs, apart from prefactors, from Eq. (1) only by the weighting factor . Both expressions for should be equivalent, as can be demonstrated for the particular case of a translationally invariant system. In this case the relationship between Eq. (5) and the Fermi sea term in Eq. (4) can be established using the expression for the group velocity suggested by Shilkova and Shirokovskii discussed below Shirokovskii et al. (1986); Shilkova and Shirokovskii (1988); Gradhand et al. (2011) (see V).

Alternatively, we have


with the interatomic torkance terms


that are obtained in analogy to the interatomic DMI parameters.

Iii Results and discussion

iii.1 Dzyaloshinskii-Moriya interaction

In the following we first focus on the behavior of the DMI in MnFeGe as a function of Fe concentration . The dependence of the DMI parameter on is plotted in Fig. 1 (a) in comparison with available theoretical results from other groups Gayles et al. (2015); Kikuchi et al. (2016). The results calculated using an explicit expression for derived recently Mankovsky and Ebert (2017) are given by open diamonds, while those based on the interatomic interaction parameters are given by solid circles. Although the latter value has contributions only from the , and interatomic DMI pair interaction terms, both results are in very good agreement with each other. They also fit reasonably well to the theoretical results by other groups shown by dashed Gayles et al. (2015) and dashed-dotted Kikuchi et al. (2016) lines. The deviations between these and the present work are most likely caused by the different approach used to treat the chemical disorder in the alloy. As it was mentioned above, the CPA alloy theory was used in the present work, while the previous results Gayles et al. (2015); Kikuchi et al. (2016) have been obtained using the so-called virtual crystal approximation. As it follows from Fig. 1 (a), changes sign at , in line with the experimental observation Grigoriev et al. (2013). A very similar concentration dependence is also observed for the component (open squares). The deviation from , that is allowed by crystal symmetry (see subsection III.4), is itself a function of but small throughout. From the element-projected plots shown in Fig. 1(b) one can see that and have their maxima at a different Fe concentration, i.e., at and for Fe and Mn, respectively. As one notes, changes its sign at if increases, while does not change sign.

(a)  (b)

Figure 1: (a) Results for in MnFeGe calculated using Eq. (3) (circles) and for (diamonds) and (empty squares) calculated using using Eq. (1) in comparison with the results of other calculations Gayles et al. (2015) (filled squares) and Kikuchi et al. (2016) (triangles). (b) The element-resolved Dzyaloshinskii-Moriya interaction in MnFeGe (triangles up) and (triangles down). The total function is again shown as circles as in (a).

The observed concentration dependence of the DMI was associated in the literature Gayles et al. (2015); Koretsune et al. (2015); Kikuchi et al. (2016) with specific features of the electronic structure and their modification with the Fe concentration . Fig. 2 shows corresponding results of electronic structure calculations making use of the CPA alloy theory, i.e., the spin- and element-resolved density of states (DOS) on Mn (a) and Fe (b) sites in MnFeGe for the three different concentrations , and .

(a)  (b)

Figure 2: The spin- and element-resolved DOS on Mn (a) and Fe (b) atoms in MnFeGe for and .

(a)  (b)  (c)  (d)

Figure 3: The spin-resolved Bloch spectral function in MnFeGe and MnFeGe for minority- (a) and (b) and majority-spin (c) and (d) states, respectively.

As one can see in the bottom panels, the occupied majority-spin states of Mn and Fe are very close to each other and hardly depend on the Fe concentration. Obviously, chemical disorder has only a weak impact for this spin subsystem, leading to a rather weak disorder-induced smearing of the energy bands. This can be seen as well in Fig. 3 (c) and (d), that show the Bloch spectral function for majority-spin states in MnFeGe and MnFeGe, respectively. On the other hand, the different exchange splitting for the electronic states on Mn and Fe sites leads to different positions for their minority-spin states and as a consequence to a pronounced disorder-induced smearing of the energy bands for the disordered MnFeGe alloys. Again this can be seen in the upper panels of Fig. 2 (a) and (b), as well as in Fig. 3 (a) and (b), showing the Bloch spectral function for minority-spin states in case of and , respectively. Moreover, the exchange splitting for Fe and Mn both decreases upon an increase of the Fe concentration. As a consequence, the Fe and Mn spin magnetic moments decrease simultaneously as can be seen in Fig. 4.

Fig. 2 indicates that the concentration-dependent modification of the electronic structure has two-fold character. First, the Fe minority-spin states move down in energy from their position above the Fermi level at small Fe concentration (, solid line in Fig. 2(b)) to a position below the Fermi energy at high Fe content (, dashed line in Fig. 2(b)). Additionally, a weak shift of the majority-spin -states of Fe towards the Fermi energy can be observed. This behavior, as discussed previously Koretsune et al. (2015); Gayles et al. (2015), leads to a sign change of the Fe-projected as well as the total DMI at . At the same time Fig. 2 (a) shows that the minority-spin -states of Mn stay essentially unoccupied over the whole concentration range. As a consequence, does not exhibit any sign changes. As the positions of the element-projected minority-spin states of Fe and Mn are rather different (see Fig. 2), the increase of the contributions of minority-spin Fe states with increasing in parallel with the decreasing contribution of corresponding Mn states leads for the alloy system to an apparent shift of the electronic energy bands. According to Refs. Gayles et al., 2015 and Koretsune et al., 2015 this should also lead to a sign change of the DMI parameter.

Finally, it is worth to mention that there are different trends in the behavior of the DMI parameter in the Mn-rich limit when comparing theoretical results (both, present and previous) with experimental data Grigoriev et al. (2013). As it was remarked by Gayles et al. Gayles et al. (2015) the origin of this difference is not clear and the authors suggest certain mechanisms to be responsible for that. We would like to add here that the micromagnetic DMI components are the results of a summation of pair interactions over all neighbours. Although the Mn–Mn DMI have in general even larger magnitude than the Fe–Fe interactions, their summation leads to a small total DMI due to their oscillating behavior as a function of distance. This leads in the case of MnGe to a significant compensation of all contributions. For a more realistic description of the experimental situation at finite temperature, involving in particular non-collinear spin texture, Monte Carlo simulations based on atomistic spin models might be important Polesya et al. (2014).

Figure 4: Spin magnetic moments of Mn (circles) and Fe (squares) in MnFeGe alloy, and the average magnetic moment per site (diamonds). Experimental results of Kanazawa et al. Kanazawa et al. (2016) are shown as green triangles.

iii.2 Spin-orbit torque

The torkance tensor element representing the spin-orbit torque (SOT) calculated for MnFeGe within the Kubo formalism Wimmer et al. (2016) is represented in Fig. 5 (a) by filled squares. In contrast to , it changes sign three times when increases. However, one has to note that this behavior is caused by two contributions to the torkance, showing a quite different concentration dependence: the Fermi surface contribution from electronic states at the Fermi energy (open circles) and the Fermi sea contribution due to all states below the Fermi energy (filled circles). Both contributions vary non-monotonously with and both change sign at , having however an opposite slope in the vicinity of this point. As a consequence, their combination leads to a partial cancellation in the total torkance that has a completely different concentration dependence when compared to the individual contributions.

Despite similarities in the behavior of and the Fermi sea torkance , they change sign at different values (0.8 and 0.5, respectively). To make a more detailed comparison, we calculate the Fermi sea torkance using the expressions in Eqs. (5) and (6). The results are plotted in Fig. 5 (b) (triangles and squares, respectively) in comparison with the results based on the linear response expression Eq. (4) (circles), demonstrating good agreement between all three types of calculations. The difference in the concentrations when the and functions change sign can obviously be attributed to the weighting factor in the expression for the DMI Mankovsky and Ebert (2017) which results in a different energy region for the dominating contributions to the function when compared to the torkance term . This is demonstrated in Fig. 6 that gives the energy-resolved DMI parameter and the Fermi sea torkance for two different Fe concentrations. In addition, note that the contributions to associated with the alloy components Mn and Fe, shown in Fig. 5 (b) by dashed and dash-dotted curves, change sign at different concentrations . Nevertheless, because of the strong exchange interaction between these two components located on the same sublattice, one has to discuss the component-averaged torkance when considering the SOT in the alloy.

(a)  (b)

Figure 5: (a) Total torkance per unit cell (solid squares) as well as its Fermi surface (empty circles) and Fermi sea (filled circles) contributions in MnFeGe calculated via the Kubo-Bastin formalism (Eq. (4)). (b) Comparison of the Fermi sea contribution to the torkance calculated via Eq. (4) (circles) with results obtained using the expressions Eq. (5) (triangles) and Eq. (6) (squares).

Finally, considering the Fermi surface and Fermi sea contributions to the SOT separately in the pure limits, i.e., for the MnGe and FeGe compounds (see Fig. 5 (a)) one finds a different sign for these contributions. This allows to conclude that the intrinsic torkance is mainly responsible for the sign change of the SOT when the Fe concentration changes from 0 to 1. It is determined by the characteristics of the electronic structure discussed above. On the other hand, in the case of disordered MnFeGe alloys the extrinsic contributions to the SOT cannot be completely neglected. Although small and only relevant at the Fermi surface, they are responsible together with the intrinsic contribution for the concentration dependence of the SOT and jointly determine the exact composition at which the torkance changes its sign.

Figure 6: Energy dependence of the DMI parameter (upper panel) and the torkance (lower panel) in MnFeGe (circles) and MnFeGe (squares). Integrated up to the Fermi energy , these functions give and .

iii.3 Anomalous and spin Hall conductivity

In order to have a more complete picture of the SOC-induced response to an external electric field in MnFeGe, we will briefly discuss corresponding results for the transport properties anomalous Hall effect (AHE) and spin-Hall effect (SHE) (see, e.g., Refs. Nagaosa et al. (2010) and Sinova et al. (2015), respectively). As the current-induced spin-orbit torkance, these phenomena are caused by a SOC-induced spin asymmetry in the electron scattering. Because of this one can expect certain correlations concerning their composition-dependent behavior.

(a)  (b)

Figure 7: (a) Anomalous Hall conductivity calculated for MnFeGe via the CPA-Kubo-Bastin formalism (circles), compared to calculations using the Berry curvature approach and the Virtual Crystal Approximation Gayles et al. (2015) (triangle) as well as to low-temperature experimental data (squares) Kanazawa et al. (2016). (b) Anomalous Hall coefficient calculated via the Kubo-Bastin equation (circles) compared to experimental data at 50 K (squares) Kanazawa et al. (2016).

For the investigated alloy system MnFeGe the anomalous Hall conductivity (AHC) calculated within the Kubo-Bastin formalism (Eq. (4)) is given in Fig. 7 (a) as full circles. As can be seen, does not change sign going from MnGe to FeGe, in agreement with previous first-principles calculations Gayles et al. (2015) and experiment Kanazawa et al. (2016). Note that the chemical disorder is treated on fundamentally different levels in the two theoretical approaches. While the present work employs the Coherent Potential Approximation, the results of Ref. Gayles et al., 2015 are based on the Virtual Crystal Approximation. This difference should be mainly responsible for the deviations between the two sets of theory data visible in the upper panel of Fig. 7, which are most pronounced on the Fe-rich side of the concentration range where even the signs appears to differ. As will be shown later, this is however not due to the extrinsic or incoherent contributions. Unfortunately, reliable experimental data in this region could not be obtained because both, the Hall as well as the longitudinal resistivity are small under the experimental conditions Kanazawa et al. (2016).

Comparison of the anomalous Hall coefficient to the experimental results of Kanazawa et al. Kanazawa et al. (2016) in the lower panel of Fig. 7 shows good agreement for the Mn-rich side of the concentration range (except for pure MnGe, see below), while deviations on the Fe-rich side are quite large. Here one should note that the measurements were performed at 50 K while the calculations assume , meaning in particular perfect ferromagnetic order. As can be seen in Fig. 3 of Ref. Kanazawa et al., 2016 the temperature dependence of magnetization as well as anomalous Hall conductivity is quite substantial for MnGe and even more so for FeGe. As mentioned above for the anomalous Hall conductivity, the experimental uncertainty is in addition rather high in the pure Fe-limit. For a more detailed understanding of these discrepancies investigations including the effects of finite temperature, sample geometry, and non-collinear magnetic structure are necessary.

Having a closer look at the Kubo-Bastin equation, Eq. (4), one can decompose the full response coefficient into several contributions with distinct physical meaning. Most obviously, the two terms and differ in the absence or presence of contributions from occupied states below the Fermi level, i.e., these are the Fermi surface and Fermi sea terms, respectively. They are plotted in Fig. 8 (a) in red (Fermi surface) and blue (Fermi sea), further decomposed into on-site (surf and sea, crosses) and off-site (surf and sea, squares and triangles, respectively) contributions. For the latter results are shown once excluding (NV, empty symbols) and once including the so-called vertex corrections (VC, full symbols) arising from the difference in the product of configuration-averaged Green functions versus the configuration average of the product. These give rise to the so-called extrinsic or incoherent contribution and are connected to the scattering-in term of the Boltzmann equation Butler (1985).

Comparing now the various terms one first of all notices that on-site terms are large (note that they are scaled by a factor of (-)0.1), opposite in sign and almost identical in magnitude, leading to an almost perfect cancellation. Turning to the off-site terms one observes a similar concentration dependence and a dominance of the Fermi surface contribution, except for and at the Fe-rich side of the concentration range. This means that the anomalous Hall conductivity is dominated by the states at the Fermi level, in particular for intermediate concentrations. Obviously, already for this reason a clear correlation between anomalous Hall coefficient and DMI strength, as suggested by Kanazawa et al. Kanazawa et al. (2016), is not supported by our findings. Finally, the vertex corrections are, as observed before Turek et al. (2014); Ködderitzsch et al. (2015); Wimmer et al. (2016), only relevant for the Fermi surface term and in this system only noticeable in the dilute limits, particularly on the Fe-rich side. Note that, as discussed before, there the density of states at the Fermi level is largest and has predominantly -like character. Interestingly, the seemingly diverging behavior for is not caused by the extrinsic contribution Lowitzer et al. (2011).

As the same spin-dependent scattering mechanisms are responsible for the SHE and AHE, both, transverse spin and charge currents can be present in the FM ordered MnFeGe system. However, in contrast to the transverse spin conductivity shown in Fig. 8 (bottom) does change its sign at . Thus, the total transverse current should be dominated by opposite spin characters in these limits. Interestingly, the AHC has a minimum of its absolute value close to the Fe concentration corresponding to the sign change of the SHC. In fact the Fermi sea contributions to and as well as both on-site terms behave very similarly over the entire concentration range whereas the Fermi surface contributions agree only on the Mn-rich side up to the minimum or sign change, respectively.


Figure 8: Anomalous (a) and spin (b) Hall conductivities, and , respectively, as functions of in MnFeGe calculated via the Kubo-Bastin formalism. Fermi surface contributions are given in red, those from the Fermi sea in blue, and their sum in black. The superscripts 0 and 1 indicate on- and off-site terms. Results for the latter are shown ex- (NV) and including vertex corrections (VC).

The spin Hall conductivity of the MnFeGe alloy system presented in Fig. 8 (bottom) as a function of Fe concentration changes sign approximately at the same composition as the DMI parameter and, accordingly, also the torkance . However, one can again see a leading role of the Fermi surface contribution to the spin-Hall conductivity, in particular at the Fe-rich side after the sign change. This implies that the sign of the SHE conductivity is determined to a large extent by the character of the states at the Fermi energy and their spin-orbit coupling, that changes with concentration according to the discussion above. Note however, that in pure FeGe the Fermi surface and Fermi sea contributions are of equal magnitude but opposite sign, leading to their partial cancellation. Concerning the importance of the vertex corrections the spin Hall conductivity behaves again similar to the AHC, in as much as they are only present at the Fermi surface and negligible over the entire concentration range considered here – again apart from the Fe-rich limit.

A more detailed analysis of the anomalous and spin Hall conductivities in terms of underlying scattering mechanisms based on their scaling behavior w.r.t. to the longitudinal (charge) conductivity in the dilute limits has been so far precluded by the large numerical cost and is left for future work. Note also, that the anomalous and spin Hall conductivities in the present work were calculated for the FM structure. Introducing a chiral non-collinear spin texture, one can expect additional contributions from the topological anomalous Bruno et al. (2004) and spin Hall Yin et al. (2015) effects, most likely displaying different concentration-dependent features.

iii.4 Symmetry considerations

We conclude with a few remarks on magnetic symmetry and the corresponding shapes of the response tensors discussed above. The B20 structure of the MnFeGe alloy system has the (nonmagnetic) space group , for ferromagnetic order with magnetization along z (one of the axes) this leads to the magnetic space group (MSG) , the magnetic point group (MPG) , and finally the magnetic Laue group (MLG) (or in the convention of Ref. Kleiner, 1966). The corresponding symmetry-allowed tensor forms for electrical () and spin () conductivity Seemann et al. (2015)111Only given for polarization along z here, for x- and y-polarization see Ref. Seemann et al., 2015. and the current-induced torkance Wimmer et al. (2016) are




Note, that this is not the highest symmetric FM-ordered structure as for (along the 3-fold axes) one would have MSG , MPG and MLG , leading to the tensor shapes



Figure 9: Comparison of all non-zero torkance tensor elements as functions of in MnFeGe calculated via the Kubo-Bastin formalism. The diagonal elements and (left y scale) are given as black squares and red circles, respectively, the off-diagonal torkances (right y scale) and are given as blue up- and green down-facing triangles.

Fig. 9 shows all non-zero tensor elements of for as chosen in this work. Apparently, the deviations between the diagonal torkances and are negligibly small over the whole concentration range, the largest differences occur once more on the Fe-rich side. For the off-diagonal torkances holds as well with the above exception. Note, that these torkances in contrast to and only contain contributions from the Fermi surface, as discussed before Wimmer et al. (2016), and, as the diagonal elements, are dominated by the intrinsic contribution. Irrespective of the magnetic point group ( for or for ), the diagonal elements are even, while the off-diagonal ones are odd w.r.t. resversal of the magnetisation direction. The same applies to both the electrical and the spin conductivity tensors.

Iv Summary

To summarize, we have presented results of calculations for the and components of the DMI vector in the B20 MnFeGe alloys as a function of Fe concentration. The sign change of this quantity evidences the change of spin helicity at , in line with experimental results as well as with theoretical results obtained by other groups. Although the approach used in the present work is more appropriate for disordered systems when compared to those used in the previous investigations, all calculations demonstrate reasonable agreement, because of the virtual-crystal-like behavior of the majority spin states Gayles et al. (2015); Kikuchi et al. (2016). In addition, we have discussed the concentration dependence of the total spin-orbit torkance and its Fermi surface and Fermi sea contributions. It was shown that for all Fe concentrations both parts have the same order of magnitude but their sign is opposite, leading to a significant compensation. By using different approaches to calculate the Fermi sea contribution to the SOT its composition-dependent features in common with the DMI were discussed. In the case of the AHE and SHE the calculated Fermi sea contributions are rather small and the behavior of these effects as functions of composition are determined mainly by the electronic states at the Fermi level. The common SOC-induced mechanisms responsible for these effects, for the investigated concentration range () these are predominantly of intrinsic origin, result in the correlation of their dependence on the Fe concentration. This is demonstrated by the finding that the minimum of the AHE magnitude and the sign change of the SHC occur at approximately the same composition.

V Appendix

According to the suggestion by Shilkova and Shirokovskii Shirokovskii et al. (1986); Shilkova and Shirokovskii (1988), the electron group velocity can be represented by the expression


Here are the eigenvalues of the KKR matrix that are determined by solving the eigenvalue problem Gradhand et al. (2011)

and vanish at corresponding to zeros of the determinant . Here are the associated eigenvectors. With this one arrives at the expression


Finally, use is made of the relation for the group velocity Shirokovskii et al. (1986); Shilkova and Shirokovskii (1988)




where is the speed of light and is the vector of Dirac matrices, that represents the relativistic current operator . With this one finally arrives at the relationship between Eq. (5) and the Fermi sea term in Eq. (4).

Financial support by the DFG via SFB 689 (Spinphänomene in reduzierten Dimensionen) and SFB 1277 (Emergent Relativistic Effects in Condensed Matter - From Fundamental Aspects to Electronic Functionality) is gratefully acknowledged.


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