J. Cent. South Univ. (2016) 23: 2173-2181

DOI: 10.1007/s11771-016-3274-y

First-principles study on electronic structure, magnetic and dielectric properties of Cr-doped Fe₃C

YANG Jian-ping(杨建平), CHEN Jin(陈津), LI Wei(李伟), HAN Pei-de(韩培德), GUO Li-na(郭丽娜)

College of Materials Science and Engineering, Taiyuan University of Technology, Taiyuan 030024, China

Central South University Press and Springer-Verlag Berlin Heidelberg 2016

Abstract: The first-principles calculations were performed to investigate the electronic structure, magnetic and dielectric properties of Cr-doped Fe₃C, in comparison to those of pure Fe₃C and Cr₃C. The obtained results show that the thermodynamic stability of Cr- doped Fe₃C becomes weaker in terms of the larger formation enthalpy, on the contrary, the metallicity and covalency are found to strengthen to some extent. The magnetic moments of Fe₃C, Fe₁₁CrC₄(g), and Fe₁₁CrC₄(s) are respectively 21.36 μ_B/cell, 16.92 μ_B/cell, and 17.62 μ_B/cell, and in Fe₁₁CrC₄(g) and Fe₁₁CrC₄(s), the Fe of Wyckoff positions of 8d and 4c is substituted by Cr. The local magnetic moment of Cr at 8d site is larger than that at 4c site in the doped structure, which is opposite to that of Fe. In low frequency band, the permittivity follows the ranking of Fe₁₁CrC₄(s)>Cr₃C>Fe₁₁CrC₄(g)>Fe₃C. Once exceeding a certain frequency, the sequence will be broken. Besides the electron transition, the polarization of atoms also makes a contribution to the dielectric properties.

Key words: Cr-doped Fe₃C; electronic structure; magnetic properties; dielectric properties

1 Introduction

q-Fe₃C (cementite) as a kind of fundamental carbide in Fe-C alloy system is the most classical and important phase existing in white cast iron and various of carbon steels, which plays a critical role for the strength and applicability of materials [1-3]. Several intrinsic properties of Fe₃C-carbide have been studied by material metallurgy researchers. HALLSTEDT et al [4] reevaluated the Gibbs energy function of cementite from 0 K to 1000 K as well as the heat capacity using density functional theory (DFT). LV [5] calculated the mechanical, electronic and magnetic properties of ortho-Fe₃C and hexa-Fe₃C by first-principles method. In order to achieve a better mechanical performance for actual industrial demand, several alloying elements, primarily transition metals of Mn, Cr, Co, and Ni, generally are doped into the Fe₃C carbide, and these addition agent can affect the structure, characteristics, morphology and growth kinetics of the Fe₃C carbide. The previous groups have also investigated the electronic structure and formation enthalpy of (Fe, M)₃C (M=Cr/Mn/Co/Ni), finding that Cr/Mn/Co/Ni doping all can improve the stability of cementite [6-7]. On account of the significant anisotropy of Fe₃C as well as (Fe, M)₃C, the surface structure and relevant physical properties of them also have been addressed in the theoretical side [7-10]. Compared to other cementite-type alloys, Cr-doped cementite, namely (Fe, Cr)₃C, is the most common, extensively consisting of in sorts of stainless steel and other chrome steel. LV et al [6] and ZHOU [11] further studied the stability, magnetic property of (Fe, Cr)₃C with different positions and contents in Cr doping through first principle calculation and obtained the favourable results. Regrettably, the influence of single Cr atom doping in different lattice sites on the above properties and electronic structure is still unclear.

(Fe, Cr)₃C not only is being considered an important strengthening phase in steel alloy, but also still appears in metallurgical raw materials. In this work, it’s mainly indicated high-carbon ferrochrome (HCFC) studied by our groups. In the production of stainless steel, the decarburization of HCFC is regarded as the intermediate process, but it determines the yield and quality of stainless steel. Recently, the solid-phase decarburization of high-carbon ferrochrome powder (HCFCP) by microwave heating, instead of bulk materials derived from inevitably generating so-called skin-effect that intensively reflects microwave [12], has attracted major interest of researchers in the metallurgy fields in view of microwave showing simultaneous ordering of rapid warming, body heating, selective heating, especially no environmental pollution and easy for automatic control,importantly avoiding the generation of large amounts of toxic chromium slag [13]. As widely accepted by researchers, the dielectric properties of ferrochrome carbide in HCFCP can significantly take account for the temperature rising characteristic and reaction performance of HCFCP in the microwave field [14-15]. CHEN et al [14] discussed the intrinsic nature of (Cr, Fe)₇C₃, the main phase in HCFCP, based on density functional theory and indicated the importance of microstructure of (Cr, Fe)₇C₃ on microwave dielectric properties of HCFCP. Besides (Cr, Fe)₇C₃, CrFe also has been investigated to concern the magnetic property rather than dielectric properties as its remarkable metallicity, which contributes to microwave heating yet [16]. Unluckily as the unneglected phase in HCFC, the dielectric and magnetic properties of (Fe, Cr)₃C are detailedly unknown all the time.

In terms of the shortage of previous research about (Fe, Cr)₃C, the electronic structure, magnetic and dielectric properties of Cr-doped Fe₃C will be synthetically discussed in our present work to give a better support and instruction for the theoretical research and practical production in the fields of metallurgy and material. Considering the limit of Cr additive in most steel alloys as well as the relatively low Cr content in (Fe, Cr)₃C contained within HCFC, single Cr atom doping Fe₃C in different lattice sites, namely Fe₁₁CrC₄, will be dramaticlly studied compared with pure Fe₃C and Cr₃C in this paper.

2 Crystal structure and computational details

Since the orthorhombic structure is extensively concerned by academia as well as meets our experimental finding by X-ray scattering techniques, the space group of Fe₃C is determined as Pnma (S.G. No. 62). Every crystal cell includes four Fe₃C units, where eight (four) iron atoms are located in the ‘‘general’’ (‘‘special’’) sites, namely Wyckoff positions of 8d (4c), and four carbon atoms are in the interstices [6-11]. When the Fe atoms of Fe₃C in different sites are substituted by one Cr atom respectively, Fe₁₁CrC₄(g) and Fe₁₁CrC₄(s) (g and s, representing general and special) are obtained. It is noteworthy that the valence-electron configurations for Fe, Cr and C atoms are 3d⁶4s², 3p⁶3d⁵4s¹ and 2s²2p², respectively. Although the differences between Fe and Cr on atomic radius couldn’t be neglected, the ideal Cr-doped Fe₃C models for calculations are similar to the structure of Fe₃C after geometry optimization, as shown in Fig. 1.

All of the density-functional-theory (DFT) calculations were accomplished using the Cambridge Sequential Total Energy Pack-age (CASTEP) with ageneralized gradient approximation (GGA+U) [17] combining the Perdew–Wang function (PW91) [18], to deal with the exchange and correlation energy of electrons. The electron–ion interaction was described by the Vanderbilt ultrasoft pseudopotentials (USPPs) [19]. To ensure the validity and accuracy, the calculations were constructed with kinetic energy cutoff of 350.0 eV and a k-point grid of 5×4×6, using Monkhorst–Pack in the first irreducible Brillouin zone [6]. The crystal structures were fully relaxed with BFGS (Broydene- Fletchere-Goldarbe-Shanno) scheme, where both of the atomic positions and cell constants were optimized simultaneously [11]. As the ground states of Fe₃C and Fe₁₁CrC₄ are ferromagnetic, all of the calculations were carried out by spin polarized method. The total energy was well-converged to less than 2×10^-6 eV per atom and the forces were reduced to 0.05 eV/^-1 per atom.

Fig. 1 Constructed models: (The small blue balls, small red balls and big green balls respectively represent Fe(g) atoms, Fe(s) atoms and C atoms; The pink and orange balls represent Cr atoms substituting for Fe atoms in the “general” and “special” sites, respectively)

3 Results and discussion

3.1 Structural optimization and thermodynamic stability

The ground state properties of Fe₃C, Fe₁₁CrC₄(g), Fe₁₁CrC₄(s), and Cr₃C are obtained from its total energy, which is calculated as a function of volume. By a series of iterations until it is fitted to the Murnaghan equation of state [20], the equilibrium lattice constants are list in Table 1. To verify the accuracy and credibility of results in our calculation, the experimental data and some related theoretical calculations with different research methods are also listed in Table 1. Besides equilibrium lattice constant, cohesive energy and formation enthalpy of them are displayed in table as well, which are calculated by the equations shown in previous literature [11].

From Table 1, it can be seen the results calculated in our present work such as lattice parameters, E_tot, E_coh, and △_rH_m are in a good agreement with the experimental values and other theoretical predictions. Obviously our calculated method performs the rationality and reliability, and these results can give enough support to further predict the properties of Fe₃C-type carbides. While in Table 1, the negative △_rH_m of Fe₃C obtained by the local density approximation (LDA) method suggests an incorrect prediction for bulk thermodynamic stability of compounds, since it’s known widely that Fe₃C belongs to a sort of meta-stable structure. In addition, two types of Cr-doped carbide are both the meta-stable phases as well, and their greater △_rH_m values mean the lower stability than Fe₃C, which is stemed from more highlighted metallic anti-bonding that refers to the chemical bonds that have the negative overlap population [26] in Cr- doped Fe₃C as given in Table 3. With respect to Cr₃C, it reveals the best stability than other carbides with the following sequence of Cr₃C>Fe₃C>Fe₁₁CrC₄(g)>Fe₁₁CrC₄(s). It is however interesting that Cr₃C can be hardly discovered in nature, which may be derived from most other carbides in Cr-C system having the lower formation enthalpy than Cr₃C [25]. Comparing two types of Cr-doped Fe₃C, the volume of Fe₁₁CrC₄(s) is slightly larger than Fe₁₁CrC₄(g) on account of Cr atom in special site possessing high exposure beyond the surface.

3.2 Chemical bond and magnetic properties

The chemical bonds of above carbides are discussed and compared in this part. Figure 2 shows the partial densities of states (PDOS) of Fe₃C, Fe₁₁CrC₄(g), Fe₁₁CrC₄(s), and Cr₃C. Apparently, the PDOSs of these carbides all can be divided into three regions: the lowest valence band, the upper valence band and the conduction unoccupied states. For Fe₃C and Cr-doped Fe₃C, the lowest valence band ranging from -14 to -11.5 eV is mostly composed of orbits for C 2s and Fe(Cr) 4s; The upper valence band can be approximatively separated into two parts: The first one is ranging from -8 to about -5 eV, which is constituted with the hybridization of C 2p and Fe(Cr) 3d orbits, reflecting the feature of covalent; The second one, mainly formed by Fe(Cr) 3d orbits with a few C 2p orbits, is from -5 eV up to Fermi level. Moreover, 3d orbits of metal atoms also have the great contributions to the conduction band, especially those of up-spin in Cr atoms as well as down-spin of Fe atoms. When Fe is replaced by Cr, the changes of PDOS mainly occur in 3d orbits of Fe(Cr), implying the importance of 3d orbits for bonding. In spite of the PDOS of Cr₃C moving along the x-axis towards the higher energy, the better stability of Cr₃C is due to the energy of most electrons placed in s and p orbits of Cr atoms below -50 eV (Not shown in figures). Similarly, there also exists Cr 3d hybridization with C 2p in PDOS of Cr₃C. No energy gap near the Fermi level as well as the finite DOS at the Fermi level can be observed in all carbides, which indicates the metallic nature. Further, the metallicity (f_m) of four kinds of carbides can be estimated by [25]

      (1)

where n_m and n_e are thermal excited electrons and valence electron density of the cell unit respectively; k_B is the Boltzmann constant; T is the thermodynamic temperature; D_f is the DOS value of cell unit at the Fermi level; V_cell is the cell volume; and N is the total number of the valance electrons in the cell. The calculated results showing in Table 2 list the order of the metallicity,Fe₁₁CrC₄(s)>Fe₁₁CrC₄(g)>Fe₃C>Cr₃C. Therefore, Cr doping improves the metallicity of Fe₃C to some extent. Furthermore, the tiny difference of f_m for Fe₁₁CrC₄(s) and Fe₁₁CrC₄(g) demonstrates there is a weak relation between the metallicity and doping site.

Table 1 Calculated and experimentally measured lattice constants, cell volume (V_cell), cell total energy (E_tot), cohesive energy (E_coh) and formation enthalpy (△_rH_m) of Fe₃C, Fe₁₁CrC₄, and Cr₃C

Fig. 2 Calculated site- and spin-polarized partial densities (PDOS) of states of (Fe, Cr)₃C carbides:

Table 2 Calculated cell volume (V_cell), DOS at the Fermi level (D_f), metallicity (f_m) and total number of valance electrons (N) of Fe₃C, Fe₁₁CrC₄, and Cr₃C

Besides the covalent and metallicity, above carbides also possess the nature of ionicity, and it can be predicted that Cr₃C has the stronger ionicity for the larger energy gap between the lowest valence and the upper valence band compared to other carbides [10]. On the basis of electronic differential density (generally defined as the electron density difference between the isolated atoms and the bonding states with the same atomic configurations) for plane shown in Fig. 3, the darker red of Cr than Fe implies more charge transfer to C atoms, verifying a remarkable electropositivity of Cr.By the further study for Fe₁₁CrC₄(s) and Fe₁₁CrC₄(g), it is observed that the electron clouds around Fe atoms prefer to be perpendicular to the “surface” of Cr atoms, which may be originated from the noteworthy attractive interaction to electrons due to their strong electropositivity. In addition, the darker red of Cr(s) atoms in the special site against Cr(g) atoms in the general site reveals a more positive valence, namely a larger contribution of electrons for cell.

Fig. 3 Electron density difference distribution Fe₁₁CrC₄(g) (a) and Fe₁₁CrC₄(s) (b) at plane

By virtue of Mulliken population analysis, it can gain an insight into the characteristic of covalent bonds. From Table 3, it is clear that C—Fe(s) represents the stronger covalent bonds in comparison to C—Fe(g) in Fe₃C, due to the shorter bond length and the larger overlap population. For C—Cr bond in Cr-doped Fe₃C and Cr₃C, C—Cr(s) also possesses the stronger covalent bonds than C—Cr(g). Discussing the average bond length and overlap population of C—Fe for Cr-doped Fe₃C and Fe₃C, the sequence of the bond length of C—Fe is Fe₁₁CrC₄(s)> Fe₃C>Fe₁₁CrC₄(g) with the order of the overlap population following Fe₁₁CrC₄(g)>Fe₃C> Fe₁₁CrC₄(s). In regard to C—M bonds (the average value of all covalent bonds composed of metal atoms and C atoms in cell unit) of Fe₁₁CrC₄(g) and Fe₁₁CrC₄(s), an identical variation tendency is observed between the overlap population and the bond length, that is the longerbond length of C—M for Fe₁₁CrC₄(s) simultaneously corresponding to the larger overlap population. For the specific behavior of C—M in Fe₁₁CrC₄, it should come from the diversity of bond angles induced by Cr atoms in different doping sites. Putting the anomaly aside, it’s acceptable that Cr dopant could enhance the covalent bond strength of C—M according to the overlap population per unit of bond length. In consideration of the surprisingly sensitivity of C-M bond for doped site, it can be sure that the covalent bond net is constituted by the covalent bond chains of M—C—M, existing in the Fe₁₁CrC₄ as well as Fe₃C and Cr₃C, just like the previous findings in Cr_28-xFe_xC₁₂ [27].

Table 3 Bond type, bond length and overlap population of Fe₃C, Fe₁₁CrC₄, and Cr₃C

In the description of Fig. 2, the electric spin status of each kind atom is shown and the remarkable asymmetry between up-spin and down-spin indicates an non-ignorable magnetic property except for Cr₃C. For d orbitals of Fe in each kind of carbide and those of Cr in Fe₁₁CrC₄, the large spin splitting occurs near the Fermi level. Specifically, the up-spin channel of Fe-d orbital is nearly completely occupied and the down-spin channel is partially occupied, opposite to the case of Cr, thus leading to the contrary for the sign of Fe and Cr in magnetic moments (M_s) as given in Table 4. Furthermore, the magnetic moments of Fe(s) and Fe(g) in Fe₃C are respectively 1.92 μ_B/atom and 1.82 μ_B/atom, which are slightly smaller in contrast to other DFT calculations.

Once Fe locating in the general or special site substituted by Cr, the magnetic moments of the rest of Fe atoms in cell all reveal an obvious reducing tendency comparing to those in Fe₃C. While the difference value between Fe(s) and Fe(g) increases,0.16 μ_B/atom, 0.24 μ_B/atom respectively for Fe₁₁CrC₄(g) and Fe₁₁CrC₄(s). As for Cr atoms in the Fe₁₁CrC₄, Cr(g) possesses a larger magnetic moment with spin-down. On the other hand, the spin polarization of C atoms resulting from the hybridization with the neighboring metal atoms, the magnetic moment also declines when Fe atoms are replaced by Cr, of which C nearest to Cr atom in the doped structure has the minimum, -0.06 μ_B/atom, and -0.05 μ_B/atom for the “general” and “special” sites severally known from Mulliken population analysis. The magnetic moments per cell unit of Fe₃C, Fe₁₁CrC₄(g) and Fe₁₁CrC₄(s) are 20.36 μ_B, 16.92 μ_B, and 17.62 μ_B respectively. It isn’t beyond doubt that Cr-doped decreases the magnetic moments of Fe₃C. Meanwhile, the variation for magnetic moments of Fe₁₁CrC₄ is related to doping sites. In other words, Cr doping in Wyckoff positions of 8d will cause a lower magnetic moment.

Table 4 Calculated spin magnetic moments of Fe₃C and Fe₁₁CrC₄

3.3 Dielectric properties

As the experiment shown, high-carbon ferrochrome powders (HCFCP) exhibit the weakly paramagnetic behavior as their permeability is slightly less than 1, and the value gradually decreases with microwave frequency rising [15]. Other than permeability, the permittivity of HCFCP could achieve a relatively high value. So, the heating process of HCFCP in the microwave filed is prevailingly determined by the dielectric properties, of which the main phase (Cr, Fe)₇C₃ makes a significant contribution to it. In the case of (Fe, Cr)₃C, as a sort of the ferromagnetic phase, its permeability couldn’t be overlooked due to the high magnetic susceptibility. Considering the limit of calculation by CASTEP in permeability, the dielectric property is still a key point in current paper. For the mechanism of dielectric properties at optical frequencies, it’s acknowledged of electronic transitions from the occupied states to the unoccupied states through the interaction with energy quantum (namely photons in optical frequency) [28-29], and Fig. 4 displays the real part (ε_r') and imaginary part (ε_r") of the permittivity for Fe₃C, Fe₁₁CrC₄(g), Fe₁₁CrC₄(s), and Cr₃C as a function of frequency (v=E/h, where v, h, E represents frequency, planck constant and energy respectively). Generally speaking, the imaginary part, namely the relative dielectric loss factor, is calculated by the matrix elements between the occupied and unoccupied electronic states; while the real part, namely the relative permittivity, is derived from the imaginary part using the Kramers–Kronig relationship [30]. From Fig. 4, it is observed that the sequence of both ε_r' and ε_r" follows the order: Fe₁₁CrC₄(s)>Cr₃C>Fe₁₁CrC₄(g)>Fe₃C in the range of infrared frequencies (hν=1.24×10^-3 eV to 0.5 eV and hν=1.24×10^-3 eV to 1.2 eV respectively). Thus, it can be obtained that the permittivity of Fe₁₁CrC₄ is greater than that of Fe₃C and concretely there exists an intimate correlation between permittivity and Cr-doped site. When exceeding 0.5 eV and 1.2 eV for ε_r' and ε_r",the former sequence will be broken. Previous studies [14, 31] have pointed out that the permittivity has the close relations with the covalent bond strength of C—M as well as the metallic anti-bonding. As Table 3 described, the covalent bond of C—M follows the order of Fe₁₁CrC₄(s)>Fe₁₁CrC₄(g)>Fe₃C>Cr₃C corresponding to the overlap population (e/) of 0.1328, 0.1320, 0.1319, 0.1211, basically in concert with the ranking of the permittivity apart from Cr₃C at the low frequency as displayed in Fig. 4. As predicted, the sequence of the metallic anti-bonding is opposite to the order of the permittivity at high frequency. In conclusion, the contribution to the dielectric properties at the low frequency is mainly derived from the covalent bond, and beyond a certain frequency, the metallic anti-bonding will play the dominant role. Here, we offer the reasonable evidence for above interpretation. The wider hybridization area in DOS, equal to covalent bond strengthening, results in covalent electrons remarkable delocalization, meaning more effortless electron transition along with more effective interactions with energy quantum, which promotes the atomic thermal vibration. Since the 4s and 4p electrons of Fe(Cr) can form the anti-bonding orbitals and strongly reflect energy quantum, the inverse relation with permittivity can be explained. In particular, the stronger ionicity of Cr₃C should take account for its specificity in dielectric performance.

Fig. 4 Calculated dielectric function of Fe₃C, Fe₁₁CrC₄, and Cr₃C:

As Fig. 2 shown, 3d electrons of Fe(Cr) not only form covalent bonds with 2p electrons of C, but also form metallic bonds, thus being weak bound electrons. Meanwhile no band gap between the valence band and conduction band, the inter-band transition of 3d electrons prefers to occur in microwave band even if not obtaining high energy. Based on above evidences, the dielectric properties at microwave frequencies (hν=1.24×10^-6 eV to 1.24×10^-3 eV) can still be indirectly calculated in terms of the non-linear regression of the dielectric properties at infrared frequencies in spite of first- principles calculations of the dielectric properties limited to optical frequencies, and this method also has been applied to the calculation of permittivity for Fe-doped Cr₇C₃ and Mn₇C₃ [14, 31]. The detailed expressions accompanied the corresponding numerical values when microwave frequency is 2.45 GHz (hν=1.02×10^-5 eV) for heating are shown in Table 5, in addition to the absorption coefficient I(ω) calculated by [28]:

          (2)

where ω represents the angular frequency of the microwave field.

Exactly as Table 5 depicted, when microwave frequency is 2.45 GHz, the sequences of both ε_r' and ε_r" for Fe₃C, Fe₁₁CrC₄, and Cr₃C are consistence with the infrared dielectric properties. Moreover, I(ω) reveals the same order as ε_r' and ε_r", signifying the best temperature rising characteristic of Fe₁₁CrC₄(s). In consideration of the same large magnitudes of Fe-doped Cr₇C₃ as Cr-doped Fe₃C for the permittivity in the microwave band [14], it seems unimaginable of the extremely low permittivity of HCFCP [15]. Besides the inevitable deviation between the theoretical calculation and actual measurement, the major reason is attributed to the powdering of massive material. The energy gap of the material increases with the size of the crystals decreasing [32], resulting in the increment of the localization of molecular orbitals and thus making electron transition difficult, of course causing the permittivity consequentially dropping in the extent of microwave frequency. Nevertheless, the occurrence of red shift of the dielectric properties with particle size reducing can prevent ε_r" from sharply lowering to some degree in the microwave band [31].

Besides the contribution of electron transition, the dielectric properties of above carbides are also influenced by the polarization of electrons or atoms in the microwave electromagnetic field, which is analogous to dipole polarization. Under the electrical field force, nearly each atom would move along with the electric field direction and deviate from orginal lattice sites, generating polarization. Owing to the large gap in atomic radius between C and Cr (Fe), C atoms may jump through the lattice clearance once getting enough energy, thus constituting defect dipole with the metal ions or anion vacancies. Since the strength of covalent bonds in M-C-M chains is far weaker than that of common ones, the freedom of the relevant atoms is remarkable, preferring to demonstrate more significant polarization.

In terms of the undulatory theory, a reasonable interpretation also can be given for the changing of the permittivity in Fig. 4. As generally acceptable, the longer wavelength corresponds to the better penetrability in materials, namely energy quantum with lower energy can reach the depth of carbides followed the enlargement of the effective impact with valence electrons, meaning the higher permittivity. Even if the first principle calculation can’t precisely characterize the real case of these compounds with the limitation of DFT, it still offers a theoretical guidance for the future research and practical production in the fields of materials and metallurgy.

Table 5 Nonlinear regression equation of permittivity of Fe₃C, Fe₁₁CrC₄ and Cr₃C (E stands for energy)

4 Conclusions

In summary, a completely theoretical calculation has been carried out to analyze the electronic structure, magnetic and dielectric properties of Cr-doped Fe₃C as well as Fe₃C and Cr₃C. The enlargement of formation enthalpy of Fe₁₁CrC₄ mainly comes from the stronger metal anti-bonding, leading to the lowering of stability. The more thermal excited electrons should be responsible for the stronger metallicity in dopant. Similarly, the more shared electrons offer a reinforce for the covalent bonds of C-M, even though the bond length has an increasement due to the existence of Cr. The calculation values for magnetic moments of unit cell are in good agreement with previous theoretical results. The Cr-doped Fe₃C has a remarkable influence on the local magnetic moments for other atoms in unit, indicating the strong interaction among atoms. For either Fe₁₁CrC₄(g) or Fe₁₁CrC₄(s), the local magnetic moment of Fe at 4c site is larger than that at 8d site in contrary to Cr. The stronger covalent bond of Cr-doped Fe₃C originating from the improving electron delocalizability makes the inter-band transition more easily, implying the higher permittivity. The effect of metallic anti-bonding gradually plays a leader as frequency rises; meanwhile the penetrativity of energy quantum increases with the energy lowering.

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(Edited by YANG Hua)

Foundation item: Project(51174252) supported by the Joint Funds of the National Natural Science Foundation of China

Received date: 2015-08-24; Accepted date: 2015-12-27

Corresponding author: CHEN Jin, Professor, PhD; Tel: +86-13111009379; E-mail: chenjin2013815@126.com