Table of Contents
Research Letters in Physics
Volumeย 2009ย (2009), Article IDย 406095, 4 pages
Research Letter

Structural and Magnetic Properties of Mn-Based Diluted Magnetic Semiconductors and Alloys

Department of Physical Sciences, Jordan University of Science & Technology, P. O. Box 3030, Irbid 221100, Jordan

Received 21 June 2009; Accepted 4 August 2009

Academic Editor: Faustinoย Aguilera-Granja

Copyright ยฉ 2009 A. Alsaad. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.


Direct supercell approach calculations of the magnetic exchange interactions in Mn-doped ScN was carried out in the local spin density approximation by using the muffin-tin-orbital Green's function method. We found that magnetic interactions are long range interactions and affected by the randomness, band gap corrections, and carrier concentrations. Using total energy minimization approach we found that the global energy minimum of MnN is obtained for zinc-blende structure. If the compound is compressed by 6%, the energy minimum corresponds to the rock-salt structure in disagreement with the experimentally observed tetragonal distorted rock-salt structure, known as ๐œƒ-phase. An isostructural phase transition for MnxSc1-xN alloys from MnN ๐œƒ-phase to โ„Ž-ScN phase was found to occur at a hydrostatic pressure of 18โ€‰GPa. We predict above room temperature ๐‘‡๐‘ for Mn concentrations of about 10% in ScNโ€‰:โ€‰Mn system.

1. Introduction

The undergoing intensive research and the current industrial and technological interests in the field of spintronics stimulate the search for high-Curie-temperature diluted magnetic semiconductors (DMSs). The typical zinc blende III-V semiconductors doped with magnetic impurities suffer from low solubility manifested in the formation of secondary phases. Clearly, there is an interest in finding an alternative semiconductor host and magnetic dopants like Mn with Tc above room temperature. One limitation of the traditional semiconductors tried up to now is the small solubility of magnetic dopants like Mn in them. To conquer this problem we, alternatively, propose the less known rock-salt structure ScN semiconductors, because it shares a common crystal structure with magnetic (or antiferromagnetic) transition metal nitrides [1]. The growth of mixed MnxSc1-xN alloys using molecular beam epitaxial growth technique has been reported [2]. In our study, the exchange magnetic interactions were investigated by fitting the total energies of nearest-neighbor pairs of parallel and antiparallel Mn spins to a Heisenberg Hamiltonian. The interactions with near and distant cells were considered. The nearest neighbor exchange interactions can be written as ๎“๐ป=โŸจ๐‘–๐‘—โŸฉ๐ฝ๐‘–๐‘—๐’๐‘–โ‹…๐’๐‘—.(1) We found that exchange magnetic interactions are long range and drastically affected by the randomness of the cell as was observed in other DMSs [3, 4]. The search for magnetic semiconductors with a curie temperature Tc above room temperature (RT) is currently one of the major issues in semiconductor spintronics [5]. For MnN, three different phases, including RS, ZB, and WZ are considered. Both ferromagnetic (FM) and antiferromagnetic (AFM) states are calculated for each compound in the three phases. The binary ScN is an RS semiconductor with in-plane lattice constant ranging between 4.50 and 4.503โ€‰ร…, indirect band gap from ฮ“-X of approximately 1โ€‰eV, and a direct transition at X point of 2.1โ€“2.4โ€‰eV [6]. In addition, experimental studies and theoretical calculations have confirmed that ScN stabilizes in a fivefold coordinated structure called h-ScN [7]. On the other hand, Mn is an early transition metal and has slightly tetragonal distorted rock-salt, known as ๐œƒ-phase [8]. Thus, it is of great interest to combine MnN with ScN to yield Mn-doped ScN DMSs and ferromagnetic MnxSc1-xN alloys. Within mean field theory, the Curie temperature has been estimated to be above 400โ€‰K for 3% Mn.

2. Methodology

First-principle calculations within the framework of the density functional theory [9, 10] and spin local density approximation (SLDA) [11, 12] are performed. We employed the full-potential linearized-augmented plane-wave (FP-LAPW) method as well as linearized muffin-tin orbital (LMTO) both in the atomic sphere approximation (ASA) and in a full potential (FP) as used in the Wien2k code [13] and WIEN97 code [14] applied to a 2-atom unit cell because they allow a shift in the diagonal elements of the Hamiltonian in a straightforward manner. Therefore, they allow us to correct the LDA underestimate of the band gap. The muffin-tin radius adopted were 1.75โ€‰a.โ€‰u. for Mn and 1.44โ€‰a.โ€‰u. for N in MnN. The total energy and eigen values were converged to 10-5โ€‰eV and 10-4โ€‰eV, respectively. The calculations were performed with spin-polarized potentials in order to analyze the ferromagnetic phases of MnN. A 6ร—6ร—6โ€‰โ€‰k-point mesh was used to ensure the convergence of Brillouin zone integrations. To study the exchange magnetic interactions as a function of Mn-Mn pairs and the effects of carrier concentration and doping on Curie temperature, we used a 64 supercell with cutoff energy of 25โ€‰Ry to ensure full convergence.

3. Results

3.1. Magnetic Stability, Magnetic Moment, and the Phase Transition in Mn-Doped ScN DMS and M๐ง๐ฑS๐œ๐Ÿ-๐ฑN Alloys

Our total energy calculations of MnN as a function of lattice constant a in RS, WZ, and ZB in Ferromagnetic (FM) and antiferromagnetic (AFM) states indicate that the global energy minimum is obtained for ZB structure. If the compound is compressed by 6%, the energy minimum corresponds to the RS structure. This result disagrees with a slightly tetragonal distorted RS structure, known as ๐œƒ phase experimentally found for MnN binary. From the curvature of total energy as a function of a for the AFM state, we deduce a bulk modulus B=259โ€‰GPa (see Table 1). Next, we consider the different magnetic configurations of MnN. Our results are summarized in Table 2. The energy difference between FM and AFM is ฮ”E=0.031โ€‰eV/atom. Previous analysis of the partial density of states has concluded that majority states are filled with three electrons and lead to localized ๐‘†=3/2 spins [1]. This is consistent with our value for the magnetic moment of MnN (see Table 2). Having confirmed that ScNโ€‰:โ€‰Mn can behave as a DMS, we turn our attention to study the structural properties of MnxSc1-xN alloys. Previously, we found that ScN/GaN and ScN/InN superlattices can exhibit isostructural phase transitions (IPTs) at certain values of hydrostatic pressure (see [15] and references therein). We found that IPTs were associated with anomalies optical and piezoelectric properties. In this work, we examine the possibility of IPTs in MnxSc1-xN alloys. Figure 1 shows the lattice constant a of the MnxSc1-xN alloys as a function of the hydrostatic pressure. We started with the theoretical lattice constant of ZB MnN and experimental lattice constant of ๐œƒ-MnN, and we studied the variation of lattice constant with hydrostatic pressure. Figure 1 shows a remarkable phenomenon: from 5 to 18โ€‰GPa the lattice parameter increases by 15% indicating drastic continuous structural transformations in this pressure range. Thus, anomalous optical, piezoelectric, and magnetic properties are expected. It also indicates that this alloy undergoes a sharp prerssure-induced isostructural phase transition at a critical hydrostatic pressure of 18โ€‰GPa from the tetragonal distorted RS ๐œƒ-phase into the fivefold coordinated h-ScN. Since the synthesis of MnxSc1-xN alloys has been achieved for a wide range of Mn concentrations, we would suggest that concern experimental groups should study temperature dependence of magnetization, resistivity, and spceific heat of MnxSc1-xN alloys as a function of hydrostatic pressure.

Table 1: Lattice parameters relaxation results for antiferromagnetic (AFM) MnN.
Table 2: Lattice constant and magnetic moment of MnN in different phases for both the FM and AFM states.
Figure 1: Lattice constant of MnxSc1-xN alloys as a function of the hydrostatic pressure. An isostructural phase transition occurs at a critical pressure of 18โ€‰GPa.
3.2. Exchange Magnetic Interactions, Critical Temperatures, and the Effects of Carrier Concentration

We next focus on Mn-doped ScN DMS. Figure 2 plots the nearest neighbor Mn-Mn exchange interactions as a function of the distance in ScNโ€‰:โ€‰Mn. We found that FM configurations have lower energy than AFM state. This ferromagnetic coupling is somehow surprising when keeping in mind that the coupling in MnN is antiferromagnetic. We explain this by the fact that the larger Mn-Mn distance will lead to less overlap between the Mn t2 orbitals, which favors ferromagnetic coupling, and also the nearest neighbor exchange interactions in ScNโ€‰:โ€‰Mn are much less than in the MnN binary. In order to account for the effect of randomness, we construct relatively large supercell consists of 128 atoms. Our (SLDA) results indicate that exchange magnetic interactions follow Ruderman-Kittel-Kasuya-Yosida (RKKY) [16, 17]. Figure 2 also indicates that strong second nearest neighbor interactions are suppressed by large exchange magnetic interactions that can be correlated with the critical temperature Tc by averaging Jij over the various atoms in the cell. A good estimate for Tc can be obtained using a mean-field approximation (MF) and even a better estimate of Tc is obtained using the cluster variation method (CVM). For Mn concentrations up to 30%, the exchange interactions of up to four nearest-neighbors are significant. The MF and CVM Curie temperatures ๐‘‡MF๐‘ and ๐‘‡CVM๐‘ as functions of Mn concentration for Mn-doped ScN are shown in Figure 3. It indicates that Tc increases with Mn concentrations and saturates above Mn concentration of 28% at a maximum Tc of 670โ€‰K. Tc above room temperatures is predicted for Mn concentration larger than 12%. Thus, ferromagnetic behavior above room temperature is possible in Mn-doped ScN. It should be noted that for small concentration of Mn (6.25%) (a cell of 64 atoms) with Mn located only at first nearest neighbors with no second nearest neighbor pair had ๐‘‡CVM๐‘=240โ€‰K and ๐‘‡MF๐‘=306โ€‰K. However, large supercells (128 atoms) with all Mn are located at second nearest neighbors with no Mn on first nearest neighbors exhibit lower values of ๐‘‡CVM๐‘=165โ€‰K and ๐‘‡MF๐‘=210โ€‰K, respectively. Next, we consider the effects of defects affecting the carrier concentration. We can account for the effect of additional doping by simply shifting the Fermi level. Figure 4 shows ๐‘‡MF๐‘ as a function of electron concentration. We consider both ๐‘›-type and ๐‘-type doping. Negative electron concentrations correspond to ๐‘-type doping, and positive values correspond to ๐‘›-type doping. The ๐‘‡MF๐‘ increases and remains high up to 2ร—1020โ€‰cm-3 but then drops to about zero for about 2ร—1020โ€‰cm-3. Such electron concentrations are rather typical for Mn-doped ScN samples. At least one sample with 3% Mn was reported to show a ferromagnetic behavior up to 50โ€‰K [18]. The ๐‘›-type doping in ScN is generated from nitrogen vacancies. Consequently, we carried out some calculations with about 10% Mn and 3% nitrogen vacancy VN corresponding to two VN per cell. The 3% VN corresponds to doping by about 6ร—1019โ€‰e/cm3. We found that ๐‘‡MF๐‘ drops by approximately 11%.

Figure 2: The exchange magnetic interaction Jij as a function of Mn-Mn nearest-neighbor distances Rij for the ScNโ€‰:โ€‰Mn diluted magnetic semiconductor.
Figure 3: The critical Curie temperature versus Mn concentration for Mn-doped ScN system. Red squares represent mean-field Curie temperatures ๐‘‡MF๐‘, and blue squares represent cluster variation method Curie temperature๐‘‡CVM๐‘.
Figure 4: The mean-field critical Curie temperature Tc as a function of electron concentration of Mn-doped ScN system.

4. Conclusions

In summary, our direct supercell simulations show that Mn-doped ScN is promising DMS systems with extraordinary optical, structural, and magnetic properties. By using total energy calculations, we found that global energy minimum of MnN is obtained for ZB structure. As the compound is slightly compressed, the energy minimum corresponds to the RS structure exhibiting a magnetic moment of a value of 2.52โ€‰๐œ‡B in disagreement with the experimental distorted RS ๐œƒ-phase found for Mn. Our calculations for the magnetic exchange interactions indicate the possibility of above room temperature Tc for Mn concentrations of about 10%. Our results on the effects of doping indicate that room temperature ferromagnetism is achieved by maintaining the ๐‘›-type carrier concentration below 1020โ€‰cm-3. Thus, the Mn-doped ScN DMS is expected to be the key candidate component for life time spintronic devices. In addition, we found that MnxSc1-xN alloys undergo an isostructural phase transition from MnN ๐œƒ-phase to h-ScN at a critical hydrostatic pressure of 18โ€‰GPa. Such a transition could be associated with several anomalous properties.


The author acknowledges E. Sigmund and his research team at Brandenburg Technical University in (BTU), Cottbus-Germany, for useful discussions. Computational support has been provided by the Theoretical physics institute at BTU in Germany.


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