Next Article in Journal
Effects of Grain Refinement on the Low-Cycle Fatigue Behavior of IN792 Superalloys
Next Article in Special Issue
Development and Optimization of VGF-GaAs Crystal Growth Process Using Data Mining and Machine Learning Techniques
Previous Article in Journal
Mitigating Corrosion Effects of Ti-48Al-2Cr-2Nb Alloy Fabricated via Electron Beam Melting (EBM) Technique by Regulating the Immersion Conditions
Previous Article in Special Issue
Boundary Conditions for Simulations of Fluid Flow and Temperature Field during Ammonothermal Crystal Growth—A Machine-Learning Assisted Study of Autoclave Wall Temperature Distribution
 
 
Font Type:
Arial Georgia Verdana
Font Size:
Aa Aa Aa
Line Spacing:
Column Width:
Background:
Article

Crystal Structure Prediction of the Novel Cr2SiN4 Compound via Global Optimization, Data Mining, and the PCAE Method

1
Materials Science Laboratory, Institute of Nuclear Sciences “Vinča”, University of Belgrade, National Institute of the Republic of Serbia, 11351 Belgrade, Serbia
2
Center for the Synthesis, Processing and Characterization of Materials for Use in Extreme Conditions “CextremeLab”, 11001 Belgrade, Serbia
3
Max Planck Institute for Solid State Research, Heisenbergstr. 1, D-70569 Stuttgart, Germany
*
Author to whom correspondence should be addressed.
Crystals 2021, 11(8), 891; https://doi.org/10.3390/cryst11080891
Submission received: 25 June 2021 / Revised: 23 July 2021 / Accepted: 26 July 2021 / Published: 30 July 2021
(This article belongs to the Special Issue Artificial Intelligence for Crystal Growth and Characterization)

Abstract

:
A number of studies have indicated that the implementation of Si in CrN can significantly improve its performance as a protective coating. As has been shown, the Cr-Si-N coating is comprised of two phases, where nanocrystalline CrN is embedded in a Si3N4 amorphous matrix. However, these earlier experimental studies reported only Cr-Si-N in thin films. Here, we present the first investigation of possible bulk Cr-Si-N phases of composition Cr2SiN4. To identify the possible modifications, we performed global explorations of the energy landscape combined with data mining and the Primitive Cell approach for Atom Exchange (PCAE) method. After ab initio structural refinement, several promising low energy structure candidates were confirmed on both the GGA-PBE and the LDA-PZ levels of calculation. Global optimization yielded six energetically favorable structures and five modifications possible to be observed in extreme conditions. Data mining based searches produced nine candidates selected as the most relevant ones, with one of them representing the global minimum in the Cr2SiN4. Additionally, employing the Primitive Cell approach for Atom Exchange (PCAE) method, we found three more promising candidates in this system, two of which are monoclinic structures, which is in good agreement with results from the closely related Si3N4 system, where some novel monoclinic phases have been predicted in the past.

1. Introduction

Tools and equipment used in metal and wood machining frequently experience severe damage during their usage, which leads to the urgent need for protective coatings to extend the lifetime of the machinery [1,2]. This particularly applies to marine equipment, where certain parts have to operate in challenging marine environments. Additionally, past nuclear accidents have led to an increase in research regarding nuclear materials and the development of coatings that can be used under such extreme conditions.
Transition metal nitrides are widely used as hard coatings, and, among them, CrN is one with many desired properties—high hardness, toughness, and corrosion resistance, good oxidation resistance, good adhesion strength, and excellent wear resistance [3,4,5,6,7,8,9,10]. However, due to its high friction coefficient, it does not perform well in some extreme conditions [2]. Delamination is considered to be critical to the wear failure of CrN coatings in seawater where microcracks play an important role in the evolution of delamination. [11].
Even though CrN is a well-established and very stable coating in wide use, the addition of alloying elements, such as Si, has been actively investigated to further improve its properties as a hard coating material [5,6,12,13,14,15,16,17,18]. Compared to CrN thin films, Cr-Si-N coatings exhibit lower friction coefficients and wear rates due to their low surface roughness. In general, their tribological and mechanical characteristics show significant improvement under different environments and conditions (dry, humid, or aqueous; dynamic or static; ambient or high temperature; etc.) compared to CrN [3,19,20,21,22,23,24,25,26,27]. Due to the finer crystal structure, the addition of Si can also lead to the elimination of large flake pits, which were previously found on the wear trace of CrN coatings [26]. This increase in silicon content also leads to a change in the crystal structure of the coating, and the particle shape changes from triangular to circular with a distribution that tends to be uniform, while the density of the coating increases [28].
Four kinds of Cr-Si-N coatings are known that are considered to be harder than the CrN coating [28]. Nanocomposite Cr-Si-N thin films (usually in the form of nanocolumns or nanoclusters of CrN embedded in an amorphous Si3N4 matrix) also have higher hardness and oxidation resistance compared with CrN thin films [5,6,15,16,17,18,29]—their hardness can be increased by up to ~9 GPa [2,3,30,31], while their oxidation resistance is significantly improved at temperatures well above the oxidation limit of ~600–700 °C of CrN [6,32,33].
Epitaxially grown Cr-Si-N thin films that appear to constitute solid solutions of Si in CrN exhibit even higher hardness than less homogeneous nanocomposite Cr-Si-N thin films—a maximum hardness value of 51 GPa was obtained for 10 mol% Si in Cr-Si-N [34]. The increased hardness of Cr-Si-N is obtained due to the formation of a fine nanocomposite structure and the refinement of CrN crystallites [18,24] as well as to the dissolution of Si in CrN [34]. The decrease of friction is attributed to the formation of SiO2 or Si(OH)2 layers in a humid environment, which plays a role as a self-lubricant, and by a smoother surface due to the Cr-Si-N amorphous phase [18,27]. Improved oxidation resistance can be explained by the formation of amorphous silicon oxide, which retards the diffusion of O as well as of Cr, Si, and N [29].
As its Si content increases, the structure of the Cr-Si-N coating changes from a crystalline to an amorphous state [35,36], and while the corrosion resistance constantly improves and the friction coefficient decreases, wear-resistance and hardness also improve until a certain Si content limit is reached beyond which the coatings start to deteriorate [25,34,37]. The electronic properties of Cr-Si-N thin films also change significantly depending on their chemical composition. While fcc-CrN exhibits metallic-like behavior, an increase of N or Si content leads to a more non-metallic character of the material [37].
Furthermore, investigations of the friction and wear properties of CrSi based coatings led to the conclusion that Cr-Si-N coatings showed better properties in comparison to the CrSi coatings [38]. Increasing the silicon content in these coatings led to the best friction and wear performance, which, in the case of an ATF system in a water environment, can reduce the wear volume by three orders of magnitude [38]. In summary, the Cr-Si-N coatings exhibit superior tribological performance due to their excellent toughness, high hardness, preferable adhesion, and good corrosion resistance [2], which all lead to the possibility of wide applications.
Gaining deeper insight into the structure–property relationship of the Cr-Si-N coating on the atomic level would greatly support the optimization of such coatings. As a first step, we focus on the possible existence of crystalline phases in the Cr/Si/N system. Considering the large hardness of Si3N4, we chose the analogous composition Cr2SiN4, where we would expect similarly high hardness as for Si3N4 itself. Thus, in this study, we identify feasible structure candidates of the composition Cr2SiN4, using global optimization techniques, data-mining, and the Primitive Cell approach for Atom Exchange (PCAE) method, followed by careful re-optimizations of the candidates on the ab initio level.

2. Materials and Methods

To perform structure prediction and gain insight into the structural stability of the possible phases existing in the Cr2SiN4 system, a combination of global optimization (GO), data mining (DM), and the PCAE method has been used [39,40]. First, we performed global optimizations on the energy landscape of Cr2SiN4 using simulated annealing [41], within the G42+ code [42]. A fast computable robust empirical two-body potential consisting of Lennard-Jones and exponentially damped Coulomb terms was employed to perform the GO searches with a reasonable computational effort [43]. Next, we have performed DM-based searches of the ICSD database [44,45] in order to find possible structure candidates for the unknown Cr2SiN4 compound.
We used the well-known KDD (knowledge discovery in databases) process, which involves selection, preprocessing, transformation, and interpretation/evaluation (or post-processing), and has been successfully used in previous studies [46,47,48]. Finally, the Primitive Cell approach for Atom Exchange (PCAE) method was employed for generating alternative structure candidates in the Cr2SiN4 compound. The PCAE method is simple, fast, and computationally inexpensive compared to the supercell approach [40].
In the current study, the starting modifications were taken from the related Si3N4 chemical system by first transforming the crystallographic (conventional) cell to the primitive cell, while keeping the symmetry and multiplicity of the atom positions (for more information, c.f. ref [40]). In the next stage, we replaced the number of atoms needed to obtain a certain stoichiometry (2 × Si by 2 × Cr atoms) on the symmetry-related Wyckoff positions. Subsequently, an ab initio full structure optimization without symmetry constraints was performed.
After the structure candidates have been identified using the GO, DM and PCAE methods, each structure candidate has been subjected to local optimization on the ab initio level. Density functional theory (DFT) calculations of the total energy, and local optimizations (including volume, cell parameters, and atomic positions), were performed using the CRYSTAL17 code [49,50] based on linear combinations of atomic orbitals (LCAO). For the local optimization runs, we employed analytical gradients [51,52], and equation of state (EOS) calculations using polynomial fitting [49,50].
Local optimizations were performed on the DFT level employing two different functionals: the Local Density Approximation (LDA) with the Perdew–Zunger (PZ) correlation functional [53] and the Generalized Gradient Approximation (GGA) with the Perdew–Burke–Ernzerhof (PBE) functional [54] for comparison. It is reasonable to choose at least two different ab initio methods, to gain better insight into the quantitative validity of the results since no compounds of the composition Cr2SiN4 are available for comparison with the experiment [55,56,57].
An all-electron basis set based on Gaussian-type orbitals was employed in the case of chromium (Cr_86-411d41G_catti_1995) [58,59], silicon (Si_86-311G**_pascale_2005) [60,61], and nitrogen (N_6-21G*_dovesi_1990) [62,63]. The symmetries of the analyzed structures were determined using the SFND [64] and RGS [65] algorithms, and duplicate structures were removed using the CMPZ algorithm [66]; these three algorithms were implemented in the KPLOT code [67]. The optimized structures of various modifications were visualized using the Vesta3 program [68].

3. Results and Discussion

3.1. Global and Local Optimization Using Empirical and Ab Initio Energy Functions

Global optimizations were performed on the energy landscapes using empirical potentials for various numbers of formula units per simulation cell and for slightly varying ionic radii, yielding a total of 5000 structure candidates. Most of these global searches resulted in low-symmetry structure candidates (triclinic and monoclinic symmetry). After detailed statistical, structural, and crystallographic analysis, the most promising ones were submitted for local optimization on ab initio level. With further local optimization on the ab initio level, we have obtained the 11 most-relevant structure candidates from global optimization (GO).
Table 1 presents the energetic ranking of these new Cr2SiN4 phases using the GGA-PBE functional, where the α-Cr2SiN4-type is the lowest in calculated total energy, and the nf5-Cr2SiN4-type the highest one. Moreover, we grouped the resulting GO structures into energetically favorable ones, ranging from the α- to the λʹ-Cr2SiN4 phase, and non-favorable Cr2SiN4 modifications marked nf1 to nf5, which might be observed under extreme conditions. In addition, each favorable structure candidate has been subjected to a DFT-LDA optimization with similar results in the energetic ranking (Table A2.)

3.1.1. Structural Analysis of the Most Promising Modifications Found after Global Optimization (GO)

The energetically most favorable modification after global optimization is denoted as α-Cr2SiN4-type and appears in the orthorhombic space group Pma2 (no. 28) with unit cell parameters of a = 5.54, b = 7.91, and c = 2.81 Å on the GGA-PBE level of calculation. The α-Cr2SiN4 phase is visualized in Figure 1a, while full structural data of all favorable candidates are presented in Table 2 for calculations with the PBE functional, and in Table A1 for those computed with the LDA functional, respectively.
In the α-modification, chromium is six-fold coordinated by nitrogen, forming two different CrN6 octahedra (with atom–atom distances of Cr(1) 2 × 1.82 Å-N, 1 × 1.89 Å-N, 1 × 1.97 Å-N, 2 × 2.13 Å-N, Cr(2) 2 × 1.91 Å-N, 2 × 1.95 Å-N, and 2 × 2.04 Å-N), while silicon is four-fold coordinated by nitrogen (with atom–atom distances of 2 × 1.77 Å-N and 2 × 1.71 Å-N) forming a tetrahedron. Moreover, the octahedra are connected by edges, while the tetrahedra are corner connected to them; additionally, the tetrahedra fall into two groups with opposite orientations.
A second energetically favorable candidate obtained from GO is denoted as β-Cr2SiN4-type. This triclinic structure appears in space group P-1 (no. 2), with cell parameters a = 7.28, b = 7.79, c = 2.74 Å, α = 93.66, β = 82.48, and γ = 120.64 calculated with GGA-PBE, and is visualized in Figure 1b. In this structure, chromium has a six-fold coordination by nitrogen forming two different CrN6 octahedra similar to the α-modification, while silicon is four-fold coordinated by nitrogen with interatomic distances for chromium (Cr(1) 2 × 1.88 Å-N, 1 × 1.93 Å-N, 1 × 1.99 Å-N, 1 × 2.00 Å-N, 1 × 2.12 Å-N, Cr(2) 1 × 1.86 Å-N, 1 × 1.90 Å-N, 1 × 1.94 Å-N, 1 × 1.96 Å-N, 1 × 2.02 Å-N, and 2 × 2.05 Å-N) and silicon (2 × 1.70 Å-N, 1 × 1.78 Å-N, and 1 × 1.81 Å-N).
As in the α-Cr2SiN4-type modification, SiN4 tetrahedra are oriented in different directions; however, in this modification, the CrN6 octahedra are face-connected and lean against each other, thus, forming a void in the center of the structure that is reminiscent of zeolite formation.
The next energetically favorable candidate found using global optimization is a monoclinic structure denoted as the δ-Cr2SiN4-type that crystallizes in space group P21/m (no. 11). This structure is presented in Figure 2a with unit cell parameters a = 6.21 b = 3.82 c = 5.54 Å, and β = 116.24, computed using the PBE functional (Table 2). Interestingly, in the δ-phase both, chromium and silicon are six-fold coordinated by nitrogen, with the octahedra being edge-connected, indicating that this candidate might be a high-pressure phase.
Additionally, the interatomic distances in the two different CrN6 octahedra are Cr(1) 1 × 1.91 Å-N, 2 × 1.94 Å-N, 1 × 1.95 Å-N, 1 × 1.97 Å-N, 1 × 2.06 Å-N, Cr(2) 1 × 1.71 Å-N, 1 × 1.88 Å-N, 2 × 1.95 Å-N, 1 × 2.12 Å-N, and 1 × 2.27 Å-N, and the atom–atom distances in the SiN6 octahedra are 1 × 1.81 Å-N, 1 × 1.93 Å-N, 2 × 1.92 Å-N, 1 × 1.85 Å-N, and 1 × 1.91 Å-N, respectively.
One more energetically favorable candidate is a monoclinic structure, denoted as ε-Cr2SiN4-type, which appears in space group P21/m (no. 11). It is visualized in Figure 2b with the unit cell parameters a = 5.09, b = 2.89, c = 8.90 Å, and β = 90.20. However, the ε-Cr2SiN4-type is composed of SiN4 tetrahedra (with interatomic distances 1 × 1.77 Å-N, 2 × 1.72 Å-N, and 1 × 1.73 Å-N), while chromium is four-fold and six-fold coordinated by nitrogen, thus, forming CrN4 tetrahedra and CrN6 octahedra (interatomic distances are Cr(1) 1 × 1.90 Å-N, 4 × 2.00 Å-N, 1 × 2.07 Å-N, Cr(2) 1 × 1.75 Å-N, 2 × 1.78 Å-N, and 1 × 1.82 Å-N). Apart from being the same space group as the δ-phase, the monoclinic ε-modification resembles more the α- and β-Cr2SiN4-types (Table 1 and Table 2 and Figure 2).
Two other interesting favorable structure candidates are monoclinic modifications belonging to space group Pm (no. 6) and are visualized in Figure 3a,b, respectively. The first one (a) is denoted the λ-Cr2SiN4-type with unit cell parameters a = 5.07, b = 2.88, c = 9.27 Å, and β = 99.77, while the other one (b) is called the λʹ-Cr2SiN4-type and has the unit cell parameters a = 5.06, b = 2.87, c = 9.18 Å, and β = 90.97. These two structures are structurally and energetically very similar, and both of them are composed of CrN4 and SiN4 tetrahedra, with CrN6 octahedra between them.
The CrN6 octahedra are edge-connected, with corner-connected tetrahedra. Similar to the previous structures of the α-, β-, ε-Cr2SiN4-type of modifications, these tetrahedra have the opposite orientations in different layers of the structure. In the λ-Cr2SiN4-type of structure, chromium is connected to nitrogen with atom–atom distances Cr(1) 1 × 1.70 Å-N, 2 × 1.79 Å-N, 1 × 1.89 Å-N, Cr(2) 1 × 1.91 Å-N, 2 × 1.93 Å-N, 2 × 2.02 Å-N, 1 × 2.19 Å-N, Cr(3) 1 × 1.91 Å-N, 2 × 1.93 Å-N, 3 × 2.09 Å-N, Cr(4) 2 × 1.75 Å-N, 1 × 1.79 Å-N, 1 × 1.81 Å-N, and 1 × 2.64 Å-N, while there are also two different types of SiN4 tetrahedra (with interatomic distances Si(1) 1 × 1.72 Å-N, 1 × 1.76 Å-N, 2 × 1.73 Å-N, Si(2) 3 × 1.74 Å-N, and 1 × 1.75 Å-N).
The modification referred to as λʹ-Cr2SiN4-type has a similar structure, with chromium being tetrahedrally and octahedrally coordinated by nitrogen in four different ways (with atom–atom distances Cr(1) 2 × 1.75 Å-N, 1 × 1.80 Å-N, 1 × 1.81 Å-N, Cr(2) 1 × 1.92 Å-N, 2 × 1.94 Å-N, 2 × 2.01 Å-N, 1 × 2.23 Å-N, Cr(3) 1 × 1.92 Å-N, 2 × 1.97 Å-N, 2 × 2.01 Å-N, 1 × 2.08 Å-N, Cr(4) 1 × 1.71 Å-N, 2 × 1.78 Å-N, and 1 × 1.88 Å-N) and two types of SiN4 tetrahedra (interatomic distances Si(1) 1 × 1.73 Å-N, 2 × 1.74 Å-N, 1 × 1.75 Å-N, Si(2) 2 × 1.74 Å-N, and 2 × 1.73 Å-N).
We note that, after optimization on the ab-initio level with the LDA-PZ functional and with the GGA-PBE functional, both structures remain distinct but stay in the same space group.

3.1.2. Structural Details of Non-Favorable Structures Found after a Global Search

At extreme conditions of temperature and/or pressure, the global optimization (GO) yielded several additional candidate structures, and Table 3 presents the structural data for the five energetically non-favorable yet structurally promising GO modifications. The first modification, lowest in the energy compared to the other structures within this group is denoted as nf1-Cr2SiN4-type and appears in space group P21/m (no. 11). It is visualized in Figure 4a with the unit cell parameters a = 5.03, b = 2.89, c = 9.25 Å, and β = 100.34.
It is composed of CrN6 octahedra positioned between two layers of nitrogen tetrahedra coordinating silicon and chromium. Hence, chromium in this structure has a four-fold as well as a six-fold coordination (with atom–atom distances Cr(1) 1 × 1.94 Å-N, 2 × 1.98 Å-N, 2 × 2.00 Å-N, 1 × 2.08 Å-N, Cr(2) 3 × 1.77 Å-N, 1 × 1.80 Å-N, and 1 × 2.72 Å-N) while silicon still remains in four-fold coordination (with the interatomic distances 1 × 1.76 Å-N and 3 × 1.74 Å-N). Both CrN4 and SiN4 tetrahedra in the upper and lower part of the structure are oriented in the opposite directions.
The next modification according to the total energy ranking is referred to as nf2-Cr2SiN4-type and crystallizes in space group Cc (no. 9). It is visualized in Figure 4b with the unit cell parameters a = 5.06, b = 14.14, c = 4.77 Å, and β = 121.05. Within this structure, chromium is five-fold coordinated by nitrogen and forms two types of polyhedra (with atom–atom distances Cr(1) 1 × 1.84 Å-N, 1 × 1.87 Å-N, 1 × 1.88 Å-N, 1 × 1.91 Å-N, 1 × 1.93 Å-N, Cr(2) 1 × 1.78 Å-N, 1 × 1.79 Å-N, 1 × 1.84 Å-N, 1 × 2.00 Å-N, and 1 × 2.11 Å-N) while silicon is four-fold coordinated by nitrogen (interatomic distances are 1 × 1.71 Å-N, 1 × 1.77 Å-N, 1 × 1.75 Å-N, and 1 × 1.76 Å-N).
Other relevant modifications are denoted as nf3-Cr2SiN4-type, nf4-Cr2SiN4-type, and nf5-Cr2SiN4-type with the first two structures appearing in the space group Pm (no. 6) and the last one showing space group P-1 (no. 2), respectively. The total energies of these five modifications on ab initio level (GGA-PBE functional) are listed in Table 1. Furthermore, we note that most of the energetically favorable and non-favorable structures found after global optimization exhibit low symmetry, mostly orthorhombic and monoclinic symmetry (Table 2 and Table 3). This is in agreement with previous theoretical reports in the closely related Si3N4 chemical system, where orthorhombic and monoclinic structures have been proposed [69].

3.2. Data Mining (DM) Based Searches Using the ICSD Database

The DM-based searches were performed within the ICSD database, which, in the latest release contains 242,828 inorganic structures, out of which more than 80% have already been assigned to distinct structure types (up to now, 9724 structure types are listed in the ICSD) [44,45]. Using the final prototype criterion as part of the KDD approach [46,47,48] to eliminate quasi-duplicate structures, the number of structures was reduced to 66 unique structure candidates in the A1B2C4 chemical system. After performing full structural optimization on the ab initio level, the number of structure candidates was further reduced. Table 4 shows the total energy ranking of the DM-based structure candidates in the Cr2SiN4 system using the GGA-PBE functional.
Full structural data for all Cr2SiN4 modifications found from the DM-based searches are presented in Table 5, while their corresponding total energies are listed in Table 4. The data-mining-based searches of the ICSD database resulted in many possible modifications, among which the four structures presented here are distinguished as being the energetically most favorable ones, while the others corresponded to non-favorable DM structure candidates.

3.2.1. Structural Analysis of Low-Energy Candidates from the DM-Based Searches

The Al2MgO4-spinel-type modification [70,71], generated from the DM-based searches and visualized in Figure 5a, is the lowest one in the calculated total energy at both the GGA-PBE and the LDA-PZ level, for the whole energy landscape including the structures obtained from the GO and the PCAE method calculations. It exhibits space group Fd-3m (no. 227) with unit cell parameters a = 7.88 Å at the GGA-PBE level of calculation with all structural data presented in Table 5.
In the Al2MgO4-type modification, chromium is six-fold coordinated forming a CrN6 octahedron with the interatomic distance Cr 6 × 1.95 Å-N, while silicon is four-fold coordinated forming a SiN4 tetrahedron with the atom–atom distance 4 × 1.74 Å-N. In this cubic modification, the CrN6 octahedra are connected by edges while the SiN4 tetrahedra are corner-connected. When performing structure optimizations of the candidates on the DFT-LDA level, the Al2MgO4-spinel-type modification remains the global minimum (Table A1 and Table A2). We note that the Al2MgO4-spinel-type of the structure appears in more than 4000 compounds (4250) with the chemical formula A1B2C4 indicating the importance of this structure-type on the energy landscape of ternary systems [44,45].
The next favorable modification found after DM is in the Na2MnCl4-type [72], which is an orthorhombic structure that appears in space group Pbam (no. 55) with unit cell parameters a = 4.73, b = 8.70, and c = 2.73Å and is visualized in Figure 5b. In this modification, both chromium and silicon are six-fold coordinated by nitrogen, thus, forming distorted octahedra that are quite different from each other.
The CrN6 octahedra are quite similar to those in the WC structure-type, while the SiN6 octahedra are “NaCl-type” octahedra. Interatomic distances in the CrN6 octahedra are longer (1 × 1.92 Å-N, 2 × 1.97 Å-N, 2 × 1.98 Å-N, and 1 × 2.01 Å-N) than in the SiN6 octahedra (4 × 1.85 Å-N, 2 × 1.88 Å-N). The SiN6 octahedra are positioned in the center and at the edges of the cell, with the CrN6 octahedra connecting them. Both edge and corner connections are observed.
The next favorable modification obtained via DM is denoted as TiMn2O4-type [73]. It is a tetragonal structure in space group P4322 (no.95) with unit cell parameters a = 5.64 and c = 7.74 Å and is visualized in Figure 6a. In the TiMn2O4 phase, chromium is both four-fold and six-fold coordinated by nitrogen, thus, forming CrN4 tetrahedra (with atom–atom distances 2 × 1.78 Å-N and 2 × 1.81 Å-N) and CrN6 octahedra (with atom–atom distances 2 × 1.89 Å-N, 2 × 1.97 Å-N, and 2 × 2.05 Å-N). Silicon is six-fold coordinated by nitrogen with interatomic distances (2 × 1.86 Å-N and 4 × 1.91 Å-N). The octahedra are edge-connected, while the CrN4 tetrahedra are corner-connected.
The next modification obtained from the data mining search is a structure denoted as Mg2SiO4- (Forsterite) type of structure [74], and it crystallizes in space group Pnma (no. 62) with unit cell parameters a = 9.42, b = 5.45, and c = 4.82 Å. Within this modification, two types of CrN6 octahedra are connected by edges and oriented in the structure in two directions with interatomic distances (Cr(1) 2 × 1.92 Å-N, 2 × 1.98 Å-N, 2 × 2.00 Å-N, Cr(2) 1 × 1.88 Å-N, 2 × 1.95 Å-N, 2 × 2.00 Å-N, and 1 × 2.02 Å-N). Silicon is four-fold coordinated by nitrogen (with atom–atom distances 1 × 1.70 Å-N, 2 × 1.76 Å-N, and 1 × 1.77 Å-N) connected by the edges; the structure is visualized in Figure 6b.

3.2.2. Structural Analysis of Non-Favorable Candidates Found after Data Mining

The first non-favorable energy minimum found after data mining appears in the Ca2RuO4-type [75] and is visualized in Figure 7a. This is an orthorhombic structure that appears in space group Pbca (no. 61) with the unit cell parameters a = 4.55, b = 4.88, and c = 10.31 Å. Chromium and silicon are both six-fold coordinated by nitrogen but form different octahedra. Similar to the energetically favorable Na2MnCl4-type modification, within this modification, the CrN6 octahedra resemble those in the WC-type of structure with the interatomic distances 1 × 1.82 Å-N, 1 × 1.89 Å-N, 1 × 1.90 Å-N, 1 × 1.94 Å-N, 1 × 1.97 Å-N, and 1 × 2.49 Å-N.
These octahedra are connected by edges to each other; however, the connection to the SiN6 octahedra is via edges and corners as well. The whole structure consists of layers of different octahedra, where the SiN6 ones are located on the faces and in the center of the cell with the CrN6 octahedra situated in-between.
The next non-favorable modification found after data mining is denoted as a HgC2O4-like type of structure and crystallizes in space group P21 (no. 4). We note that the starting HgC2O4 structure [76] after DFT optimization has been structurally modified, however, within the same space group (no.4), thus, resulting in a HgC2O4-like structure. This is a monoclinic structure with the unit cell parameters a = 5.34, b = 5.09, c = 5.36, and β = 115.62, with the structural parameters with corresponding energies given in Table 4 and Table 5.
Within this structure, chromium is six-fold coordinated by nitrogen forming CrN6 octahedra (atom–atom distance Cr(1) 1 × 1.83 Å-N, 1 × 1.88 Å-N, 1 × 1.94 Å-N, 1 × 1.98 Å-N, 1 × 2.03 Å-N, 1 × 2.19 Å-N, Cr(2) 1 × 1.91 Å-N, 1 × 1.94 Å-N, 1 × 1.95 Å-N, 1 × 1.99 Å-N, 1 × 2.00 Å-N, and 1 × 2.09 Å-N), connected by faces and corners among each other. Silicon is four-fold coordinated forming edge- and corner-connected SiN4 tetrahedra with the interatomic distances 1 × 1.72 Å-N, 1 × 1.73 Å-N, 1 × 1.75 Å-N, and 1 × 1.77 Å-N. The structure is visualized in Figure 7b.
The next modification by energy shows a Ca2IrO4-type [77] structure; it exhibits the space group P-62m (no. 189) with the unit cell parameters a = 8.33 and c = 2.70 and is visualized in Figure 8a. Within the structure, chromium is six-fold and seven-fold coordinated by nitrogen with the interatomic distances Cr(1) 6 × 1.98 Å-N, Cr(2) 6 × 2.08 Å-N, 3 × 2.42 Å-N, Cr(3) 1 × 1.88 Å-N, 4 × 2.02 Å-N, and 2 × 2.18 Å-N. The CrN6 octahedra are face-connected resembling the ones in the WC-type of a structure, while the CrN7 polyhedra are edge- and corner-connected. Similarly, the SiN6 octahedra are edge- and corner-connected, with the atom–atom distances 2 × 1.76 Å-N, 2 × 1.79 Å-N, and 2 × 1.92 Å-N.
Another interesting modification obtained from the data mining search is the orthorhombic structure denoted as a CaB2O4-like structure, visualized in Figure 8b. This modification crystallizes in space group Pccn (no. 56) with the unit cell parameters a = 7.98, b = 14.42, and c = 4.85. Similarly, as with the HgC2O4-like modification, the CaB2O4-like structure is modified during the local optimization from the original prototypic CaB2O4 structure [78] but still within the same space group (no. 56).
In this structure, chromium is five-fold and six-fold coordinated by nitrogen forming two different polyhedra with the atom–atom distances Cr(1) 1 × 1.83 Å-N, 1 × 1.87 Å-N, 1 × 1.98 Å-N, 1 × 1.99 Å-N, 1 × 2.01 Å-N, 1 × 2.05 Å-N, Cr(2) 1 × 1.81 Å-N, 1 × 1.82 Å-N, 1 × 1.88 Å-N, 1 x 1.92 Å-N, and 1 x 2.07 Å-N, and one has a SiN5 polyhedron with the interaction distances 2 × 1.81 Å-N, 1 × 1.88 Å-N, and 2 × 1.90 Å-N.
A final interesting modification from the data mining search is denoted as Mn2SnS4-type [79] and is visualized in Figure 9. This orthorhombic structure appears in the space group Cmmm (no. 65) with the unit cell parameters a = 5.58, b = 7.82, and c = 2.76. In this structure, both chromium and silicon, are six-fold coordinated by nitrogen with edge-connected octahedra and the interatomic distances Cr 6 × 1.96 Å-N, Si 4 × 1.85 Å-N, and 2 × 1.93 Å-N.
We note that most of the structure candidates found using DM-based searches show orthorhombic symmetry (Table 5), in some cases reminiscent of the structurally related Si3N4 chemical system where orthorhombic structures have also been found [69]. In this context, we would like to remark on the Cu2HgI4 type of structure [80]. This structure type has been recently predicted to exist as a modification in a study of novel hard phases of Si3N4 [69].
The same Cu2HgI4 type has also been found in our DM-based searches; however, it is energetically much worse than most of the other DM or GO/PCAE-based structure candidates (Etot = −5193.312 Eh calculated using the GGA-PBE functional). Full structural optimization resulted in the original prototypic structure in tetragonal space group I-42m (no. 121) with unit cell parameters a = 4.34 and c = 8.09 Å, at the GGA-PBE level of computation (both chromium and silicon are fourfold coordinated by nitrogen forming tetrahedra with interatomic distances of Cr 4 × 1.80 Å-N and Si 4 × 1.75 Å-N).

3.3. Structural Searches Using the PCAE Method

Finally, the Primitive Cell approach for Atom Exchange (PCAE) method was employed for generating alternative structure candidates in the Cr2SiN4 compound, starting from typical structures in the related Si3N4 system, the γ-, β-, and α-phase of Si3N4. Ranking the ab initio minimized structures according to the calculated total energy using the GGA-PBE functional, the most promising candidates generated using the PCAE method are presented in Table 6.

Structural Details of Candidates Found Using the PCAE Method

The lowest energy minimum found using the PCAE method was denoted the γ-Cr2SiN4-type modification. Figure 10a shows a prototypic γ-phase in the Si3N4 system [71], which was used as starting structure for generating the γ-Cr2SiN4-type. The Si3N4 γ-phase crystallizes in the cubic space group I-43d (no. 220), [71] forming corner connected tetrahedra of silicon atoms (Figure 10a). However, after local optimization in the Cr2SiN4 system using both GGA-PBE and LDA-PZ functionals, it converts to the γ-Cr2SiN4-type modification. It is a low-energy candidate in the Cr2SiN4 system; however, it is structurally completely different from the starting γ-phase in the Si3N4 system (compare Figure 10a,b).
The γ-Cr2SiN4-type modification crystallizes in the monoclinic space group Cc (no. 9) with unit cell parameters a = 5.62, b = 8.96, c = 5.36 Å, and β = 117.93, with both cations—chromium and silicon—being six-fold coordinated by nitrogen where these octahedra are edge- and face-connected (Figure 10b). We deal with two different types of CrN6 octahedra with the interatomic distances Cr(1) 1 × 1.84 Å-N, 1 × 1.85 Å-N, 1 × 1.92 Å-N, 1 × 1.96 Å-N, 1 × 2.01 Å-N, 1 × 2.13 Å-N, Cr(2) 1 × 1.83 Å-N, 1 × 1.90 Å-N, 1 × 1.92 Å-N, 1 × 1.96 Å-N, 1 × 2.01 Å-N, and 1 × 2.03 Å-N; the atom–atom distances in the SiN6 octahedra are 1 × 1.74 Å-N, 1 × 1.75 Å-N, 1 × 1.81 Å-N, 1 × 2.08 Å-N, 1 × 2.20 Å-N, and 1 × 2.34 Å-N). In the closely related Si3N4 compound, there has been a prediction of novel monoclinic phases from first-principles calculations [69].
The next minimum found using the PCAE method is marked as Cr2SiN4-PCAE-1 phase, which is energetically less favorable than the γ-phase (Table 6). The Cr2SiN4-PCAE-1 type has been generated similarly to the previous one, starting from the β-phase of Si3N4 in the hexagonal P63/m (no. 176) space group [81,82]. After ab initio structural optimization in the Cr2SiN4 system, the structure converted to a monoclinic modification denoted Cr2SiN4-PCAE-1 that crystallizes in space group Pm (no. 6) with unit cell parameters a = 7.04465, b = 3.03610, c = 7.03270, β = 110.7203 (Table 7).
In this structure type, both chromium and silicon are four-fold and five-fold coordinated by nitrogen forming different types of polyhedra (Figure 11a). There are two different CrN4 tetrahedra and two different CrN5 polyhedra, with the atom–atom distances Cr(1) 2 × 1.86 Å-N, 1 × 1.89 Å-N, 1 × 1.95 Å-N, 1 × 2.01 Å-N, Cr(2) 2 × 1.81 Å-N, 1 × 1.88 Å-N, 1 × 1.92 Å-N, 1 × 1.93 Å-N, Cr(3) 2 × 1.74 Å-N, 1 × 1.75 Å-N, 1 × 1.99 Å-N, 1 × 2.18 Å-N, Cr(4) 2 × 1.77 Å-N, and 2 × 1.78 Å-N.
In the corners of the cell, there are four SiN4 tetrahedra with interatomic distances of 1 × 1.74 Å-N, 2 × 1.76 Å-N, and 1 × 1.83 Å-N. Additionally, there is one SiN5 polyhedron corner connected to one of the tetrahedra (atom–atom distances of 1 × 1.72 Å-N, 1 × 1.77 Å-N, 2 × 1.78 Å-N, and 1 × 2.49 Å-N), where chromium is completely located in the inner part of the unit cell, and the connection between polyhedra is formed via edges and corners (Figure 11a).
Structurally and energetically related is the Cr2SiN4-PCAE-2-type of structure presented as a final non-favorable structure candidate generated using the PCAE method. In this case, the α-type structure of Si3N4 with trigonal P31c (no. 159) space group [82,83] was used as starting point. However, after full structural optimization on the GGA-PBE level, the symmetry of the Cr2SiN4-PCAE-2-type is completely reduced to space group P1 (no. 1) with unit cell parameters of a = 7.87856, b = 7.96102, c = 5.78635, α = 89.9706, β = 89.8616, and γ = 120.2646 (Table 7).
Within this triclinic modification, both chromium and silicon are four-fold coordinated by nitrogen thus forming tetrahedra (Figure 11b). In this modification there are eight different CrN4 tetrahedra, with the atom–atom distances Cr(1) 1 × 1.77 Å-N, 2 × 1.80 Å-N, 1 × 1.86 Å-N, Cr(2) 2 × 1.78 Å-N, 1 × 1.79 Å-N, 1 × 1.81 Å-N, Cr(3) 2 × 1.79 Å-N, 2 × 1.80 Å-N, Cr(4) 1 × 1.77 Å-N, 1 × 1.78 Å-N, 1 × 1.80 Å-N, 1 × 1.81 Å-N, Cr(5) 1 × 1.77 Å-N, 1 × 1.79 Å-N, 1 × 1.81 Å-N, 1 × 1.87 Å-N, Cr(6) 1 × 1.78 Å-N, 1 × 1.80 Å-N, 2 × 1.82 Å-N, Cr(7) 1 × 1.78 Å-N, 2 × 1.79 Å-N, 1 × 1.81 Å-N, Cr(8) 1 × 1.78 Å-N, 2 × 1.79 Å-N, and 1 × 1.80 Å-N).
Silicon is also four-fold coordinated by nitrogen resulting in two different SiN4 tetrahedra with the interatomic distances Si1 1 × 1.73 Å-N, 1 × 1.74 Å-N, 1 × 1.75 Å-N, 1 × 1.76 Å-N, Si2 2 × 1.74 Å-N, and 2 × 1.75 Å-N. The SiN4 tetrahedra are mostly positioned at the corners of the cell with three tetrahedra located inside along with CrN4 tetrahedra located entirely inside the cell. Nevertheless, all tetrahedra within this phase are corner-connected (Figure 11b). A summary of the structural data of the presented PCAE structures is shown in Table 7; other structure candidates generated using the PCAE method were energetically much less favorable and, thus, have not been included.

3.4. Energy Landscape of Cr2SiN4 on the Ab Initio Level

The global optimization, data mining, and PCAE based searches resulted in structure candidates that were, after detailed structural and crystallographic analysis, reduced to the eleven energetically most favorable Cr2SiN4 modifications. Table 8 presents the energetic ranking of these modifications, where the Al2MgO4-spinel-type appears lowest in calculated total energy with the value of −5193.507 Eh, thus, representing the global minimum among the candidates obtained in the various searches. If the calculations are performed using DFT-LDA (Table A2), the spinel structure remains the global minimum, and the energetic ranking of the other modifications is very similar, with few exceptions.
Figure 12 presents the energy versus volume (E(V)) curves on the ab initio level using the GGA-PBE functional for the energetically most favorable Cr2SiN4 modifications. We note that the global minimum in the Cr2SiN4 system is the Al2MgO4-spinel phase. This prominence of the Al2MgO4-type candidate on the energy landscape of Cr2SiN4 is not unreasonable, since several earlier calculations in the related (binary) Si3N4 system have also found a Al2MgO4-spinel-like phase [71,84,85].
At high-temperature conditions, one might expect structures, like the β-, ε-, λ-, and λʹ-Cr2SiN4-type to possibly become competitive, as well as the TiMn2O4-type and Mg2SiO4-type modifications from the DM-based searches. Similarly, the most relevant modifications that might appear in the high-pressure region are the Na2MnCl4-type, and the α-, γ-, and δ-Cr2SiN4-types. Therefore, enthalpy vs. pressure, H(p), curves were computed for these five modifications (Figure 13).
A high-pressure phase transition was predicted between the spinel and the Na2MnCl4-type at a pressure of ~33 GPa (Figure 13). In addition, there was a phase transition between the Na2MnCl4-type and the metastable α-Cr2SiN4-type modifications at ~15 GPa (Figure 13), i.e., the α-phase was more stable than the Na2MnCl4-type modification below 15 GPa in the Cr2SiN4 system.
In summary, the energy landscape of Cr2SiN4 is highly complex with a wide range of structurally different modifications possible. On the ab initio level, the global minimum corresponds to the AlMg2O4-type of structure. This modification is also known as a spinel structure, formulated as AB2X4, with a fcc close-packed array of anions X, and A and B cations occupying some or all of the octahedral and tetrahedral sites in the lattice, respectively. The structural features found in this structure type are the most dominant ones in the low-energy region of the landscape of Cr2SiN4 at standard pressure, where most of the structures are found to exhibit an octahedral coordination of chromium by nitrogen and a tetrahedral one for silicon, respectively.
However, some of the structure candidates observed exhibit six-fold coordination with an octahedral environment for both Cr and Si atoms (e.g., the γ- and the δ-Cr2SiN4-type, the Na2MnCl4-type, and the Mn2SnS4-type), while there is only one stable modification (Cr2SiN4-PCAE-2-type) exhibiting tetrahedral coordination by nitrogen for both cations. In addition, a few structures show unusual five-fold and seven-fold coordination, but these are energetically non-favorable.
The appearance of spinel as a global minimum in Cr2SiN4 and the observation of analogous coordination environments of Cr and Si in most of the structures found as low-energy minima on the landscape are strong indications that this compound should be synthetically accessible. Furthermore, a spinel-type modification of Cr2SiN4 could be of great importance, since ferrite spinels and related structures are of technological interest due to their magnetic ordering, which can be ferrimagnetic or antiferromagnetic depending on the structure and the nature of the metal ions.
Similarly, the results of recent investigations demonstrating that spinel coatings can be used to protect metals, such as chromium, from oxidation or corrosion, serve as another indication for the possible technological and industrial usefulness of the proposed Cr2SiN4 structure candidates [86,87,88]. Another interesting point is that the global minimum AlMg2O4-spinel-type of the structure shows the highest cubic Fd-3m symmetry, while most of the predicted structure candidates show much lower symmetry.
Here, we note that the spinel structure contains so many atoms that it was not feasible to be realized in the periodic simulation cell employed for the global optimizations; as a consequence, the closely related α-Cr2SiN4-type structure was obtained instead. Quite generally, data-mining-based searches produced high-symmetry candidates (except for the HgC2O4-type, which is monoclinic), while global optimization and the PCAE method mostly produced structures with lower symmetry, with the orthorhombic space group Pma2 (no. 28) of the α-Cr2SiN4-type as the highest symmetry space group.
We note that each of the methods used brought us a new perspective: data mining found the global minimum and suggested known structure types that can be stable in the Cr2SiN4 system, the global optimization resulted in a large number of new unknown but kinetically stable low-energy structures and provided a general overview over the broad structural variety present in the system at low energies, while the PCAE method generated the most diverse modifications, ranging from structures consisting of networks with only tetrahedral coordination polyhedra of the cations by nitrogen to modifications with only octahedral coordination environments.

4. Conclusions

A combination of global optimization, data mining, and the PCAE method was used to explore the energy landscape of Cr2SiN4 and to perform structure prediction in the Cr2SiN4 system. Global optimization was performed using simulated annealing and a fast computable robust empirical two-body potential. Data-mining-based searches reduced a large number of crystal structures from the ICSD database to four energetically favorable structures and five structure candidates that might be feasible modifications at extreme conditions for the not-yet-synthesized Cr2SiN4 compound.
Additionally, the Primitive Cell approach for Atom Exchange (PCAE) method was employed for generating alternative structure candidates in the Cr2SiN4 system with starting modifications taken from the related Si3N4 chemical system. Every structure candidate found in these searches was subjected to crystallographic analysis and all the promising ones to a local optimization on the ab initio level.
The local optimizations were performed on the DFT level employing the LDA-PZ and the GGA-PBE functional, for comparison, since there exists no experimental data that one could compare the results with. There was good agreement between the results from the two chosen functionals regarding the total energy ranking, space group symmetry, and other structural data of the various structure candidates after relaxation, which strongly supports the plausibility of the proposed candidates to correspond to actual (meta)stable modifications in the Cr2SiN4 system.
The explorations of the energy landscape of the Cr2SiN4 system resulted in numerous predicted new structures/modifications not yet observed in the experiment. Within each method used in this study, we grouped our results into energetically favorable and non-favorable Cr2SiN4 modifications, with the latter ones perhaps accessible for extreme thermodynamic conditions. Among the eleven energetically most favorable candidates, the global minimum was the AlMg2O4-spinel-type exhibiting the cubic Fd-3m symmetry.
At high pressures of ca. ~33 GPa, a phase transition between the spinel-type and the Na2MnCl4-type modifications should take place. Thus, we present a large number of feasible structures for modifications in the synthetically not-yet-explored Cr2SiN4 system, which might be suitable for many technological applications, such as high-speed cutting, wood machining applications, hydraulic piston pumps, valves, gears, shafts, and propellers, as corrosion-resistant coatings and low-cost water-based lubricating systems.

Author Contributions

Conceptualization, D.Z., B.M., J.C.S. and T.Š.; methodology, D.Z., M.P. and T.Š.; data curation, J.C.S., T.Š., D.Z. and M.P.; writing—original draft preparation, T.Š., D.Z. and M.P.; writing—review and editing, D.Z., B.M. and J.C.S. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by the Ministry of Education, Science and Technological Development of Serbia (Project number: 1702001).

Data Availability Statement

Additional data may be requested from the first author.

Conflicts of Interest

The authors declare no conflict of interest.

Appendix A

Table A1. The modifications, space groups, unit cell parameters, and atomic positions for the most favorable Cr2SiN4 modifications after structural optimization on the DFT-LDA level.
Table A1. The modifications, space groups, unit cell parameters, and atomic positions for the most favorable Cr2SiN4 modifications after structural optimization on the DFT-LDA level.
Modifications and Space GroupsCell ParametersPosition of Atoms
Al2MgO4-spinel-type_LDA
Fd-3m
No 227
a = 7.76Cr 0.000000 0.000000 0.000000
Si 0.625000 0.625000 0.625000
N 0.752556 0.752556 0.752556
α-Cr2SiN4-type_LDA
Pma2
No 28
a = 5.45 b = 7.80 c = 2.76Cr 0.750000 0.241721 0.552936
Cr 0.500000 0.000000 0.898141
Si 0.750000 0.614777 0.000000
N 0.750000 0.006165 0.421951
N 0.750000 0.489793 0.499478
N 0.501351 0.244258 0.983987
Na2MnCl4-type_LDA
Pbam
No 55
a = 4.67 b = 8.58 c = 2.69Cr 0.432611 0.175929 0.500000
Si 0.000000 0.000000 0.000000
N 0.133271 0.203741 0.000000
N 0.257704 0.966687 0.500000
γ-Cr2SiN4-type_LDA
Cc
No 9
a = 5.56 b = 8.82 c = 5.25 β = 117.96Cr 0.499339 0.356416 0.521849
Cr 0.490863 0.639616 0.502192
Si 0.000000 0.578114 0.000000
N 0.817340 0.495466 0.665199
N 0.336682 0.499101 0.681972
N 0.677149 0.750383 0.851076
N 0.670732 0.238989 0.855745
β-Cr2SiN4-type_LDA
P-1
No 2
a = 7.18 b = 7.69 c = 2.70 α = 94.01 β = 82.69 γ = 121.02Cr 0.350127 0.864148 0.734578
Cr 0.863665 0.518329 0.302902
Si 0.625158 0.737213 0.910010
N 0.050410 0.680530 0.762885
N 0.352905 0.668370 0.167669
N 0.662487 0.971411 0.739846
N 0.713401 0.667644 0.365727
δ-Cr2SiN4-type_LDA
P21/m
No 11
a = 6.14 b = 3.76 c = 5.41 β = 115.88Cr 0.091491 0.750000 0.659687
Cr 0.148173 0.750000 0.246670
Si 0.610570 0.750000 0.913336
N 0.638880 0.250000 0.419381
N 0.142755 0.250000 0.721438
N 0.367862 0.750000 0.044580
N 0.131910 0.250000 0.172992
TiMn2O4-type_LDA
P4322
No 95
a = 5.56 c = 7.61Cr 0.500000 0.290089 0.000000
Cr 0.233800 0.233800 0.625000
Si 0.000000 0.260505 0.000000
N 0.238872 0.500821 0.998335
N 0.247363 0.028667 0.009638
Mg2SiO4-type_LDA
Pnma
No 62
a = 9.23 b = 5.35 c = 4.77Cr 0.500000 0.500000 0.500000
Cr 0.752388 0.750000 0.005094
Si 0.911386 0.750000 0.581141
N 0.915976 0.750000 0.228570
N 0.580994 0.750000 0.754642
N 0.831042 0.496221 0.748887
ε-Cr2SiN4-type_LDA
P21/m
No 11
a = 5.07 b = 2.86 c = 8.45 β = 90.40Cr 0.780604 0.250000 0.510721
Cr 0.923710 0.750000 0.845133
Si 0.427115 0.250000 0.804711
N 0.570806 0.750000 0.868258
N 0.885468 0.750000 0.109395
N 0.589494 0.750000 0.396942
N 0.052827 0.250000 0.362060
λ-Cr2SiN4-type_LDA
Pm
No 6
a = 4.96 b = 2.84 c = 8.88 β = 98.40Cr 0.914225 0.500000 0.418382
Cr 0.707639 0.500000 0.700020
Cr 0.303954 0.000000 0.721261
Cr 0.508118 0.500000 0.052804
Si 0.000000 0.000000 0.000000
Si 0.419874 0.000000 0.378878
N 0.545716 0.000000 0.572397
N 0.460020 0.500000 0.846268
N 0.704067 0.000000 0.081337
N 0.551407 0.500000 0.308625
N 0.057263 0.500000 0.603299
N 0.068995 0.000000 0.346274
N 0.943534 0.000000 0.807418
N 0.155450 0.500000 0.072091
λ’-Cr2SiN4-type_LDA
Pm
No 6
a = 4.99 b = 2.82 c = 8.84 β = 90.95Cr 0.175453 0.500000 0.329781
Cr 0.898546 0.500000 0.677506
Cr 0.311343 0.000000 0.668615
Cr 0.483688 0.500000 0.973214
Si 0.000000 0.000000 0.000000
Si 0.681904 0.000000 0.380834
N 0.683473 0.000000 0.573821
N 0.506564 0.500000 0.783113
N 0.663254 0.000000 0.037342
N 0.818343 0.500000 0.305474
N 0.181392 0.500000 0.535694
N 0.363881 0.000000 0.300294
N 0.023309 0.000000 0.806317
N 0.153474 0.500000 0.070996
Table A2. The total energy and relative energy values compared to the global minimum (spinel structure taken as the zero of energy) of the energetically most favorable Cr2SiN4 modifications found using various search methods and later locally optimized on the ab initio level using the LDA-PZ functional. DM stands for data mining, GO stands for global optimization, and PCAE stands for primitive cell approach for atom exchange methods.
Table A2. The total energy and relative energy values compared to the global minimum (spinel structure taken as the zero of energy) of the energetically most favorable Cr2SiN4 modifications found using various search methods and later locally optimized on the ab initio level using the LDA-PZ functional. DM stands for data mining, GO stands for global optimization, and PCAE stands for primitive cell approach for atom exchange methods.
Modification
and Space Group
Search MethodTotal Energy
(Eh)
Relative Energy
(kcal/mol)
Al2MgO4-spinel-type_LDADM−5180.7290.0
α-Cr2SiN4-type_LDAGO−5180.69421.963
Na2MnCl4-type_LDADM−5180.67235.768
γ-Cr2SiN4-type_LDAPCAE−5180.66738.906
β-Cr2SiN4-type_LDAGO−5180.65347.691
δ-Cr2SiN4-type_LDAGO−5180.65347.691
TiMn2O4-type_LDADM−5180.62167.771
Mg2SiO4-type_LDADM−5180.62068.399
ε-Cr2SiN4-type_LDAGO−5180.61571.536
λ-Cr2SiN4-type_LDAGO−5180.60677.184
λ’-Cr2SiN4-type_LDAGO−5180.60478.439

References

  1. Benlatreche, Y.; Nouveau, C.; Aknouche, H.; Imhoff, L.; Martin, N.; Gavoille, J.; Rousselot, C.; Rauch, J.-Y.; Pilloud, D. Physical and Mechanical Properties of CrAlN and CrSiN Ternary Systems for Wood Machining Applications. Plasma Process. Polym. 2009, 6, S113–S117. [Google Scholar] [CrossRef] [Green Version]
  2. Wang, H.; Ye, Y.; Wang, Y. Structure, corrosion, and tribological properties of CrSiN coatings with various Si contents in 3.5% NaCl solution. Surf. Interface Anal. 2018, 50, 471–479. [Google Scholar] [CrossRef]
  3. Yang, D.; Chen, H.; Ye, Y.; Wang, C.; Zhao, H.; Gong, D. Doping silicon to enhance the anti-corrosion and anti-wear abilities of chromium nitride coating in seawater. Surf. Topogr. Metrol. Prop. 2018, 6, 044001. [Google Scholar] [CrossRef]
  4. Iwasaki, Y.; Mizuno, Y.; Nakayama, T.; Suzuki, T. Preparation of Cr–Si–N–O thin films epitaxially grown on MgO substrates by pulsed laser deposition. Vaccum 2020, 179, 109498. [Google Scholar] [CrossRef]
  5. Mercs, D.; Bonasso, N.; Naamane, S.; Bordes, J.-M.; Coddet, C. Mechanical and tribological properties of Cr–N and Cr–SI–N coatings reactively sputter deposited. Surf. Coat. Technol. 2005, 200, 403–407. [Google Scholar] [CrossRef]
  6. Kim, J.W.; Kim, K.H.; Lee, D.; Moore, J. Study on high-temperature oxidation behaviors of Cr–Si–N films. Surf. Coat. Technol. 2006, 200, 6702–6705. [Google Scholar] [CrossRef]
  7. Lee, J.-W.; Kuo, Y.-C.; Wang, C.-J.; Chang, L.-C.; Liu, K.-T. Effects of substrate bias frequencies on the characteristics of chromium nitride coatings deposited by pulsed DC reactive magnetron sputtering. Surf. Coat. Technol. 2008, 203, 721–725. [Google Scholar] [CrossRef]
  8. Dinu, M.; Mouele, E.S.M.; Parau, A.C.; Vladescu, A.; Petrik, L.F.; Braic, M. Enhancement of the Corrosion Resistance of 304 Stainless Steel by Cr–N and Cr(N,O) Coatings. Coatings 2018, 8, 132. [Google Scholar] [CrossRef] [Green Version]
  9. Meng, C.; Yang, L.; Wu, Y.; Tan, J.; Dang, W.; He, X.; Ma, X. Study of the oxidation behavior of CrN coating on Zr alloy in air. J. Nucl. Mater. 2019, 515, 354–369. [Google Scholar] [CrossRef]
  10. Lin, J.; Zhang, N.; Sproul, W.D.; Moore, J.J. A comparison of the oxidation behavior of CrN films deposited using continuous dc, pulsed dc and modulated pulsed power magnetron sputtering. Surf. Coat. Technol. 2012, 206, 3283–3290. [Google Scholar] [CrossRef]
  11. Shan, L.; Wang, Y.; Li, J.; Jiang, X.; Chen, J. Improving tribological performance of CrN coatings in seawater by structure design. Tribol. Int. 2015, 82, 78–88. [Google Scholar] [CrossRef]
  12. Shah, H.N.; Jayaganthan, R.; Kaur, D. Influence of reactive gas and temperature on structural properties of magnetron sputtered CrSiN coatings. Appl. Surf. Sci. 2011, 257, 5535–5543. [Google Scholar] [CrossRef]
  13. Wo, P.; Munroe, P.; Li, Z.; Jiang, Z.-T.; Xie, Z.; Zhou, Z.; Li, K.Y. Factors governing the mechanical behaviour of CrSiN coatings: Combined nanoindentation testing and transmission electron microscopy. Mater. Sci. Eng. A 2012, 534, 297–308. [Google Scholar] [CrossRef] [Green Version]
  14. Bobzin, K.; Bagcivan, N.; Immich, P.; Bolz, S.; Cremer, R.; Leyendecker, T. Mechanical properties and oxidation behaviour of (Al,Cr)N and (Al,Cr,Si)N coatings for cutting tools deposited by HPPMS. Thin Solid Films 2008, 517, 1251–1256. [Google Scholar] [CrossRef]
  15. Vepřek, S. New development in superhard coatings: The superhard nanocrystalline-amorphous composites. Thin Solid Films 1998, 317, 449–454. [Google Scholar] [CrossRef]
  16. Morgiel, J.; Grzonka, J.; Mania, R.; Zimowski, S.; Lábár, J.L.; Fogarassy, Z. Relation between microstructure and hardness of nano-composite CrN/Si3N4 coatings obtained using CrSi single target magnetron system. Vaccum 2013, 90, 170–175. [Google Scholar] [CrossRef]
  17. Martinez, E.; Sanjinés, R.; Karimi, A.; Esteve, J.; Lévy, F. Mechanical properties of nanocomposite and multilayered Cr–Si–N sputtered thin films. Surf. Coat. Technol. 2004, 180–181, 570–574. [Google Scholar] [CrossRef]
  18. Park, J.H.; Chung, W.S.; Cho, Y.-R.; Kim, K.H. Synthesis and mechanical properties of Cr–Si–N coatings deposited by a hybrid system of arc ion plating and sputtering techniques. Surf. Coat. Technol. 2004, 188–189, 425–430. [Google Scholar] [CrossRef]
  19. Lin, H.-H.; Chou, C.-C.; Lee, J.-W. Tribological properties of Cr–Si–N nanocomposite film adherent silicon under various environments. Thin Solid Films 2010, 518, 7509–7514. [Google Scholar] [CrossRef]
  20. Azzi, M.; Benkahoul, M.; Szpunar, J.; Klemberg-Sapieha, J.; Martinu, L. Tribological properties of CrSiN-coated 301 stainless steel under wet and dry conditions. Wear 2009, 267, 882–889. [Google Scholar] [CrossRef]
  21. Lee, J.-W.; Chang, Y.-C. A study on the microstructures and mechanical properties of pulsed DC reactive magnetron sputtered Cr–Si–N nanocomposite coatings. Surf. Coat. Technol. 2007, 202, 831–836. [Google Scholar] [CrossRef]
  22. Lee, H.; Jung, W.; Han, J.; Seo, S.; Kim, J.; Bae, Y. The synthesis of CrSiN film deposited using magnetron sputtering system. Surf. Coat. Technol. 2005, 200, 1026–1030. [Google Scholar] [CrossRef]
  23. Zhang, G.; Wang, L.; Wang, S.; Yan, P.; Xue, Q. Structure and mechanical properties of reactive sputtering CrSiN films. Appl. Surf. Sci. 2009, 255, 4425–4429. [Google Scholar] [CrossRef] [Green Version]
  24. Geng, Z.; Wang, H.; Wang, C.; Wang, L.; Zhang, G. Effect of Si content on the tribological properties of CrSiN films in air and water environments. Tribol. Int. 2014, 79, 140–150. [Google Scholar] [CrossRef]
  25. Shao, T.; Ge, F.; Pei, C.; Huang, F.; Sun, D.; Zhang, S. Effects of Si content on Tribo-corrosion behavior of Cr1−xSixN coatings prepared via magnetron sputtering. Surf. Coat. Technol. 2018, 356, 11–18. [Google Scholar] [CrossRef]
  26. Shan, L.; Zhang, Y.-R.; Wang, Y.-X.; Li, J.-L.; Jiang, X.; Chen, J.-M. Corrosion and wear behaviors of PVD CrN and CrSiN coatings in seawater. Trans. Nonferr. Met. Soc. China 2016, 26, 175–184. [Google Scholar] [CrossRef]
  27. Park, I.-W.; Kang, D.S.; Moore, J.J.; Kwon, S.C.; Rha, J.J.; Kim, K.H. Microstructures, mechanical properties, and tribological behaviors of Cr–Al–N, Cr–Si–N, and Cr–Al–Si–N coatings by a hybrid coating system. Surf. Coat. Technol. 2007, 201, 5223–5227. [Google Scholar] [CrossRef]
  28. Lu, S.; Wang, Y.; Gaoand, P.; Meng, D. Effect of Si Content on Structure and Friction and Wear Properties of CrSiN Coatings. IOP Conf. Ser. Earth Environ. Sci. 2020, 440, 022028. [Google Scholar] [CrossRef]
  29. Wang, Q.; Lin, Y.; Zhou, F.; Kong, J. The influence of Ni concentration on the structure, mechanical and tribological properties of Ni–CrSiN coatings in seawater. J. Alloy. Compd. 2020, 819, 152998. [Google Scholar] [CrossRef]
  30. Kim, G.; Kim, B.; Lee, S. High-speed wear behaviors of CrSiN coatings for the industrial applications of water hydraulics. Surf. Coat. Technol. 2005, 200, 1814–1818. [Google Scholar] [CrossRef]
  31. Chang, W.J.; Zhang, H.; Chen, Y.Y.; Li, J.; Zhang, X.; Jiang, P.Z.; Fan, X.W.; Duo, S.W. Tribological Performances of CrSiN Coatings Deposited by High Power Pulse Magnetron Sputtering. Solid State Phenom. 2018, 281, 540–545. [Google Scholar] [CrossRef]
  32. Lou, B.-S.; Chang, Y.-C.; Lee, J.-W. High Temperature Oxidation Behaviors of CrNx and Cr-Si-N Thin Films at 1000 °C. Coatings 2019, 9, 540. [Google Scholar] [CrossRef] [Green Version]
  33. Mikula, M.; Grančič, B.; Drienovsky, M.; Satrapinskyy, L.; Roch, T.; Hájovská, Z.; Gregor, M.; Plecenik, T.; Čička, R.; Kúš, P. Thermal stability and high-temperature oxidation behavior of Si–Cr–N coatings with high content of silicon. Surf. Coat. Technol. 2013, 232, 349–356. [Google Scholar] [CrossRef]
  34. Suzuki, K.; Suzuki, T.; Endo, T.; Nakayama, T.; Suematsu, H.; Niihara, K. Epitaxial growth of chromium nitride thin films with addition of silicon. Phys. Status Solidi 2015, 12, 545–548. [Google Scholar] [CrossRef]
  35. Xu, X.M.; Zhang, H.; Luo, F.F.; Zhou, Z.H.; Duo, S.W. The Properties of CrSiN Coatings of Different Si Content. Appl. Mech. Mater. 2014, 687–691, 4323–4326. [Google Scholar] [CrossRef]
  36. Wang, Q.M.; Kim, K.H. Microstructural control of Cr–Si–N films by a hybrid arc ion plating and magnetron sputtering process. Acta Mater. 2009, 57, 4974–4987. [Google Scholar] [CrossRef]
  37. Martínez, E.; Sanjinés, R.; Banakh, O.; Lévy, F. Electrical, optical and mechanical properties of sputtered CrNy and Cr1−xSixN1.02 thin films. Thin Solid Films 2004, 447–448, 332–336. [Google Scholar] [CrossRef]
  38. Ma, B.; Luo, B.; Wang, Z.; Meng, C.; He, X. Friction and Wear Properties of CrAl-Based Coatings for Nuclear Fuel Cladding. Front. Energy Res. 2021, 9, 24. [Google Scholar] [CrossRef]
  39. Zagorac, J.; Schön, J.C.; Matović, B.; Škundrić, T. Predicting Feasible Modifications of Ce2ON2 Using a Combination of Global Optimization and Data Mining. J. Phase Equilibria Diffus. 2020, 41, 538–549. [Google Scholar] [CrossRef]
  40. Zagorac, D.; Zagorac, J.; Schön, J.C.; Stojanović, N.; Matović, B. ZnO/ZnS (hetero)structures: Ab initio investigations of polytypic behavior of mixed ZnO and ZnS compounds. Acta Crystallogr. Sect. B Struct. Sci. Cryst. Eng. Mater. 2018, 74, 628–642. [Google Scholar] [CrossRef]
  41. Kirkpatrick, S.; Gelatt, C.D.; Vecchi, M.P. Optimization by Simulated Annealing. Science 1983, 220, 671–680. [Google Scholar] [CrossRef] [PubMed]
  42. Schön, J.C. Nanomaterials—What energy landscapes can tell us. Process. Appl. Ceram. 2015, 9, 157–168. [Google Scholar] [CrossRef]
  43. Schön, J.C.; Jansen, M. Determination of candidate structures for simple ionic compounds through cell optimisation. Comput. Mater. Sci. 1995, 4, 43–58. [Google Scholar] [CrossRef]
  44. Bergerhoff, G.; Brown, I.D. Crystallographic Databases; Allen, F.H., Bergerhoff, G., Sievers, R., Eds.; International Union of Crystallography: Chester, UK, 1987. [Google Scholar]
  45. Zagorac, D.; Müller, H.; Ruehl, S.; Rehme, S. Recent developments in the Inorganic Crystal Structure Database: Theoretical crystal structure data and related features. J. Appl. Crystallogr. 2019, 52, 918–925. [Google Scholar] [CrossRef] [Green Version]
  46. Zagorac, J.; Rosic, M.; Schön, J.C.; Matovic, B. Structure prediction of aluminum nitride combining data mining and quantum mechanics. CrystEngComm 2017, 19, 5259–5268. [Google Scholar] [CrossRef]
  47. Cvijović-Alagić, I.; Rakin, M.; Laketić, S.; Zagorac, D. Microstructural study of Ti45Nb alloy before and after HPT processing using experimental and ab initio data mining approach. Mater. Charact. 2020, 169, 110635. [Google Scholar] [CrossRef]
  48. Zagorac, J.; Jovanovic, D.; Volkov-Husovic, T.; Matovic, B.; Zagorac, D. Structure prediction, high pressure effect and properties investigation of superhard B6O. Model. Simul. Mater. Sci. Eng. 2020, 28. [Google Scholar] [CrossRef]
  49. Dovesi, R.; Erba, A.; Orlando, R.; Zicovich-Wilson, C.M.; Civalleri, B.; Maschio, L.; Rérat, M.; Casassa, S.; Baima, J.; Salustro, S.; et al. Quantum-mechanical condensed matter simulations with CRYSTAL. Wiley Interdiscip. Rev. Comput. Mol. Sci. 2018, 8, e1360. [Google Scholar] [CrossRef]
  50. Dovesi, R.; Pascale, F.; Civalleri, B.; Doll, K.; Harrison, N.M.; Bush, I.; D’Arco, P.; Noël, Y.; Rérat, M.; Carbonnière, P.; et al. The CRYSTAL code, 1976–2020 and beyond, a long story. J. Chem. Phys. 2020, 152, 204111. [Google Scholar] [CrossRef] [PubMed]
  51. Doll, K.; Saunders, V.R.; Harrison, N.M. Analytical Hartree–Fock gradients for periodic systems. Int. J. Quantum Chem. 2001, 82, 1–13. [Google Scholar] [CrossRef] [Green Version]
  52. Doll, K.; Dovesi, R.; Orlando, R. Analytical Hartree–Fock gradients with respect to the cell parameter for systems periodic in three dimensions. Theor. Chem. Acc. 2004, 112, 394–402. [Google Scholar] [CrossRef] [Green Version]
  53. Perdew, J.P.; Zunger, A. Self-interaction correction to density-functional approximations for many-electron systems. Phys. Rev. B 1981, 23, 5048–5079. [Google Scholar] [CrossRef] [Green Version]
  54. Perdew, J.P.; Burke, K.; Ernzerhof, M. Generalized gradient approximation made simple. Phys. Rev. Lett. 1996, 77, 3865–3868. [Google Scholar] [CrossRef] [Green Version]
  55. Schön, J.C.; Čančarević, Ž.; Jansen, M. Structure prediction of high-pressure phases for alkali metal sulfides. J. Chem. Phys. 2004, 121, 2289–2304. [Google Scholar] [CrossRef] [PubMed]
  56. Zagorac, D.; Doll, K.; Schön, J.C.; Jansen, M. Ab initiostructure prediction for lead sulfide at standard and elevated pressures. Phys. Rev. B 2011, 84, 045206. [Google Scholar] [CrossRef]
  57. Zagorac, J.; Schön, J.C.; Jansen, M. Prediction of structure candidates for zinc oxide as a function of pressure and investigation of their electronic properties. Phys. Rev. B 2014, 89, 075201. [Google Scholar] [CrossRef]
  58. Catti, M.; Sandrone, G.; Valerio, G.; Dovesi, R. Electronic, magnetic and crystal structure of Cr2O3 by theoretical methods. J. Phys. Chem. Solids 1996, 57, 1735–1741. [Google Scholar] [CrossRef]
  59. Ruiz, E.; Llunell, M.; Alemany, P. Calculation of exchange coupling constants in solid state transition metal compounds using localized atomic orbital basis sets. J. Solid State Chem. 2003, 176, 400–411. [Google Scholar] [CrossRef]
  60. Pascale, F.; Zicovich-Wilson, C.; Orlando, R.; Roetti, C.; Ugliengo, P.; Dovesi, R. Vibration Frequencies of Mg3Al2Si3O12 Pyrope. An ab Initio Study with the CRYSTAL Code. J. Phys. Chem. B 2005, 109, 6146–6152. [Google Scholar] [CrossRef] [PubMed]
  61. Noel, Y.; Catti, M.; D’Arco, P.; Dovesi, R. The vibrational frequencies of forsterite Mg2SiO4: An all-electron ab initio study with the CRYSTAL code. Phys. Chem. Miner. 2006, 33, 383–393. [Google Scholar] [CrossRef]
  62. Dovesi, R.; Causa’, M.; Orlando, R.; Roetti, C.; Saunders, V.R. Ab initio approach to molecular crystals: A periodic Hartree–Fock study of crystalline urea. J. Chem. Phys. 1990, 92, 7402–7411. [Google Scholar] [CrossRef]
  63. Zagorac, D.; Djukic, M.; Jordanov, D.; Matović, B. Theoretical study of AlN mechanical behaviour under high pressure regime. Theor. Appl. Fract. Mech. 2019, 103, 102289. [Google Scholar] [CrossRef]
  64. Hundt, R.; Schön, J.C.; Hannemann, A.; Jansen, M. Determination of symmetries and idealized cell parameters for simulated structures. J. Appl. Crystallogr. 1999, 32, 413–416. [Google Scholar] [CrossRef] [Green Version]
  65. Hannemann, A.; Hundt, R.; Schön, J.C.; Jansen, M. A New Algorithm for Space-Group Determination. J. Appl. Crystallogr. 1998, 31, 922–928. [Google Scholar] [CrossRef]
  66. Hundt, R.; Schön, J.C.; Jansen, M. CMPZ– an algorithm for the efficient comparison of periodic structures. J. Appl. Crystallogr. 2006, 39, 6–16. [Google Scholar] [CrossRef] [Green Version]
  67. Hundt, R. KPLOT: A Program for Plotting and Analysing Crystal Structures; Technicum Scientific Publishing: Stuttgart, Germany, 2016. [Google Scholar]
  68. Momma, K.; Izumi, F. VESTA 3 for three-dimensional visualization of crystal, volumetric and morphology data. J. Appl. Crystallogr. 2011, 44, 1272–1276. [Google Scholar] [CrossRef]
  69. Cui, L.; Hu, M.; Wang, Q.; Xu, B.; Yu, D.; Liu, Z.; He, J. Prediction of novel hard phases of Si3N4: First-principles calculations. J. Solid State Chem. 2015, 228, 20–26. [Google Scholar] [CrossRef]
  70. Yamanaka, T.; Takéuchi, Y. Order-disorder transition in MgAl2O4 spinel at high temperatures up to 1700 °C. Z. Krist. 1983, 165, 65–78. [Google Scholar] [CrossRef]
  71. Kroll, P. Pathways to metastable nitride structures. J. Solid State Chem. 2003, 176, 530–537. [Google Scholar] [CrossRef]
  72. Goodyear, J.; Ali, S.A.D.; Steigmann, G.A. The crystal structure of Na2MnCl4. Acta Crystallogr. Sect. B Struct. Crystallogr. Cryst. Chem. 1971, 27, 1672–1674. [Google Scholar] [CrossRef]
  73. Bertaut, E.; Vincent, H. Etude par diffraction neutronique de la forme ordonnee de l’orthotitanate de manganese-structure cristalline et structure magnetique. Solid State Commun. 1968, 6, 269–275. [Google Scholar] [CrossRef]
  74. Smyth, J.; Hazen, R. The crystal structures of forsterite and hortonolite at several temperatures up to 900 °C. Am. Mineral. 1973, 58, 588–593. [Google Scholar]
  75. Friedt, O.; Braden, M.; André, G.; Adelmann, P.; Nakatsuji, S.; Maeno, Y. Structural and magnetic aspects of the metal-insulator transition inCa2−xSrxRuO4. Phys. Rev. B 2001, 63, 174432. [Google Scholar] [CrossRef] [Green Version]
  76. Christensen, A.N.; Norby, P.; Hanson, J.C. A crystal structure determination of HgC2O4 from synchrotron X-ray and neutron powder diffraction data. Z. Krist. Cryst. Mater. 1994, 209, 874–877. [Google Scholar] [CrossRef]
  77. Matar, S.F.; Etourneau, J. (CaO)nIrO2 (n = 1, 2, 4) family: Chemical scissors effects of CaO on structural characteristics correlated to physical properties. Ab initio study. J. Solid State Chem. 2017, 255, 82–88. [Google Scholar] [CrossRef]
  78. Shashkin, D.P.; Simonov, M.A.; Belov, N.V. Crystalline structure of calciborite—CaB2O4=Ca2[BO3BO]2. Dokl. Akad. Nauk SSSR 1970, 195, 345–348. [Google Scholar]
  79. Partik, M.; Stingl, T.; Lutz, H.D.; Sabrowsky, H.; Vogt, P. Strukturverfeinerung und magnetische Messungen an Mn2SnS4. Z. Anorg. Allg. Chem. 1995, 621, 1600–1604. [Google Scholar] [CrossRef]
  80. Hahn, H.; Klingler, W. Zur Struktur des βCu2HgJ4 und des β-Ag2HgJ4. Z. Anorg. Allg. Chem. 1955, 279, 271–280. [Google Scholar] [CrossRef]
  81. Schneider, J.; Johnson, F.N.; Laschke, K. Structure refinements of β-Si3N4 at temperatures up to 1360 °C by X-ray powder investigation. Z. Krist. Cryst. Mater. 1994, 209, 328–333. [Google Scholar] [CrossRef]
  82. Yang, P.; Fun, H.K.; Rahman, I.A.; Saleh, M. Two phase refinements of the structures of α-Si3N4 and β-Si3N4 made from rice husk by Rietveld analysis. Ceram. Int. 1995, 21, 137–142. [Google Scholar] [CrossRef]
  83. Toraya, H. Crystal structure refinement of α-Si3N4 using synchrotron radiation powder diffraction data: Unbiased refinement strategy. J. Appl. Crystallogr. 2000, 33, 95–102. [Google Scholar] [CrossRef] [Green Version]
  84. Kroll, P.; Milko, M. Theoretical Investigation of the Solid State Reaction of Silicon Nitride and Silicon Dioxide forming Silicon Oxynitride (Si2N2O) under Pressure. Z. Anorg. Allg. Chem. 2003, 629, 1737–1750. [Google Scholar] [CrossRef]
  85. Wang, H.; Chen, Y.; Kaneta, Y.; Iwata, S. First-principles investigation of the structural, electronic and optical properties of olivine-Si3N4 and olivine-Ge3N4. J. Phys. Condens. Matter 2006, 18, 10663–10676. [Google Scholar] [CrossRef]
  86. Wang, R.; Sun, Z.; Pal, U.B.; Gopalan, S.; Basu, S.N. Mitigation of chromium poisoning of cathodes in solid oxide fuel cells employing CuMn1.8O4 spinel coating on metallic interconnect. J. Power Sources 2018, 376, 100–110. [Google Scholar] [CrossRef]
  87. Hassan, M.A.; Mamat, O.B. Mitigation of Chromium Poisoning of Ferritic Interconnect from Annealed Spinel of CuFe2O4. Processes 2020, 8, 1113. [Google Scholar] [CrossRef]
  88. Rose, L. On the Degradation of Porous Stainless Steel in Low and Intermediate Temperature Solid Oxide Fuel Cell Support Materials; University of British Columbia: Vancouver, BC, Canada, 2011. [Google Scholar]
Figure 1. Visualization of favorable Cr2SiN4 modifications: (a) α-Cr2SiN4-type in space group Pma2 (no. 28); (b) β-Cr2SiN4-type in space group P-1 (no. 2). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Figure 1. Visualization of favorable Cr2SiN4 modifications: (a) α-Cr2SiN4-type in space group Pma2 (no. 28); (b) β-Cr2SiN4-type in space group P-1 (no. 2). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Crystals 11 00891 g001
Figure 2. Visualization of favorable Cr2SiN4 modifications: (a) δ-Cr2SiN4-type in space group P21/m (no. 11). (b) ε-Cr2SiN4-type in space group P21/m (no. 11). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Figure 2. Visualization of favorable Cr2SiN4 modifications: (a) δ-Cr2SiN4-type in space group P21/m (no. 11). (b) ε-Cr2SiN4-type in space group P21/m (no. 11). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Crystals 11 00891 g002
Figure 3. Visualization of favorable Cr2SiN4 modifications found in space group Pm (no. 6): (a) λ- Cr2SiN4-type; (b) λʹ- Cr2SiN4-type. Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Figure 3. Visualization of favorable Cr2SiN4 modifications found in space group Pm (no. 6): (a) λ- Cr2SiN4-type; (b) λʹ- Cr2SiN4-type. Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Crystals 11 00891 g003
Figure 4. Visualization of non-favorable Cr2SiN4 modifications: (a) nf1-Cr2SiN4-type in space group P21/m (no. 11); (b) nf2-Cr2SiN4-type in space group Cc (no. 9). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Figure 4. Visualization of non-favorable Cr2SiN4 modifications: (a) nf1-Cr2SiN4-type in space group P21/m (no. 11); (b) nf2-Cr2SiN4-type in space group Cc (no. 9). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Crystals 11 00891 g004
Figure 5. Visualization of favorable Cr2SiN4 modifications: (a) Al2MgO4-spinel-type in space group Fd-3m (no. 227); (b) Na2MnCl4-type that appears in space group Pbam (no. 55). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Figure 5. Visualization of favorable Cr2SiN4 modifications: (a) Al2MgO4-spinel-type in space group Fd-3m (no. 227); (b) Na2MnCl4-type that appears in space group Pbam (no. 55). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Crystals 11 00891 g005
Figure 6. Visualization of favorable Cr2SiN4 modifications: (a) TiMn2O4-type in space group P4322 (no. 95); (b) Mg2SiO4-type in space group Pnma (no.62). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Figure 6. Visualization of favorable Cr2SiN4 modifications: (a) TiMn2O4-type in space group P4322 (no. 95); (b) Mg2SiO4-type in space group Pnma (no.62). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Crystals 11 00891 g006
Figure 7. Visualization of non-favorable Cr2SiN4 modification from data-mining: (a) Ca2RuO4-type in space group Pbca (no. 61), (b) HgC2O4-type in space group P21 (no. 4).
Figure 7. Visualization of non-favorable Cr2SiN4 modification from data-mining: (a) Ca2RuO4-type in space group Pbca (no. 61), (b) HgC2O4-type in space group P21 (no. 4).
Crystals 11 00891 g007
Figure 8. Visualization of non-favorable Cr2SiN4 modifications obtained from data-mining: (a) Ca2IrO4-type in space group P-62m (no. 189); (b) CaB2O4-type in space group Pccn (no. 56). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Figure 8. Visualization of non-favorable Cr2SiN4 modifications obtained from data-mining: (a) Ca2IrO4-type in space group P-62m (no. 189); (b) CaB2O4-type in space group Pccn (no. 56). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Crystals 11 00891 g008
Figure 9. Visualization of non-favorable Cr2SiN4 modification obtained from data-mining referred to as Mn2SnS4-type in space group Cmmm (no 65).
Figure 9. Visualization of non-favorable Cr2SiN4 modification obtained from data-mining referred to as Mn2SnS4-type in space group Cmmm (no 65).
Crystals 11 00891 g009
Figure 10. Visualization of: (a) the Si3N4 γ-phase in space group I-43d (no. 220); (b) γ- Cr2SiN4-type in space group Cc (no. 9). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Figure 10. Visualization of: (a) the Si3N4 γ-phase in space group I-43d (no. 220); (b) γ- Cr2SiN4-type in space group Cc (no. 9). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Crystals 11 00891 g010
Figure 11. Visualization of the non-favorable PCAE structures: (a) Cr2SiN4-PCAE-1-type in space group Pm (no. 6); (b) Cr2SiN4-PCAE-2-type in space group P1 (no. 1). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Figure 11. Visualization of the non-favorable PCAE structures: (a) Cr2SiN4-PCAE-1-type in space group Pm (no. 6); (b) Cr2SiN4-PCAE-2-type in space group P1 (no. 1). Green, red, and yellow spheres denote Cr, Si, and N atoms, respectively.
Crystals 11 00891 g011
Figure 12. Energy vs. volume, E(V), curves for the most favorable Cr2SiN4 modifications calculated using the GGA-PBE functional. Energies per formula unit are given in Hartree (Eh).
Figure 12. Energy vs. volume, E(V), curves for the most favorable Cr2SiN4 modifications calculated using the GGA-PBE functional. Energies per formula unit are given in Hartree (Eh).
Crystals 11 00891 g012
Figure 13. (a) Enthalpy vs. pressure, H(p), curves computed for the five most relevant structures, including the high-pressure region. (b) Plots on the right side show H(p) curves focused on two transitions. Top: H(p) curves for the spinel- and the Na2MnCl4-type (transition pressure was found to be ~33 GPa); Bottom: H(p) curves between the Na2MnCl4-type and the α-Cr2SiN4-type modifications (transition pressure would be ~15 GPa). The calculations were performed using the GGA-PBE functional and the energies per formula unit are given in Hartree (Eh).
Figure 13. (a) Enthalpy vs. pressure, H(p), curves computed for the five most relevant structures, including the high-pressure region. (b) Plots on the right side show H(p) curves focused on two transitions. Top: H(p) curves for the spinel- and the Na2MnCl4-type (transition pressure was found to be ~33 GPa); Bottom: H(p) curves between the Na2MnCl4-type and the α-Cr2SiN4-type modifications (transition pressure would be ~15 GPa). The calculations were performed using the GGA-PBE functional and the energies per formula unit are given in Hartree (Eh).
Crystals 11 00891 g013
Table 1. The total energy (in Eh) and relative energy values (in kcal/mol) compared to the global minimum (spinel structure taken as the zero of energy) of Cr2SiN4 modifications found after global optimization on an empirical potential level and locally optimized using the GGA-PBE functional.
Table 1. The total energy (in Eh) and relative energy values (in kcal/mol) compared to the global minimum (spinel structure taken as the zero of energy) of Cr2SiN4 modifications found after global optimization on an empirical potential level and locally optimized using the GGA-PBE functional.
ModificationTotal Energy
(Eh)
Relative Energy (kcal/mol)
α-Cr2SiN4-type−5193.47420.708
β-Cr2SiN4-type−5193.43843.298
δ-Cr2SiN4-type−5193.41955.221
ε-Cr2SiN4-type−5193.41358.986
λ-Cr2SiN4-type−5193.40762.750
λʹ-Cr2SiN4-type−5193.40464.634
nf1-Cr2SiN4-type−5193.39868.399
nf2-Cr2SiN4-type−5193.38874.674
nf3-Cr2SiN4-type−5193.38576.556
nf4-Cr2SiN4-type−5193.36489.734
nf5-Cr2SiN4-type−5193.36489.734
Table 2. The modifications, space groups, unit cell parameters, and atomic positions for favorable Cr2SiN4 modifications found after global optimization and later locally optimized on the ab initio level using the GGA-PBE functional.
Table 2. The modifications, space groups, unit cell parameters, and atomic positions for favorable Cr2SiN4 modifications found after global optimization and later locally optimized on the ab initio level using the GGA-PBE functional.
Modifications
and Space Group
Cell ParametersPosition of Atoms
α-Cr2SiN4-type
Pma2
No 28
a = 5.54 b = 7.91 c = 2.81Cr 0.750000 0.245688 0.560883
Cr 0.500000 0.000000 0.891696
Si 0.750000 0.616760 0.000000
N 0.750000 0.011076 0.423540
N 0.750000 0.493745 0.499960
N 0.501383 0.244129 0.983362
β-Cr2SiN4-type
P-1
No 2
a = 7.28 b = 7.79 c = 2.74 α = 93.66 β = 82.48 γ = 120.64Cr 0.347419 0.861114 0.730714
Cr 0.862711 0.520348 0.305878
Si 0.627078 0.740684 0.913120
N 0.050229 0.677562 0.759435
N 0.353428 0.666353 0.160724
N 0.660109 0.973354 0.749444
N 0.717565 0.676085 0.369516
δ-Cr2SiN4-type
P21/m
No 11
a = 6.21 b = 3.82 c = 5.54 β = 116.24Cr 0.088537 0.750000 0.660564
Cr 0.155145 0.750000 0.253988
Si 0.613292 0.750000 0.917590
N 0.639615 0.250000 0.413635
N 0.137168 0.250000 0.721296
N 0.368220 0.750000 0.042876
N 0.136099 0.250000 0.176958
ε-Cr2SiN4-type
P21/m
No 11
a = 5.09 b = 2.89 c = 8.90 β = 90.20Cr 0.778189 0.250000 0.506779
Cr 0.918790 0.750000 0.827219
Si 0.419972 0.250000 0.798720
N 0.567333 0.750000 0.861544
N 0.897872 0.750000 0.121156
N 0.589340 0.750000 0.395794
N 0.060536 0.250000 0.368680
λ-Cr2SiN4-type
Pm
No 6
a = 5.07 b = 2.88 c = 9.27 β = 99.77Cr 0.951900 0.500000 0.415607
Cr 0.698619 0.500000 0.708230
Cr 0.291904 0.000000 0.722310
Cr 0.507805 0.500000 0.040389
Si 0.000000 0.000000 0.000000
Si 0.455229 0.000000 0.394275
N 0.535616 0.000000 0.585846
N 0.455096 0.500000 0.844293
N 0.704956 0.000000 0.076886
N 0.586474 0.500000 0.329108
N 0.050793 0.500000 0.599924
N 0.108035 0.000000 0.351718
N 0.939400 0.000000 0.811337
N 0.163111 0.500000 0.068461
λ’-Cr2SiN4-type
Pm
No 6
a = 5.06 b = 2.87 c = 9.18 β = 90.97Cr 0.166652 0.500000 0.355602
Cr 0.889145 0.500000 0.685518
Cr 0.307908 0.000000 0.681019
Cr 0.485319 0.500000 0.980324
Si 0.000000 0.000000 0.000000
Si 0.670339 0.000000 0.395017
N 0.676765 0.000000 0.583978
N 0.498298 0.500000 0.794695
N 0.665262 0.000000 0.039248
N 0.812605 0.500000 0.324037
N 0.176521 0.500000 0.552065
N 0.351051 0.000000 0.317489
N 0.015000 0.000000 0.810727
N 0.151227 0.500000 0.066773
Table 3. The modifications, space groups, unit cell parameters, and atomic positions for non-favorable Cr2SiN4 modifications found using global optimization and later optimized at the GGA-PBE level of calculation.
Table 3. The modifications, space groups, unit cell parameters, and atomic positions for non-favorable Cr2SiN4 modifications found using global optimization and later optimized at the GGA-PBE level of calculation.
Modifications
and Space Group
Cell ParametersPosition of Atoms
nf1-Cr2SiN4-type
P21/m
No 11
a = 5.03 b = 2.89 c = 9.25 β = 100.34Cr 0.780740 0.750000 0.501443
Cr 0.025858 0.250000 0.824580
Si 0.517842 0.750000 0.797882
N 0.959527 0.250000 0.630184
N 0.552291 0.250000 0.393501
N 0.609701 0.750000 0.135709
N 0.136923 0.250000 0.122932
nf2-Cr2SiN4-type
Cc
No 9
a = 5.06 b = 14.14 c = 4.77 β = 121.05Cr 0.622331 0.095134 0.360180
Cr 0.380879 0.098904 0.725602
Si 0.000000 0.191719 0.000000
N 0.487148 0.004091 0.555289
N 0.511786 0.374204 0.196387
N 0.720274 0.147401 0.064041
N 0.358846 0.192090 0.368624
nf3-Cr2SiN4-type
Pm
No 6
a = 6.79 b = 3.09 c = 6.88 β = 109.29Cr 0.319643 0.500000 0.397294
Cr 0.308694 0.500000 0.793094
Cr 0.034585 0.000000 0.406174
Cr 0.733922 0.500000 0.593240
Si 0.000000 0.000000 0.000000
Si 0.588865 0.000000 0.169164
N 0.515186 0.500000 0.666342
N 0.819399 0.000000 0.531146
N 0.551036 0.500000 0.283640
N 0.215615 0.000000 0.242977
N 0.384133 0.000000 0.929487
N 0.000403 0.500000 0.870324
N 0.122011 0.500000 0.540245
N 0.829057 0.000000 0.140470
nf4-Cr2SiN4-type
Pm
No 6
a = 7.37 b = 3.05 c = 7.56 β = 115.96Cr 0.779088 0.000000 0.218259
Cr 0.459516 0.500000 0.327876
Cr 0.253478 0.000000 0.544973
Cr 0.396471 0.500000 0.935322
Si 0.000000 0.500000 0.000000
Si 0.852505 0.000000 0.603621
N 0.330961 0.500000 0.474928
N 0.889506 0.500000 0.738026
N 0.613308 0.000000 0.401256
N 0.355218 0.000000 0.802744
N 0.932400 0.000000 0.070113
N 0.262965 0.500000 0.082041
N 0.643042 0.500000 0.129399
N 0.988794 0.000000 0.464379
nf5-Cr2SiN4-type
P-1
No 2
a = 7.17 b = 3.06 c = 7.41 α = 89.69 β = 66.68 γ = 88.06Cr 0.654478 0.292004 0.523373
Cr 0.288987 0.742844 0.838266
Si 0.865354 0.748679 0.767528
N 0.255163 0.244316 0.972502
N 0.804235 0.255276 0.687399
N 0.477326 0.210250 0.368818
N 0.127792 0.732554 0.709190
Table 4. The total energy and relative energy values compared to the global minimum (spinel structure taken as the zero of energy) of Cr2SiN4 modifications obtained from DM-based searches and calculated using GGA-PBE.
Table 4. The total energy and relative energy values compared to the global minimum (spinel structure taken as the zero of energy) of Cr2SiN4 modifications obtained from DM-based searches and calculated using GGA-PBE.
ModificationTotal Energy
(Eh)
Relative Energy
(kcal/mol)
Al2MgO4-spinel-type−5193.5070.0
Na2MnCl4-type−5193.43644.553
TiMn2O4-type−5193.41458.358
Mg2SiO4-type−5193.40365.261
Ca2RuO4-type−5193.40265.889
HgC2O4-like−5193.40067.144
Ca2IrO4-type−5193.34999.147
CaB2O4-like−5193.347100.402
Mn2SnS4-type−5193.342103.539
Table 5. The modifications, space groups, unit cell parameters, and atomic positions for Cr2SiN4 modifications obtained from data-mining-based searches and local optimization at the GGA-PBE level.
Table 5. The modifications, space groups, unit cell parameters, and atomic positions for Cr2SiN4 modifications obtained from data-mining-based searches and local optimization at the GGA-PBE level.
Modifications
and Space Group
Cell ParametersPosition of Atoms
Al2MgO4-spinel-type
Fd-3m
No 227
a = 7.88Cr 0.000000 0.000000 0.000000
Si 0.625000 0.625000 0.625000
N 0.752483 0.752483 0.752483
Na2MnCl4-type
Pbam
No 55
a = 4.74 b = 8.70 c = 2.73Cr 0.433387 0.175989 0.500000
Si 0.000000 0.000000 0.000000
N 0.133667 0.203146 0.000000
N 0.256351 0.966597 0.500000
TiMn2O4-type
P4322
No 95
a = 5.64 c = 7.74Cr 0.500000 0.288490 0.000000
Cr 0.234522 0.234522 0.625000
Si 0.000000 0.259306 0.000000
N 0.239859 0.499775 0.998379
N 0.246452 0.027106 0.010564
Mg2SiO4-type
Pnma
No 62
a = 9.42 b = 5.45 c = 4.82 Cr 0.500000 0.500000 0.500000
Cr 0.751225 0.750000 0.005741
Si 0.911733 0.750000 0.580414
N 0.915086 0.750000 0.227101
N 0.579248 0.750000 0.754925
N 0.831733 0.498905 0.747339
Ca2RuO4-type
Pbca
No 61
a = 4.55 b = 4.88 c = 10.32Cr 0.951271 0.088328 0.314395
Si 0.000000 0.000000 0.000000
N 0.189814 0.299961 0.071415
N 0.821277 0.910789 0.170556
HgC2O4-like
P21
No 4
a = 5.34 b = 5.09 c = 5.36 β = 115.62Cr 0.009785 0.463302 0.266681
Cr 0.242643 0.853311 0.472408
Si 0.651871 0.000000 0.959796
N 0.021251 0.353294 0.916553
N 0.626651 0.296871 0.103741
N 0.597719 0.030584 0.610720
N 0.079595 0.179181 0.498154
Ca2IrO4-type
P-62m
No 189
a = 8.33 c = 2.70Cr 0.000000 0.000000 0.000000
Cr 0.333333 0.666667 0.500000
Cr 0.699230 0.000000 0.500000
Si 0.337748 0.000000 0.000000
N 0.173727 0.000000 0.500000
N 0.473996 0.000000 0.500000
N 0.448912 0.247641 0.000000
CaB2O4-like
Pccn
No 56
a = 7.98 b = 14.42 c = 4.85Cr 0.931376 0.565538 0.393557
Cr 0.170647 0.535703 0.989804
Si 0.857355 0.679567 0.867484
N 0.864237 0.698217 0.499220
N 0.303715 0.441717 0.754883
N 0.009972 0.618966 0.076401
N 0.377123 0.568169 0.113939
Mn2SnS4-type
Cmmm
No 65
a = 5.58 b = 7.82 c = 2.76Cr 0.750000 0.750000 0.500000
Si 0.000000 0.000000 0.000000
N 0.000000 0.247324 0.000000
N 0.220861 0.000000 0.500000
Table 6. The total energy and relative energy values compared to the global minimum (spinel structure taken as the zero of the energy) of Cr2SiN4 modifications found using the PCAE method and locally optimized using the GGA-PBE functional.
Table 6. The total energy and relative energy values compared to the global minimum (spinel structure taken as the zero of the energy) of Cr2SiN4 modifications found using the PCAE method and locally optimized using the GGA-PBE functional.
ModificationTotal Energy
(Eh)
Relative Energy
(kcal/mol)
γ-Cr2SiN4-type−5193.43545.181
Cr2SiN4-PCAE-1-type−5193.38576.556
Cr2SiN4-PCAE-2-type−5193.37483.459
Table 7. The modifications, space groups, unit cell parameters, and atomic positions for favorable Cr2SiN4 modifications found using the PCAE method and the GGA-PBE functional.
Table 7. The modifications, space groups, unit cell parameters, and atomic positions for favorable Cr2SiN4 modifications found using the PCAE method and the GGA-PBE functional.
Modification
and Space Group
Cell ParametersPosition of Atoms
γ-Cr2SiN4-type
Cc
(no. 9)
a = 5.62 b = 8.96 c = 5.36 Å, β = 117.93Cr 0.505134 0.354319 0.539894
Cr 0.490988 0.640587 0.506788
Si 0.000000 0.574728 0.000000
N 0.820626 0.494637 0.668512
N 0.339534 0.498028 0.687817
N 0.683793 0.745757 0.858424
N 0.673275 0.237591 0.860703
Cr2SiN4-PCAE-1-type Pm
(no. 6)
a = 7.04 b = 3.04 c = 7.03 β = 110.72Cr 0.338406 0.500000 0.381358
Cr 0.068281 0.000000 0.404484
Cr 0.778353 0.500000 0.589017
Cr 0.381419 0.500000 0.771064
Si 0.000000 0.000000 0.000000
Si 0.613136 0.000000 0.165992
N 0.569205 0.500000 0.274738
N 0.859037 0.000000 0.522005
N 0.985060 0.500000 0.869495
N 0.164949 0.500000 0.544984
N 0.227376 0.000000 0.231306
N 0.437810 0.000000 0.912940
N 0.551129 0.500000 0.636169
N 0.853139 0.000000 0.153320
Cr2SiN4-PCAE-2-type P1
(no. 1)
a = 7.88 b = 7.96 c = 5.79 α = 89.97 β = 89.86 γ = 120.26Cr 0.179061 0.774468 0.214657
Cr 0.576899 0.834251 0.216822
Cr 0.514893 0.179271 0.216823
Cr 0.596707 0.344636 0.708045
Cr 0.010451 0.684706 0.713360
Cr 0.678545 0.756495 0.700070
Cr 0.343219 0.429431 0.991834
Cr 0.923504 0.343769 0.996260
Si 0.000000 0.000000 0.000000
Si 0.263900 0.513623 0.496139
Si 0.839296 0.185951 0.496185
Si 0.163373 0.091041 0.497914
N 0.743253 0.861393 0.985305
N 0.495442 0.322138 0.989374
N 0.052018 0.604045 0.985425
N 0.711195 0.932465 0.477493
N 0.419187 0.211059 0.484630
N 0.145337 0.648381 0.483835
N 0.406296 0.578413 0.243870
N 0.773280 0.267856 0.250745
N 0.088745 0.948405 0.247062
N 0.418188 0.578819 0.734852
N 0.770928 0.262416 0.742269
N 0.078587 0.945416 0.743265
N 0.427572 0.932217 0.132893
N 0.761872 0.590844 0.634583
N 0.087863 0.251396 0.996965
N 0.090039 0.265519 0.498530
Table 8. The total energies and relative energy values compared to the global minimum (spinel structure taken as the zero of energy) of the energetically most favorable Cr2SiN4 modifications found using various search methods and later locally optimized on the ab initio level using the GGA-PBE functional. DM stands for data mining, GO stands for global optimization, and PCAE stands for Primitive Cell approach for Atom Exchange method.
Table 8. The total energies and relative energy values compared to the global minimum (spinel structure taken as the zero of energy) of the energetically most favorable Cr2SiN4 modifications found using various search methods and later locally optimized on the ab initio level using the GGA-PBE functional. DM stands for data mining, GO stands for global optimization, and PCAE stands for Primitive Cell approach for Atom Exchange method.
ModificationSearch MethodTotal Energy (Eh)Relative Energy
(kcal/mol)
Al2MgO4-spinel-typeDM−5193.5070.0
α-Cr2SiN4-typeGO−5193.47420.708
β-Cr2SiN4-typeGO−5193.43843.298
Na2MnCl4-typeDM−5193.43644.553
γ-Cr2SiN4-typePCAE−5193.43545.181
δ-Cr2SiN4-typeGO−5193.41955.221
TiMn2O4-typeDM−5193.41458.358
ε-Cr2SiN4-typeGO−5193.41358.986
λ-Cr2SiN4-typeGO−5193.40762.750
λʹ-Cr2SiN4-typeGO−5193.40464.634
Mg2SiO4-typeDM−5193.40365.261
Publisher’s Note: MDPI stays neutral with regard to jurisdictional claims in published maps and institutional affiliations.

Share and Cite

MDPI and ACS Style

Škundrić, T.; Zagorac, D.; Schön, J.C.; Pejić, M.; Matović, B. Crystal Structure Prediction of the Novel Cr2SiN4 Compound via Global Optimization, Data Mining, and the PCAE Method. Crystals 2021, 11, 891. https://doi.org/10.3390/cryst11080891

AMA Style

Škundrić T, Zagorac D, Schön JC, Pejić M, Matović B. Crystal Structure Prediction of the Novel Cr2SiN4 Compound via Global Optimization, Data Mining, and the PCAE Method. Crystals. 2021; 11(8):891. https://doi.org/10.3390/cryst11080891

Chicago/Turabian Style

Škundrić, Tamara, Dejan Zagorac, Johann Christian Schön, Milan Pejić, and Branko Matović. 2021. "Crystal Structure Prediction of the Novel Cr2SiN4 Compound via Global Optimization, Data Mining, and the PCAE Method" Crystals 11, no. 8: 891. https://doi.org/10.3390/cryst11080891

Note that from the first issue of 2016, this journal uses article numbers instead of page numbers. See further details here.

Article Metrics

Back to TopTop