Configuration Dependent Electronic and Optical Properties of WZ-CuInS2
Bo Gao, Fu-Ling Tang*, Hong-Tao Xue, Fu-Zhen Zhang, Yu-Wen Cheng
Department of Materials Science and Engineering, Lanzhou University of Technology, State Key Laboratory of Advanced Processing and Recycling of Non-ferrous Metals, Lanzhou, China
To cite this article:
Bo Gao, Fu-Ling Tang, Hong-Tao Xue, Fu-Zhen Zhang, Yu-Wen Cheng. Configuration Dependent Electronic and Optical Properties of WZ-CuInS2. American Journal of Optics and Photonics. Vol. 4, No. 4, 2016, pp. 32-39. doi: 10.11648/j.ajop.20160404.12
Received: September 15, 2016; Accepted: October 13, 2016; Published: November 3, 2016
Abstract: We used the first-principles calculations based on density functional theory to calculate the electronic and optical properties of wurtzite CuInS2 (WZ-CuInS2) in which the copper and indium atoms share the same lattice site. It is found that WZ-CuInS2 is metallic for local aggregative indium and copper atomic configurations, or is a semiconductor for local even-distributed configurations. Metallic configurations have higher lattice energies while semi conductive configurations have lower lattice energies. As the degree of the local aggregation of Cu and In atoms increases, the band gap of the WZ-CuInS2 decreases. The optical properties of WZ-CuInS2 were also calculated and found that the optical band gap also decreases as local aggregation of Cu and In atoms with increases. The metallic configurations have a higher absorption coefficient.
Keywords: First Principles Calculation, Atomistic Configuration, Electronic Properties, Optical Properties, WZ-CuInS2
As new members of the photovoltaic materials, I-II-VI2 semiconductor compounds (for example, CuGaSe2 and CuInSe2) have been well realized [1-3]. For CuInS2 polymorphic structures, chalcopyrite phase (CP-CuInS2) is the most common structure, zincblende phase (ZB-CuInS2) is metastable, and wurtzite phase (WZ-CuInS2) structure was synthesized recently [4, 5]. Unlike in traditional CP-CuInS2 solar cell material, Cu and In atoms randomly share the same lattice site with the same half possibility in WZ-CuInS2 unit cell. This characteristic makes it flexible in stoichiometry and suitable for high-efficient solar cells . Acting as a new valuable solar cell material, WZ-CuInS2 has attracted widespread attentions. Because of its excellent band gap (1.45-1.5 eV) matching with the solar spectrum, it displays higher light absorption efficiency over some other materials . Optimized WZ-CuInS2 solar cells had the conversion efficiency up to 5% at elevated temperatures . In addition, it also has other features, for example, good electrical stability, environment friendly and economic prospects [9-11]. Drawing by these advantages, many research groups recently have devoted to synthesize this material with various nanocrystalline approaches [12-13].
The random distribution of Cu-In in WZ-CuInS2 introduces the flexibility of stoichiometry and possibly makes its Fermi energy easily changed over a wider range [13-15]. Hence, different Cu-In configuration possibly leads to various electronic and optical properties. At present, few theoretical investigations on the electronic and optical properties of WZ-CuInS2 have been carried out, especially, at atomistic level. From common first principles calculation within density functional theory, the lattice and electronic structures can be well obtained, but it couldn’t precisely predict band gap and optical properties. The hybrid Hartree-Fock-like functional by Heyd, Scuseria, and Ernzerhof (HSE) can improve the calculation accuracy [16, 17]. Many groups have proven that the HSE06 function made a good description not only for the electronic properties but also for the optical properties [18-23]. So the HSE06 function was used to study the configuration dependent lattice stability and the configuration effect on the electronic and optical properties of WZ-CuInS2.
The unit cell of CuS (with the space group P63mc, a = 3.906 Å, c = 6.429 Å) was used as the starting point for In-doping calculation. Half of Cu atoms were substituted by In atoms. We prepared many different Cu-In configurations by using the Monte Carlo Alloy Theoretic Automated Toolkit (ATAT) [24-26]. In this work, based on the first principles density functional theory, the Vienna Ab-initio simulation package (VASP) [27-29] was utilized, supplementing with the projector augmented wave (PAW) method [30, 31]. For the pseudopotential that was used, the electronic configurations are [Ar] 3d104s1, [Kr] 5s25p1, and [Ne] 3s23p4 for copper, indium, and sulfur respectively. The plane wave energy cutoff is 410 eV and the Brillouin zone is sampled by an 8×8×5 Monkhorst–Pack k-mesh to calculate these structures. We used the tetrahedron method to calculate the total lattice energy and the density of states (DOS) for all atomistic configurations . In order to obtain their equilibrium structures, the Density Functional Theory (DFT) was used to relax the cell lattice parameters and their ion positions to obtain their lowest energy structures. The HSE06 hybrid functional with Hartree–Fock screening parameter = 0.2 was employed to calculate the electronic and optical properties.
The response of matters to electromagnetic fields is described by the complex dielectric function. The dielectric matrix can be calculated on condition that the electronic ground state is determined. The complex dielectric function is a bridge between the microscopic and macroscopic measurements of the material and plays an important role in the study of the optical properties of semiconductors. Using the complex dielectric functions and the absorption coefficient , the optical properties can be presented. Then the imaginary part of the dielectric function was calculated using the equation:
where the indices is conduction band state, is the valence band state. is the volume, is the k-point weight, is the energy state, is the cell periodic part and is the unit vector. Then the real part of dielectric function tensor was got using KramersKronig transformation:
where denotes the principal value and is an infinitesimal number .
3. Results and discussion
In WZ-CuInS2 lattice, the sub-lattice structure is a tetrahedron: S atom at the center and four Cu/In atoms around it. In every tetrahedron, Cu and In atoms may have different occupancies. There must be five and only five possible occupancies in the tetrahedrons, named a, b, c, d, e respectively in Fig. 1. In the tetrahedron a, the S atom is surrounded by two Cu atoms and two In atoms. In b/c, the S atom is surrounded by three/one Cu atom(s) and one/three In atom(s). In d/e, the S atom is surrounded by four Cu/In atoms. All of the WZ-CuInS2 lattices are constituted by some of these five type tetrahedral structures. In addition, the typical bond lengths of In/Cu-S are also shown in Fig. 1.
There are eight WZ-CuInS2 structural configurations with different sub-lattices and their total energies were listed in Table 1. We name five WZ-CuInS2 structures as type I (a-e), and name other three WZ-CuInS2 structures as type II (f-h). Their percentages for tetrahedrons a-e are listed in Table 1. Type I lattices haven’t d or e tetrahedron, while Type II lattices have d or/and e tetrahedron. For example, in the lattice structure e of type I, half tetrahedrons are of type b, and the others are of type c. These structures are shown in Fig. 2.
*a-e denote the five possible tetrahedral structures in Fig. 1.
**0 to 1 denotes the percentage of every tetrahedral structure (a-e in Fig. 1) in the lattice structure.
3.1. Type I WZ-CuInS2
Type I WZ-CuInS2 structures just have a, b, c type tetrahedrons (Fig. 1). For example, structure a (Fig. 2a) just composes the type a tetrahedrons, and has the lowest lattice energy. In fact, this structure is the most stable structure we studied. The atomic stack way of the structure a which is the simplest is: along ] direction, the Cu cation and In cation are alternately stacked; along ] every S atom bonds to two Cu and two In cations. For the WZ-CuInS2 structure e (Fig. 2e), along ] direction, the first layer just contains Cu cations, the second layer contains both Cu cations and In cations; the third layer just contains In cations; and the forth layer again contains both Cu cations and In cations. In such a pattern, the atoms are arranged consecutively and periodically. This means that along ] the first S atom is bonded to three Cu and one In cations, and the following S atom is bonded to one Cu and three In cations. While structure e has higher lattice energy, it hasn’t the type a tetrahedron. It can be seen that the lattice energy gradually increases as the percentage of type a tetrahedrons reduces.
3.1.1. Electronic Properties
From the density of states (DOS) and band structure diagram, we can judge a system is a metal, semiconductor or insulator from its band gaps. The DOS of structures a-e of type I was got by HSE06, as presented in Fig. 3, and found that the electronic density near the Fermi level increases as the occupancy of type a tetrahedron decreases. From partial density of states (PDOS), we can find that the electronic state near the Fermi level of structure e is formed by 5s-orbital of In atoms.
The band structure of these configurations, is shown as in Fig.4. The calculated band gap of structure a is about 1.21 eV, which is closer to the experimental band gaps (1.47 eV) . Structure d’s band gap is about 0.12 eV and structure e has no band gap at gamma-point. The Fig. 4 shows that structure a-d have direct band gap, in which the top of the valence band and the bottom of the conduction band lie along the gamma-point. As shown in DOS and band structure diagram, the band gap of structures a-d becomes smaller with the decrease of type a tetrahedron’s percentage. Structures a-d exhibit semiconductor properties while structure e has a similar DOS of metals.
In structure a or e, there are four Cu, four In and eight S atoms. Their Bader's atomic charges are shown in Table 2. For structure a, S atoms gain 0.93 and 0.94 e (electrons). Cu and In atoms lose 0.52 and 1.35 e, respectively. However, for structure e, S atoms gain 0.88 and 1.10 e, and Cu and In atoms lose 0.49 and 1.25 e. Compared with structure a, two Cu atoms in structure e lose much more electrons. This may be a reason for their DOS difference in Fig. 3.
3.1.2. Optical Properties
The absorption coefficient denotes when a beam of light with a particular wavelength illuminates into a material the distance that it can propagate before it is absorbed. Through the dielectric function, the absorption coefficient can be got by thisformula:
The absorption spectra of these structures are given in Fig. 5. The absorption coefficient rises to peak and then slip down. When the photon frequency is larger than 25 eV, it will be close to zero. Structures a-e have similar absorption curves whose peaks appear at 12 eV with a value of . Structure e shows a very special absorption spectra, reaching maximum at about 6 eV with a much higher absorption peak (). Its absorption coefficient is about two times of other structures. From the absorption spectra, the optical band gap can be figured out through the formula: (is the energy of photon ). The inset of Fig. 5 displays the relationship between and for structure a and b. The dotted lines present the values of the optical band gap. Because the optical band gap of other structures is very narrow, we do not show them here. The optical band gap of structure a is about 1.19 eV which is in good accordance with the experimental result (1.282 eV) . The optical band gap of the structure b is about 1.06 eV. However the structure e hasn’t optical band gap, displaying metallic properties. Generally, with the increase of the percentage of type a tetrahedron, the optical band gap decreases, the coefficient of absorption rises. Finally, the structure e exhibits metallic properties.
According to the relationship between the complex refractive , the refractive indices n and the extinction coefficient , we can get the following two formulas:
The refractive indices of structures a-e are shown in Fig. 6a. With the increase of the energy of the photon, n experiences a little decline at first then slightly rises soon later. When the photon energy is large enough, n will increase to approximately 0.8. The extinction coefficient of materials can also be found (in Fig. 6b). It rises to peak at which point the photon energy is about 6 eV, and then slip down. Not only the refractive indices but also the extinction coefficient of structure e is quite different from those of structures a-d.
3.2. Type II WZ-CuInS2
There are three different structures presented in type II, f-h (Table 1). Unlike in type I structures, tetrahedron(s) d and/or e appear in type II structures. In tetrahedron d or e, four Cu or In atoms are aggregative around S atom. In CuIn1−xGaxSe2 system, In and Ga atoms are aggregated to form phase separation at low temperature . In CuIn(Se1−xSx)2 system, Se and S atoms tempt to form phase separation .
The structure h is shown in Fig. 2h. This is a more complex structure than others, which contains all the five tetrahedrons. Along ], it can be divided into two layers: the first layer contains Cu and S atoms and the second layer contains In and S atoms, and these two layers appear alternatively. Generally, the structures’ lattice energies of type II is higher than those of type I structures. In other words, when the indium and copper atoms’ distribution is more aggregative, its lattice energy will become higher.
The DOS of type II structures f-h (Fig. 7a) shows that there are density states appearing above the Fermi level. And the electronic state near Fermi level is also from the 5s-orbital of In atoms. We can also notice that there is no band gap for structures f-h from Fig. 4. That is to say, they are all metallic. But structure h is more metallic than structures f and g because it has higher density states near the Fermi level. The absorption spectrum is also calculated (Fig. 7b). With the ascending of the energy of the photon, absorption spectrum increases at first but sharply reduces later and tends to be flat eventually. Structures f-h of type II have similar but smaller absorption coefficient compared with those of structures a-d of type I.
Here we must remind that WZ-CuInS2 attracted many interests recently as a potential semiconductor solar cell material. According to their lattice energies, the experimentally synthesized WZ-CuInS2 may be a mixture of different atomistic configurations. WZ-CuInS2 with local aggregative indium and copper atomic configurations are energically less stable, and its metallic properties may do harm to solar cell performance. Anyway, our studies will be helpful to understand this material. Further experimental and theoretical research is needed to confirm the existence of metallic configurations in WZ-CuInS2based solar cells, to investigate their effects, and to avoid them.
Based on the first-principles calculations we calculated the electronic and optical properties of wurtzite CuInS2 with different local atomic configurations. The main findings are: 1) Cu-In configuration has a significant effect on the stabilities and properties of wurtzite CuInS2. 2) As the degree of the local aggregation of Cu and In atoms increases, the band gap of the WZ-CuInS2 decreases. 3) WZ-CuInS2 is metallic for local aggregative Cu and In configurations, or is a semiconductor for local even-distributed configurations. 4) The lattice energy increases as the system changes from semiconductive to metallic.
This work was financially supported by the National Nature Science Foundation of China (11164014 and 11364025). This work was performed in the Gansu Supercomputer Center.