Band Gap Engineering ofCd1-xBexSeAlloys

Hindawi Publishing Corporation International Journal of Metals Volume 2014, Article ID 286393, 7 pages http://dx.doi.org/10.1155/2014/286393 Research Article Band Gap Engineering of Cd1−𝑥Be𝑥Se Alloys Djillali Bensaid,1 Mohammed Ameri,1 Nadia Benseddik,2 Ali Mir,2 Nour Eddine Bouzouira,1 and Fethi Benzoudji2 1 2 Laboratory of Physical Chemistry of Advanced Materials, University of Djillali Liabes, BP 89, 22000 Sidi Bel Abbes, Algeria Physics Department, Science Faculty, University of Sidi Bel Abbes, 22000 Sidi Bel Abbes, Algeria Correspondence should be addressed to Djillali Bensaid; [email protected] Received 13 August 2013; Revised 3 February 2014; Accepted 2 March 2014; Published 13 May 2014 Academic Editor: Velimir Radmilovic Copyright © 2014 Djillali Bensaid et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited. The structural and electronic properties of the ternary Cd1−𝑥 Be𝑥 Se alloys have been calculated using the full-potential linear muffintin-orbital (FP-LMTO) method based on density functional theory within local density approximation (LDA). The calculated equilibrium lattice constants and bulk moduli are compared with previous results. The concentration dependence of the electronic band structure and the direct and indirect band gaps are investigated. Moreover, the refractive index and the optical dielectric constant for Cd1−𝑥 Be𝑥 Se are studied. The thermodynamic stability of the alloys of interest is investigated by means of the miscibility. This is the first quantitative theoretical prediction to investigate the effective masses, optical and thermodynamic properties for Cd1−𝑥 Be𝑥 Se alloy, and still awaits experimental. 1. Introduction In recent years, the wide-gap II–VI compounds are widely investigated because of the attractive applications in fabricating blue-green and blue optoelectronic devices, such as light-emitting diodes and laser diodes [1–4]. The applications include the use of II–VI compound based materials as light sources, in full colour displays, and for increasing the information density in optical recording [5, 6]. The beryllium containing II–VI compounds had been found to possess an enhanced ability to significantly reduce the defect propagation due to a greater prevalence of strong covalent bonding and lattice hardening in the materials [7, 8]. The strong covalent bonding in beryllium-based II–VI compounds achieves a considerable lattice hardening, which avoids multiplication of defects during the operation of II–VI semiconductor laser devices [9, 10] Be𝑥 Cd1−𝑥 Se alloys have attracted great attention because they are promising for the fabrication of full-colour visible optical devices due to a large difference in the energy gaps 𝐸𝑔 of the binary constituents (CdSe, 𝐸𝑔 = 1.74 eV; BeSe, 𝐸𝑔 = 5.5 eV) [11]. In the present theoretical work, band gap of zinc-blende CdSe is varied systematically by alloying with Be. In order to investigate the optoelectronic nature of these alloys, their structural, electronic, and optical properties are calculated. All calculations are based on density functional full-potential linear muffin-tin orbital (FP-LMTO) method with perdewwang local density approximation (LDA). 2. Method of Calculations The calculations reported here were carried out using the ab initio full-potential linear muffin-tin orbital (FP-LMTO) method [12–15] as implemented in the Lmtart code [16]. The exchange and correlation potential was calculated using the local density approximation (LDA) [17]. The FP-LMTO is an improved method compared to previous LMTO techniques, and it treats muffin-tin spheres and interstitial regions on the same footing, leading to improvements in the precision of the eigenvalues. At the same time, the FP-LMTO method, in which the space is divided into an interstitial region (IR) and nonoverlapping muffin-tin spheres (MTS) surrounding the atomic sites, uses a more complete basis than its predecessors. In the IR regions, the basis set consists of plane waves. Inside the MT spheres, the basis set is described by radial solutions of the one particle Schrödinger equation (at fixed energy) and their energy derivatives multiplied by spherical harmonics. 2 International Journal of Metals Table 1: Lattice constants 𝑎 and bulk modulus 𝐵 of Cd1−𝑥 Be𝑥 Se compared with experimental results, Vegard’s law, and other theoretical calculations. 𝑥 0 0.25 0.5 0.75 1 a This work 6.06 5.90 5.71 5.46 5.10 Lattice constant 𝑎(Å) Exp. Vegard’s law 6.052a 5.82 5.58 5.34 5.14e Other calc. 6.025b 5.13f –5.04g Bulk modulus 𝐵 (GPa) [B󸀠 ] This work Exp. Other calc. 55.05 [4.17] 55c 54d 57.72 [3.93] 63.19 [4.15] 66.6 [3.85] 81.25 [3.77] 92e 77 [3.55]f –80 [3.11]g Ref [25], b Ref [26], c Ref [27], d Ref [28], e Ref [29, 30], f Ref [31], g Ref [32]. The charge density and the potential are represented inside the MTS by spherical harmonics up to 𝑙max = 6. The integrals over the Brillouin zone are performed up to 35 special 𝑘-points for binary compounds and 27 special 𝑘 points for the alloys in the irreducible Brillouin zone (IBZ) using Blochl’s modified tetrahedron method [18]. The selfconsistent calculations are considered to be converged when the total energy of the system is stable within 10−6 Ry. In order to avoid the overlap of atomic spheres, the MTS radius for each atomic position is taken to be different for each composition. We point out that the use of the full-potential calculation ensures that the calculation is not completely independent of the choice of sphere radii. Structural properties of Cd1−𝑥 Be𝑥 Se are calculated using Murnaghan’s equation of state [19] as follows: 𝐵 𝑉 (𝑉 /𝑉) 0 𝐵𝑉 𝐸 (𝑉) = 𝐸0 + 0󸀠 ( 0󸀠 + 1) − 󸀠0 0 , 𝐵0 𝐵0 − 1 𝐵0 − 1 (1) 𝜀 (𝜔) = 𝜀1 (𝜔) + 𝑖𝜀2 (𝜔) . (2) 8 󵄨2 𝑑𝑆𝑘 󵄨 , ∑ ∫ 󵄨󵄨󵄨𝑝𝑛𝑛󸀠 (𝑘)󵄨󵄨󵄨󵄨 2𝜋𝜔2 𝑛𝑛󸀠 󵄨 ∇𝜔𝑛𝑛󸀠 (𝑘) (3) 𝐵󸀠 where 𝐸0 is the total energy of the supercell, 𝑉0 is the unit volume, 𝐵0 is the bulk modulus at zero pressure, and 𝐵0󸀠 is the derivative of bulk modulus with pressure. Optical properties of Cd1−𝑥 Be𝑥 Se are calculated using a fine 𝑘 mesh of 1500 points for the present calculation. The dielectric function of a crystal depends on the electronic band structure and its investigation by optical spectroscopy which is a powerful tool in the determination of the overall optical behavior of a compound. It can be divided into two parts, real and imaginary as follows: The imaginary part of the complex dielectric function, 𝜀2 (𝜔), in cubic symmetry compounds can be calculated by the following relation [20, 21]: 𝜀2 (𝜔) = while 𝜀1 (𝜔) is used to calculate the real part of the complex dielectric function as follows: ∞ 𝜔󸀠 𝜀 (𝜔󸀠 ) 2 2 𝑑𝜔󸀠 . 𝜀1 (𝜔) = 1 + 𝑝 ∫ 𝜋 0 𝜔󸀠2 − 𝜔󸀠2 (4) Refractive index is calculated in terms of real and imaginary parts of dielectric function by the following relation 𝑛 (𝜔) = 1/2 1/2 1 [{𝜀1 (𝜔)2 + 𝜀2 (𝜔)2 } + 𝜀1 (𝜔)] . √2 (5) 3. Result and Discussion In order to study the structural properties of Cd1−𝑥 Be𝑥 Se (0 < 𝑥 < 1), alloys are modeled at various compositions of Be with a step of 0.25. Structure optimization of each compound is performed by minimizing the total energy with respect to the unit cell volume and 𝑐/𝑎 ratio using Murnaghan’s equation of state [19]. The crystal structure of CdSe and BeSe zinc-blende with space group 𝐹43𝑚 (no. 216). Structural parameters such as lattice constant, 𝑎 (Å), are calculated from the stable volume and are presented in Table 1. It is clear from the table that our calculated results for the binary compounds are in good agreement with the available experimental and calculated data. Figures 1 and 2 show the variation of the calculated equilibrium lattice constant and bulk modulus as a function of concentrations 𝑥 for the Cd1−𝑥 Be𝑥 Se alloy. The obtained results for the composition dependence of the calculated equilibrium lattice parameter almost follow Vegard’s law [22]. In going from CdSe to BeSe, when the Be-content increases, the values of the lattice parameters of the Cd1−𝑥 Be𝑥 Se alloy decrease. This is due to the fact that the size of the Be atom is smaller than the Cd atom. On the opposite side, one can see from Figure 2 that the value of the bulk modulus increases as the Be concentration increases. The calculated band structure and partial density of states for Cd1−𝑥 Be𝑥 Se (0 < 𝑥 < 1) are presented in Figure 3. It is clear from the figure that Cd1−𝑥 Be𝑥 Se (0 < 𝑥 < 1) is a direct band gap material. The substitution of Be does not affect the direct band gap nature of the compound but increases the gap, which is clear from Figure 2(d). The direct band gap varies from 0.39 to 4.45 eV and the indirect band gap also increases from 1.89 to 3.71 eV with the increase in Be concentration between 0.25 and 0.75. It is obvious from the data presented in Table 2 that our calculated values for the band gaps of CdSe and BeSe are closer to the experimental results than the other calculated ones. The reason for our better results is the use of effective Perdew and Wang potential in the LDA scheme [17] and high 𝑘-points (1500). DFT always underestimates the band gaps; the origin of band structures is 3 6.2 85 6.0 80 Bulk modulus (GPa) Lattice parameter (Å) International Journal of Metals 5.8 5.6 5.4 Cd1−x Bex Se 75 70 65 60 5.2 55 5.0 0.0 0.2 0.4 0.6 0.8 0.0 1.0 0.2 Composition x 0.4 0.6 0.8 1.0 Be content x LDA Vegard’s law (b) (a) Figure 1: Variation in lattice constants 𝑎 and bulk modulus 𝐵 of Cd1−𝑥 Be𝑥 Se as a function of composition 𝑥. Table 2: Fundamental direct and indirect band gaps of Cd1−𝑥 Be𝑥 Se compared with the experimental and other calculations. 𝑥 This work 0 0.39 0.25 0.84 0.5 0.75 1 1.44 2.47 4.45 a b Direct energy band gap, 𝐸𝑔Γ−Γ Indirect energy band gap, 𝐸𝑔Γ−𝑋 Exp. Other calc. This work Exp. Other calc. 1.75a 0.34b , 0.26c 2.31 5.4d 5.4e , 3.82f , 3.79g 2.12h , 2.56h [𝑥 = 0.2] 2.65i [0.24], 2.45j [𝑥 = 0.35] 2.65j [𝑥 = 0.46] 4.72k –4.04l c d e f g h 1.89 3.41 2.74 3.71 2.47 2.44 6.32 4–4.5m j k 2.39k , 2.31l Ref [33], Ref [26], Ref [27], Ref [34], Ref [35], Ref [36], Ref [37], Ref [38], Ref [39], Ref [40], Ref [41], Ref [42], m Ref [43]. presented in Figure 3. In general, the band structures of these three compositions 𝑥 (0.25, 0.5, 0.75) are very similar. The uppermost valence band is mainly formed by Se 4p states. The valence band maximum appears to be almost degenerate at the Γ and 𝑋 𝑘 points for three concentrations (0.25, 0.5, and 0.75), the energy at 𝑋 being (1.04, 1.29, and 1.24) eV lower than that at Γ, respectively. On the other hand, the conduction band minimum occurs at Γ, so there is a direct gap of 0.84, 1.44, and 2.47 eV at Γ and an indirect Γ–𝑋 gap of 1.89, 2.74, and 3.71 eV for three concentrations (0.25, 0.5, and 0.75), respectively. To the best of our knowledge, there are no theoretical or experimental data on the energy band gaps for 𝑥 = 0.25, 0.5, and 0.75 available in the literature to make a meaningful comparison. It is clear from the results that the conduction band is mainly composed of Be-2p state for all ternary alloys. Figures 3(a) and 3(b) show that the lower part of the valence band is composed of Cd-4d and the upper part is mainly dominated by Se-4p state. This is due to the nature of bonding. At 𝑥 = 0.25, 0.5, and 0.75 partial covalent bond is stronger so the charge is shared by Se-4p and Be-2s states. i Band gap bowing l The calculated band gap versus concentration was fitted by a polynomial equation. The results are shown in Figure 2(d) and are summarised as follows: Cd1−𝑥 Be𝑥 Se 󳨀→ { 𝐸Γ−Γ = 0.466 − 0.088𝑥 + 3.99𝑥2 𝐸Γ−𝑋 = 1.978 + 2.593𝑥 − 1.737𝑥2 . (6) The variation in the band gap of Cd1−𝑥 Be𝑥 Se provides promising results of the use of the compound in optoelectronic devices working in visible to ultraviolet regions. Depending on the need and requirement of a particular application, any desired band gap between 0.39 and 4.45 eV can be achieved. We have calculated the frequency dependent imaginary dielectric function and real dielectric function. The effects of using 𝑘 points in the BZ have already been discussed in the earlier work by Khan et al. [23]. The knowledge of both the real and the imaginary parts of the dielectric function allows the calculation of important optical functions. In this work, we also present and analyse the refractive index 𝑛(𝜔) given by (4). 4 International Journal of Metals Γ X M Γ R X 14 13 12 11 10 9 8 7 6 5 4 3 2 1 0 −1 −2 −3 −4 −5 −6 −7 EF Energy (eV) 14 13 12 11 10 9 8 7 6 5 4 3 2 1 0 −1 −2 −3 −4 −5 −6 −7 EF Energy (eV) EF Energy (eV) 14 13 12 11 10 9 8 7 6 5 4 3 2 1 0 −1 −2 −3 −4 −5 −6 −7 Γ X M (a) Γ R X (b) Γ X M Γ R X (c) 5 Cd1−x Bex Se Energy gaps (eV) 4 3 2 1 0 0.0 0.2 0.4 0.6 Composition x 0.8 1.0 Γ–Γ Γ–X (d) Figure 2: Calculated band structure of (a) Cd0.75 Be0.25 Se, (b) Cd0.5 Be00.5 Se, (c) Cd0.25 Be0.75 Se, and (d) band gap as a function of 𝑥. The calculated imaginary part of the dielectric function for Cd1−𝑥 Be𝑥 Se (𝑥 = 0.25, 0.5 and 0.75) in the energy range 0–12 eV is shown in Figure 3. It is clear from the figure that for 𝑥 = 0.25, 0.50, 0.75, and 1.0 the critical points in the imaginary part of the dielectric function occur at about 0.85, 1.45, 2.48, and 4.45 eV, respectively. These points are closely Γ−Γ ; 0.84, 1.44, 2.47, and related to the direct band gaps 𝐸𝐺 4.45 eV of Cd1−𝑥 Be𝑥 Se for the corresponding values of 𝑥 = 0. 25, 0.50, 0.75 and 1. The calculated real parts of the complex dielectric function 𝜀1 (𝜔) for Cd1−𝑥 Be𝑥 Se are presented in Figure 3. It is clear from the figure that the static dielectric constant, 𝜀1 (𝜔), is strongly dependent on the band gap of the compound. The calculated values of 𝜀1 (𝜔) for Cd1−𝑥 Be𝑥 Se at 𝑥 = 0, 0.25, 0.50, 0.75 and 1.0 are 4.35, 3.94, 3.74, 3.57, and 3.42 for corresponding direct band gaps 0.39, 0.84, 1.44, 2.47, and 4.45 eV, respectively. These data explain that the smaller energy gap yields larger 𝜀1 (0) value. This inverse relation of 𝜀1 (𝜔) with the band gap can be explained by the Penn model [24] as follows: 𝜀1 (0) ≈ 1 + ( ℎ𝜔𝑝 𝐸𝑔 2 ). (7) The calculated values of the optical dielectric constant 𝜀(𝜔) and refractive index 𝑛(𝜔) are listed in Table 3; comparison with the available data has been made where possible. As compared with other calculations, it seems that the values of 𝑛(𝜔) obtained from FP-LMTO method for the end-point compounds (i.e., CdSe and BeSe) are in good agreement with the theoretical results, together with the refractive index 𝑛(𝜔) = √𝜀 at zero pressure. Note that 𝜀 is obtained from the zero-frequency limit of 𝜀1 (𝜔), and it corresponds to the electronic part of the static dielectric constant of the material, a parameter of fundamental importance in many aspects of materials properties. It is clear from Figure 4 that 5 16 14 Cd0.75 Be0.25 Se 14 16 12 12 10 10 8 8 𝜀(𝜔) 𝜀(𝜔) International Journal of Metals 6 6 4 4 2 2 0 0 −2 −2 −4 Cd0.5 Be0.5 Se −4 0 1 2 3 4 5 6 7 8 9 10 11 12 13 14 0 1 2 3 4 5 6 Energy (eV) 7 8 9 10 11 12 13 14 Energy (eV) 𝜀2 (𝜔) 𝜀1 (𝜔) 𝜀2 (𝜔) 𝜀1 (𝜔) (a) (b) 16 Cd0.25 Be0.75 Se 14 12 10 𝜀(𝜔) 8 6 4 2 0 −2 −4 0 1 3 2 4 5 6 7 8 9 10 11 12 13 14 Energy (eV) 𝜀2 (𝜔) 𝜀1 (𝜔) (c) Figure 3: Frequency dependent imaginary part and real part of dielectric functions of Cd1−𝑥 Be𝑥 Se. Table 3: Refractive index, optical dielectric constant of Cd1−𝑥 Be𝑥 Se alloys for different compositions 𝑥. 𝑥 0 0.25 0.5 0.75 1 a Refractive index 𝑛 Exp. 2.64a This work 2.08 1.98 1.93 1.89 1.85 b c d e f Other calc. 2.47b This work 4.36 3.947 3.74 3.57 3.43 Optical dielectric constant 𝜀 Exp. Other calc. 5.2c 5.05d , 4.89e 6.1f 6.09g g Ref [44], Ref [45], Ref [46], Ref [47], Ref [48], Ref [48], Ref [49]. the refractive index of the material decreases with the increase in the Be concentration. Figure 4 shows the variation of the computed static optical dielectric constant and static refractive index versus composition for Cd1−𝑥 Be𝑥 Se alloys. The computed static optical dielectric constant and static refractive index versus composition were fitted by polynomial equation. The results are summarized as follows: Cd1−𝑥 Be𝑥 Se 󳨀→ { 𝜀 (0) = 4.3400 − 1.5610𝑥 + 0.6662𝑥2 𝑛 (0) = 2.0745 − 0.3685𝑥 + 0.1485𝑥2 . (8) International Journal of Metals 2.10 4.4 2.05 4.2 2.00 4.0 𝜀(0) n(0) 6 1.95 3.8 1.90 3.6 1.85 3.4 0.0 0.2 0.4 0.6 0.8 1.0 0.0 Composition x (a) 0.2 0.6 0.4 Composition x 0.8 1.0 (b) Figure 4: Computed static optical dielectric constant and static refractive index as function of composition for Cd1−𝑥 Be𝑥 Se. 4. Conclusions Density functional calculations are carried out for the first time to investigate structural and optoelectronic properties Cd1−𝑥 Be𝑥 Se. Structure as well as bonding nature of the material significantly varies with Be concentration. The lattice constant of the crystal decreases linearly with 𝑥. The calculated band structure predicts that the alloys have direct band gaps, which increase with the increase in 𝑥. On the basis of wide range of fundamental direct band gaps (0.39– 4.45 eV) and indirect band gaps (1.89–3.71 eV) between 0.25 and 0.75, it can be concluded that the material can be used in optoelectronic devices working in the IR, visible, and UV regions of the spectrum. [7] [8] [9] [10] Conflict of Interests The authors declare that there is no conflict of interests regarding the publication of this paper. References [1] H. Luo and J. K. 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Kruse et al., “Lattice dynamics and bond polarity of be-chalcogenides a new class of II-VI materials,” Physica Status Solidi B, vol. 215, no. 1, pp. 87–91, 1999. Journal of Nanotechnology Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 International Journal of International Journal of Corrosion Hindawi Publishing Corporation http://www.hindawi.com Polymer Science Volume 2014 Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 Journal of Smart Materials Research Hindawi Publishing Corporation http://www.hindawi.com Composites Volume 2014 Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 Journal of Metallurgy BioMed Research International Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 Nanomaterials Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 Submit your manuscripts at http://www.hindawi.com Journal of Materials Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 Journal of Nanoparticles Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 Nanomaterials Journal of Advances in Materials Science and Engineering Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 Scientifica Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 The Scientific World Journal Hindawi Publishing Corporation http://www.hindawi.com Journal of Journal of Journal of Journal of Nanoscience Coatings Crystallography Ceramics Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 International Journal of Biomaterials Hindawi Publishing Corporation http://www.hindawi.com Volume 2014 Journal of Textiles Volume 2014 Hindawi Publishing Corporation http://www.hindawi.com Volume 2014