 NANO EXPRESS
 Open Access
 Published:
SelfConsistent Hybrid Functional Calculations: Implications for Structural, Electronic, and Optical Properties of Oxide Semiconductors
Nanoscale Research Letters volume 12, Article number: 19 (2017)
Abstract
The development of new exchangecorrelation functionals within density functional theory means that increasingly accurate information is accessible at moderate computational cost. Recently, a newly developed selfconsistent hybrid functional has been proposed (Skone et al., Phys. Rev. B 89:195112, 2014), which allows for a reliable and accurate calculation of material properties using a fully ab initio procedure. Here, we apply this new functional to wurtzite ZnO, rutile SnO_{2}, and rocksalt MgO. We present calculated structural, electronic, and optical properties, which we compare to results obtained with the PBE and PBE0 functionals. For all semiconductors considered here, the selfconsistent hybrid approach gives improved agreement with experimental structural data relative to the PBE0 hybrid functional for a moderate increase in computational cost, while avoiding the empiricism common to conventional hybrid functionals. The electronic properties are improved for ZnO and MgO, whereas for SnO_{2} the PBE0 hybrid functional gives the best agreement with experimental data.
Background
Metal oxides exhibit many unique structural, electronic, and magnetic properties, making them useful for a broad range of technological applications. Metal oxides are exclusively used as transparent conducting oxides (TCOs) [1], find applications as building blocks in artificial multiferroic heterostructures [2] and as spinfilter devices [3], and even include a huge class of superconducting materials. To develop new materials for specific applications, it is necessary to have a detailed understanding of the interplay between the chemical composition of different materials, their structure, and their electronic, optical, or magnetic properties.
For the development of new functional oxides, computational methods that allow theoretical predictions of structural and electronic properties have become an increasingly useful tool. When optical or electronic properties are under consideration, electronic structure methods are necessary, with the most popular approach for solids being density functional theory (DFT). DFT has proven hugely successful in the calculation of structural properties of condensed matter systems and the electronic properties of simple metals [4]. The earliest developed approximate exchangecorrelation functionals, however, face limitations, for example severely underestimating band gaps of semiconductors and insulators.
Over the last decade, several new, more accurate, exchangecorrelation functionals have been proposed. Increased predictive accuracy often comes with an increased computational cost, and the adoption of these more accurate functionals has only been made possible through the continued increase in available computational power. One such more accurate, and more costly, approach is to use socalled hybrid functionals. These are constructed by mixing a fraction of HartreeFock exactexchange with the exchange and correlation terms from some underlying DFT functional. Calculated material properties, such as lattice parameters and band gaps, however depend on the precise proportion of HartreeFock exactexchange, α. Typical hybrid functionals treat α as a fixed empirical parameter, chosen by intuition and experimental calibration. A recently proposed selfconsistent hybrid functional approach for condensed systems [5] avoids this empiricism and allows parameterfree hybrid functional calculations to be performed. In this approach, the amount of HartreeFock exactexchange is identified as the inverse of the dielectric constant, with this constraint achieved by performing an iterative sequence of calculations to selfconsistency.
Here we apply this new selfconsistent hybrid functional to wurtzite ZnO and rutile SnO_{2}, both materials with potential applications as TCOs, and MgO, a wide band gap insulator [6]. We examine the implications of the selfconsistent hybrid functional for the structural, electronic, and optical properties. In the next section, we present the theoretical background, describe the selfconsistent hybrid functional, and give the computational details. We then present results for the structural, electronic, and optical properties for ZnO, SnO_{2}, and MgO, and compare these to data calculated using alternative exchangecorrelation functionals and from experiments. The paper concludes with a summary and an outlook.
Methods
Density functional theory and hybrid functionals
DFT is a popular and reliable tool to theoretically describe the electronic structure of both crystalline and molecular systems. DFT provides a meanfield simplification of the manybody Schrödinger equation. The central variable is the electron density \(n(\vec {r}) = \psi ^{*}(\vec {r})\psi (\vec {r})\), determined from the electronic wavefunctions \(\psi (\vec {r})\), and the Hamiltonian is described as a functional of the \(n(\vec {r})\). Within the generalised KohnSham scheme, the potential is
The Hartree potential, v _{H}(r), and the external potential, v _{ext}(r), are in principle known. The exchangecorrelation potential, \(v_{\text {xc}}(\vec {r},\vec {r}^{\prime })\), however, is not and must be approximated. Most successful early approximations make use of the local density approximation and the semilocal generalised gradient approximation (GGA), for example, in the parametrisation of Perdew, Burke, and Ernzerhof (PBE) [7]. These approximations already allowed reliable descriptions of structural properties within the computational resources available at the time, but lacked accuracy when determining band energies, especially fundamental band gaps, and d valence band widths of semiconductors. These properties are particularly important for reliable calculations of electronic and optical behaviours of semiconductors.
In recent years, socalled hybrid functionals have gained in popularity. In a hybrid functional, some proportion of the local exchangecorrelation potential is replaced by HartreeFock exactexchange terms, giving a better description of electronic properties. The explicit inclusion of exactexchange HartreeFock terms make these calculations computationally much more demanding compared to the earlier GGA calculations, and hybrid functional calculations have become routine only in recent years. The fraction of HartreeFock exactexchange admixed in these hybrid functionals, α, is usually justified on experimental or theoretical grounds, and then fixed for a specific functional. This adds an empirical parameter and forfeits the ab initio nature of the calculations. One popular choice of α=0.25 is realised in the PBE0 functional [8].
In this work, we are concerned with fullrange hybrid functionals, for which the generalised nonlocal exchangecorrelation potential is
A common approach is to select α to reproduce the experimental band gap of solid state systems. Apart from adding an empirical parameter into the calculations, fitting the band gap of a material requires reliable experimental data. Moreover, this approach does not guarantee that all electronic properties, e.g. d band widths or defect levels, are correct [9]. Recently, it has been argued from the screening behaviour of nonmetallic systems that α can be related to the inverse of the static dielectric constant [10, 11]
which may then be computed in a selfconsistent cycle [5, 12]. This iteration to selfconsistency requires additional computational effort, but removes the empiricism of previous hybrid functionals and restores the ab initio character of the calculations. The utility of this approach, however, depends on the accuracy of the resulting predicted material properties. Here, we are interested in the implications for the structural, electronic, and optical properties of oxide semiconductors, and consider ZnO, SnO_{2}, and MgO as an illustrative set of materials.
Computational Details
The calculations presented in this work have been performed using the projectoraugmented wave (PAW) method [13], as implemented in the Vienna ab initio simulation package (VASP 5.4.1) [14–16]. For the calculation of structural and electronic properties, standard PAW potentials supplied with VASP were used, with 12 valence electrons for Zn atom (4s ^{2}3d ^{10}), 14 valence electrons for Sn (5s ^{2}4d ^{10}5p ^{2}), 8 valence electrons for Mg (2p ^{6}3s ^{2}), and 6 valence electrons for O (2s ^{2}2p ^{4}), respectively. When calculating dielectric functions, we have used the corresponding GW potentials, which give a better description of highenergy unoccupied states.
To evaluate the performance of the selfconsistent hybrid approach, we have calculated structural and electronic data using three functionals: GGA in the PBE parametrisation [7], the hybrid functional PBE0 [8], and the selfconsistent hybrid functional [5], which we denote scPBE0.
Structural relaxations were performed for the regular unit cells within a scalarrelativistic approximation, using dense k point meshes for Brillouin zone integration (8×8×6 for wurtzite ZnO, 6×6×8 for rutile SnO_{2}, and 10 × 10 × 10 for rocksalt MgO). For each material, we performed several fixedvolume calculations, in the cases of ZnO and SnO_{2} allowing internal structural parameters to relax until all forces on ions were smaller than 0.001 eV Å^{−1}. Zeropressure geometries were determined by then fitting a cubic spline to the total energies with respect to the unit cell volumes.
To evalutate the selfconsistent fraction of HartreeFock exactexchange, α, the dielectric function ε _{ ∞ } is calculated in an iterative series of full geometry optimisations. To calculate ε _{ ∞ }, for each of the ground state structures, the static dielectric tensor has been calculated (including local field effects) from the response to finite electric fields. For noncubic systems (ZnO, SnO_{2}), ε _{ ∞ } was obtained by averaging over the spur of the static dielectric tensor \(\frac {1}{3}\left (2\epsilon _{\infty }^{\perp }+\epsilon _{\infty }^{\parallel }\right)\). We have considered ε _{ ∞ } to be converged when the difference between two subsequent calculations falls below ±0.01 [5].
Results and Discussion
Structural properties
ZnO crystallises in the hexagonal wurtzite structure of space group P6_{3}mc (No. 186). SnO_{2} crystallises in the tetragonal rutile structure of space group P4_{2}/mnm (No. 136). MgO crystallises in the cubic rocksalt structure of space group Fm\(\bar {3}\)m (No. 225). Each crystal structure was first fully geometry optimised, as described in the computational details section. The energy/volume data for the GGA, PBE0, and scPBE0 exchangecorrelation potentials are plotted in the upper panels of Fig. 1. The GGA functional significantly overestimates the ground state volume relative to experimental values for all three materials. This is due to shortcomings in this simpler early exchangecorrelation potential. The PBE0 functional adds a fixed proportion of HartreeFock exactexchange (α=0.25) and produces structural properties in much better agreement with experimental data.
For our scPBE0 calculations, for each material, the static dielectric constant converged in three iterations (Fig. 1, lower panels). Here, computationally the most expensive part is the full geometry optimisation using the PBE0 functional. Each subsequent step in the selfconsistent loop to determine the amount of HartreeFock exactexchange starts from optimised crystal structures of the previous step and reduces the computational costs considerably.
Using the selfconsistent amount of HartreeFock exactexchange in the selfconsistent hybrid functional yielded structural properties in slightly better agreement with experimental data (Fig. 1, upper panels). The improved description of structural properties using the scPBE0 functional is also evident from the lattice constants a (and c), which are given together with those obtained with the other two functionals and experimental data in Table 1.
The quality of the structural data compared to experiment can also be seen from Fig. 2 where the coefficients of the different obtained ground state volumes with respect to the experimental one are plotted for the three different oxides. Again, the results obtained with the new selfconsistent hybrid functional show closest agreement with experiment.
Electronic and Optical Properties
Figure 3 shows electronic band structures calculated using scPBE0 for wurtzite ZnO, rutile SnO_{2}, and rocksalt MgO. The calculated (versus experimental) direct band gaps are 3.425 eV (3.4449 eV [17]) for ZnO, 3.827 eV (3.596 eV [18]) for SnO_{2}, and 8.322 eV (7.833 eV [19]) for MgO, respectively (Table 1). Figure 4 shows the GGA, PBE0, and scPBE0 calculated band gaps alongside the experimental values. It can be seen that PBE0 calculated band gaps are underestimated compared to the experimental ones for all three oxides, but being very close for SnO_{2}. The scPBE0 calculated band gaps are larger than the PBE0 values, thereby improving the results for ZnO and MgO, but worsen the result for SnO_{2}. In general, the band gaps calculated using the hybrid functionals (PBE0, scPBE0) are within ten per cent of the experimental band gaps.
The scPBE0 calculations provide accurate structural properties and band gaps versus experimental data, and we can therefore be relatively confident when calculating properties less easily accessible directly by experiment. We have calculated the real (ε _{1}) and imaginary (ε _{2}) parts of the dielectric functions via Fermi’s Golden rule summing over transition matrix elements. For these calculations, we used the recommended VASP GW pseudopotentials and considerably increased the number of empty bands to ensure converged results.
Figure 5 shows the real (ε _{1}) and imaginary (ε _{2}) parts of the dielectric functions calculated with the GGA, PBE0, and scPBE0 functionals. Because the GGA functional significantly underestimates the band gap, the imaginary parts of the dielectric functions exhibit an onset, corresponding to the first allowed direct transition at the fundamental band gap, at lower energies. The onset energy improves considerably when switching to the PBE0 hybrid functional and improves further compared to experiment when using the selfconsistent hybrid functional. For the two hybrid functionals, the overall shape of the real and imaginary parts of the dielectric functions are very similar in their peak structure but differ compared to the pure GGA functional. One reason for this difference might be the improvements in the d band width and position when using the hybrid functionals compared to the pure GGA one. Clarifying this would require a more indepth comparison of the different band structures and how their specific features influence the dielectric functions.
Conclusions
We have presented a theoretical investigation on the application of a new selfconsistent hybrid functional to oxide semiconductors ZnO, SnO_{2}, and MgO. We have presented and compared calculated structural, electronic, and optical properties of these oxides to experimental data, and have discussed the implications of using the new selfconsistent hybrid functional. We find that the selfconsistent hybrid functional gives calculated properties with accuracies as good as or better than the PBE0 hybrid functional. The additional computational cost due to the selfconsistency cycle is justified by avoiding the empiricism of similar hybrid functionals, which restores the ab initio character of these calculations.
Abbreviations
 DFT:

Density functional theory
 GGA:

Generalised gradient approximation
 PAW:

Projectoraugmented wave
 PBE:

Perdew, Burke, and Ernzerhof
 TCOs:

Transparent conducting oxides
 VASP:

Vienna ab initio simulation package
References
 1
Minami T (2005) Transparent conducting oxide semiconductors for transparent electrodes. Semicond Sci Technol 20: S35.
 2
Fritsch D, Ederer C (2010) Epitaxial strain effects in the spinel ferrites CoF e_{2}O_{4} and NiF e_{2}O_{4} from first principles. Phys Rev B 82: 104117.
 3
Caffrey NM, Fritsch D, Archer T, Sanvito S, Ederer C (2013) Spinfiltering efficiency of ferrimagnetic spinels CoF e_{2}O_{4} and NiF e_{2}O_{4}. Phys Rev B 87: 024419.
 4
Hasnip PJ, Refson K, Probert MIJ, Yates JR, Clark SJ, Pickard CJ (2014) Density functional theory in the solid state. Phil Trans R Soc A 372: 20130270.
 5
Skone JH, Govoni M, Galli G (2014) Selfconsistent hybrid functional for condensed systems. Phys Rev B 89: 195112.
 6
Fritsch D, Schmidt H, Grundmann M (2006) Pseudopotential band structures of rocksalt MgO, ZnO, and Mg_{1−x }Zn_{ x }O. Appl Phys Lett 88: 134104.
 7
Perdew JP, Burke K, Ernzerhof M (1996) Generalized gradient approximation made simple. Phys Rev Lett 77: 3865.
 8
Adamo C, Barone V (1999) Toward reliable density functional methods without adjustable parameters: The PBE0 model. J Chem Phys 110: 6158.
 9
Walsh A, Da Silva JLF, Wei SH (2008) Theoretical description of carrier mediated magnetism in cobalt doped ZnO. Phys Rev Lett 100: 256401.
 10
Alkauskas A, Broqvist P, Pasquarello A (2011) Defect levels through hybrid density functionals: insights and applications. Phys Stat Sol B 248: 775.
 11
Marques MAL, Vidal J, Oliveira MJT, Reining L, Botti S (2011) Densitybased mixing parameter for hybrid functionals. Phys Rev B 83: 035119.
 12
Gerosa M, Bottani CE, Caramella L, Onida G, Di Valentin C, Pacchioni G (2015) Electronic structure and phase stability of oxide semiconductors: performance of dielectricdependent hybrid functional DFT, benchmarked against GW band structure calculations and experiments. Phys Rev B 91: 155201.
 13
Blöchl PE (1994) Projector augmentedwave method. Phys Rev B 50: 17953.
 14
Kresse G, Hafner J (1993) Ab initio molecular dynamics for liquid metals. Phys Rev B 47: 558.
 15
Kresse G, Hafner J (1994) Ab initio moleculardynamics simulation of the liquidmetal −amorphoussemiconductor transition in germanium. Phys Rev B 49: 14251.
 16
Kresse G, Furthmüller J (1996) Efficiency of abinitio total energy calculations for metals and semiconductors using a planewave basis set. Comput Mat Sci 6: 15.
 17
Liang WY, Yoffe AD (1968) Transmission spectra of ZnO single crystals. Phys Rev Lett 20: 59.
 18
Reimann K, Steube M (1998) Experimental determination of the electronic band structure of SnO_{2}. Solid State Commun 105: 649.
 19
Whited RC, Flaten CJ, Walker WC (1973) Exciton thermoreflectance of MgO and CaO. Solid State Commun 13: 1903.
 20
Reeber RR (1970) Lattice parameters of ZnO from 4.2° to 296° K. J Appl Phys 41: 5063.
 21
Schulz H, Thiemann KH (1979) Structure parameters and polarity of the wurtzite type compounds SiC2H and ZnO. Solid State Commun 32: 783.
 22
Heltemes EC, Swinney HL (1967) Anisotropy in lattice vibrations of zinc oxide. J Appl Phys 38: 2387.
 23
Haines J, Léger JM (1996) Xray diffraction study of the phase transitions and structural evolution of tin dioxide at high pressure: relationships between structure types and implications for other rutiletype dioxides. Phys Rev B 55: 11144.
 24
Summitt R (1968) Infrared absorption in singlecrystal stannic oxide: optical latticevibration modes. J Appl Phys 39: 3762.
 25
Hazen RH (1976) Effects of temperature and pressure on the cell dimension and Xray temperature factors of periclase. Am Mineral 61: 266.
 26
Jasperse JR, Kahan A, Plendl JN, Mitra SS (1966) Temperature dependence of infrared dispersion in ionic crystals LiF and MgO. Phys Rev 146: 526.
Acknowledgements
This research has received funding from the European Union’s Horizon 2020 research and innovation programme under grant agreement No 641864 (INREP). This work made use of the ARCHER UK National Supercomputing Service (http://www.archer.ac.uk) via the membership of the UK’s HPC Materials Chemistry Consortium, funded by EPSRC (EP/L000202) and the Balena HPC facility of the University of Bath. BJM acknowledges support from the Royal Society (UF130329).
Authors’ contributions
AW and BJM conceived the idea. DF performed the calculations, analysed the data, and wrote the manuscript. DF, BJM, and AW participated in the discussions of the calculated results. All the authors have read and approved the final manuscript.
Competing interests
The authors declare that they have no competing interests.
Author information
Rights and permissions
Open Access This article is distributed under the terms of the Creative Commons Attribution 4.0 International License (http://creativecommons.org/licenses/by/4.0/), which permits unrestricted use, distribution, and reproduction in any medium, provided you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made.
About this article
Received
Accepted
Published
DOI
Keywords
 Density functional theory
 Hybrid functionals
 Semiconducting oxides
 Dielectric functions
PACS Codes
 71.15.Mb
 71.20.Nr
 78.20.Bh