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International Journal of Photoenergy
Volume 2012 (2012), Article ID 928503, 8 pages
Effect of Electronegativity and Charge Balance on the Visible-Light-Responsive Photocatalytic Activity of Nonmetal Doped Anatase TiO2
1School of Physics, State Key Laboratory of Crystal Materials, Shandong University, Jinan 250100, China
2Advanced Materials and Process Engineering Laboratory, The University of British Columbia, Vancouver, BC, Canada V6T 1Z4
3MEMS Department, Duke University, Durham, NC 27708-0300, USA
Received 4 July 2011; Accepted 8 August 2011
Academic Editor: Jinlong Zhang
Copyright © 2012 Jibao Lu 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 origin of visible light absorption and photocatalytic activity of nonmetal doped anatase TiO2 were investigated in details in this work based on density functional theory calculations. Our results indicate that the electronegativity is of great significance in the band structures, which determines the relative positions of impurity states induced by the doping species, and further influences the optical absorption and photocatalytic activities of doped TiO2. The effect of charge balance on the electronic structure was also discussed, and it was found that the charge-balance structures may be more efficient for visible light photocatalytic activities. In addition, the edge positions of conduction band and valence band, which determine the ability of a semiconductor to transfer photoexcited electrons to species adsorbed on its surface, were predicted as well. The results may provide a reference to further experimental studies.
Titanium dioxide (TiO2) is one of the most promising materials due to its low-cost, nontoxic, long-term stability and high oxidative power, which can be used in a wide range of technical fields, such as photocatalytic degradation of pollutants and photoelectrochemical conversion of solar energy [1, 2]. However, because of its large band gap (3.0–3.2 eV), TiO2 is only responsive to ultraviolet irradiation ( nm), which only accounts for ca.4% of sunlight. In order to extend the photo response of TiO2 into the visible region and enhance its photocatalytic activity, a great deal of effort has been made to lower its threshold energy for photoexcitation as well as improve the electronic properties of TiO2. One of the effective strategies is doping TiO2 with nonmetallic elements, such as N [2–10], C [11–14], S [15–19], and B [20–23], all of which showed considerable photocatalytic activity under visible light.
While most researchers focus on the phenomena of redshift induced by special species doping, a thorough and systematical analysis of the modification mechanism of TiO2, especially the essential reasons of causing various electronic structures doped with different nonmetallic elements, do not catch due attention of scientists. To explore a common rule of the band structure modification for nonmetal doping, we systematically compared the doping effects of four nonmetal species (B, C, N, and F) on anatase TiO2. For easy comparison, we only considered the electronic properties of structures with substitutional nonmetal X (X = B, C, N, and F) to O in this paper, though the formation energies were also calculated to reveal the relative stabilities of the doped structures. To check the influence of charge balance, we have calculated the electronic structures of codoped TiO2 with N : H, C : 2H, and B : 3H, respectively (note that the oxygen vacancies, which are not considered here, may also form to compensate the unbalanced charge, which can induce deep defect levels in the band gap  and usually lead to increment of the recombination). In addition, the role of the electronegativity of doping species in the optical absorption and photocatalytic activity of anatase TiO2 was elucidated in this paper, and we have found that the impurity states move further away from the valence band maximum (VBM) with the increment of the electronegativity difference between the substitutional elements and oxygen. Also, the edge positions of conduction band (CB) and valence band (VB) for doped anatase TiO2 were predicted, which should serve as a reference to future experimental studies.
2. Computational Details
Our theoretical study was carried out in the framework of density functional theory (DFT) within generalized gradient approximation (GGA) . The Vienna ab initio Simulation Package [28, 29] (VASP) was implemented in the calculations, in which the plane-wave basis set, Vanderbilt ultrasoft pseudopotentials and the exchange-correlation functional of Perdew et al. (PBE) were used . The underestimation of band gap by DFT calculations does not affect the analysis, since we only care about the relative changes of the gap, and the PBE functional has been demonstrated to be reliable by previous studies . We simulated the nonmetal-doped TiO2 model using a 48-atom supercell, in which one O atom is substituted by one impurity atom, and this corresponds to an impurity concentration of about 2%, namely, with , (where D is the corresponding dopant). The supercell geometry and the doped position of the anatase TiO2 system are shown in Figure 1. The cutoff energy for the basis set was chosen to be 500 eV, and the surface Brillouin zones were sampled at 2 × 2 × 2 Γ-centered -points . The density of state (DOS) for the bulk TiO2 was performed at the equilibrium volume using the tetrahedron method with Blöchl corrections for accuracy . Considering that the impurity concentration is very low, the volume of supercell is kept fixed while the atomic positions are fully relaxed until that all forces are smaller than 10−4 eV/Å.
3. Results and Discussion
3.1. Electronegativity Effect on the Electronic Structures
As we know, electronegativity is the intrinsic property which measures the escaping tendency of electrons from atomic species. Based on DFT theory, Parr and coworkers  have given the precise definition to the electronegativity of a neutral atom, which is the negative value of the chemical potential in the ground state: where and are the ground-state electronic energy and the number of electrons, respectively. Formula (1) can then be rewritten using differential equation: where and represent the ionization potential (IP) and electron affinity (EA) of the atom. We can see that Formula (2) has the same expression with the Mulliken’s definition of the electronegativity . The electronegativities of several species calculated by Formula (2) are listed in Table 1.
When the nonmetallic elements are brought to the bulk TiO2, charges will redistribute until the electrochemical potentials of the compound reach equilibrium. To unravel the inherent relationship of the electronic properties induced by different doping species, which possessed unique electronegativity, the total density of state (TDOS) and projected density of state (PDOS) for the doped TiO2 are calculated and displayed in Figure 2. For comparison, the TDOS and PDOS of pure anatase are also calculated and shown in Figures 2(a) and 2(a′). We can see that the edge of the valence band is mainly contributed by the O 2p atomic orbitals with a large bandwidth of about 5.0 eV, whereas the conduction band is almost entirely composed of empty Ti 3d orbitals.
For the F-doped TiO2, (see Figures 2(b) and 2(b′)), the replacement of one O atom with one F atom exerts little effect on the band-gap narrowing. The impurity states introduced by F 2p atomic orbitals locate mainly in the lower energy range (from −5.5 eV to −4.5 eV) of the valence band, which implies that only the substitutional F to O cannot lead to any significant shift in the fundamental absorption edge of TiO2, consistent with the former experimental results [36, 37]. It is noticed that the electronegativity mainly determines the properties of the outermost atomic orbitals, which simultaneously influence the impurity states induced by F doping. Hence, the larger electronegativity of fluorine (Table 1) should be responsible for the lower energy range of the impurity states in the valence band.
Similar doping effects also appear in Cl-doped sample. Because the electronegativity of chlorine is just a little larger than that of oxygen, they have the similar power of attracting electrons. Accordingly, the impurity states induced by Cl 3p states should mix with the O 2p states in the valence band. The calculated DOS provides evidence for the distribution character of these states. From Figures 2(c) and 2(c′), we can see clearly that the band gap reduces little as compared with the pure anatase TiO2, and the Cl 3p states lie in the whole valence band, (from −5.5 eV to −0.1 eV), showing strong delocalization characteristic of Cl- ion.
For substitutional N to O anatase model (see Figures 2(d) and 2(d′)), due to the closer electronegativity of N to that of O, the oxidative power of N is similar to that of O element. Accordingly, the N 2p states locate just above or in the VBM. Since some of the impurity states overlap and mix with the VBM, new edge of valence band can be formed instead of pure O 2p atomic orbitals, which shifts towards the higher energy and results in the band gap narrowing of about 0.43 eV. Consequently, the decrease of the photo-excitation energy leads to the redshift of absorption and extends the photo response into visible region. These results are in good agreement with previous experimental studies [6, 16, 17] and our former theoretical calculations [8, 18].
Figure 2(e) presents that the substitutional C to O atom in anatase TiO2 introduces one empty and two occupied localized states in the middle of the gap, which are contributed by the C 2p states. Experimentally, evidence of states within the band gap arising from these levels for C-doped titania has been found by XPS [38, 39].
In addition, the band gap between the highest O 2p states and the lowest Ti 3d states has little change as compared with the undoped TiO2. Therefore, the observed redshift of optical absorption would be mainly attributed to the existence of impurity states in the mid gap of TiO2. It is interesting that the electronegativity of carbon is close to that of nitrogen (see Table 1). However, these gap states are located at 0.68, 1.01, and 1.6 eV away from the VBM. We tentatively postulate that it is mainly due to the higher chemical valence of carbon than oxygen, which results in the shift of C 2p states towards the CB.
For the case of B-doped TiO2, the substitution of B for O induces some new impurity gap states, which are dominated by the B 2p atomic orbitals. In addition, since the electronegativity of boron is much smaller than that of oxygen but approaches to that of titanium, the redox potentials of boron will be close to that of titanium as compared with oxygen, which leads to the impurity gap states lying below or overlapping with the conduction band, (see Figures 2(f) and 2(f′)). It is well established that the existence of impurity states in the mid gap can lower the energy barrier in the light absorption process. Therefore, these B 2p states should be responsible for the improvement of visible light absorption of TiO2.
Additionally, to compare the relative stabilities of anatase TiO2 samples doping with different elements, we calculated the formation energies as follows: where and are the total energy of doped and pure anatase supercell, respectively. The symbols and represent the chemical potential of oxygen and doped elements, respectively. Here we only focus on the so-called oxygen-rich synthesis condition, where the chemical potential for oxygen is related to the chemical potential for gaseous O2 at 1 bar. We report our results in Table 2 with the optimized Ti-D bond lengths also listed. It can be noted that the formation energy decreases with the increase of electronegativity of dopant. In particular, for the F-doped case, the formation energy has a negative valve, which implies that it is thermodynamically preferred. In addition, it is worthwhile to mention that the substitutional (for O) doping could be much easier under oxygen-poor condition due to the lower oxygen partial pressure, while the relative stabilities between the structures doped with different ions remain the same as those under oxygen-rich condition.
3.2. Effect of Charge Balance on the Electronic Structures
To understand the effect of charge balance on the electronic structures, we balance the charge of N, C, and B with one H, two H, and three H atoms, respectively, which is reasonable because the doped TiO2 materials were usually processed with amine solution [3–5], H2 , or BH3 atmosphere [20, 21]. In the calculations, one O atom is replaced by N : H species, C : 2H species, and B : 3H species, respectively (see Figure 3). The corresponding DOS of N : H-doped, C : 2H-doped, and B : 3H-doped TiO2 are calculated and shown in Figure 4. Obviously, for the C-doped TiO2, when the charge balance structure is obtained, three isolated gap states are replaced by one occupied state, which is located near the VBM, (see Figures 4(c) and 4(c′)). From Figure 4, we can see clearly that with the decrease of the electronegativity difference between oxygen and substitutional elements, (N, C, and B), the impurity states become closer to the VBM. In addition, when the charges are balanced, the electron donors (H) may contribute to the lowering of the energy levels related to the acceptors (N, C, and B), resulting in the impurity states downward to the VBM, which agrees well with the previous studies . Accordingly, the N : H species may enhance the mixing of impurity states induced by N 2p states and O 2p atomic orbitals in the VBM, and finally new valence bands can be formed, which could contribute to the formation of the band-band transition, in favor of the visible-light-driven catalytic activities. When it comes to the B : 3H-codoped case, though the impurity energy level moves a little toward the VBM, the isolated states are still localized in the midgap because of the large difference of the electronegativity between substitutional boron and oxygen. Therefore, based on these understandings, we can draw a conclusion that if the electronegativity of oxygen is close to that of the doping species, together with the simultaneous formation of charge-balance structure, the doped TiO2 may possess high photocatalytic activity under visible light.
Additionally, we also studied the N : F codoping effect on the anatase TiO2, which are expected to be efficient to the visible light photocatalytic activity according to the analysis above. The supercell is simulated by replacing two O atoms with one N atom and one F atom, respectively (see Figure 3(d)), and the corresponding structure and DOS are shown in Figure 4(a). It is apparent that the impurity states induced by N and F doping locate in different range of the valence band, which can be ascribed to their unique electronegativities as we discussed above. Obviously, the absorption edge of new band in the visible light originated from the doped N atoms rather than doped F atoms, consistent with the former studies [36, 37]. Furthermore, the impurity states are fully filled with the electrons at the ground state, which can be attributed to the fact that the doped F- ion compensates the charge of N3- ion. Therefore, similar to the case of N : H codoping, the N : F complex results in the formation of the charge-balance structure and could enhance the mixing of impurity states with the VBM, which favors the band-band transition and the photocatalytic activities under visible light.
3.3. Prediction of Redox Potentials from Atomic Electronegativity
As we know, the ability of a semiconductor to transfer photoexcited electrons to species adsorbed on its surface is governed by the band energy position of the semiconductor and the redox potentials of the adsorbate, which is related to the electronegativity . Therefore, to thoroughly understand the effects of the electronegativity on the doped TiO2, we have calculated the positions of CB and the VB edge using the concept of the semiconductor electronegativity, which is defined as the geometric mean of the electronegativities of the constituent atoms: where , , and are the electronegativity of the constituent atom, the number of species, and the total number of atoms in the compound, respectively .
The CB edge position of a semiconductor at the point of zero charge () can be expressed empirically by where and are the band gap energy of the semiconductor and the energy of free electrons on the hydrogen scale (~4.5 eV) . Although this method cannot give precise absolute values due to the neglect of structural factors, it may give a rough estimate of the relative positions of normal hydrogen electrode (NHE), which could provide a reference to future experimental studies.
Due to the well-known drawback of DFT theory, our DFT calculations under GGA level give band gaps of about 2.2 eV, smaller than the experimental values (3.23 eV) . In order to correct the underestimation of band gaps, we employed scissor operator, that is, a systematic upward shifting of the unoccupied states by a constant amount. In addition, we postulate that the amount of the band gaps underestimation would not be affected by doping effect because long-range screening properties of doped TiO2 are expected to be similar to those in pure TiO2. Therefore, in this paper we use a rigid constant shift of the band gaps for both pure and doped TiO2, namely, 1.03 eV. Consequently, the adjusted band gaps are 3.23 eV for pure TiO2, which is in line with the experimental values.
According to the strategies mentioned above, the rough CB edge potential of pure anatase TiO2 is −0.27 eV with respect to NHE. Subsequently the VB edge position is determined as 2.96 eV based on its band gap energy. The corrected band gap energy () and the corresponding CB and VB edge positions versus NHE are shown in Figure 4.
It can be found that the electronegativity of doping species produces certain influence on the oxidative potential of doped TiO2. Generally, when the impurity states locate in the lower range of the valence band or mixing with the VBM, (see Figures 5(b)–5(g)), the doped TiO2 possess more oxidative power with the increasing of the electronegativity of the doping species or complex. When it comes to the B : H-codoped, C- and B-doped cases, these materials also obey such rule, (see Figures 5(h)–Figure 5(k)). However, since there are some isolated states in the midgap, the situations may become more complicated, which need further studies. Moreover, it can be known from the results that though F-doping could not contribute to the optical absorption spectra, it possesses strong oxidative potential, which could enhance the redox ability of TiO2. In addition, it has been studied that the doped F atoms could reduce the electron-hole recombination rate and further enhances the photocatalytic activity [36, 44]. Therefore, the N : F-codoped TiO2 may possess high-photocatalytic activity under visible light irradiation, which makes it an excellent candidate for further applications.
Finally, since surface conditions are of key importance in heterogeneous photocatalysis, a further discussion on how the findings can be applied to doped surfaces is necessary. On the pure TiO2 surfaces, additional surface states will be introduced in the electronic structures due to the surface reconstruction or dangling bonds formed on it, whereas for the deep inner layers below surfaces the electronic structure retains its bulk character. So that the above findings can be rationally applied to the doping of inner layers of surfaces, while when they are applied to the doping of the several outermost layers of surfaces, additional calculations and analysis are needed to give a verification.
Our results show that when the electronegativity of the doping species is larger than that of oxygen, such as F and Cl, the impurity states induced mainly by outermost atomic orbitals locate in the lower energy range of the valence band, which cannot contribute to the redshift of absorption. Whereas when the electronegativity of the doping species is smaller than that of oxygen, the impurity states will lie above the VBM. Especially, if the difference is small, such as N, the impurity states can mix and overlap with the O 2p states, leading to the photo response of TiO2 under visible light irradiation. In addition, once the charge balance structures are obtained, the electron donors can lower the impurity states levels and enhance the mixing of N 2p atomic orbitals with O 2p states. Also, we have found that the N:F complex may be more efficient to the visible light photocatalytic activities. Hence, on the basis of these understandings, we have proposed a new way to interpret the mechanism of the redshift and predict the photocatalytic activities doping with different species. Furthermore, based on the definition of the semiconductor electronegativity, the CB and VB edge positions have been predicted, which demonstrated that the doped TiO2 possess favorable redox potentials under visible light, making them promising materials for further applications. Based on the above analysis, we conclude that a careful selection of codopants to yield a charge-balance codoped system is an effective way to improve the visible-light-responsive photocatalytic activity of nonmetal doped TiO2.
This work is supported by the National Basic Research Program of China (973 program, Grant no. 2007CB613302), National Natural Science Foundation of China under Grant no. 11174180 and 20973102, Natural Science Foundation of Shandong Province under Grant no. ZR2011AM009.
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