Elements doping to expand the light response of SrTiO3
Graphical abstract
Introduction
Hydrogen, as an environmental friendly fuel, is attracting more and more attentions. Since the production of hydrogen through photoinduced water splitting on titanium oxide was discovered [1], semiconductor-based photocatalyst has prompted many investigations, due to its advantage of using the abundant, long lasting, and clean solar energy. In order to construct an efficient photocatalytic water splitting reaction, some photocatalysts, such as oxides, oxynitrides, and sulfides, have been explored [2]. SrTiO3, as one of the promising photocatalytic candidates, has attracted many attentions due to its excellent photocatalytic performance in water splitting [3]. However, SrTiO3 only responds to UV light, which occupies only 4% of the solar light, because of its relatively large band gap (3.2 eV). Many methods, such as dye sensitization [4], [5], quantum dot sensitization [6], [7], and element doping, have been reported to enhance the utilization of solar light for wide band gap semiconductors. The element doping received much more attentions owing to its process simplicity and low cost [8], [9].
For elements doped SrTiO3, the change in electronic band structures can be divided into two kinds: (1) Forming a new mid gap state between the valence band (VB) and conduction band (CB), such as Rh, Cr, Ir, or Ru doped SrTiO3 [10], [11], [12], [13]. (2) Changing the VB or CB through the mixing of energy level between dopant and host elements, such as N, F, C, or S doped SrTiO3[14], [15], [16], [17], [18]. Summarizing the UV–Vis absorption spectra of elements doped SrTiO3, we find that the red shift for most of these samples is slight. The origin of the slight change in absorption edge can be attributed to that the new mid gap state is most close to the VB/CB or the change of VB/CB is small.
Cr-doped SrTiO3 is a promising photocatalyst for solar hydrogen production, which exhibited the highest performance in hydrogen evolution among the elements doped SrTiO3 under visible light irradiation. For Cr3+ doped SrTiO3, the visible light response is attributed to the formation of a new mid gap state, which is about 1.0 eV higher than the valence band top of SrTiO3 formed by O 2p orbits [20]. The experimental band gap for Cr3+-doped SrTiO3 is 2.48 eV [13]. It was well known that the p–d repulsion can reduce the band gap of semiconductors by raising the position of valance band top [19]. The p–d repulsion is proportional to 1/(ɛp–ɛd)(ɛp: the orbital energy of p orbit, ɛd: the orbital energy of d orbit). The p–d repulsion becomes strong when the energy difference between ɛp and ɛd becomes smaller, which significantly contributes to the band gap narrowing. The orbital energy of p orbit of B− ions is close to that of Cr 3d, meaning that the strong p–d repulsion between B2p and C3d if compared to other typical nonmetal elements such as O 2p, S2p, and C2p (Fig. 1). Therefore, it may be a good choice to further broaden the optical absorption region of Cr3+-doped SrTiO3 by enhancing the position of the mid gap state formed by Cr 3d through p–d repulsion between Cr 3d and the p orbits of B. Here, we successfully synthesized Cr,B-codoped-SrTiO3 by one-step hydrothermal method using TiB2 as the Ti precursor and discussed synergistic effects of Cr and B on the band gap narrowing (2.07 eV) of SrTiO3.
Section snippets
Preparation of the photocatalysts
Analytical grade Sr(NO3)2, Cr(NO3)3·9H2O, SrCO3, TiB2, TiO2, and NaOH were used as raw materials without further purification. The Cr, B-codoped-SrTiO3, B-doped-SrTiO3 and Cr-doped SrTiO3 powder were synthesized by hydrothermal method. In the synthesis process of Cr,B-codoped-SrTiO3, firstly, Sr(NO3)2 (0.005 mol), Cr(NO3)3·9H2O (0.00025 mol), and TiB2 (0.00475 mol) were added to Teflon-lined stainless autoclave (60 ml). Then 50 ml water was added to the autoclave. After stirring 5 min, 6 g NaOH was
Crystal structures
Fig. 2 shows the XRD patterns of samples (Cr,B-codoped-SrTiO3 and B-doped-SrTiO3) synthesized under different conditions. For samples synthesized by hydrothermal treatment for 72 h, the patterns (Fig. 2b and c) can be indexed as the cubic SrTiO3 (JCPDS No. 89-4934). But TiB2 impurities were observed in the sample synthesized for 24 h (Fig. 2a), which indicating that TiB2 can directly transfer into SrTiO3 without processing TiO2 as the intermediate phase. The crystal cell parameters for
Conclusions
Cr,B-codoped-SrTiO3 was synthesized by one-step hydrothermal method using TiB2 as the Ti precursor. Based on the results of XPS, FT-IR, and Raman, we proposed that B existed in the forms of both substitution to oxygen and interstitial atoms in the bulk of SrTiO3. Due to strong p–d replusion of Cr 3d with 2p levels of substitutional B, which uplift the position of new mid gap state and induced more delocalized in-gap energy bands, the Cr,B-codoped SrTiO3 had stronger visible light absorption and
Acknowledgements
The authors gratefully acknowledge financial support from the National Basic Research Program of China (973 Program, 2013CB632404), the National Natural Science Foundation of China (Nos. 51102132, 11174129, 51272101, and 51272102).
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