Unraveling of cocatalysts photodeposited selectively on facets of BiVO4 to boost solar water splitting

1Particulate photocatalytic overall water splitting (OWS) based on inorganic semiconductor materials with relative good photostability has been demonstrated as one of the most promising ways of realizing scalable and economically viable solar hydrogen production to address energy- and environment-related issues–. To achieve high solar-to-hydrogen (STH) energy conversion efficiency, it is necessary to increase the quantum efficiency of photocatalytic OWS over a wide range of wavelengths, particularly the use of visible light,. However, extended visible light utilization is generally accompanied by a decreased driving force of the photogenerated carriers to make charge separation extremely difficult. Furthermore, the construction of OWS systems faces serious challenges originating from the sluggish kinetics of water oxidation involving uphill energy barrier and multiple electron transfer. Consequently, visible-light-driven photocatalytic OWS systems are not only limited in number, but also show lower efficiency than those driven by ultraviolet light–. Accordingly, it is highly desirable to precisely design and modify photocatalysts with efficient visible light utilization for promotion of water oxidation.

2N-type monoclinic bismuth vanadate (BiVO4) has emerged as one of the most promising visible-light-responsive photocatalysts and photoanodes for water oxidation since Kudo’s report in 1998–. Owing to its advantages, such as efficient light absorption in the visible light region, good carrier mobility, controllable exposed facets, and non-toxic properties, BiVO4 semiconductor has been widely and successfully employed as the water oxidation photocatalyst for the assembly of Z-scheme OWS systems using solid conductor (i.e., Au, reduced graphene oxide) or redox couple (i.e., Fe3+/2+, [Fe(CN)6]3−/4−) as electron mediator,,–. Specifically, our previous work revealed that the spatial separation of photogenerated electrons and holes can be achieved on the anisotropic facets of BiVO4, based on which reduction and oxidation cocatalysts are selectively deposited on different facets to remarkably promote its water oxidation and the efficiency of OWS under visible light. Although the BiVO4 photocatalyst has been widely investigated for the assembly of artificial Z-scheme OWS systems, the apparent quantum efficiency (AQE) and STH conversion efficiency achieved so far are still considerably below what is expected. This is mainly due to the shortage of effective cocatalyst regulation and the lack of in-depth understanding of the microscopic mechanisms behind it,. Notably, for the assembly of the redox couple-mediated Z-scheme OWS system shown in Fig. 1, the loading of effective cocatalysts is extremely important not only for the acceleration of interfacial electron transfer between the H2-evolving photocatalyst (HEP) and the O2-evolving photocatalyst (OEP), but also for the promotion of surface reaction kinetics of water splitting–. Therefore, it is a long-term task to develop innovative cocatalysts and unravel their structures as well as influence mechanism on water splitting.

3In this study, we address the sluggish water oxidation of BiVO4 via in situ photodeposition of dual innovative cocatalysts, with emphasis on elucidating the local structures of the cocatalysts and the mechanism of promotion of water oxidation. We demonstrate that the nanocomposite of FeOOH and CoOOH (denoted as FeCoOx) in situ formed on the {110} facet of BiVO4 not only lowers Gibbs free energy barrier of water oxidation, but also makes a better promotion on the electron transfer as well as charge separation compared with the commonly used CoOx cocatalyst. Furthermore, the Ir cocatalyst in situ deposited on the {010} facet of BiVO4 was found to exhibit superior reduction ability of [Fe(CN)6]3− ions to our previously reported Au. Based on the facet-selective loading of the innovative dual-cocatalysts, the evolution rate of O2 on the BiVO4 was significantly enhanced, and a particulate Z-scheme OWS system with an AQE of 12.3% at 420 nm and a STH of 0.6%, was finally fabricated using [Fe(CN)6]3−/4− as a redox mediator and ZrO2/TaON or MgTa2O6−xNy/TaON as the HEP. Our results demonstrate the importance and effectiveness of developing suitable cocatalysts for enhancing interfacial charge separation and surface water oxidation kinetics in promoting solar energy conversion.

4The anisotropic BiVO4 with exposed {010} and {110} facets was prepared according to our previous study. The Ir nanoparticles and FeCoOx nanocomposite were in situ photodeposited on the surface of BiVO4 from an aqueous solution containing the precursors K2IrCl6, CoSO4, and redox [Fe(CN)6]3− ions. The as-obtained sample is hereafter denoted as Ir-FeCoOx/BiVO4. As expected from our previous findings on the spatial separation of photogenerated electrons and holes on the anisotropic BiVO4, the Ir nanoparticles, and FeCoOx nanocomposite were clearly observed to be selectively deposited on the {010} and {110} facets of BiVO4, respectively (Fig. 2a, b). For comparison, the in situ photodeposition of single Ir or CoOx particles on BiVO4 was similarly obtained (denoted as Ir/BiVO4 and CoOx/BiVO4), and the sample was characterized by field-emission scanning electron microscopy (FESEM) to further confirm the facet-selective deposition (Supplementary Fig. 1). It should be noted that the morphology of the cocatalysts located on the {110} facet of Ir-FeCoOx/BiVO4 (Fig. 2b) is clearly different from that of the CoOx/BiVO4 sample (Supplementary Fig. 1b), demonstrating the possible interaction between Fe and Co-based compounds. And the change in the long wavelength range of UV-Vis diffuse reflectance spectra (DRS) can confirm the successful deposition of the dual-cocatalysts (Supplementary Fig. 2). The deposited Ir species were verified to exist as metallic Ir nanoparticles by means of X-ray absorption near edge structure (XANES) spectroscopy (Supplementary Fig. 3) and high-resolution transmission electron microscopy image (Supplementary Fig. 4).

5To unravel the formation of the FeCoOx nanocomposite on the {110} facets of BiVO4, the existing state and dispersion of both Fe and Co elements on FeCoOx/BiVO4 (free of Ir nanoparticles to rule out its possible interference during characterization) were first analyzed. According to the elemental mapping results shown in Supplementary Fig. 5, both Fe and Co species are similarly located and dispersed, accompanied by the existence of O, which further demonstrates that Co and Fe combine together in the form of oxidation state during the photo-oxidation process. The deposition of Fe should result from redox ions in the reaction solution. The coexistence of both Fe and Co can be further revealed by electron energy loss spectroscopy analysis (Supplementary Fig. 6). And their oxidation states can be confirmed to be Fe3+ and Co3+ by the Fe and Co K-edge XANES measurements through comparing with the reference materials (Fig. 2c, d, respectively).

6Second, the radial distance space spectra χ(R) of Fe and Co in FeCoOx/BiVO4 and their corresponding references were analyzed, which provides more convincing support for the formation of nanocomposite. As shown in Fig. 2e and Supplementary Fig. 7, the peaks located at approximately 2.72 Å assigned to the Fe–O–Co bond are consistently observed in both the Fe and Co K-edge of the FeCoOx/BiVO4 sample, but no scattering path signals attributing to the Co–Co bond (2.41 Å) from Co foil, Fe–Fe bond (2.47 Å) from Fe foil, Co–O–Co bond (2.69 Å) from CoOOH, or Fe–O–Fe bond (2.86 Å) from FeOOH can be observed. This clearly reveals that the formation of nanocomposite is a homogeneous phase of bimetallic hydroxide, instead of single-phase Fe or Co hydroxides. It should be pointed out that the possible nanocomposite of Fe2O3 and Co2O3 can be ruled out by comparing the fingerprint feature pattern of normalized XANES μ(E) spectra (Fig. 2c, d and Supplementary Fig. 8a, b) and the first derivative of the normalized XANES μ(E) spectra (Supplementary Fig. 8c, d). In particular, as shown in Supplementary Fig. 8c, d, the peak positions of FeCoOx/BiVO4 are closer to the FeOOH and CoOOH references. Based on these results, the phase species of the FeCoOx on the surface of BiVO4 sample can be deduced to be more similar to FeOOH/CoOOH with respect to Fe2O3/Co2O3. In addition, compared with the corresponding single-phase hydroxides FeOOH and CoOOH, Fe/BiVO4 sample exhibits much shorter Fe–O bond and longer Co–O bond, and the length of Co–O–Fe bond is between Co–O–Co and Fe–O–Fe (Fig. 2e). This demonstrates the existence of electron transfer and a strong interaction between Fe and Co in the FeCoOx/BiVO4 sample, providing further proof about the formation of the nanocomposite.

7Third, the formation of the nanocomposite can be further verified by the results of quantitative χ(R) space spectra fitting and wavelet transform of χ(k). As seen in Supplementary Table 1, Fe–O–Co bond with similar coordination numbers (Fe–O–Co: 2 at ca. 2.745 Å in Fe K-edge; Co–O–Fe: 2 at ca. 2.761 Å in Co K-edge) can be confirmed. The good fitting results of χ(R) and χ(k) space spectra (Fig. 2f, g and Supplementary Fig. 9) with reasonable R-factors and the obtained fitting parameters (Supplementary Table 1) provide a quantitative illustration of the existence of Fe–O–Co bond originating from the nanocomposite structure. As similarly revealed in Fig. 2h, i, the Fe–O–Co bond located at [χ(k), χ(R)] of [4.2, 2.74] or Co–O–Fe bond ([6.4, 2.76]) as well as the Fe–O bond ([4.8, 1.64]) or Co–O bond ([4.2, 1.88]) with two scattering path signal can be observed for both Fe and Co K-edge wavelet transform of χ(k) spectra of FeCoOx/BiVO4, but the characteristic scattering path signal of Fe–Fe bond ([8.4, 2.52]), Co–Co bond ([7.8, 2.42]), Fe–O–Fe bond ([5.6 2.82]) or Co–O–Co bond ([6.8, 2.78]) is not observed as similarly as the reference sample (Supplementary Fig. 10).

8As shown in Fig. 1, the water oxidation process of OEP is strongly dependent on both the reduction and oxidation cocatalysts. Therefore, understanding the effect of deposited Ir and FeCoOx cocatalysts is highly desirable. As depicted in Fig. 3a, the ability of the deposited metallic Ir to reduce [Fe(CN)6]3− ions was evaluated and found to exhibit a much higher cathode current than that of our previously reported Au nanoparticles on BiVO4, indicating its superior performance in activating and reducing the [Fe(CN)6]3− ions. In addition, the deposition of Ir or Au cocatalyst on the surface of BiVO4 can significantly decrease the charge-transfer resistance (Rct) across the semiconductor/electrolyte interface (Fig. 3b), further revealing the effectiveness of the deposited cocatalysts in accelerating the electron transfer from BiVO4 to the [Fe(CN)6]3− ions (values of Rs and Rct listed in Supplementary Table 2). Meanwhile, the promotion effect of Ir is better than that of Au.

9To determine the effect of the FeCoOx nanocomposite, the efficiencies of charge separation and injection (denoted as ηsep and ηinj, respectively) on the FeCoOx/BiVO4 photoanode (CoOx/BiVO4 and BiVO4 as references) were evaluated by referring to a previous photoelectrochemical analysis. Figure 3c and Supplementary Fig. 11a show that the current of the BiVO4 photoanode can be remarkably promoted after the deposition of FeCoOx and CoOx in both cases, with and without the use of a hole scavenger, among which FeCoOx exhibits a much better promotion effect than CoOx. On this basis, both ηsep and ηinj on the FeCoOx/BiVO4 photoanode were calculated to be higher than that of the CoOx/BiVO4 photoanode (Supplementary Fig. 11c, d), demonstrating the better promotion effect of the FeCoOx nanocomposite on both the separation of photogenerated carriers and the injection of holes into the reaction solution (i.e., surface reaction) with respect to CoOx. The excellent promotion of FeCoOx on the surface reaction can be further supported by the electrochemical impedance spectroscopy (EIS) results given in Fig. 3d and Supplementary Table 3, based on which the Rct resistance on the FeCoOx/BiVO4 electrode is the smallest among the three electrodes investigated. On the other hand, the superior promotion effect of FeCoOx on the charge separation can also be evidenced by its larger open-circuit potential (OCP) on the FeCoOx/BiVO4 compared with CoOx/BiVO4 (Fig. 3e). Based on the previous result that a larger difference of OCPs under dark and illumination conditions corresponds to more intense band bending, therefore the FeCoOx/BiVO4 sample can be deduced to own a more intense band bending than the CoOx/BiVO4 sample, leading to a significantly improved ηsep and the more intense band bending should result from the p-n heterojunction between FeCoOx and BiVO4.

10Encouraged by the understanding of the functionalities of both reduction and oxidation cocatalysts (i.e., Ir and FeCoOx), the synergistic effect of dual-cocatalysts on the charge separation was examined using the surface photovoltage (SPV) spectrum. As shown in Fig. 3f, the sample with both Ir and FeCoOx deposited exhibits a greater SPV amplitude with respect to the sample with single Ir or FeCoOx loaded. It should be mentioned that a much better promotion effect is also observed for the sample with facet-selective deposition of Ir and FeCoOx compared to that with facet-selective deposition of Au and CoOx. These results reveal the importance of both facet-selective deposition of dual-cocatalysts and the development of innovative cocatalysts for maximizing the promotion effect.

11Density functional theory (DFT) calculations were performed to further elucidate the microscopic mechanism of the promotion effect of the FeCoOx cocatalyst on the O2-evolving reaction (OER) from the viewpoint of both surface catalysis and interfacial charge transfer. As shown in Fig. 4a–c, the CoOx–FeOx–CoOx–FeOx and CoOx–CoOx–CoOx–CoOx clusters were simply extracted and placed on the {110} facets of BiVO4 to simulate the FeCoOx/BiVO4 and CoOx/BiVO4 interfaces, respectively, which origin from the structure of EXAFS measurement. And the schematic of the whole OER mechanism on the FeCoOx/BiVO4 and CoOx/BiVO4 is given in Supplementary Fig. 12 and illustrated in detail in supporting information. Fig. 4d and e presents the Gibbs free energy change diagram of the four elementary steps of OER on the surface of FeCoOx/BiVO4 and CoOx/BiVO4, during which the Co and Fe sites on FeCoOx/BiVO4 were mainly considered as the active sites, respectively. It was demonstrated that the rate-determining step of FeCoOx/BiVO4 (Co or Fe site) and CoOx/BiVO4 is the adsorption of one OH− to form OOH∗ from O∗. The largest decrease of the Gibbs free energy barrier was observed for FeCoOx/BiVO4 (Co site), whereas the OER performance of FeCoOx/BiVO4 (Fe site) is much weaker than that of the corresponding Co site, suggesting that the Co site acts as the main OER site.

12Next, we plotted the calculated densities of states (DOS) of the BiVO4 {110} surface, CoOx/BiVO4 {110} interface, and FeCoOx/BiVO4 {110} interface (Fig. 4f, g, h and Supplementary Fig. 13). Both CoOx and FeCoOx are set to be located at the {110} facets of BiVO4. For the bare BiVO4 {110} surface, there is a direct bandgap about 2.1 eV between the valence band and conduction band (Fig. 4f). However, when the CoOx–FeOx–CoOx–FeOx cluster is settled on the {110} surface of BiVO4, a mixed band mainly composed of Co 3d, Fe 3d, and O 2p states emerges between the valence band and conduction band (Fig. 4g). It has been demonstrated that the localization of photoexcited holes, as well as subsequent charge separation can be promoted through the formation of mixed bands. In addition, the DOS of the CoOx/BiVO4 {110} interface (Fig. 4h) has no similar result as that of the FeCoOx/BiVO4 {110} interface (Fig. 4g, bandgap = 2.0 eV), implying that the loading of FeCoOx on BiVO4 should have better charge separation. In order to microscopically understand the better electron transfer on the FeCoOx with respect to the CoOx, their bader charges were calculated and compared. As given in Supplementary Table 4, the changing trend of bader charge on the Co active site after introduction of Fe (increase from 1.2 a.u. in CoOx/BiVO4 to 1.3 a.u. in FeCoOx/BiVO4) is in line with the changing one of experimental valence state (Supplementary Fig. 14). Compared to the CoOx/BiVO4, the higher bader charge on the Co active site in FeCoOx/BiVO4 indicates its stronger oxidation capacity as well as more beneficial electron transfer. In addition, as shown in Supplementary Fig. 15, the d-band center (Ed) value of Co active sites in FeCoOx/BiVO4 was calculated as −1.63 eV, which is sharply increased with respect to the CoOx/BiVO4 (−2.56 eV). This demonstrates that the electronic structure of Co active sites can be well modulated and optimized in the FeCoOx/BiVO4 due to the introduction of Fe atoms to get much stronger adsorption properties to the OER intermediates according to the d-band center theory,. According to previous experimental and theoretical demonstration, the Fe site is relatively inactive during the OER process,. So we deduce that the role of Fe is to assist in modifying the geometric and electronic structure of Co in the OER together with our results that very limited contributions of Fe 3d states are observed for the mixed band (Fig. 4g). These conclusions from DFT calculation well match with the aforementioned experimental results.

13The modified BiVO4 was employed as an OEP for the assembly of efficient Z-scheme OWS systems together with ZrO2/TaON or MgTa2O6−xNy/TaON as a HEP under visible light irradiation. The HEPs were prepared and modified with cocatalysts according to previously reported procedures,,, and the diffraction structure and morphology features were coarsely revealed by their powder X-ray diffraction patterns and FESEM images (Supplementary Figs. 16, 17). The contents of deposited Ir and Co on BiVO4 were optimized to be 0.8 and 0.2 wt%, respectively, via the photocatalytic O2 evolution reaction (Supplementary Figs. 18, 19). As seen in Fig. 5a, stable evolution curves of H2 and O2 with the stoichiometric molar ratio of 2:1 can be observed at the experimental region using the optimized photocatalysts, indicating the successful achievement of the OWS process. Moreover, regardless of using ZrO2/TaON or MgTa2O6−xNy/TaON as the HEP, similar OWS activities with the initial rates of H2 and O2 evolution (ca. 160 and 80 μmol/h, respectively) were separately observed, implying that the O2 evolution on BiVO4 is the rate-determining step, as similarly observed in our previous study. It should be pointed out that when the Ir-CoOx(Imp.)/BiVO4 with Ir and Co randomly impregnated is employed as the OEP, the OWS will not be achieved owing to the significantly decreased O2-evolving activity (Supplementary Fig. 20). This indicates the importance of facet-selective deposition of dual-cocatalysts in promoting the O2-evolving activity and fabricating a successful OWS system. The multiple cycles of time-course curves shown in Supplementary Figs. 21 and 22 demonstrate the good photostability of the system constructed in this study. The AQE value of OWS as a function of absorption wavelength was found to be in good accordance with the UV-Vis DRS of the OEP and HEP, indicating that the Z-scheme OWS system is driven by visible light excitation (Fig. 5b and Supplementary Fig. 23). The optimal AQE value of OWS at 420 ± 10 nm is 12.3%, and the AQE value at the 500 ± 10 nm is about 3%, demonstrating the wide visible light utilization. According to the activity measurements under the irradiation of AM 1.5 G (Fig. 5c), the STH energy conversion efficiency was calculated to be 0.6%. To the best of our knowledge, both the AQE and STH values should be the highest among the suspending particulate photocatalytic OWS systems using inorganic semiconductor materials with visible light utilization, regardless of one-step or two-step (i.e., Z-scheme) systems.

14Here, we show a highly efficient Z-scheme OWS system with benchmarked AQE and STH value over particulate inorganic semiconductor photocatalysts with visible light utilization. The success is mainly ascribed to the in situ facet-selective photodeposition of innovative dual-cocatalysts (Ir nanoparticles and FeCoOx nanocomposite), based on which the sluggish water oxidation on BiVO4 can be largely overcome. Besides the finding and structural unraveling of efficient cocatalysts, the microscopic work mechanism of both reduction and oxidation cocatalysts on the interfacial charge transfer and surface catalysis has been well elucidated respectively. These results should be encouraging and enlightening to the design and assembly of OWS systems for more efficient solar-to-chemical energy conversion.

15ZrO2-modified TaON (Zr/Ta = 0.1) sample and MgTa2O6−xNy/TaON (Mg/Ta = 0.15) composite were used as the HEPs. The ZrO2-modified sample was synthesized by nitridation of the ZrO2/Ta2O5 composite and the MgTa2O6−xNy/TaON was prepared by nitridation of the MgTa2O6/Ta2O5 composite under an ammonia flow (20 mL min–1) at 1123 K for 15 h by referring to the previous works,. BiVO4 was chosen as the OEP, which was similarly synthesized according to our previous hydrothermal process. Typically, 10 mmol NH4VO3 and 10 mmol Bi(NO3)3·5H2O were dissolved in 2.0 M nitric acid solution, whose pH value was then adjusted to be about 0.5 with ammonia solution (25–28 wt%). The mixed solution was strongly stirred until the observation of a light yellow precipitate that was further aged for about 2 h and then transferred to a Teflon-lined stainless steel autoclave for 10 h hydrothermal treatment at 473 K.

16The deposition of Ir or CoOx on the surface of BiVO4 was carried out by the photodeposition method. Typically, 0.2 g BiVO4 powder was dispersed in deionized water containing a calculated amount of K2IrCl6 (2.0 wt%) or CoSO4 (2.0 wt%), and hole (CH3OH) or electron (NaIO3) scavenger, separately. The well-mixed solution was then irradiated by 300 W xenon lamp free of any cut-off filter for 2 h. The as-obtained powders after filtration and washing are correspondingly denoted as Ir/BiVO4 and CoOx/BiVO4, which were used for further characterizations and tests.

17Both of the samples were similarly prepared by the in situ photodeposition. Meanwhile, 25 mM phosphate buffer solution (PBS, pH = 6, 50 mL) containing a calculated amount of CoSO4 and [Fe(CN)6]3− ions was prepared for the synthesis of FeCoOx/BiVO4, while 25 mM phosphate buffer solution (PBS, pH = 6, 50 mL) containing a calculated amount of K2IrCl6, CoSO4 and [Fe(CN)6]3− ions was prepared for synthesis of Ir-FeCoOx/BiVO4.

18The deposition of nanoparticulate rhodium-chromium mixed oxides (denoted as RhyCr2−yO3) as a cocatalyst was carried out by the photodeposition method. 0.2 g ZrO2-modified TaON or MgTa2O6−xNy/TaON was dispersed in 20 v% 150 mL methanol solution. A certain amount of Na3RhCl6 and K2CrO4 (1.0 wt% Rh and 1.5 wt% Cr vs. photocatalyst for ZrO2/TaON and 2.0 wt% Rh and 3.75 wt% Cr vs. photocatalyst for MgTa2O6-xNy/TaON) were added as the precursors. The deposition was carried out under the full-spectral irradiation of 300 W xenon lamp for 6 h. Whereafter, the irradiated solution was centrifuged and washed with distilled water, and then dried at 353 K for overnight to get powder for use.

19The BiVO4 photoanode was prepared according to the previous work. First of all, Bi(NO3)3·5H2O, NH4VO3, and polyvinyl alcohol were dissolved in 60% HNO3 to prepare the precursor solution. Then the precursor solution was spin-coated on the FTO followed by heat treatment at 623 K for 2 h in air to form the BiVO4 seed layer. Second, the treated FTO was immersed in 2.0 M HNO3 aqueous solution containing Bi(NO3)3·5H2O and NH4VO3, whose pH was adjusted to be 0.9 by adding NH3·H2O drop by drop. The formed BiVO4 precursor film solution was transferred to a Teflon-lined autoclave with the as-prepared substrate for hydrothermal treatment at 473 K for 12 h. The BiVO4 photoanode film was finally calcined at 773 K for 4 h.

20As for the selective deposition of Ir and FeCoOx cocatalysts on the BiVO4 photoanode, similar in situ photodeposition method as the powder was adopted. Specifically, the photoanode was immersed in 25 mM phosphate buffer solution (PBS, pH = 6, 50 mL) containing the K2IrCl6 or/and CoSO4 (K2IrCl6: 40 μL; CoSO4: 10 μL, the concentration of solution: 1 mg/mL) and K3[Fe(CN)6] (0.5 mM) and irradiated for 3 h. Similarly, CoOx was photodeposited on the surface of BiVO4 to prepare the CoOx/BiVO4 photoanode.

21The AQE was measured using a Pyrex top-irradiation-type reaction vessel and a 300 W xenon lamp fitted with band-pass filters (ZBPA420, Asahi Spectra Co., FWHM: 10 nm). The number of photons reaching the solution was measured using a calibrated Si photodiode (LS-100, EKO Instruments Co., LTD.), and the AQE (ϕ) was calculated using the following Eq. (1):where A, R, and I are coefficients, A represents a coefficient (4 for H2 evolution; 8 for O2 evolution) and R represents the evolution rate of H2 or O2. As measured and calculated, the total number of incident photons at the wavelength of 420, 460, 480, 500, and 560 nm are 8.4 × 1020, 6.5 × 1020, 7.1 × 1020, 4.8 × 1020, and 6.9 × 1020 photons h−1, respectively. The evolution rates of H2 on the system containing RhyCr2–yO3-ZrO2/TaON and Ir-FeCoOx/BiVO4 photocatalysts under the wavelength of 420, 460, 480, 500, and 560 nm were tested to be 41.6, 23.0, 17.5, 7.4, and 0 μmol h−1, respectively. The evolution rates of H2 on the system containing RhyCr2–yO3-MgTa2O6–xNy/TaON and Ir-FeCoOx/BiVO4 photocatalysts under the wavelength of 420, 460, 480, and 560 nm were tested to be 42.4, 19.0, 9.0, and 0 μmol h−1, respectively.

22The STH energy conversion efficiency (η) was calculated according to the following Eq. (2):where RH, ΔG°, P, and S denote the rate of H2 evolution (mol s−1) in photocatalytic water splitting, standard Gibbs energy of water (237.13 × 103 J mol−1), intensity of simulated sunlight (0.1 W cm−2), and irradiation area (4.0 cm2), respectively. The light source was an AM 1.5 G solar simulator (XES-40S2-CE, San-Ei Electric), and a top-irradiation reaction vessel was used. The initial rates of H2 and O2 evolution are about 36 and 18 μmol/h, separately.

23As for the tests of linear sweep voltammetry (LSV) and EIS, a platinum plate was used as a counter electrode and the saturated calomel electrode (SCE) as the reference electrode. The phosphate buffer solution (pH = 6, 0.1 M) with 5 mM K3[Fe(CN)6] aqueous solution and phosphate buffer solution (pH = 6, 0.1 M) were used as the electrolyte. The potential of the working electrode was controlled by a potentiostat (CHI 660E) for the LSV test and potentiostat (Solartron analytic AMETEK) for the EIS test. Before the measurement, the solution was purged with argon gas. The Nyquist plots calculated from EIS were performed from 100,000 to 0.1 Hz. Data were fitted using Zview software.

24Current–voltage (J–V) curves under irradiation and darkness were recorded on an electrochemical workstation (CHI 660E). The OCP of photoanode were recorded under illumination and darkness using electrochemical workstation (Solartron analytic AMETEK). A 300 W xenon lamp was used as the light source and the irradiation intensity was high enough to produce a flat band condition of the photoanodes. The electrolyte for J–V curves and OCP was 1 M KBi (pH = 9). 0.2 M Na2SO3 was added to the electrolyte as a hole scavenger if necessary.