TiO2 Photocatalytic Materials 2014View this Special Issue
Research Article | Open Access
D. Regonini, A. K. Alves, F. A. Berutti, F. Clemens, "Effect of Aging Time and Film Thickness on the Photoelectrochemical Properties of TiO2 Sol-Gel Photoanodes", International Journal of Photoenergy, vol. 2014, Article ID 472539, 10 pages, 2014. https://doi.org/10.1155/2014/472539
Effect of Aging Time and Film Thickness on the Photoelectrochemical Properties of TiO2 Sol-Gel Photoanodes
This work has focused on the investigation of a non-aqueous based sol-gel process to produce TiO2 based photoelectrodes for solar water splitting. In particular, the effect of the aging time of the sol and TiO2 film thickness on the photoelectrochemical properties of the photoanodes has been investigated. In order to achieve optimal performances (i.e., photocurrent density up to 570 µA/cm2 and IPCE of 26% at 300 nm), the sol needs to be aged for 3 to 6 h, before being dip-coated to produce the photoanodes. The importance of the aging time can also be appreciated from the optical properties of the TiO2 films; the absorbance threshold of the sol-gel aged for 3–6 h is slightly shifted towards longer wavelenghts in comparison to 0 h aging. Aging is necessary to build up a well-interconnected sol-gel network which finally leads to a photoelectrode with optimized light absorption and electron collection properties. This is also confirmed by the higher IPCE signal of aged photoelectrodes, especially below 340 nm. Among thicknesses considered, there is no apparent significant difference in the photoresponse (photocurrent density and IPCE) of the TiO2 sol-gel films.
The photoelectrochemical solar water splitting promoted by TiO2 has been first reported in 1972 by Fujishima and Honda  and extensively investigated over the last 40 years [2–4]. TiO2 is recognized as an environmentally friendly, economically accessible, photostable, and biologically inert photocatalyst [3, 4], although its large band-gap (3.0 to 3.2 eV) allows only the absorption of a small portion of the photons available from the solar spectrum . To date, various attempts to modify the band-gap of TiO2 by introducing suitable dopants within its lattice [3, 5, 6] have failed to deliver a material with an enhanced photoactivity. Such doping increases visible light absorption but increases also the probability of charge carriers recombination (i.e., new defects formed within the doped structure act as traps  for e− and h+). More promising results are instead obtained by inducing oxygen nonstoichiometry in TiO2 via thermal treatment in a reducing atmosphere; in this case, the conductivity and to some extent the optical properties of the oxide are improved and the photoactivity is also enhanced, with the oxide remaining free from defects typically introduced whenever attempting to dope with foreign species [8–10]. It is also possible to optimize the electron transport properties of TiO2 by selecting the most appropriate morphology for a given application [11, 12]. Concerning solar driven water splitting, Hartmann et al.  suggested that mesoporous TiO2 sol-gel represents the ideal morphology to ensure good electronic interconnectivity and therefore a much more efficient collection of the photogenerated e− than in TiO2 nanoparticles. It should also be considered that, unlike mesoporous sol-gel films, TiO2 nanoparticles are too small to support an inbuilt electrical field , meaning there is no space-charged layer  to assist the water splitting process. Under such conditions, the surface intermediates (Tis–O• radicals, Tis–O–O–Tis peroxo species) involved in the photooxidation of water act as scavengers of in the conduction band of TiO2 nanoparticles; hence, the photocurrent is drastically reduced . Concerning the electron transport within a network of nanoparticles, it has been shown that it is aided by self-doping, occurring under illumination and enhancing the conductivity of the nanoparticles . Therefore, Augustyński et al.  argue that the superior water splitting performances of sol-gel should not be ascribed to the good electronic interconnectivity but rather to the absence of a space-charged layer in the case of nanoparticles. Based on our recent studies on TiO2 sol-gel, electrospun fibres, and nanoparticles , we suggest that both the absence of an inbuilt electric field in nanoparticles and the better interconnectivity (due to the Ti–O–Ti network) within the sol-gel are contributing to the better performances of sol-gel photoanodes. Among the possible sol-gel routes to obtain TiO2 from a Ti alkoxide precursor, a better control over the structure of the sol and nanocrystallinity in the spin- (or dip-) coated films can be established, for example, by replacing water with an organic acid and an alcohol and also by using nonionic surfactants such as Triton X-100  or Tween 20 [19, 20]. A similar approach is adopted and implemented within this work. As discussed later in Section 3, an added value and novelty of this work are the development of a system where the thickness of the film is not influenced by the aging time and the viscosity of the sol but only by the number of dip-coated layers. This allows a direct comparison between photoanodes aged for different times (as they have the same thickness). Furthermore, only few studies on the effect of film thickness on the photochemistry of the sol-gel are available to date. Yasumori et al. [21, 22] showed a nearly linear correlation between the thickness (up to 400 nm) of sol-gel photocatalyst and the amount of H2 produced. Similarly, it has been recently reported that at a given wavelength (365 nm) the IPCE also increases (almost) linearly with the thickness of TiO2 sol-gel photoanode (maximum thickness investigated was 1.3 µm) . Nevertheless, further investigations are required to understand to which extent (in terms of thickness, porosity, aging, and crystallinity) a carefully chosen sol-gel synthetic route can lead to TiO2 photoanodes with optimal electron transport properties. The aims of this work are(i)to investigate the effect of film thickness on the photocurrent density and the IPCE response of TiO2 sol-gel films,(ii)to optimize the photoelectrochemical properties of our sol-gel processing method [17, 24] by investigating the influence of aging time on the performances of TiO2 photoanodes.
As a result of this study, a robust correlation between the processing method (aging and thickness), the microstructure, and crystallinity of the sol-gel photoelectrodes and their photoelectrochemical properties is established by the use of different characterization techniques (Section 2.2) and presented in detail in Section 3.
2. Materials and Methods
2.1. Fabrication of TiO2 Sol-Gel Photoelectrodes
The sol-gel photoelectrodes were prepared according to the following procedure: 2.84 mL (9.6 mmol) of titanium tetraisopropoxide [Ti()4, Merck] was mixed in 2.84 mL (50 mmol) of acetic acid (Sigma-Aldrich) and kept under magnetic stirring for 10 minutes. The sol was then additionally kept in the dark for 15 minutes, before adding 0.8 mL (7.8 mmol) of acetylacetone (Acac, Sigma-Aldrich), 0.1 mL of Triton-x-100 (Sigma-Aldrich) , and a solution of 0.32 g (5wt.%) of PVB (Mowital B 30H, Omya) in 8 ml of dry EtOH. The sol was finally aged in the dark for different times, 0 h (i.e., no aging), 3 h, or 6 h, before being dip-coated (Compact DipMaster 50 Dip Coater, Chemat Scientific Inc.) on FTO glass substrates (Pilkington NSG TEC 8A, Xop Física) previously cleaned by sonication in isopropanol for 10 minutes, rinsed with distilled water and EtOH, and dried under an air flow. Dip coating parameters to obtain a 1-layer-thick green sol-gel photoelectrode were (a) substrate dipping/withdrawal speed of 50 mm/min and (b) dipping time of 30 s. In the case of multilayered films, the entire procedure described above was repeated to obtain 2 or 3 layers of green sol-gel photoanodes. All the photoelectrodes were left to dry for 24 h before being calcinated at 500°C in air (heating rate of 1.6°C/min, dwelling time: 2 h). In the case of multilayers photoanodes, the time interval between each dip coating was also kept for 24 h and the calcination done only once, when all the desired layers had been dip-coated on the FTO glass.
Measurements were performed using a Rheolab MC 120 (Anton Paar GmbH, Germany) rheometer. The viscosity (Pa·s) and the shear stress (Pa) of the sols were measured as a function of the shear rate (from 100 to 1000 s−1) at different time intervals (0, 3, and 6 h) to monitor changes of flow behavior occurring during the aging process.
2.2.2. Morphology, Microstructure, and Crystallinity
The morphology, microstructure, and thickness of the photoelectrodes were analyzed by scanning electron microscopy (SEM, either TS5136 MM-Tescan or a Field Emission Nova NanoSEM 230-Nova FEI) and the crystal phases determined by grazing angle X-ray diffraction (GAXRD) analysis, performed on TiO2 thin film photoelectrodes (grazing angle ω = 1°, using a Panalytical, X’Pert Pro instrument (Cu-Kα1, λ = 1.5406 Å). The porosity of the thin film photoelectrodes was estimated from SEM images using the freeware ImageJ.
2.2.3. Specific Surface Area of Photoelectrodes
The surface area of the thin films was determined by dye adsorption/desorption measurements, using a commercial N719 dye (Sigma-Aldrich), assuming a dye monolayer coverage of the TiO2 and a dye molecular footprint of 180 Å2 . Photoelectrodes were first left to dry at 80°C overnight and then soaked for 3 h in a 0.2 mM solution of N719 in tert-butanol/acetonitrile (1 : 1 in volume). Samples were removed from the above solution, rinsed with EtOH and acetonitrile, and left to dry at 60°C for 1 h. The N719 dye adsorbed onto the TiO2 films was desorbed by soaking (1 h) the films in a known volume of 0.01 M KOH in water. From UV-Vis (UV 3600 Spectrophotometer, Shimadzu) absorbance analysis and knowing the porosity of the films, it was then possible to calculate the specific surface area of the TiO2 photoelectrodes aged for different times.
2.2.4. Photoelectrochemical and Optical Characterizations
The photocurrent measurements were performed using a 3-electrode system (working electrode: TiO2 photoanode; counter electrode: platinum plate, XM120, Radiometer Analytical; reference electrode: Ag/AgCl/3M-KCl, XR300, Radiometer Analytical) inserted into a cappuccino cell  filled with 10 mL of 1 M KOH solution (pH = 13.8) and connected to a potentiostat (Voltalab80 PGZ 402, Radiometer Analytical). The cappuccino cell was irradiated by a Xe lamp (solar simulator, Oriel Lamp by LOT-Oriel AG), at an intensity correspondent to 1.5AM (1 sun, 1,000 W/m2), and the resulting photocurrent density () measured as a function of a potential sweep from −900 to +600 mV (vs the Ag/AgCl ref. electrode), at a scan rate of 20 mV/sec.
Additionally, incident photon to current efficiency (IPCE) action spectra were also performed adopting a 2-electrode system, using a Xe lamp (by LOT-Oriel AG) as light source and a monochromator (Omni-λ 300, LOT-Oriel AG). A typical experiment consisted in illuminating a TiO2 photoanode (immersed in 1 M KOH) with light of wavelength () ranging from 600 nm to 300 nm (at 1 nm step). A Keithley 2450 source meter was used to provide a bias (0.00 V or 0.23 V) between the photoanode and a Pt counter electrode and to measure the photocurrent as a function of the wavelength, . The power of the irradiating source, , was recorded with a ThorLabs PM100USB power meter and the values calculated as For the photocurrent and IPCE measurements, a minimum of 5 specimens for each different type of photoelectrodes were tested and results are given together with their relative standard deviations. UV-Visible analysis (UV 3600 Spectrophotometer, Shimadzu) was performed to determine the transmittance and diffuse reflectance of the photoelectrodes (, ) and the FTO substrate (, ), ranging from 650 to 250 nm (sampling interval 1 nm). The absorbance, that is, optical density, opt. dens. , is then given by where is the absorption coefficient and is the thickness of the film. The indirect band-gap of the photoelectrodes was extrapolated from a plot of versus , Tauc plot .
3. Results and Discussion
As expected, the rheology measurements performed on the TiO2 sol-gel system, Figure 1, are showing an increase in shear stress and viscosity occuring during the aging process of the sol, which was monitored at 0, 3, and 6 h. The increase in shear stress and viscosity is more pronounced between 0 and 3 h than between 3 and 6 h aging, suggesting that the most significant physical and chemical changes within the TiO2 sol are occuring within the first 3 h of the aging process. This is in good agreement with previous reports on the preparation of sols using metal alkoxide based precursors . The results of the SEM analysis, summarized in Table 1, reveal that aging time has no effect on the thickness of the photoanode, which remains as 0.6 ± 0.1 µm for 1 layer TiO2 dip-coated after 0, 3, or 6 h aging. This was expected, considering there is no real gelling effect (i.e., shear thinning effect) in the TiO2 sol; from Figure 1, it is clear that the sol behaves almost as a newtonian fluid . The viscosity is almost independent of the shear rate and the shear stress shows linear behavior versus the shear rate. It is therefore assumed that the film thickness is mainly influenced by the solid TiO2 content (kept constant in this study) inside the sol-gel system. The TiO2 sol system does not show a real gelling effect for the following reasons.(i)The water required for hydrolysis of Ti()4 is initally absent and it is only slowly released in the sol via reaction between the alcohol (EtOH) and the acetic acid. The Ti–O–Ti network can also be created by alcoholysis of the Ti alkoxide precursor, which again is slower than hydrolysis and easier to control .(ii)It has been previously shown that chelating agent such as Acac, used in this study, despite causing the Ti alkoxide precoursor to be more prone to hydrolysis/alcoholysis, is in fact slowing down (or preventing) gelation because it offers alternative paths to the polymerization reaction .(iii)An excess of acetic acid is used in our system and this is also known to retard the gelation of Ti alkoxides by promoting the formation of stabilized dimeric complexes (the coordination of Ti also changes from 4 to 6 upon addition of acetic acid) .
Our study shows that it is possible to prepare films with thickness independent of aging time; as previously mentioned, this allows evaluating the impact of aging time on the ability of the photoelectrodes to sustain electron transport.
The results of the GAXRD analysis of the photoelectrodes (after calcination at 500°C) are summarized in Figure 2. Anatase is the dominant phase (>95%) in all the photoelectrodes, although a small amount of rutile is also present. An additional and important fact emerging from Figure 2 is the impact of the sol-gel aging process on the crystallinity of the film. By comparing the XRD spectra of 1-layer-thick photoelectrodes (i.e., same thickness) without aging (0 h) and aged for 3 or 6 h, the anatase peaks appear to be more pronounced in the case of aged films. In other terms, when the aging step is not performed (0 h), the XRD signals of the FTO substrates dominate over the TiO2 peaks. This is best appreciated when comparing the anatase peak at 25.4° and the FTO peak at 26.6°. Crystallinity is indeed a very important requirement towards the design of effective photocatalysts for the formation of H2 via solar water splitting . Additionally, the analysis of the crystalline particles size by applying the Scherrer equation  to the anatase peak (101) at 2θ = 25.3 − 25.4°, Figure 2, reveals that they are sufficiently big to allow efficient electron transport. The size of the crystalline domains for all the different photoelectrodes is approximately 30 nm and sufficiently larger domains (at least >15 nm) are generally suggested to be required to facilitate transport of electrons during the water splitting process .
Despite having no significant effect on the thickness of TiO2 films, aging time appears to influence the optical properties of the photoanodes, as shown in Figure 3; the absorbance threshold of the sol-gel aged for 3 and 6 h is slightly shifted towards higher wavelenghts in comparison to 0 h aging. Furthermore, for a given wavelenght, by comparing the 1-layer photoelectrodes aged for difference times, it is evident that the absorbance intensity is higher in 6 h aged films. This is best appreciated in the region 300–320 nm, Figure 3, and must be a consequence of the chemical and physical changes  occuring within the sol. As previously discussed, the sizes of crystalline domains are very similar (approximately 30 nm) in all the photoelectrodes and cannot explain the differences in their optical properties. However, XRD analysis, Figure 2, has shown that aged photoelectrodes have a higher degree of crystallinity than nonaged films and, as a result, may interact differently with the incident light. We therefore tentatively assign the shift of the absorbance threshold to differences in the light scattering phenomena occuring within films aged for different times.
The optical properties are also in good agreement with the photocurrent measurements, reported in Figures 4(a)–4(c) for different aging times, 0, 3, and 6 h. By taking the value of the photocurrent density at 0.23 V versus Ag/AgCl (i.e., 1.23 V vs RHE in 1 M KOH), the reponse increases from 460 µA/cm2 for 0 h aging time to 550 and 570 µA/cm2 in the case of 3 and 6 h aging time, respectively. The standard deviation between the photocurrent measurements for a given aging time is typically in the order of ±10% and it can be concluded that there is no significant difference between the photoresponses of the sol-gel aged after 3 and 6 h, whereas the sol-gel with no aging (i.e., 0 h) clearly has the lowest performance. We ascribe the shift observed in the absorbance, Figure 3, and the enhanced photocurrent density in aged photoelectrodes, Figure 4, to the building-up of the sol-gel network occuring during the aging process. Clearly, the formation of such network has an impact on both the crystallinity and the optical properties as well as ability to collect the photogenerated electrons.
Additional information on the photoelectrochemical properties of sol-gel films is provided by the IPCE analysis in Figures 5(a)–5(c). The study of the IPCE curve, particularly in the region 300–340 nm, provides information on the electron transport properties of the photoelectrodes. What clearly emerges from the IPCE analysis, in good agreement with the photocurrent density measured previously discussed (Figures 4(a)–4(c)), is the superior ability of aged films (see comparison between 0 h aging, Figure 4(a), and 3 h, Figure 4(b), and 6 h aging, Figure 4(c)) to absorb photons and collect them at the back FTO electrode. Despite having practically the same IPCE in the range of 460 to 340 nm, the SG/1 layer/6 h photoelectrodes provide higher IPCE than SG/1 layer/0 h films for λ < 340 nm: 10% versus 7% at 340 nm, 17.5% versus 12.5% at 320 nm, and 26% versus 20% at 300 nm, as shown in Figures 5(a) and 5(c). The values for SG/1-layer/3 h aging, 7.5% at 340 nm, 14% at 320 nm, and 20% at 300 nm, Figure 5(b), are in between those of 0 and 6 h aging. The reason for the higher photocurrent density of 3 and 6 h aging times in comparison with 0 h aging time can therefore be confidently linked to the superior ability of aged photoelectrodes to collect electrons photogenerated from the absorption of shorter wavelength (300 nm ≤ λ ≤ 340 nm). Considering that the photoanodes were “front illuminated” and the absorption coefficient (α) of the light is a decreasing function of λ (i.e., shorter λ have higher α than longer λ), light of 300 nm ≤ λ ≤ 340 nm is mostly absorbed in the 10 to 100 nm region  closest to the electrolyte. Therefore, in the SG/1 layer/0–6 h aged photoelectrodes, the photogenerated electrons have to diffuse through the entire film (0.6 ± 0.1 µm) in order to be collected at the FTO back contact. This requires an excellent network interconnectivity, which can be ensured by aging the photoelectrodes, as clearly shown in Figures 4(a)–4(c) and Figures 5(a)–5(c). SEM analysis also reveals an additional feature responsible for the good performances of the SG photoelectrodes: their mesoporosity, Figures 6(a)-6(b), is in fact crucial to ensure penetration of the electrolyte within the photoanode. It should be noted that Figures 6(a)-6(b) show the microstructure of 6 h aged photoelectrodes; however, no significant differences in the morphology and mesoporosity of photoelectrodes aged for 0 or 3 h were observed. From the analysis of Figures 6(a)-6(b), it is not possible to provide an exact value for the pore size within the TiO2 films; however, it is clear that such pores are bigger than 10 nm and are very likely to allow a good contact/interface within the film and electrolyte . In contrast, whenever the diameter of the pore is below 10 nm, the bulk of the film may not be in contact with the electrolyte and therefore does not contribute to the charge transfer process, limiting the film’s photoactivity . It is likely that the presence of 5wt.% PVB in the sol also contributes to establish such an optimal porous structure, although further studies are necessary to confirm this hypothesis.
The porosity of the thin films photoelectrodes has been estimated (from SEM micrograph) to be 21.8 ± 0.6%, 20.2 ± 0.7%, and 19.4 ± 0.5% for 0, 3, and 6 h aged photoelectrodes, respectively. As expected, considering the rather small window of investigated range of aging time (0 to 6 h), no major changes are observed. It has also been possible to estimate the specific surface area of the photoelectrodes by dye adsorption/desorption. Again, no significant differences were osberved, with values of 22 ± 3 m2/g, 20 ± 2 m2/g, and 19 ± 2 m2/g for 0, 3, and 6 h aged photoelectrodes, respectively. Typically, larger modifications of surface area and porosity as a function of aging time are better appreciated by extending the aging to days or even weeks . Nevertheless, there seems to be a trend suggesting a small decrease in porosity and surface area as the aging time increases; this could be due to further condensation reactions and formation of Ti–O–Ti within the sol. Such small changes of porosity and surface area (observed between 0 and 6 h aging time) may also contribute to generate differences in the light scattering behaviour and optical properties of the various photoelectrodes.
In addition to the influence of aging time, we have also investigated the effect of film thickness on the performances of the photoanodes, while keeping the aging time of the sol constant (6 h), attempting to optimize their light absorption properties. As it can be appreciated from Table 1, by increasing the number of dip-coated layers from 1 to 2 and 3, the thickness of the film increases from 0.6 ± 0.1 µm to 1.1 ± 0.1 µm and 1.6 ± 0.2 µm, respectively. As an example, the SEM cross section profile of a SG/3-layer-thick photoanode is given in Figure 6(b).
The photocurrent measurements of multilayered photoanodes are reported in Figures 4(d)-4(e). By comparison with Figure 4(c) (1 layer, 6 h aging), it can be concluded that the photocurrent is not affected by the thickness/number of layers dip-coated on the FTO substrate and remains in the order of 550 to 570 µA/cm2 at 0.23 V vs Ag/AgCl. Likewise, the IPCE curves of SG/2 layers/6 h and films, Figures 5(d)-5(e), are very similar to the IPCE response of SG/1 layer/6 h, Figure 5(c). The IPCE values of SG/3 layers/6 h, SG/2 layers/6 h, and SG/1 layer/6 h are, respectively, 12, 11, and 10% at 340 nm, 18, 19, and 17.5% at 320 nm, and 25, 25, and 26% at 300 nm. This is in contrast with a recent report  on a nearly linear increase in the IPCE on TiO2 films up to 1.3 µm thick, but once more it confirms the good electron transport properties of the photoelectrodes; the photogenerated charge carriers from light of 300 nm ≤ λ ≤ 340 nm can be also successfully collected in multilayers film (up to 1.6 µm thick, Table 1).
Even at 300 nm, where the light’s penetration depth is estimated to be 10–30 nm, based on the absorption spectrum by Eagles  and accounting for film’s porosity and the presence of anatase , the IPCE is still 25% in both SG/3 layers/6 h and SG/2 layers/6 h. Films thinner than 0.6 ± 0.1 µm (1 layer with dip coating parameter adopted within this work) were not considered in this study; it has been recently reported that 0.2 µm thick mesoporous sol-gel provides photocurrent density (related to solar water splitting) in the range of 1 mA/cm2  and it could be argued that also in our case thinner films may lead to an improved photoresponse. A final consideration to highlight regarding the sol-gel photoelectrodes is their weak response in the region 400–440 nm, which can be appreciated in all the IPCE spectra, Figures 5(a)–5(e). The indirect band-gap of the photoelectrodes, Table 1, estimated by applying the Tauc plot to the optical data in Figure 3 is in the range of 3.21 to 3.25 eV, corresponding to an absorption threshold of 386.3 to 381.5 nm. The IPCE response well above the absorption threshold can be explained by the presence of shallow donor states within the TiO2; for example, the use of carbon based precursors for the preparation of the TiO2 sol-gel, as well as the sintering performed in air, is likely to introduce oxygen vacancies within the oxide. The presence of oxygen vacancies acting as donor states  also emerges from the Tauc plot of the photoelectrodes. As an example, the Tauc plot of SG/1 layer/6 h is shown in Figure 7. In addition to the indirect band-gap, extrapolated to be 3.21 ± 0.08 eV, there is a tail (Figure 7 inset) corresponding to a sub-band-gap of 2.90 ± 0.06 eV. Similar donor levels were also highlighted in a previous study on the activation energy for conduction in TiO2 . Finally, the trapping of a small amount of visible light within the photoanode could also be a consequence of the mesoporosity of the film, Figures 6(a)-6(b).
The optimization of a sol-gel process aimed at producing mesoporous TiO2 based photoelectrodes for solar water splitting has been presented within this work. In particular, we have investigated two parameters, aging time of the sol and thickness of the TiO2 films, and their impact on the photoelectrochemical properties of the material. Our results show that aging the sol for 3 to 6 h before the dip coating onto FTO substrates is crucial to ensure optimal performance of the photoelectrodes. It should be noticed that the aging time did not influence the thickness of the film. It is assumed that the concentration of the titanium tetraisopropoxide in the sol-gel system should instead affect the coating thickness (and should possibly also modify the long stability of the sol); this will be investigated in a separate study. The absorbance threshold of aged sol-gels is slightly shifted towards higher wavelenghts in comparison to 0 h aging and their photocurrent density (up to 570 µA/cm2, among the highest photocurrent densities reported for TiO2 sol-gel) and IPCE response (10% at 340 nm and 26% at 300 nm) confirm the superiority of aged films also in terms of network interconnectivity and electron collection properties. It is also evident that the crystallinity of the films is improved after aging. No significant changes of the photoresponse were instead observed by increasing the thickness of the TiO2 films. The presence of weak IPCE signals in all TiO2 photoelectrodes, above 400 nm, is explained in terms of donor levels (oxygen vacancies) introduced during the processing and sintering of the sol-gel. Due to its wide band-gap (above 3 eV), TiO2 alone cannot lead towards the development of photoelectrochemical water splitting devices with a 10% solar to hydrogen (STH) efficiency (the threshold above which such technology becomes industrially viable ). However, considering its unique properties, the study and the optimization of the photoelectrochemical behavior of TiO2 based mesoporous photoanodes are very important, as we believe they can be used as an efficient, stable, and robust support for materials/particles capable of harvesting visible light.
Conflict of Interests
The authors declare that there is no conflict of interests regarding the publication of this paper.
The authors gratefully thank the financial support by the Brazilian Swiss Joint Research Programme (BSJRP 0112-11) and by the Swiss National Science Foundation under Project no. R’Equip 206021-121306 (Fundamental Aspects of Photocatalysis and Photoelectrochemistry/Basic Research Instrumentation for Functional Characterization). Dr. Artur Braun (EMPA) is also kindly acknowledged for the provision of experimental facilities. The photoelectrochemical (cappuccino) cell was machined at the Empa Machine Shop based on the original design provided by the Laboratory for Photonics and Interfaces, EPFL Lausanne. Dr. Fabio La Mattina and A. Kupferschmid (Empa) are also gratefully acknowledged for their contribution to the IPCE set-up.
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