Synthesis, Characterization, Properties, and Applications of Nanosized Photocatalytic MaterialsView this Special Issue
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Kyung-Jong Noh, Hyo-Jin Oh, Bo-Ra Kim, Sang-Chul Jung, Wooseung Kang, Sun-Jae Kim, "Photoelectrochemical Properties of Supported on -Based Thin Films Converted from Self-Assembled Hydrogen Titanate Nanotube Powders", Journal of Nanomaterials, vol. 2012, Article ID 475430, 6 pages, 2012. https://doi.org/10.1155/2012/475430
Photoelectrochemical Properties of Supported on -Based Thin Films Converted from Self-Assembled Hydrogen Titanate Nanotube Powders
A photoanode was fabricated using hematite (α-Fe2O3) nanoparticles which had been held in a thin film of hydrogen titanate nanotubes (H-TiNT), synthesized by repetitive self-assembling method on FTO (fluorine-doped tin oxide) glass, which were incorporated via dipping process in aqueous Fe(NO3)3 solution. Current voltage (I-V) electrochemical properties of the photoanode heat-treated at 500°C for 10 min in air were evaluated under ultraviolet-visible light irradiation. Microstructure and crystallinity changes were also investigated. The prepared Fe2O3/H-TiNT/FTO composite thin film exhibited about threefold as much photocurrent as the Fe2O3/FTO film. The improvement in photocurrent was considered to be caused by reduced recombination of electrons and holes, with an appropriate amount of Fe2O3 spherical nanoparticles supported on the H-TiNT/FTO film. Nanosized spherical Fe2O3 particles with about 65 wt% on the H-TiNT/FTO film showed best performance in our study.
Hydrogen production through photoelectrochemical (PEC) water splitting process has been paid much attention as a promising solution to the global energy problem [1–4]. Transition metal oxide semiconductors have been considered candidate materials as a photoelectrode for this process. Among them, one of the most extensively explored materials is Fe2O3-based materials with optical energy bandgap of ~2.2 eV [5–7]. However, some major issues have been raised in the fabrication of a Fe2O3 photoanode as well as electrocatalyst, such as low electrical conductivity of the material itself and necessity of less than 5 nm particle synthesis, to avoid electron-hole recombination related to the extremely short diffusion distance of holes, among others [8, 9]. Along with the transition metal oxide semiconductors, TiO2 with optical energy bandgap of 3.0~3.2 eV has also been much investigated as an electrode material due to its favorable characteristics, such as photoelectrochemical stability, nontoxicity, and low cost for fabrication [10–12]. In our present study, we focused on the fabrication and optimization of nanosized Fe2O3 supported on TiO2-based nanotube materials for PEC cell performance for the water splitting process. The materials are expected to exhibit the advantages of the porous TiO2-based nanotube thin film support, as they are fully utilized to enhance the photoelectrochemical performance of supported Fe2O3 nanoparticles.
To overcome the aforementioned limitations in the PEC application, in this paper, porous TiO2 film converted by heat treatment from the H-TiNT (hydrogen-titanate nanotube) film fabricated by repetitive self-assembling method on the FTO substrates was utilized to support Fe2O3 nanoparticles. The materials were characterized, and their I-V PEC performance under ultraviolet-visible (UV-Vis) light irradiation for the water splitting process was carefully investigated to optimize the Fe2O3 particles on the support.
2. Experimental Procedure
Repetitive self-assembling of oppositely charged ions in an aqueous solution was applied to directly coat the H-TiNT powder, which was obtained from a hydrothermal technique detailed in our previous reports, on a transparent conducting substrate of FTO glass [13–17]. FTO glass (Asahi Glass Co.) used as a transparent conductive substrate was surface-treated for 20 min in 0.2 M polyethyleneimine (PEI, Aldrich) aqueous solution containing positively charged ions. All the aqueous solutions were prepared using distilled water of 1.8 MΩ. The surface-pretreated FTO glass was immersed for 20 min in an aqueous 10 g/L H-TiNT solution dispersed together with 0.2 M tetrabutylammonium hydroxide (TBAOH, Aldrich) to produce negatively charged ions. Using the same method, an H-TiNT-treated film was subsequently immersed in 0.2 M polydiallyldimethylammonium chloride (PDDA, Aldrich) aqueous solution containing positively charged ions. Repetition of these processes yielded an H-TiNT film coated on the FTO glass with approximately 700~1000 nm thickness as previously reported in our research [15–17]. The obtained H-TiNT/FTO glass was dried under UV-Vis light irradiation (Hg-Xe 200 W lamp, Super-cure, SAN-EI Electric) to remove water and all the surfactants, such as PEI, TBAOH, and PDDA using photocatalytic removal reaction occurred by H-TiNT particles with the optical energy bandgap of 3.5 eV , without any sintering. Then, for the Fe2O3 nanoparticle coating process, the dried H-TiNT/FTO substrates were dipped in an aqueous 1.0 M Fe(NO3)3 solution for 6~24 hrs. It was also done by multiple dipping of the samples in the solution along with the heat treatment after each dipping, at 500°C for 10 min in air atmosphere. In order to have thin thickness of the Fe2O3 film which has a bandgap of 2.2 eV, the optical energy bandgap of the Fe2O3/H-TiNT/FTO samples was controlled to be in the range of 3.24~2.9 eV. The heat treatment was done inside a box furnace with the heating rate of 500°C/sec to produce the final photoanode thin film with α-Fe2O3 phase, where the rapid heating rate was accomplished by plunging the samples into the hot zone of the furnace maintained at 500°C.
The microstructures, crystallinities, optical energy band gap, and I-V electrochemical properties of the as-prepared heat-treated thin films were analyzed using scanning electron microscopy (SEM; S-4700, Hitachi), Raman spectroscopy (Renishaw, inVia Raman microscope), UV-Vis spectroscopy (S-3100, Sinco), and cyclic voltammetry (μAutolab type III, Micro Autolab), respectively. To measure the I-V electrochemical property, a calomel electrode and a Pt wire were used as the reference and counter electrodes, respectively, when the Fe2O3/H-TiNT composite film was used as the working electrode in an aqueous 1.0 M NaOH deaerated solution under irradiation of 130 mW/cm2 UV-Vis spectrum (Hg-Xe 200 W lamp, Super-cure, SAN-EI Electric). The measured potentials versus calomel electrode were converted to the reversible hydrogen electrode (RHE) scale.
3. Results and Discussion
Figure 1 displays the SEM photos for the surface microstructures of the Fe oxide and the H-TiNT films coated as a photoanode material on the pure FTO substrate, which were all heat-treated at 500°C for 10 min in air. Figure 1(a) is the surface of the heat-treated FTO substrate with 300~500 nm sized grains and a roughness of ±200 nm. Figures 1(b) and 1(c) are the images of Fe oxide films with 27.16 and 100 wt% of Fe2O3, respectively, coated on the surface of the FTO substrate after multiple dips in an aqueous 1 M Fe(NO3)3 solution, drying, and heat treatment. Here, the amounts of Fe2O3 were calculated by multiplying the measured concentration of combined elements of Sn and Fe by energy-dispersive spectroscopy, assuming a complete conversion of Fe(NO3)3 to Fe2O3. Figure 1(d) illustrates the H-TiNT film on the FTO substrate obtained by the repetitive self-assembling method as described in the experimental procedure. Figure 1(b) depicts the FTO substrate partially covered with less than 10 nm wide Fe2O3 particles. Figures 1(c) and 1(d) present the FTO substrate fully covered with 10~30 nm sized Fe2O3 particles and H-TiNT nanoparticles, respectively. It can be seen in Figure 1(d) that the H-TiNT nanoparticles consist of spherical and longitudinal particles transformed from ~10 nm wide and ~100 nm long tubular-shaped particles. It was confirmed by SEM and TEM techniques that the films in Figures 1(c) and 1(d) have less than 1 μm thick film coatings, especially Figure 1(d) was 700~1000 nm thick . To confirm the phase or crystallinity of the specimens in Figures 1(a), 1(c), and 1(d), the Raman spectra are presented in Figure 2. The crystallographic characteristics of heat-treated FTO, Fe2O3, and H-TiNT films were also compared with those of the untreated FTO film (not shown). From the micrographs in Figure 1 and the corresponding Raman spectra in Figure 2, the microstructure of the heat-treated sample was found to consist of spherical α-Fe2O3, longitudinal titanate, and the spherical anatase TiO2 phase, which was similarly observed and reported in our previous work .
The specimens in Figure 1 were initially applied to the photoanode for the water splitting process, where their I-V electrochemical characteristics were evaluated using a linear sweep voltammetry in the range of +0.7~+1.5 V versus the RHE under 130 mW/cm2 UV-Vis light illumination (Figure 3). The current signals of all the specimens were detected with an onset voltage of around 0.9 V versus RHE. Both the heat-treated FTO and H-TiNT/FTO films yielded relatively very low currents up to the applied potential of 1.3 V versus the RHE, indicating that water splitting is electrochemically difficult at 1.23 V versus RHE. When the Fe2O3 film partially covered the FTO substrate (Fe2O3 = 27.16 wt%), its current significantly increased (1.39 mA/cm2) at 1.23 V versus RHE, whereas the Fe2O3 film, which fully covered the surface of the FTO substrate, yielded a relatively low value, although higher than those of the heat-treated FTO and H-TiNT/FTO films. This variation indicates that not all the currents generated by the thick or full Fe2O3 film coating can be completely collected through the FTO conducting layer, compared with those generated by the thin or partial Fe2O3 film coating. As shown in Figures 1(b) and 1(c), it is thought that the collection of electrons in these specimens was not perfectly accomplished by the 5~30 nm Fe2O3 particles due to the typical recombination of electron hole [18, 19], although the amount of generated electrons on the thick or full Fe2O3 film coating on the FTO substrate with UV-Vis light irradiation could become ample enough. Thus, it is obviously known that the amount or size of the Fe2O3 particles supported on the FTO substrate should be appropriately controlled to increase the current. However, because it was found that the current decreased abruptly with the Fe2O3 more than 27.16 wt% as in our preliminary experiments, our focus should be directed to the reduction of the Fe2O3 particle size or the insertion of a new easy path layer to the FTO substrate beneath the Fe2O3 film for energy band alignment. It would be more effective to protect the recombination of electrons and holes photogenerated in real system. Various amounts of Fe2O3 nanoparticles were supported on an H-TiNT/FTO composite film using the self-assembling or dipping procedure, as shown in Figure 4.
Figures 4 and 5 show the I-V electrochemical characteristics curves and the current at 1.23 V versus RHE, with varied Fe2O3 amounts supported on an H-TiNT/FTO composite film by controlling the dipping time or multiple dippings in an aqueous Fe(NO3)3 solution, respectively. This was followed by heat treatment at 500°C for 10 min in air to obtain the hematite-Fe2O3 phase. Here, the amount of Fe2O3 was also calculated by multiplying the measured concentration of combined elements of Ti and Fe by energy-dispersive spectroscopy, assuming a complete conversion of TiO2 and Fe2O3 from H-TiNT and Fe(NO3)3. As the supported amount of Fe2O3 nanoparticles increases, the onset voltage decreases to approximately 0.7 V versus RHE, whereas their generated current significantly increases. The current density increase can be easily understood by the reasoning that more Fe2O3 involved due to the advantage of TiO2 in the sample would enhance the visible light absorption. Performance improvements were similarly observed with the integrated materials, for the same purpose as ours, such as Fe-modified TiO2 nanotubes  and CuS/ZnS porous nanosheets . As shown in Figure 5, the current at 1.23 V versus RHE peaks at 4.81 mA/cm2 with 65.48 wt% of the supported Fe2O3 nanoparticles on the H-TiNT/FTO film, which is about threefold as much current as the Fe2O3/FTO film. The generated current then decreases abruptly and would become saturated to approximately 1.4 mA/cm2 due to formation of thick Fe2O3 film.
Figure 6 shows the representative SEM photos of the surface microstructures of the H-TiNT/FTO film supporting various amounts of Fe2O3 nanoparticles of Figure 4, which were obtained at 500°C for 10 min heat treatment. The Fe2O3 nanoparticles observed on the SEM surfaces with the amounts, when compared to Figure 6(d) which evidently covered the entire surface of the film, are different than the heat-treated H-TiNT/FTO (Figure 1(d)). At 96.07 wt% Fe2O3, the H-TiNT surface is almost perfectly covered by thick and more than 5 nm Fe2O3 particles similarly to those in Figure 1(c), although the surfaces fully covered with Fe2O3 nanoparticles had some pores. It was checked in preliminary work that the specimen of Figure 1(c) had about 2.9 eV of the optical energy bandgap, which means obtainment of thin Fe2O3 layer because bulky Fe2O3 material has about 2.2 eV. However, when covered with Fe2O3 nanoparticles, approximately more than 70 wt% of the specimens yielded relatively low current, still indicating the existence of a large recombination of electrons and holes photogenerated because their values are larger than those in the Fe2O3/FTO film. Consequently, it can be known that the maximum current can be obtained after heat treatment when supporting the appropriate amount of hematite-Fe2O3 nanoparticles around 65 wt% on the H-TiNT/FTO film. When the Fe2O3/FTO film is compared with the H-TiNT/FTO film, the H-TiNT coating cannot yield enough current. However, this coating can contribute greatly to the generation of an enhanced current as an easy path layer by reducing the recombination of electrons and photogenerated holes. Although Fe2O3 nanoparticles produce current, larger amounts or thick Fe2O3 nanoparticles result in the partial collection of generated current at the FTO electrode by increasing losses such as the recombination of electrons and holes and leakage current by high resistivity of Fe2O3 film. Thus, it can be said from our data that the insertion of an easy electron path layer beneath the Fe2O3 top layer is necessary to enhance the current for an efficient water splitting process. In the near future, our studies will be focused in detail on the importance and effect of the H-TiNT film to support Fe2O3 nanoparticles to increase the collected current at the FTO substrate. This can be conducted by the easy collection of photogenerated electrons from a Fe2O3 top layer, with controlled nanosizes of less than 10 nm, through detailed characterizations of H-TiNT and Fe2O3 materials.
To overcome the limitations of the Fe2O3 material for PEC application, H-TiNT film prepared by the repetitive self-assembling method on the FTO substrate was utilized to support Fe2O3 nanoparticles.
The Fe(NO3)3/H-TiNT composite films were heat-treated at 500°C for 10 min in air with very rapid heating rate of 500°C/sec. The materials were characterized, and their I-V electrochemical performance under UV-Vis light irradiation for the water splitting process was carefully investigated to determine the optimized Fe2O3 particle content. The heat-treated hematite-Fe2O3 phase film showed superior generation and collection of current with appropriate amounts of Fe2O3 on the H-TiNT film, with mixture of a longitudinal titanate phase and a spherical anatase TiO2 phase. The onset voltage at 65.48 wt% supported Fe2O3 decreased to approximately 0.7 V versus RHE, and its current peaked at 4.81 mA/cm2 at 1.23 V versus RHE. Although the Fe2O3 nanoparticles produced current, larger amounts or thick Fe2O3 nanoparticles resulted in a loss of generated current by increasing the recombination of electrons, holes, and leakage current by high resistivity of Fe2O3 film, and so forth. In conclusion, it can be suggested that the insertion of an easy electron path layer beneath the Fe2O3 top layer is necessary to enhance the current for an efficient water splitting process.
This paper was supported by the Basic Science Research Program through the National Research Foundation of Korea (NRF) funded by the Ministry of Education, Science and Technology (no. 2011–0016699).
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