We improve the conversion efficiency of Ag2S quantum dot (QD)-sensitized TiO2 nanotube-array electrodes by chemically depositing ZnO recombination barrier layer on plain TiO2 nanotube-array electrodes. The optical properties, structural properties, compositional analysis, and photoelectrochemistry properties of prepared electrodes have been investigated. It is found that for the prepared electrodes, with increasing the cycles of Ag2S deposition, the photocurrent density and the conversion efficiency increase. In addition, as compared to the Ag2S QD-sensitized TiO2 nanotube-array electrode without the ZnO layers, the conversion efficiency of the electrode with the ZnO layers increases significantly due to the formation of efficient recombination layer between the TiO2 nanotube array and electrolyte.
quantum dotsTiO2 nanotubeAg2Ssolar cells
In recent years, dye-sensitized solar cells (DSSCs) have attracted much attention as a promising alternative to conventional p-n junction photovoltaic devices because of their low cost and ease of production [1–4]. A high power conversion efficiency of 11.3% was achieved . The conventional DSSCs consist of dye-sensitized nanocrystalline TiO2 film as working electrode, electrolyte, and opposite electrode. In DSSCs, the organic dyes act as light absorbers and usually have a strong absorption band in the visible. Various organic dyes such as N719 and black dye have been applied for improving the efficiency, light absorption coverage, stability, and reducing the cost. However, the organic dyes have a weak absorbance at shorter wavelengths. Materials that have high absorption coefficients over the whole spectral region from NIR to UV are needed for high power conversion efficiency. During the last few years, instead of organic dyes, the narrow band gap semiconductor quantum dots (QDs) such as CdS [6, 7], CdSe [7–9], PbS [10, 11], InAs , and InP  have been used as sensitizers. The unique characteristics of QDs over the organic dyes are their stronger photoresponse in the visible region, tunable optical properties, and band gaps simply by controlling the sizes. The QD-sensitized solar cells (QDSSCs) have been considered the next-generation sensitizers . In either DSSCs or QDSSCs, the nanoparticle porous film electrode plays a key role in the improvement of power conversion efficiency. Recently, to improve the properties of TiO2 film electrode, one-dimensional nanostructure arrays as working electrodes, including nanowires and nanotubes, have been proposed and studied. Compared with the nanoparticle porous films, aligned one-dimensional nanostructure arrays can provide a direct pathway for charge transport and superior optical absorption properties. Therefore, more and more studies focus on QDSSCs based on one-dimensional nanomaterials, such as the TiO2 nanotubes (TNTs) [15–17].
Among QDs, Ag2S is an important material for photocatalysis [18–20] and electronic devices [21–24]. Ag2S has a large absorption coefficient and a direct band gap of 0.9 to 1.05 eV, which makes Ag2S an effective semiconductor material for photovoltaic application. In the past several years, although there are some reports on the photovoltaic application of Ag2S [10, 25], few studies on Ag2S QDSSCs based on TNTs are reported. In this work, we report on the synthesis of Ag2S QD-sensitized TNT photoelectrode combining the excellent charge transport property of the TNTs and absorption property of Ag2S. Besides, to improve the efficiency of as-prepared photoelectrodes, we interpose a ZnO recombination barrier layer between TNTs and Ag2S QDs to reduce the charge recombination in Ag2S QDSSCs because the ZnO layer can block the recombination of photoinjected electrons with redox ions from the electrolyte. Recently, we have reported the improved conversion efficiency of CdS QD-sensitized TiO2 nanotube array using ZnO energy barrier layer . Similar method has been used by Lee et al. to enhance the efficiency of CdSe QDSSCs by interposing a ZnO layer between CdSe QDs and TNT . Our results show that Ag2S QD-sensitized TiO2 nanotube-array photoelectrodes were successfully achieved. The more important thing is that the conversion efficiency of the Ag2S-sensitized TNTs is significantly enhanced due to the formation of ZnO on the TNTs.
Titanium foil (99.6% purity, 0.1 mm thick) was purchased from Goodfellow (Huntingdon, England). Silver nitrate (AgNO3, 99.5%) and glycerol were from Junsei Chemical Co. (Tokyo, Japan). Ammonium fluoride (NH4F), sodium sulfide nonahydrate (Na2S, 98.0%), and zinc chloride (ZnCl2, 99.995+%) were available from Sigma-Aldrich (St. Louis, MO, USA).
Synthesis of TNTs
Vertically oriented TNTs were fabricated by anodic oxidation of Ti foil, which is similar to that described by Paulose et al. . Briefly, the Ti foils were first treated with acetone, isopropanol, methanol, and ethanol, followed by distilled (DI) water and finally drying in a N2 stream. Then, the dried Ti foils were immersed in high-purity glycerol (90.0 wt.%) solution with 0.5 wt.% of NH4F and 9.5 wt.% DI water and anodic oxidized at 60 V in a two-electrode configuration with a cathode of flag-shaped platinum (Pt) foil at 20°C for 25 h. After oxidation, the samples were washed in DI water to remove precipitation atop the nanotube film and dried in a N2 stream. The obtained titania nanotube film was annealed at 450°C in an air environment for 2 h.
Synthesis of Ag2S-sensitized plain TNT and ZnO/TNT electrodes
The ZnO thin films on TNTs were prepared by using the successive ionic layer adsorption and reaction method, as described elsewhere [27, 29]. Briefly, the annealed TNT electrodes were immersed in 0.01 M ZnCl2 solution complexed with an ammonia solution for 15 s and then in DI water at 92°C for 30 s, with the formation of solid ZnO layer. Finally, the as-prepared TNT electrodes were dried in air and annealed at 450°C for 30 min in air for better electrical continuity. Ag2S QDs were assembled on the crystallized TNT and ZnO/TNT electrodes by sequential chemical bath deposition (CBD) [25, 30]. Typically, one CBD process was performed by dipping the plain TNT and ZnO/TNT electrodes in a 0.1 M AgNO3 ethanol solution at 25°C for 2 min, rinsing it with ethanol, and then dipped in a 0.1 M Na2S methanol solution for 2 min, followed by rinsing it again with methanol. The two-step dipping procedure is considered one CBD cycle. After several cycles, the sample became dark. In this study, 2, 4, and 8 cycles of Ag2S deposition were performed (denoted as Ag2S(2), Ag2S(4), and Ag2S(8), respectively). Finally, the as-prepared samples were dried in a N2 stream. The preparation process of as Ag2S-sensitized ZnO/TNT electrode is shown in Figure 1. For comparison, Ag2S-sensitized TNT electrodes without ZnO films were also fabricated by the same process.
The surface morphology of the as-prepared electrodes was monitored using a scanning electron microscope (SEM) (Nova230, FEI Company, Eindhoven, Netherland). The mapping and crystal distribution of the samples were done using a scanning transmission electron microscope (TEM) (Tecnai G2 F30, FEI Company Eindhoven, Netherland) to which an Oxford Instruments (Abingdon, Oxfordshire, UK) energy dispersive X-ray spectroscopy (EDS) detector was coupled. The surface compositions of the samples were analyzed using EDS. The crystalline phase and structure were confirmed by using X-ray diffraction (XRD) (Rigaku D/MAX 2500 V diffractor; Rigaku Corporation, Tokyo, Japan). The UV-visible (UV-vis) absorbance spectroscopy was obtained from a S-4100 spectrometer with a SA-13.1 diffuse reflector (Scinco Co., Ltd, Seoul, South Korea).
The photoelectrochemical measurements were performed in a 300-mL rectangular quartz cell using a three-electrode configuration with a Pt foil counter electrode and a saturated SCE reference electrode, and the electrolyte was 1.0 M Na2S. The working electrode, including the TNTs, ZnO/TNTs, Ag2S(n)/TNTs, and Ag2S(n)/ZnO/TNTs (n = 2, 4, and 8), with a surface area of 0.5 cm2 was illuminated under UV-vis light (I = 100 mW cm-2) with a simulated solar light during a voltage sweep from -1.4 to 0 V. The simulated solar light was produced by a solar simulator equipped with a 150-W Xe lamp. The light intensity was measured with a digital power meter.
Results and discussion
Morphology of the TNTs
Figure 2a shows the SEM image of the plain TNT film fabricated by anodization of Ti foil before coating with ZnO and Ag2S, which reveals a regularly arranged pore structure of the film. The average diameter of these pores is found to be approximately 200 nm and the thickness of the wall of the TNTs approximately 30 nm.
Characterization of the Ag2S QD-sensitized ZnO/TNT (and TNTs) electrodes
Figure 2a shows the surface SEM image of the Ag2S(4)/TNT film. It can be clearly seen from Figure 2b that Ag2S is deposited as spherical nanoparticles on the TNTs and the wall thickness of the Ag2S(4)/TNTs is similar to that of the plain TNTs. In addition, a uniform distribution of the Ag2S nanoparticles with diameters of approximately 10 nm is also observed.
For a comparison, the surface SEM image of the ZnO/TNTs covered by Ag2S after four CBD cycles (i.e., the Ag2S/ZnO/TNT electrode) is shown in Figure 2c. It is found that after the formation of the ZnO thin layer on the TNTs, the diameter and distribution of Ag2S nanoparticles did not change much. However, the diameter of the ZnO-coated TNTs increased slightly compared to that of the plain TNTs shown in Figure 2b. These results are similar to previous reports [26, 27].
The detailed microscopic structure of the Ag2S(4)/ZnO/TNTs was further investigated by a high-resolution transmission electron microscope (HR-TEM). Figure 3a shows the low-magnification TEM image of the Ag2S(4)/ZnO/TNTs. It can be clearly seen that many Ag2S nanoparticles with diameters of approximately 10 nm were deposited into the TNTs. This is supported by our earlier observation in the SEM measurement (Figure 2c). Figure 3b shows the high-magnification image of the Ag2S(4)/ZnO/TNTs. It is observed that the crystalline Ag2S nanoparticles were grown on crystalline TNTs. In addition, the HR-TEM image in Figure 3b reveals clear lattice fringes, the observed lattice fringe spacing of 0.268 nm is consistent with the unique separation (0.266 nm) between (120) planes in bulk acanthite Ag2S crystallites.
To determine the composition of the nanoparticles, the corresponding energy dispersive x-ray (EDX) spectrum of the Ag2S(4)/ZnO/TNTs was carried out in the HR-TEM as seen in Figure 3c. The characteristics peaks in the spectrum are associated with Ag, Ti, O, Zn, and S. The quantitative analysis reveals the atomic ratio of Ag and S is close to 2:1, indicating the deposited materials are possible Ag2S.
In order to determine the structure of the Ag2S(4)/ZnO/TNTs, the crystalline phases of the Ag2S(4)/ZnO/TNTs and the corresponding TNTs were characterized by XRD, as shown in Figure 3d. The XRD pattern shows peaks corresponding to TiO2 (anatase), ZnO (hexagon), and Ag2S (acanthite). The observed peaks indicate high crystallinities in the TNTs, ZnO, and Ag2S nanoparticles, consistent with the SEM results shown in Figure 2. The results further confirm that the obtained films are composed of TiO2, ZnO, and Ag2S.
Optical and photoelectrochemistry properties of Ag2S QD-sensitized TNT electrodes in the presence of ZnO layers
Figure 4 shows optical absorption of annealed TNTs, ZnO/TNTs, and Ag2S(n)/ZnO/TNTs (n = 2, 4, and 8). It can be seen from Figure 4 that both plain TNTs and ZnO/TNTs absorb mainly UV light with wavelengths smaller than 400 nm. However, for the ZnO/TNT film, the absorbance of the spectra slightly increases compared to that for plain TNTs, suggesting the formation of ZnO thin film on TNTs. This result is similar to that for ZnO-coated TiO2 films in DSSCs , which can be attributed to the absorption of the ZnO layers coated on TNTs. After Ag2S deposition, the absorbance of the Ag2S(n)/ZnO/TNT films increases with the cycles of Ag2S chemical bath deposition process. Moreover, a significant shift of the spectral photoresponse is observed in the Ag2S(n)/ZnO/TNT films, indicating that the Ag2S deposits can be used to sensitize TiO2 nanotube arrays with respect to lower energy (longer wavelength) region of the sunlight. In addition, the absorbance increases with the increase in the cycles of Ag2S deposition, resulting from an increased amount of Ag2S nanoparticles.
For the performance comparison of as-prepared Ag2S-sensitized TNT and ZnO/TNT electrodes, the curves of photocurrent density vs. the applied potential for the Ag2S(n)/TNT and Ag2S(n)/ZnO/TNT (n = 2, 4, and 8) electrodes in the dark and under simulated AM 1.5 G sunlight irradiation (100 mW cm-2) are shown in Figure 5.
It is clearly seen from Figure 5 that for a chemical bath deposition (CBD) cycle n and an applied potential, the photocurrent density of the Ag2S(n)/ZnO/TNT electrode is higher than that of the Ag2S(n)/TNTs without ZnO layer. This can be explained from the increased absorbance of the Ag2S(n)/ZnO/TNT electrode shown in Figure 4 and the energy diagram of Ag2S-sensitized ZnO/TNT solar cells presented in Figure 6a. Due to the formation of ZnO energy barrier layer over TNTs, the charge recombination with either oxidized Ag2S quantum dots or the electrolyte in the Ag2S-sensitized ZnO/TNT electrode is suppressed compared to the Ag2S-sensitized TNTs. This explanation can be supported by the dark current density-applied potential characteristics of the Ag2S(n)/ZnO/TNTs and Ag2S(n)/TNTs because the dark current represented the recombination between the electrons in the conduction band and the redox ions of the electrolyte. As an example, Figure 6b shows the curves of dark density vs. the applied potential for the Ag2S(4)/ZnO/TNTs and Ag2S(4)/TNTs. Apparently, for the Ag2S-sensitized TNTs with ZnO-coated layers, the dark current density decreases significantly. In addition, it is found that for both Ag2S-sensitized ZnO/TNT and TNT electrodes, the photocurrent density at an applied potential increases with increasing CBD cycles, which can be attributed to a higher incorporated amount of Ag2S that can induce a higher photocurrent density. This result is consistent with the observed UV-vis absorption spectra shown in Figure 4. Similar results have been obtained in CdS-sensitized QDSSCs . Moreover, it should be noted that although the conduction band (CB) level of ZnO is slightly higher than that of TiO2 (Figure 6a), it seems that the electron transfer efficiency from Ag2S to ZnO is not much lower than that from Ag2S to ZnO because the photocurrent density of the Ag2S/ZnO/TNTs is more higher than that of the Ag2S/TNTs. This phenomenon can be explained as follows. According to Marcus and Gerischer's theory [32–34], the rate of electron transfer from electron donor to electron acceptor depends on the energetic overlap of electron donor and acceptor which are related to the density of states (DOS) at energy E relative to the conductor band edge, reorganization energy, and temperature. Therefore, in our case, even though The CB level of electron donor (Ag2S) is lower than that of electron acceptor (TiO2 or ZnO), the electron transfer may also happen if there is an overlap of the DOS of Ag2S and TiO2 (or ZnO), which may be the reason for the photocurrent generation in Ag2S-sensitized TNT electrodes. The more important thing is that for semiconductor nanoparticles, the DOS may be strongly influenced by the doped impurity , the size of the nanoparticles , and the presence of surrounding media such as liquid electrolyte (i.e., Na2S electrolyte in our case) . This means that the DOS of semiconductor nanoparticles may distribute in a wide energy range. Recently, the calculation results  showed that the DOS of Ag2S can distribute in a wide energy range from about -14 to 5 eV, indicating that the electron can probably transfer from Ag2S to TiO2 or ZnO due to the overlap of the electric states of Ag2S and TiO2 or ZnO. Besides, considering that the difference between the CB level of TiO2 and that of ZnO is not so large, it may be possible that the electron transfer rate from Ag2S to ZnO is not much lower than that from Ag2S to TiO2. The photocurrent and photovoltage of Ag2S QD-sensitized TiO2 electrode have been experimentally found not only by us but also by others [10, 25].
Figure 7 shows the photoconversion efficiency η as a function of applied potential (vs. Ag/AgCl) for the Ag2S(8)/ZnO/TNT and Ag2S(8)/TNT electrodes under UV-vis light irradiation. The efficiency η is calculated as , η (%) = [(total power output-electric power input)/light power input] × 100 = jp [(Erev |Eapp|)/I0] × 100, where jp is the photocurrent density (milliamperes per square centimeter), jp × Erev is the total power output, jp × Eapp is the electrical power input, and I0 is the power density of incident light (milliwatts per square centimeter). Erev is the standard state-reversible potential, which is 1.23 V/NHE. The applied potential is Eapp = Emeans - Eaoc, where Emeans is the electrode potential (vs. Ag/AgCl) of the working electrode at which photocurrent was measured under illumination and Eaoc is the electrode potential (vs. Ag/AgCl) of the same working electrode under open circuit conditions, under the same illumination, and in the same electrolyte. It can be clearly seen from Figure 7 that the Ag2S(8)/ZnO/TNT electrode shows a higher photoconversion efficiency compared to the Ag2S(8)/TNT electrode with a ZnO layer for an applied potential. In particular, a maximum photoconversion efficiency of 0.28% was obtained at an applied potential of -0.67 V vs. Ag/AgCl for the Ag2S(8)/ZnO/TNT electrode, while it was 0.22% for the Ag2S(8)/TNT electrode at an applied potential of -0.67 V. The maximum photoconversion efficiency of the Ag2S(8)/ZnO/TNT electrode is about 1.3 times that of the Ag2S(8)/TNT electrode. However, it should be noted that the efficiency of the Ag2S-sensitized TNT electrode is worse than the value obtained from Ag2S QD-sensitized nanocrystalline TiO2 film, which was recently reported by Tubtimtae et al. . The main reason may be due to the different architecture of TiO2 electrode. Ag2S QDs cannot be deposited in large numbers on the inner surface of TNTs due to the limited space in TNTs, while the number of Ag2S QDs deposited on the surface of nanocrystalline TiO2 film is almost not limited. This means that compared to the TNTs, more Ag2S QDs can be deposited on nanocrystalline TiO2 film and absorb more light leading to a higher photocurrent. Besides, in our case, we use TNT electrode and 1 M Na2S electrolyte. However, Tubtimtae et al. used nanocrystalline TiO2 film and a polysulfide electrolyte consisted of 0.5 M Na2S, 2 M S, 0.2 M KCl, and 0.5 M NaOH in methanol/water. Clearly, the electrolyte will affect the performance of the devices. Moreover, the photocurrent measurements are performed under different conditions. A three-electrode configuration was employed in our experiments. However, a two-electrode configuration was used in the experiments of Tubtimtae et al. In addition, our results show that the efficiency obtained from Ag2S-sensitized TNTs is also lower than that of CdS-sensitized TiO2 electrode . The main reason for this may be that the CB level of Ag2S is lower than that of TiO2 as shown in Figure 6a, but the CB level of CdS is higher than that of TiO2. Therefore, the electron transfer is more efficient in CdS/TNT solar cells. The comparison of our current experiments with those by Tubtimtae et al. indicates that there is still much scope for improving the performance of the Ag2S-sensitied ZnO/TNT electrode. Nevertheless, our results show that the ZnO layer leads to an increased η.
In conclusion, Ag2S quantum dot-sensitized TiO2 nanotube array photoelectrodes were successfully achieved using a simple sequential chemical bath deposition (CBD) method. In order to improve the efficiencies of as-prepared Ag2S quantum dot-sensitized solar cells, the Ag2S quantum dot-sensitized ZnO/TNT electrodes were prepared by the interposition of a ZnO energy barrier between the TNTs and Ag2S quantum dots. The ZnO thin layers were formed using wet-chemical process. The formed ZnO energy barrier layers over TNTs significantly increase the power conversion efficiencies of the Ag2S(n)/ZnO/TNTs due to a reduced recombination.
This work was supported by the Korea Science and Engineering Foundation (KOSEF) grant funded by the Korea Ministry of Education, Science and Technology (MEST) (no. 2010-0026150).
Department of Nuclear and Quantum Engineering, Korea Advanced Institute of Science and Technology (KAIST)
Physics Division, PINSTECH, Nanomaterials Research Group
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