Enhanced photoelectrochemical properties of nanocrystalline TiO2 electrode by surface sensitization with CuxO quantum dots.

Nanoporous anatase TiO2 films were fabricated by a screen-printing method, and CuxO quantum dots (QDs) were deposited on the TiO2 films through successive ionic layer adsorption and reaction (SILAR). The amount of CuxO QDs on the TiO2 films are controlled by changing the number of SILAR cycles. The morphology, microstructure, optical, and photoelectrochemical properties of different CuxO sensitized TiO2 films (CuxO/TiO2) were investigated in detail. The nanoporous TiO2 film offers a large surface area for anchoring QDs. QD deposited samples exhibited a significant improvement in photoelectrochemical performance than the bare of TiO2. CuxO/TiO2, prepared with 7 SILAR cycles, showed the best photoelectrochemical properties, where the photocurrent density was enhanced to 500.01 μA/cm2 compared with 168.88 μA/cm2 of bare TiO2 under visible light. These results indicate that the designed CuxO/TiO2 structure possesses superior charge separation efficiency and photoelectrochemical properties.

Introduction

Titanium dioxide (TiO2) has attracted great interest for water splitting[1, 2], quantum dot-sensitized solar cells[3, 4], optical sensors[5, 6], photocatalytic degradation[7] and other applications[8-10], due to its unique optical and photoelectric properties. Nevertheless, the intrinsic band gap of TiO2 (3.0 eV for rutile and 3.2 eV for anatase) limits its photoelectrochemical utility[11]. Specifically, the wide band gap restricts the photoresponse of TiO2 to only ultraviolet region, with the wavelengths below 380 nm, which constitutes less than 5% of the solar spectrum. Therefore, many studies have been conducted to extend the TiO2 optical absorption range to the visible light region, in order to expand the portion of the solar spectrum for which TiO2 can be utilized.

In recent years, quantum dots (QDs) have become increasingly attractive for similar applications as TiO2, because of their unique electronic and optical properties[12, 13], such as their high extinction coefficients[14, 15], tunable band gap[16, 17], multiple exciton generation[18, 19], and an expandable optical absorption range by controlling particle size[20, 21]. Various QDs, including CdS[22], CdSe[23], PbS[24], PbSe[25], and so on[26, 27], have been thoroughly studied. Although these studies have demonstrated that QDs-sensitized TiO2 can efficiently absorb visible light, inherent disadvantages of these QDs, such as a fixed visible light absorption range, the toxicity of elements, and the use of rare elements, limit their applications in biology, environment, medicine, and solar cells[28]. As a result, it is important to discover environmentally friendly QD materials. Recently, the development of copper oxides as both the core photocatalytic material and the photoelectrochemical material has drawn increasing amounts of attention[29-31]. Copper materials, which are multifunctional p-type semiconductors, with a band gap ranging between 1.5 and 2.4 eV[32], are environmentally friendly and can absorb in the visible light region[33, 34]. Until now, to the best of our knowledge, previous studies have not reported the surface sensitization of a nanocrystalline TiO2 electrode with CuxO QDs.

Unlike many syntheses of QDs, such as electrode deposition[35], photocatalytic reduction[36], and sol-gel method[37], our study uses a novel technique to fabricate CuxO QDs via successive ionic layer adsorption and reaction (SILAR) method[38]. SILAR is a simple fabrication methodology that combines successive layer adsorption with chemical redox reaction. The typical process involves successively immersing the TiO2 materials in and H2O2 aqueous solutions successively for as many cycles as desired to achieve a uniform deposition of CuxO QDs. Not only is the overall process environmentally friendly, cost-effective, and can be carried out in normal atmospheric pressure and room temperature, but the density of QDs can also be easily controlled by merely varying the number of deposition cycles.

In this study, we report the preparation of nanoporous anatase TiO2 films on transparent conductive fluorine-doped tin oxide (FTO) substrates by screen-printing and the subsequent deposition of CuxO QDs on the TiO2 films via SILAR. The number of deposition cycles, and thus QD loading density, was varied to investigate the effect on the photoelectrochemical properties of nanocrystalline TiO2 electrode and derive the optimal density of CuxO QDs that enhanced the photoelectrochemical activity. The sample was also recycled 7 times to demonstrate its improved absorbance in the visible range and enhanced photoelectrochemical properties.

Experimental

Preparation of TiO2 films

All the chemical reagents were used as received. The colloidal were prepared by hydrolysis of titanium tetraisopropoxide as described by elsewhere[39]. The TiO2 films were synthesized directly on transparent fluorine-doped tin oxide (FTO, TEC-8, LOF) conducting glass substrates by screen-printing, followed by calcining the samples at 500 °C for 30 min in air.

Immobilization of CuxO quantum dots onto TiO2 films

The CuxO QDs were deposited onto the TiO2 photoanodes in situ by successive SILAR cycles. For CuxO deposition, the TiO2 photoanodes were successively immersed in two different solutions for 5 min in each solution, first, in and second in H2O2 aqueous solutions. Following each immersion, the TiO2 photoanodes were rinsed with deionized water. The were resulting from Cu(AC)2 and NH3 H2O. These sequential steps are considered as one SILAR cycle. The SILAR cycle was repeated for 0, 3, 5, 7, and 9 times. Samples are denoted as S0, S3, S5, S7, and S9, respectively. The relevant reactions for preparing CuxO QDs can be written as follows[40]:

Characterization techniques

Microstructures and the crystallinity of CuxO sensitized TiO2 films were characterized by field-emission scanning electron microscopy (FE-SEM, Hitachi, S4800), transmission electron microscopy (TEM), high resolution transmission electron microscopy (HR-TEM) (TEM, JME-2100, Japan), and X-ray diffraction (XRD, MAC, M18XHF) using CuKα radiation (1.54 Å). Absorption spectra were obtained by a UV-Vis spectrophotometer (UV-2550, Shimadzu). Photoluminescence (PL) and Raman spectra were recorded by a micro-Raman spectroscopy system (Renishaw PLC in Via-Reflex). X-ray photoelectron spectroscopy (XPS, Thermo, ESCALAB 250) was employed to analyze the surface composition of the samples. The elemental distributions and concentrations were analyzed by Energynergy dispersive spectroscopy (EDS, Oxford Inca) accompanying the FE-SEM.

Photoelectrochemical measurements

Photoelectrochemical measurements were carried out in a three-electrode configuration with the as-prepared sample as the working electrode, Pt foil as the counter electrode, and saturated Ag/AgCl as the reference electrode[41]. A 0.1 M Na2SO3 aqueous solution was used as the electrolyte. Photocurrent measurements were taken as a function of voltage by an electrochemistry workstation (CHI 660D, Shanghai Chenhua instrument). The working electrode was illuminated by a 300 W Xe lamp. An ultraviolet cutoff filter was inserted in between the light source and the quartz cell to exclude UV light with wavelength below 420 nm. Photoresponses of the different samples were determined by using a light on-off cycle of 60 s at a bias of 0 V versus the Ag/AgCl electrode.

Results and Discussion

XRD patterns

Figure 1 shows XRD patterns of S0 and S9. The XRD pattern of the substrate (FTO) was used as a reference. After the TiO2 products were formed on the FTO substrates, all FTO diffraction peaks became weaker. Both S0 and S9 samples have similar patterns, in that they display three peaks at 2θ = 36.02°, 62.56°, and 69.01°. These peaks can be attributed to the (101), (002), and (301) diffraction peaks of anatase TiO2, respectively, as they are in good agreement with the standard pattern of anatase TiO2 (PDF#65-1119). In addition, the diffraction peaks of CuxO QDs are not observed in S9, implying the low content and small size of QDs. Therefore, we can conclude that the formation of CuxO QDs does not influence the crystalline structure of the TiO2 electrodes.

Figure 1

XRD patterns of S0, S9, and FTO substrate.

Morphological analysis

Figure 2 presents SEM images of TiO2 films coated with CuxO QDs. The magnification and high magnification SEM images (Fig. 2a and b) show that the TiO2 film is porous and uniform. Figure 2c–f shows SEM images of the TiO2 after depositing 3, 5, 7, and 9 cycles of CuxO QDs. No morphological changes were observed among the samples deposited with CuxO QDs, due to the low content and small size of the CuxO QDs; however, EDS data of S7 (Fig. 2(g)) reveal that the sample consists of Ti, O, and Cu elements, confirming the presence of CuxO QDs.

Figure 2

SEM images of S0 (a) close-up view (b) high resolution view (c) S3, (d) S5, (e) S7, (f) S9; and (g) EDS spectrum of S7.

TEM and SAED characterization was employed to examine the crystal structure and growth direction of TiO2 as well as the particle size of the CuxO QDs. Figure 3(a) shows that CuxO QDs were in contact with the TiO2 film. The size of TiO2 nanoparticles and CuxO QDs were approximately 34 nm and 10 nm, respectively. When the imaging was focused around the TiO2 and TiO2/CuxO interface, various crystalline facets were clearly observed, as shown in Fig. 3b and c. The larger crystalline region in Fig. 3b was confirmed to be TiO2. The observed lattice plane spacings are 0.17 nm and 0.34 nm corresponding to the (211) and (110) planes of anatase TiO2. Above the anatase TiO2 crystallites, we also observed the interplanar spacings of 0.21 and 0.23 nm (Fig. 3c), which could be indexed to elementary Cu (111) (d = 0.21 nm), CuO (111) (d = 0.23 nm), or Cu2O (002) (d = 0.21 nm). In addition, the SAED pattern in Fig. 3d demonstrates that the TiO2 electrodes exhibit a single crystal structure.

Figure 3

(a) TEM images of CuxO/TiO2 (S7), (b) HRTEM of TiO2 (S0), (c) HRTEM of CuxO/TiO2 (S7), and SAED pattern of the same CuxO/TiO2 in part (a).

XPS analysis

In order to clarify the elemental composition and valence state of CuxO QDs, XPS characterizations was conducted. As shown in Fig. 4a, the general survey spectrum for CuxO QDs modified TiO2 electrodes contains Cu, O, Ti, and C elements. The small amount of carbon could have resulted from adventitious hydrocarbons from the XPS instrument itself and can be taken as the standard signal for the correction of other peaks[42]. From the Ti 2p spectrum (Fig. 4b), two main peaks at bonding energies of 458.6 and 461.4 eV were assigned to Ti 2p3/2 and Ti 2p1/2, respectively[43, 44]. Figure 4c shows a representative Cu 2p core level XPS spectrum with two peaks at 933.2 and 953.0 eV for atmospheric conditions at room temperature, and the oxidation products include Cu2O and CuO[45, 46]. Furthermore, two fitted peaks (Fig. 4d) from the O 1 s spectrum are observed around 529.7 and 531.9 eV, which can be assigned to the lattice oxygen and surface hydroxyl oxygen of TiO2 [47], respectively.

Figure 4

XPS spectra of S7: (a) Survey spectrum (b) Ti 2p, (c) Cu 2p, and (d) O 1s.

UV-Visible absorption spectra

Figure 5 shows the absorption spectra of TiO2 electrodes sensitized with different SILAR cycles of CuxO QDs. The average absorbance can be calculated and the results are listed in Table 1. It can be seen that with an increase in the number of SILAR cycles, the absorbance increases at wavelengths 400 to 700 nm. This can be attributed to the SPR of Cu QDs and narrow band gap of CuO and Cu2O[48]. In addition, the red-shift of the absorption edge of CuxO/TiO2 is due to the broadening of size distribution of CuxO QDs[49]. Based on the UV-Visible absorption spectra, a plot of (αhv)2 versus energy (hv) is shown in Fig. 6, and the Eg values of different CuxO samples are shown in Table 1. It can be seen that the absorption bands of CuxO/TiO2 show large variation, which change from 2.90 to 2.50 eV. The band gap of CuxO/TiO2 (S9) was 2.50 eV, which was smaller than that of TiO2 (2.90 eV). These results suggest that the formation of the CuxO/TiO2 nanostructures decreased the recombination of photogenerated electrons and holes and improved the photoelectrochemical ability of the TiO2 electrodes.

Figure 5

UV-Visible absorption spectra of CuxO/TiO2 prepared with different SILAR cycles.

Table 1

The average absorbance with 400–700 nm, band gap, and photocurrent values of TiO2/CuxO electrodes.

Samples	Average absorbance (a.u.)	Band gap (eV)	Photocurrent values (dark) (μA/cm2)	Photocurrent values (light) (μA/cm2)
S0	0.68	2.98	37.60	168.88
S3	0.82	2.75	97.47	248.95
S5	0.89	2.69	123.79	390.98
S7	0.92	2.63	166.74	500.01
S9	0.94	2.50	145.30	424.15

Figure 6

Plots of (αhv)2 versus energy (hv) for CuxO/TiO2 prepared with different SILAR cycles.

PL spectra

To investigate charge transfer between photogenerated electctrons and hole pairs, photoluminescence (PL) emission spectroscopy was used to measure the recombination of free charge carriers. The emission peaks at 420 and 475 nm are assigned to exciton-casued PL resulting from band edge free excitons and defects of TiO2 [50]. PL peak intensity correlates directly with the defect densities in materials. The higher PL intensity typically indicates a higher recombination rate of the photo-generated electrons and holes[51]. As shown in Fig. 7, the PL intensity of CuxO/TiO2 reveals a significant decreases with increasing CuxO QDs. This is due to a decrease of radiative recombination processes[52]. When the CuxO QDs are deposited on TiO2 electrodes, TiO2 can easily bond with the CuxO QDs to form the CuxO/TiO2 composites. The photo-induced electrons can be trapped in the Cu 2p energy level below the conduction band in the CuxO/TiO2 composites, which inhibit the recombination of electron-hole pairs. The intensity of the peaks at 420 and 475 nm are the lowest for S7, which exhibit high quantum efficiency and higher photoelectrochemical properties.

Figure 7

PL spectra of different samples.

Photoelectrochemical studies

Figure 8 shows the time-dependent photocurrent curves of CuxO/TiO2 under visible light illumination. It is generally known that transient photocurrent always reflect the transfer and separation of photoinduced charge carriers under intermittent illumination. As the light is turned on, the photocurrent values increase while the photocurrent values decrease rapidly as the light is turned off. This suggests that all samples have good reproducibility. In addition, photocurrents increase with more SILAR cycles, which indicate that the photocurrent of CuxO/TiO2 have a significant enhancement compared to bare TiO2. Moreover, after 7 SILAR cycles, the sample shows the highest photocurrent value of ca. 138 μA/cm2, which is about 13 times higher than that for bare TiO2. Nevertheless, when the SILAR cycles increase to 9, the photocurrent value decreases to ca. 120 μA/cm2. The increase in photocurrent may be attributed to the stronger SPR effect of CuxO QDs, which improves the light absorption of TiO2. With more than 9 SILAR cycles, the aggregation of CuxO QDs lead to a large particle size of CuxO QDs, which could block the surface active sites of TiO2 and act as potential barrier of charge transfer, resulting in a decrease of the photoelectrochemical properties[53-56].

Figure 8

Transient photocurrents of CuxO/TiO2 prepared with different SILAR cycles.

Figure 9 shows the LSV curves of the different samples in the dark and under light irradiation. Photocurrent values are shown in Table 1. The photocurrents of the CuxO/TiO2 samples improved compared with that of bare TiO2, suggesting that the CuxO/TiO2 exhibit a stronger ability to separate photo-generated electron-hole pairs. The CuxO/TiO2 prepared with a different number of SILAR cycles (0, 3, 5, 7 and 9 times) exhibited photocurrent values of 168.88, 248.95, 390.98, 500.01, and 424.15 μA/cm2 at 1.0 V (vs Ag/AgCl) under visible light irradiation, respectively. Clearly, photocurrent densities of the CuxO/TiO2 first increase then decrease with increasing the SILAR cycles. The S7 showed the strongest photocurrent value, and exhibits the best photoelectrochemical property, which is consistent with the PL results. When 9 SILAR cycles were used, the CuxO QDs aggregated to form a compact granular morphology, resulting in a lower surface area and reduced photocurrent[57].

Figure 9

LSV spectra of CuxO/TiO2 electrodes in dark and under visible light irradiation.

Conclusions

In summary, CuxO QDs are deposited on the nanoporous anatase TiO2 films by a screen-printing method, followed by successive ionic adsorption and reaction (SILAR). The microstructure, morphology, and loading amounts of the CuxO QDs on the TiO2 films are controlled by changing the number of SILAR cycles. The CuxO/TiO2 absorbs more light and exhibits enhanced photoelectrochemical properties compared to bare TiO2. Moreover, under visible light illumination, the TiO2 sensitized with 7 SILAR cycles of CuxO QDs shows the best photoelectrochemical properties, where the photocurrent density is increased to 500.01 μA/cm2, 2.96 times higher than the bare TiO2 electrode with 168.88 μA/cm2. The superior photoelectrochemical properties of the CuxO/TiO2 nanostructures could be ascribed to the large surface area of nanoporous TiO2 electrode and the SPR effect of CuxO QDs. The electrode design of CuxO/TiO2 will be beneficial for application of solar energy conversion and wastewater degradation.