Research Article | Open Access
Lin Li, Xiaoping Zou, Hongquan Zhou, Gongqing Teng, "Cu-Doped-CdS/In-Doped-CdS Cosensitized Quantum Dot Solar Cells", Journal of Nanomaterials, vol. 2014, Article ID 314386, 8 pages, 2014. https://doi.org/10.1155/2014/314386
Cu-Doped-CdS/In-Doped-CdS Cosensitized Quantum Dot Solar Cells
Cu-doped-CdS and In-doped-CdS cosensitized (Cu-doped-CdS/In-doped-CdS) quantum dot solar cells (QDSCs) are introduced here. Different cosensitized sequences, doping ratios, and the thickness (SILAR cycles) of Cu-doped-CdS and In-doped-CdS are discussed. Compared with undoped CdS QDSCs, the short circuit current density, UV-Vis absorption spectra, IPCE (monochromatic incident photon-to-electron conversion), open circuit voltage, and so on are all improved. The photoelectric conversion efficiency has obviously improved from 0.71% to 1.28%.
Recently, introducing dopants to modify the properties of semiconductor nanocrystals was applied to improve the power conversion efficiency of QDSCs. Among so many quantum dot materials, CdS is an important II-VI compound semiconductor and its band width is 2.42 eV at room temperature . CdS has good optical properties in the visible light region. For the conduction, band energy level of CdS is above the conduction band of TiO2 and it is good for generation and delivery of electrons. CdS also has large extinction coefficient and photochemical stability. Moreover, we can control the size of CdS quantum dots to obtain wide absorbed spectrum [2–9]. Doping optically active transition metal ions was possible to modify the electronic and photophysical properties of QDs. For example, Lee and his coworkers prepared a cosensitized TiO2 electrode by CdSe and Mg-doped-CdSe quantum dots (QDs) to broad spectrum in visible region. The power conversion efficiency of the cosensitized QDs photoelectrochemical solar cells (PECs) showed 1.03%, which was higher than that of individual QDs-sensitized PECs. The incident-photon-to-current conversion efficiency of the cosensitized PECs showed absorption peaks at 541 and 578 nm corresponding to the two QDs and displayed a broad spectral response over the entire visible spectrum in the 500–600 nm wavelength domains . Also, Santra and Kamat employed Mn2+ doping of CdS and they have now succeeded in significantly improving QDSC performance. QDSC constructed with Mn-doped-CdS/CdSe deposited on mesoscopic TiO2 film as photoanode, Cu2S/graphene oxide composite electrode, and sulfide/polysulfide electrolyte deliver power conversion efficiency of 5.4% . They both applied metal ions modifying semiconductor quantum dot to get high , , and absorption peaks. However, the majority of doping was limited to single doping.
In this paper, we double doped the quantum dot sensitizer, introduced two levels , and doped the CdS quantum dot with Cu, In. Compared with undoped CdS QDSCs, the short circuit current density, UV-Vis absorption spectra, IPCE (monochromatic incident photon-to-electron conversion), open circuit voltage, and so on are all improved. The photoelectric conversion efficiency has obviously improved from 0.71% to 1.28%. Compared with single doping CdS QDSCs, the short circuit current density also improved.
2. Materials and Methods
2.1. TiO2 Films
TiO2 thin films were prepared on FTO conductive glass by screen printing method and then annealed for 30 minutes at 450°C. The thickness of TiO2 film was about 7~8 μm and the working area was . Then Cu, In had been doped in quantum dots by SILAR method (successive ionic layer adsorption method).
2.2. Preparation of Cosensitized TiO2 Electrode with Cu-Doped-CdS and In-Doped-CdS Quantum Dots
First, 0.1 M Cd(NO3)2 ethanol solution was prepared with the Cu source (CuCl2) added into the Cd(NO3)2 ethanol solution, forming a precursor solution of cation. 0.1 M Na2S methanol solution was prepared as the precursor solution of anionic S2−. To obtain Cu-doped-CdS quantum dots, the TiO2 photoanode was immersed into Cd(NO3)2 and CuCl2 hybrid ethanol solution for 5 min, cleaned with alcohol and dried with nitrogen, and then immersed it into Na2S methanol solution for 5 min, cleaned with methanol and dried with nitrogen. After doing this, the TiO2 film was deposited by a layer of Cu-doped-CdS quantum dots. Similarly, obtaining In-doped-CdS quantum dots is by changing the Cu source with In source (InCl3).
2.3. Counter Electrode
Two layers of the mixed solution of chloroplatinic acid and isopropanol are coated on the conductive surface of FTO glass. Then put the Pt electrode into the muffle furnace sintering at 450°C for 30 min, cooled to 100°C and taken out, sealed with plastic wrap. The electrolyte of the solar cell is inorganic polysulfide electrolyte (0.5 M Na2S, 2 M S and 0.2 M KCl).
3. Results and Discussions
For explaining the properties of Cu-doped-CdS and In-doped-CdS cosensitized QDSCs better, firstly, we discuss Cu-doped-CdS QDSCs and In-doped-CdS QDSCs in our previous experiments briefly.
Figure 1(a) was the curves of Cu-doped-CdS QDSCs. As we can see from it, compared with undoped CdS QDSCs, the short circuit current density of Cu-doped-CdS QDSCs has a significant improvement. The specific parameters were in Table 1. The reasons for this are that by doping Cu, it enhanced the conduction band of CdS QDs  and enhanced the energy level difference of TiO2 conduction band and Cu-doped-CdS conduction band, so that it enhanced the injection power of excitons and then the short circuit current density of Cu-doped-CdS QDSCs has a significant improvement. About In-doped-CdS QDSCs, the improvement was not so significant (Figure 1(b) and Table 2). The enhancement of CdS conduction band inspired us to introduce another higher conduction band to obtain better injection power. Next, we discuss Cu-doped-CdS/In-doped-CdS QDSCs.
3.1. Different Cosensitized Sequences
Figure 2 describes the UV-Vis absorption spectra of undoped CdS quantum dot sensitized TiO2 photoanode and different cosensitized sequences of Cu-doped-CdS and In-doped-CdS quantum dot sensitized TiO2 photo anode. The doping molar molar ratio of Cu is 1 : 100, doping molar ratio of In was 1 : 5, the SILAR cycles of CdS quantum dots was 4, and the SILAR cycles of Cu doped CdS quantum dots and In doped CdS quantum dots were 2, respectively.
As for analysis from Figures 2(a) and 2(b), with Cu, In doped, the absorption spectra of the samples regardless of Cu-doped-CdS/In-doped-CdS (394 nm) or In-doped-CdS/Cu-doped-CdS (377 nm) began to move towards the long wavelength compared with undoped CdS (364 nm) sensitized TiO2 photoanode. And the band gaps of the samples decrease. The band gaps of undoped CdS sensitized TiO2 photoanode, Cu-doped-CdS/In-doped-CdS sensitized TiO2 photoanode and In-doped-CdS/Cu-doped-CdS sensitized TiO2 photoanode are 3.41 eV, 3.29 eV and 3.15 eV, respectively. Among them, the absorption spectra of TiO2/In-doped-CdS/Cu-doped-CdS samples red-shift compared with TiO2/Cu-doped-CdS/In-doped-CdS samples and the exciton absorption peak of TiO2/In-doped-CdS/Cu-doped-CdS sample is 394 nm. Compared with undoped CdS quantum dots, the range of spectral response of double doped CdS quantum dots broaded, in other words the range of spectral response of double doped CdS sensitized TiO2 photo-anode red-shift. When changing the cosensitized sequences, because the color of Cu was darker than the color of In, the color of the prepared TiO2/In-doped-CdS/Cu-doped-CdS photoanode films was also darker, so that the spectral response range of TiO2/In-doped-CdS/Cu-doped-CdS was wider than the response spectrum range of the TiO2/Cu-doped-CdS/In-doped-CdS.
As we can see in Figure 3 and Table 3, the photoelectric conversion efficiency of undoped CdS QDSCs (SILAR 4 times) was 0.71%, By introduced In-doped-CdS quantum dots, the short circuit current density improved from 5.79 mA/cm2 to 6.49 mA/cm2 and the photoelectric conversion efficiency was also enhanced. Among them, the photoelectric conversion efficiency of TiO2/Cu-doped-CdS/In-doped-CdS QDSCs was higher than TiO2/In-doped-CdS/Cu-doped-CdS QDSCs, reaching 1.13%, and the short circuit current density and the open circuit voltage were both the highest.
The reasons for the increase of the conversion efficiency of the solar cell can be comprehended from two aspects. (1) Compared with undoped quantum dots and Cu-doped-CdS quantum dots, cosensitization of double doped CdS quantum dots can better increase the range and intensity of the absorption spectrum of the solar cell, improve the utilization rate of the incident light, improve the rate of capture of the photons, and increase the photocurrent density and the open circuit voltage, and double doped CdS electrode had lower dark current which was benefited for delivery of the electrons, inhibited for recombination of the electrons, thus ultimately improving photoelectric conversion efficiency of the solar cell. (2) TiO2/Cu-doped-CdS/In-doped-CdS system can form a ladder band structure, as shown in Figure 4. The conduction band and valence band position of the three materials increased in the sequence of TiO2 < Cu-doped-CdS < In-doped-CdS. The ladder structure was in favor of electron delivery and collection, reduced the recombination of electrons, and increased and , and the photoelectric conversion efficiency of the solar cell increased. For TiO2/In-doped-CdS/Cu-doped-CdS system, because it did not match the level structure, it introduces defects and impurities by doping, which led to the decrease of photoelectric conversion efficiency.
3.2. Doping Ratios and the Thickness (SILAR Cycles)
Figures 5(a) and 5(b) have shown the physical graphs of Cu-doped-CdS/In-doped-CdS quantum dot sensitized TiO2 photoanodes by SILAR 4 cycles ((a) Cu-doped-CdS(2), In-doped-CdS(2)) and 8 cycles ((b) Cu-doped-CdS(4), In-doped-CdS(4)). As can be seen from the graph, with SILAR cycles increasing, the color of the photoanodes was gradually deepened.
The UV-Vis absorption spectra were different for different SILAR cycles of Cu-doped-CdS/In-doped-CdS quantum dot sensitized TiO2 photoanode. Figure 6(a) has shown the UV-Vis absorption spectra of SILAR 4 cycles of Cu-doped-CdS/In-doped-CdS quantum dot sensitized TiO2 photoanode. The doping ratio of Cu : Cd was 1 : 100, doping ratio of In : Cd was 1 : 5, and the SILAR cycles were increased. Figure 6(b) has shown the absorption spectrum which was converted from Figure 6(a) by using formula .
By calculating the band gap of Figure 6(b), we found that the SILAR cycles of Cu-doped-CdS and In-doped-CdS gradually increased. Exciton absorption peak of the samples gradually moved towards the long wavelength and the band gap decreased. The reason was that with SILAR cycles increasing, the Cu-doped-CdS quantum dots and In-doped-CdS quantum dots deposited on TiO2 photoanode gradually increased, which increased the light absorption of the samples and broadened the range of spectral response and the size of Cu-doped-CdS/In-doped-CdS quantum dots also increased, thus finally leading to the samples redshift. Two kinds of doping ratios were discussed here that different SILAR cycles had different effects on of Cu-doped-CdS/In-doped-CdS QDSCs.
The first kind was that doping ratio of Cu : Cd was 1 : 500 and doping ratio of In : Cd was 1 : 5. Figure 7 has shown curves of different SILAR cycles of Cu-doped-CdS/In-doped-CdS QDSCs. Table 4 has shown the performance parameters of different SILAR cycles quantum dot sensed solar cells.
As we can see from Figure 7(a) and Table 4, the short circuit current density and the conversion efficiency of the solar cell were increased with SILAR cycles increasing. When the SILAR cycles increased to 8, the and of the solar cell reached the maximum value (6.98 mA/cm2 and 0.99%). If the SILAR cycles kept increasing, the parameters of the solar cells began to decline. The reason was that when the SILAR cycles was increased, a large number of Cu-doped-CdS/In-doped-CdS quantum dots were generated and deposited onto the TiO2 electrode. These factors made the delivery and collection of electrons more easy, so as to improve the and . However, when the amount of QDs continued to increase, superfluous Cu-doped-CdS/In-doped-CdS accumulated on the TiO2 surface of electrode. This result in a long distance delivery of the photoexcited electrons in different quantum dots. It prolonged the time of electron injection, increased the delivery resistance, and resulted in the decrease of photocurrent density. Moreover, superfluous quantum dots can also block the pores of TiO2, so it was bad for the electrolyte permeating in photoanode and it also hindered delivery of the electrons.
As we can see analysis from upside, the energy levels of TiO2/Cu-doped-CdS(1)/In-doped-CdS(1) are not matching very well and we choose increasing Cu : Cd doping ratio as the Fermi level can go higher into the conduction band. So, we choose that the second kind of doping ratio of Cu : Cd was 1 : 100 and the doping ratio of In was 1 : 5. Figure 7(b) has shown the curve of different SILAR cycles of Cu-doped-CdS/In-doped-CdS QDSCs. Table 5 has shown the performance parameters corresponding to Figure 7(b).
The regular patterns of four pictures were the same, but the photoelectric conversion efficiency of the latter was the highest with 1.28%. So, from the four charts above, we can see that when the doping ratio of Cu : Cd was 1 : 100, the doping ratio of In : Cd was 1 : 5, the SILAR cycles of Cu-doped-CdS and In-doped-CdS were both 4 cycles, and the photoelectric conversion efficiency was the maximum.
At last, we discuss the curves of IPCE of different SILAR cycles of Cu-doped-CdS/In-doped-CdS QDSCs (Figure 8(a)).
As can be seen from the graph, with SILAR increasing, IPCE value and the spectral response range of the solar cell were greatly improved, and the initial absorption wavelength increased from 600 nm (SILAR 4 cycles) to 680 nm (SILAR 8 cycles). As we can see from the curve, with SILAR increasing, the starting absorption wavelength was obviously red-shifted and this was consistent with the ultraviolet absorption spectrum and curves mentioned previously, and the conversion efficiency of the solar cell improved significantly.
The internal electron transfer complex properties of the Cu-doped-CdS/In-doped-CdS quantum dot sensitized solar cell were important parameters. We tested EIS of the samples. Figure 8(b) has shown the EIS spectrum of Cu-doped-CdS/In-doped-CdS QDSCs. Table 6 has shown the spectrum parameters corresponding to the EIS.
It was seen from Table 6 that, with the increase of SILAR cycles, the composite resistance of photoanode and electrolyte was reduced from 6774 Ω to 4960 Ω; in other words, the composite ability of the electrons was enhanced. The delivery probability of electrons between Cu-doped-CdS quantum dots and In-doped-CdS quantum dots increases and this also resulted in an increased probability of electrons. But when SILAR cycles had been 8, the amount of Cu-doped-CdS/In-doped-CdS quantum dots had been larger than that of SILAR 4 cycles, so the photogenerated electrons increases and the short circuit current density increases.
In cosensitized CdS quantum dot sensitized solar cell system, for TiO2/Cu-doped-CdS/In-doped-CdS QDSCs, double doping can increase the range and intensity of the absorption spectrum, improve the utilization rate of the incident light, increase the rate of photons capture, and increase the photocurrent density and open circuit voltage. It has low dark current and highly active electronic delivery, high inhibition of electronic recombination, which ultimately improves the photoelectric conversion efficiency of the solar cell. The conversion efficiency of TiO2/Cu-doped-CdS/In-doped-CdS QDSCs is higher than TiO2/In-doped-CdS/Cu-doped-CdS QDSCs. The system TiO2/Cu-doped-CdS/In-doped-CdS can form a ladder band structure and this kind of ladder type structures is in favor of electron delivery and collection, reduces the recombination center, and increases and , so the photoelectric conversion efficiency of the solar cell is improved. With the ratio of Cu : Cd (1 : 100), In : Cd (1 : 5), SILAR cycles (4) of the conversion efficiency of Cu-doped-CdS/In-doped-CdS QDSCs reached the maximum value.
Conflict of Interests
The authors declare that there is no conflict of interests regarding the publication of this paper.
This work was partially supported by Key Project of Beijing Natural Science Foundation (3131001), Key Project of Natural Science Foundation of China (91233201), Key Project of Beijing Education Committee Science & Technology Plan (KZ201211232040), State 863 Plan of MOST of PR China (2011AA050527), Beijing National Laboratory for Molecular Sciences (BNLMS2012-21), Key Laboratory for Semiconductor Materials Science of Institute of Semiconductors of CAS (KLSMS-1101), State Key Laboratory for New Ceramic and Fine Processing of Tsinghua University (KF1210), Key Laboratory for Renewable Energy and Gas Hydrate of Chinese Academy of Sciences (y207ka1001), Beijing Key Laboratory for Sensors of BISTU (KF20131077208), and Beijing Key Laboratory for Photoelectrical Measurement of BISTU (GDKF2013005).
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