Improved Performance of CdS/CdTe Quantum Dot-Sensitized Solar Cells Incorporating Single-Walled Carbon Nanotubes
Improved Performance of CdS/CdTe Quantum Dot-Sensitized Solar Cells Incorporating Single-Walled Carbon Nanotubes
Bulletin of the Korean Chemical Society. 2014. Oct, 35(10): 2895-2900
Copyright © 2014, Korea Chemical Society
  • Received : March 25, 2014
  • Accepted : June 03, 2014
  • Published : October 20, 2014
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About the Authors
Hokyeong, Shin
Taehee, Park
Jongtaek, Lee
Junyoung, Lee
Jonghee, Yang
Jin Wook, Han
Whikun, Yi

We fabricated quantum dot-sensitized solar cells (QDSSCs) using cadmium sulfide (CdS) and cadmium telluride (CdTe) quantum dots (QDs) as sensitizers. A spin coated TiO 2 nanoparticle (NP) film on tin-doped indium oxide glass and sputtered Au on fluorine-doped tin oxide glass were used as photo-anode and counter electrode, respectively. CdS QDs were deposited onto the mesoporous TiO 2 layer by a successive ionic layer adsorption and reaction method. Pre-synthesized CdTe QDs were deposited onto a layer of CdS QDs using a direct adsorption technique. CdS/CdTe QDSSCs had high light harvesting ability compared with CdS or CdTe QDSSCs. QDSSCs incorporating single-walled carbon nanotubes (SWNTs), sprayed onto the substrate before deposition of the next layer or mixed with TiO 2 NPs, mostly exhibited enhanced photo cell efficiency compared with the pristine cell. In particular, a maximum rate increase of 24% was obtained with the solar cell containing a TiO 2 layer mixed with SWNTs.
As a third-generation photovoltaic cell, quantum dot-sensitized solar cells (QDSSCs) have been studied by many research groups due to their low production cost and high energy conversion efficiency. 1 Typical QDSSCs consist of a QD-modified photo-anode (working electrode) and a counter electrode (CE) separated by a salt electrolyte. QDs, which are nanoparticles made of semiconductor materials whose physical and chemical characteristics are size dependent, have been introduced as sensitizing materials because of their excellent opto-electronic properties. Notable properties of QDs include tunability of band gap energy, narrow emission spectrum, broad excitation spectrum, good photostability, high extinction coefficient, and multiple exciton generation (MEG). 1,2 Over the past few years, cadmium chalcogenide (CdX, X=S, Se or Te) QDs have attracted attention due to their distinguished properties such as easy fabrication, tunability by size control, 3,4 and efficient MEG. Specifically, CdSe and CdS are mainly used in CdX QD research. 1 CdTe with a bulk energy band gap of 1.54 eV is well matched with the solar light spectrum, 5 which indicates that the lightabsorption of CdTe would extend to the near infrared region and that the electron injection rate from CdTe QDs to TiO 2 would be faster than CdSe QDs of the same size. 6 CdTe has the second highest extinction coefficient among CdX QDs, 7 with CdS having the highest extinction coefficient. Bulk CdS has a band gap of 2.34 eV and a relatively conductive band edge of −4.14 eV. 8 Therefore, CdS energy bands form a cascade structure with TiO 2 and CdTe energy bands. An appropriate cascade structure helps enhance the separation of electron-hole pairs. 9,10 Additionally, a CdS/CdTe co-sensitizer would have an advantage of enhancing light harvesting capability. 11
For CdX QDSSCs, sulfide/polysulfide (S 2− /S n 2− ) is commonly used as the electrolyte. Sulfide ions are capable of scavenging photo-generated holes, and the presence of polysulfide electrolyte is necessary for the stability of metal chalcogenide-based QDSSCs. 12,13 Typically, the photo-anode consists of a mesoporous TiO 2 layer attached to the transparent conducting oxide glass. 13 In general, a Pt CE has been used in CdX QDSSCs; however, it was recently demonstrated that Au is a better CE material for QDSSCs due to its inertness. QDSSCs using Au as the CE have shown better performance compared to cells using Pt. 5,14
Single-walled carbon nanotubes (SWNTs) have the potential to improve the performance of solar cells. In air, O 2 molecules adsorbed on the surface of SWNTs withdraw electrons, which enrich holes in SWNTs. 15 Zhong Z. and coworkers 16 reported that SWNTs act as efficient hole-transfer agents when used as a p-type semiconducting material. The use of SWNTs in solar cells could promote separation of photo-generated electron-hole pairs.
In this work, tin-doped indium oxide (ITO)/TiO 2 and fluorine-doped tin oxide (FTO)/Au film were used as the photo-anode and CE, respectively, and CdS and CdTe QDs were adopted as sensitizers of QDSSCs. The appropriate alignment of each material was designed based on consideration of the energy band edge ( Fig. 1 ). 5,8,17 SWNTs were mixed with TiO 2 paste or were sprayed between the QD layers. The effect of SWNTs introduced into CdTe/CdS QDSSCs was studied by the photocell efficiency (PCE) and impedance parameters.
Preparation of CdTe QDs. CdTe QDs were synthesized following a previously reported aqueous synthesis method. 18,19 The process was comprised of three steps: preparation of NaHTe and cadmium ion solutions and growth of CdTe QDs. Te and NaBH 4 (molar ratio 1:4) powder were dissolved in deionized water. The mixture was placed in a refrigerator for about 2 hrs. As the chemical reaction took place, as shown below, a NaHTe solution was obtained.
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For preparation of the cadmium ion solution, CdCl 2 was dissolved in deionized water, and thioglycolic acid (TGA) was added to the solution as a stabilizer. Freshly prepared NaHTe solution was added to the CdCl 2 solution, and the pH was adjusted to 11 using 1 M NaOH solution, at 100 °C under a N 2 atmosphere. The molar ratio of Cd 2+ :TGA:HTe was fixed at 2:5:1. After NaHTe had been added, growth of QDs began, and different particle sizes were obtained by controlling the reflux time.
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(a) Structure schematic and (b) energy band diagram for the CdS/CdTe quantum dot-sensitized solar cell.
Preparation of Cell Electrodes. The porous TiO 2 photoanode was prepared by spin coating TiO 2 paste onto a 2.5 × 2.5 cm 2 ITO glass plate, followed by sintering at 450 °C for 30 min. The TiO2 colloidal paste was prepared by mixing TiO 2 powder (Degussa P25), acetylacetone, deionized water, Triton X-100, and polyethylene glycol (PEG). 20 A successive ionic layer adsorption and reaction (SILAR) method was used to deposit CdS QDs onto the TiO 2 film. 11 The TiO 2 film was dipped into an ethanol solution containing Cd(NO 3 ) 2 (0.5 M) for 5 min followed by washing with ethanol and was then dipped for another 5 min into a Na 2 S methanol solution (0.5 M) followed by washing again with methanol. These two steps were termed one SILAR cycle, and the processes were repeated 8 times followed by annealing at 400 °C for 15 min. A direct adsorption (DA) method was used to deposit CdTe QDs onto the film. 3,19 One DA cycle consisted of dipping the TiO 2 /CdS film into a colloidal solution of presynthesized CdTe QDs for 30 min at 50 °C and drying in ambient atmosphere. The amount of deposited CdTe QDs was increased by repeating the cycle. The active area of the cell was 0.16 cm 2 . CEs were prepared by sputtering Au onto the FTO glass.
Treatment of Cells Incorporating SWNTs. SWNTs were dispersed in ethanol by sonication. Two methods were used to incorporate SWNTs into cells: using a TiO 2 paste mixed with SWNTs (SWNTs/TiO 2 powder = 0.005 wt %) and spraying SWNTs (SWNTs 16 μg/cm 2 ) onto the surfaces of the CdS and CdTe QD layers and the Au CE.
Assembly of Cells. The photo-anode and Au CE were sandwiched between 100 μm thick polymer sheets in order to prevent evaporation of the electrolyte. Polysulfide electrolyte solution was prepared by dissolving Na 2 S (0.5 M), S powder (0.125 M), and KCl (0.2 M) in water/methanol (volume ratio, 7:3) solution. A co-solvent was used to decrease the surface tension of the electrolyte solution, leading to smooth penetration of the electrolyte into the mesoporous TiO 2 matrix. 11 The electrolyte was inserted into the cell via a syringe, filling the space between the two electrodes.
Results and Discussion
Figure 2(a) shows the absorption spectrum of CdTe QDs in colloidal solution in the ultraviolet-visible light wavelength range. In the visible light area, the absorption maxima for samples 1-3 were observed at 484, 498, 515 nm, respectively. A red shift of the absorption spectra was observed with increasing QD growth time. The CdTe QD size could be calculated with the following equation: 7
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in which D (nm) is the size of a CdTe QD and λ (nm) is the wavelength of the first excitonic absorption peak of each sample in the visible wavelength range. Calculated QD sizes from the equation were 1.84, 2.29 and 2.71 nm for the three samples, respectively. Consequently, a red shift occurred with increasing QD size because of the quantum confinement effect. Figure 2(b) shows typical fluorescence spectra of CdTe QDs (at an excitation wavelength of 430 nm). In the spectra, the full width at half maximum (FWHM) values of the samples were 0.26, 0.31, 0.18 eV for 40, 80 and 120 min samples, respectively, which indicates a narrow size distribution and high monodispersity for the synthesized CdTe QDs. 21 A 40 min QD growth time was used for our experiment samples because the driving force for faster injection of electrons into TiO 2 increased as the size of the QDs decreased. 3
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(a) Ultraviolet-visible light absorption and (b) photo-luminescence spectra of CdTe QDs.
The scanning electron microscope (SEM) image in Figure 3(a) shows a compact surface layer for the TiO 2 /CdS(8)/CdTe(5) film. Cd and Te characteristic peaks are clearly seen in the energy dispersive spectrum in Figure 3(b) , which confirms that CdTe QDs successfully assembled on the surface of the TiO 2 /CdS(8) film via the DA process.
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(a) SEM image and (b) Energy-dispersive X-ray spectroscopy spectrum of TiO2/CdS(8)/CdTe(5) film.
The photo-current density-voltage ( J-V ) curves of different cell types are shown in Figure 4 . The shapes of the J-V curves for CdS/CdTe QDSSCs were concave upwards, which indicates that the contact resistance between the CdS and CdTe layers was quite large. In fact, the CdS/CdTe structure has significant structural defects at the interface. 22 The combination of CdS/CdTe is structurally imperfect, but CdS/CdTe QDSSCs displayed high cell performance compared to the cell containing only CdTe as a sensitizer. Although the cell without CdS had a relatively low efficiency, the concave downwards curve suggests that the cell has a low contact resistance.
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J-V curves of different cell types. The cells have cosensitive or different deposition cycles.
Performance parameters (open circuit voltage ( V oc ), short circuit current density ( J sc ), fill factor ( FF ), and PCE (η)) of the cells are listed in Table 1 . As mentioned above, because of structural mismatch between CdS and CdTe, FF values of the cell with only CdTe was mostly higher than that of the CdS/CdTe cell. The PCE of CdS/CdTe QDSSCs was higher than for CdTe QDSSCs, which was evident by comparing the incident photon to current efficiency (IPCE) spectra ( Figure 5 ) for the cells. The cell with only CdS had a broad, low intensity, and the cell with only CdTe had a high, narrow intensity. Thus, light harvesting ability was best accomplished with a combination of CdS and CdTe, as manifest by the enhanced spectrum profile for TiO 2 /CdS(8)/CdTe(5). Because of this harvesting ability, J sc values of CdS/CdTe cell was higher than that of cell with only CdTe.
J-Vcurve parameters of cells with CdTe QD sensitizer or CdS/CdTe co-sensitizer with different deposition cycles
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J-V curve parameters of cells with CdTe QD sensitizer or CdS/CdTe co-sensitizer with different deposition cycles
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IPCE spectra of cells with CdS or CdTe or both as sensitizer.
The performance of QDSSCs depended on the deposition cycles for preparing the photo-anode. An effect of the DA cycle on device performance was studied, and an optimum number of cycles was found for CdTe QDs. As the deposition cycles were increased, the PCE of the cell also generally increased. However, the PCE with CdTe QDs decreased with greater than 5 DA cycles. An increase in deposition cycles corresponded to a greater thickness of CdTe QDs. As the thickness of the CdTe layer became too thick, diffusion of charge carriers became difficult and recombination more readily occurred. A photo-anode prepared using 5 DA cycles of CdTe exhibited the best performance in our experiments.
Figure 6 shows J-V curves of CdS/CdTe QDSSCs containing SWNTs, and their parameters are listed in Table 2 . Samples containing SWNTs had higher PCE values compared with the pristine cell (TiO 2 /CdS(8)/CdTe(5)), except for the cell with SWNTs sprayed on the CdTe layer.
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J-V curves of cells with SWNTs.
J-Vcurve parameters for the cell with SWNTs and the pristine cell
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J-V curve parameters for the cell with SWNTs and the pristine cell
The increase in PCE was clearly caused by the increase in FF or J sc values or both, which means that SWNTs act as excellent carrier transfer agents. The PCE of the cell with SWNTs sprayed on the CdS layer increased with increased FF despite a decreased J sc . The SWNT film has a band gap of 0.6 eV with conduction and valence band energies at −4.8 and −5.4 eV vs . vacuum, respectively. 17 Thus, the presence of SWNTs between the CdS and CdTe layers was not appropriate from an energetic point of view, and it was possible to predict that SWNTs would act as barriers, as demonstrated by the reduction of J sc for such cells compared with the pristine cell. However, as mentioned above, contact resistance between the CdS and CdTe layers was poor, and the presence of SWNTs could partially make up for the contact resistance, leading to an increase in FF, a reason for the increase in PCE. Only the cell with SWNTs sprayed on the CdTe layer exhibited a decrease in PCE compared with the pristine cell. In this case, all of the factors decreased, which suggests that SWNTs largely act as barriers in the cell. In cells with SWNTs sprayed on the Au CE or cells containing TiO 2 mixed with SWNTs, significant increases in J sc and FF values were observed, a reflection of SWNTs acting as good carrier transfer agents at each electrode.
In addition, characterization of QDSSCs could be more rigorously analyzed using impedance data. Figure 7 and Table 3 show electrochemical impedance spectroscopy (EIS) spectra and the details for each solar cell, respectively. All of the plots exhibited Gerischer impedance, indicating low charge recombination resistance. 23 In fact, resistance between the CE and electrolyte (R 1 ) was not calculated from the EIS analysis program because the resistance of the active layers (R 2 ) was relatively large. The plots ranging from 100 KHz to 1 Hz provided information about charge transfer between layers. In the Gerischer model, the smaller semicircle represents lower resistance of active layers. Both the cell containing TiO 2 mixed with SWNTs and the cell with SWNTs sprayed on the Au CE clearly show smaller semicircles compared with the pristine cell. And both the cell with SWNTs sprayed on the CdS layer and the cell with SWNTs sprayed on the CdTe layer show slightly larger semicircles compared with the pristine cell due to resistance by SWNTs to acting as barriers.
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Nyquist plots of cells with SWNTs. Insets represent the circuit model of our cell and Bode plots, respectively.
EIS spectral parameters
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EIS spectral parameters
The f max values were obtained from Bode plots, and capacitance values (constant-phase elements (CPE2)) were calculated from the formula, CPE2=1/2πf max R 2 . The cell containing TiO 2 mixed with SWNTs had the largest capacitance and the cell with SWNTs sprayed on the CdTe layer, which had worst performance, had the smallest capacitance.
As noted above, spraying SWNTs on the CdS layer was energetically unfavorable. This finding was confirmed by the increase in the R 2 value. On the other hand, both the cell containing TiO 2 mixed with SWNTs and the cell with SWNTs sprayed on the Au CE show the decrease in the R 2 values, which indicate that SWNTs acting as good carrier transfer lowered the resistance of the active layers.
In the cell containing TiO 2 mixed with SWNTs, SWNTs could act as barriers due to the increased resistance of TiO 2 itself (R s ). However, the PCE increased with the increase in J sc , indicating that SWNTs could also act as good carrier transfer agents.
Consequently, SWNTs can act as either barriers or excellent carrier transferers. In the cell containing TiO 2 mixed with SWNTs, the ability of SWNTs to act as carrier transfer agents surpassed their barrier effect. The cell also had a long electron lifetime (τ e ), which indicates a low recombination rate of carriers between electrodes. The cell with SWNTs sprayed on the Au CE also had a long electron lifetime compared with pristine cell. The cell with SWNTs sprayed on the CdTe layer had an increased R 2 value and the PCE decreased from reduction of the FF value; however, the electron lifetime of the cell increased. In this cell, electronhole pairs were relatively well separated, but resistance in the cell could be high. Although cells with SWNTs sprayed on the CdTe layer or the Au CE had the same electron lifetimes and SWNTs present in the electrolyte, the presence of SWNTs between CdTe and the electrolyte made SWNTs act as barriers. In other words, though electron-hole pairs were well separated by presence of SWNTs, cell performance could depend on where SWNTs were in the cell.
CdS/CdTe QDSSCs were fabricated by SILAR and DA methods. In addition, application of SWNTs in cells was assessed for performance improvement. SWNTs could act as either a barrier or excellent carrier transfer agents and when the ability of SWNTs to act as carrier transfers surpassed their barrier effect, cell performance could be improved. With the exception of the cell with SWNTs sprayed on the CdTe layer, the performances of the other cell fabrications improved. In particular, the cell containing TiO 2 mixed with SWNTs exhibited a 24% increase in PCE compared with the pristine cell, which suggests that SWNTs acted as good carrier transfer agents that enhanced the performance of the solar cell. We expect that various applications of SWNTs to cell fabrication could be a significant factor in improving performance parameters such as energy level and resistance.
This study was supported by the National Research Foundation of Korea funded by the Ministry of Education, Science, and Technology (2011-0028850).
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