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International Journal of Photoenergy
Volume 2014 (2014), Article ID 835760, 10 pages
Research Article

Improvement of Dye Solar Cell Efficiency by Photoanode Posttreatment

1Consiglio Nazionale delle Ricerche (CNR), Istituto per lo Studio dei Materiali Nanostrutturati (ISMN), Via Gobetti 101, 40129 Bologna, Italy
2Abdus Salam International Centre for Theoretical Physics (ICTP), Strada Costiera 11, 34151 Trieste, Italy
3Vinca Institute of Nuclear Sciences, University of Belgrade, P.O. Box 522, 11001 Belgrade, Serbia
4Consiglio Nazionale delle Ricerche (CNR), Istituto per la Microelettronica e i Microsistemi (IMM), Via Gobetti 101, 40129 Bologna, Italy

Received 11 April 2014; Revised 14 June 2014; Accepted 18 June 2014; Published 9 July 2014

Academic Editor: Maria da Graça P. Neves

Copyright © 2014 Tanja Ivanovska et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.


The basic concept for efficiency improvement in dye-sensitized solar cells (DSSC) is limiting the electron-hole recombination. One way to approach the problem is to improve the photogenerated charge carriers lifetime and consequently reduce their recombination probability. We are reporting on a facile posttreatment of the mesoporous photoanode by using a colloidal solution of TiO2 nanoparticles. We have investigated the outcome of the different sintering temperature of the posttreated photoanodes on their morphology as well as on the conversion efficiency of the DSSC. The DSSCs composed of posttreated photoanodes at 450°C showed an increase in and consequently an increase in efficiency of 10%. Investigations were made to determine the electron recombination via the electrolyte by the OCVD technique. We found that the posttreatment has the effect of reducing the surface trap states and thus increases the electron lifetime, which is responsible for the increase of the overall cell efficiency.

1. Introduction

The introduction of the original concept of the dye-sensitized solar cell (DSSC) in 1991 [1] opened up a new line of studies in the field of photovoltaic research and technology. Since then the DSSC undertook the role of an admirable challenger of the first and second generation of solar cells especially on the subject of low energy production process and the use of low cost materials. However, efficiency wise the DSSC is some way off the market available silicon solar cells [2]. In the past 20 years a lot of work and investigation have been put into developing a more efficient and more stable DSSC, developing new concepts, such as the solid state dye-sensitized solar cells [3, 4], which have most recently evolved into the perovskite solar cells [5, 6]. In addition, there has been a continuous work towards perfecting and optimizing all constituents of the dye cell, especially the mesoporous photoanode [7, 8], the dye [9, 10], and the electrolyte [11] or hole conducting material [12].

The mesoporous photoanode has been employed in all types of sensitized solar cells. Regardless of the sensitizing, electrolyte or the hole conducting material (HCM) best performances were given by DSSC devices with a mesoporous TiO2 film acting as a photoanode. However, one of the challenges of improving the efficiency of the DSSC is enhancing the charge separation and electron transport through the mesoporous photoelectrode. Considering this, it is no wonder that there have been numerous papers published over the years on the improvement of the charge injection and transport in the TiO2.

The basic concept for efficiency improvement in the dye-sensitized solar cells is limiting the electron-hole recombination. One way to approach the problem is to reduce the resistivity of the mesoporous titania in order to improve the photogenerated electron mean free path and consequently reduce the electron-hole recombination probability. Since the mesoporosity of the anatase titania is essential for achieving a high surface area, the most reported methods of improving the conductivity have been the incorporation of carbon nanotubes in the matrix [13, 14], or changing the shape or the surface area of the TiO2 nanocrystals [8, 15], employing TiO2 nanotubes [16], or even the growth of mesoporous TiO2 single crystals [17].

Another approach is to improve the charge separation and reduce the charge recombination dynamics. There have been investigations in using thin layers of insulating metal oxides on top of the surface of the mesoporous TiO2 photoanode in order to block the recombination [18, 19]; layers of some rare-earth elements have been used for surface modification due to favorable change in the electronic properties of the photoanode [20]. The mechanism of surface passivation of the photoanode [21, 22] has also been used in order to reduce recombination by minimizing the effect of surface traps states.

To this date the most common practice of surface treatment in highly efficient DSSC has been the TiCl4 treatment. A lot has been published on the benefits of the TiCl4 surface treatment of the mesoporous films [2325]; however, the interpretation of the mechanism by which the improvement is achieved according to the literature is not fully established. There are several different reasons stated for the improved overall efficiency of the cell. Indeed there are extensive studies [26, 27] reporting on a series of beneficial effects on the recombination and the surface electric field. There is a correlation in the change of the surface morphology as a result of the surface treatment with change in light harvesting and change in transport and recombination dynamics. To summarize, the effects greatly depend on the starting “quality” of the photoanode. It has been reported that the surface treatment is in fact affecting the porosity of the photoanode; thus there is a fine tuning between the porosity of the treated film and the concentration of the TiCl4 solution [25]. Nevertheless, despite the increase in efficiency there are inevitably some experimental difficulties in working with such volatile material that requires some specific safety and laboratory conditions. The common practice of the treatment is dipping each electrode in a TiCl4 water solution held at 70–80°C for 30 min, for best and reproducible results reusing the solution are not advised [24, 28]. Additionally preparing a TiCl4 water solution of the wanted concentration is a very delicate procedure taking into account that diluting TiCl4 can cause formation of HCl fumes. This is a relatively complicated part for a surface treatment of the photoanode considering the simplicity of the preparation and assembly of the complete dye cell.

In this paper we are proposing the use of a simple surface treatment via colloidal solution of TiO2 nanoparticles. We have investigated the effects of the TiO2 photoanode surface treatment by drop casting colloidal solution of 5 nm TiO2 nanoparticles in order to improve the efficiency of DSSC using a time-efficient and low material consumption technique. Spectroscopic and morphological characterizations were performed to investigate the morphological changes of the photoanode. Electrical characterization was performed by means of solar cell current-voltage characterization and open circuit voltage decay measurements. The effects of surface trap states modification as the main reason behind the efficiency changes of the solar cells are discussed.

The aim of this work was to investigate a facile posttreatment of the photoanode that could substitute the TiCl4 treatment, providing a comparable conversion efficiency improvement. In respect with this objective we would like to note that our intention was not focused towards competing with record efficiency DSSCs but rather in understanding the physics behind the obtained results.

2. Materials and Methods

2.1. Colloidal Solution Preparation

The colloidal solution of TiO2 nanoparticles was prepared according to adapted procedure of Rajh et al. [29]. 6 mL of TiCl4 cooled to −20°C was added drop-wise to 200 mL Milli-Q deionized water, held at 4°C under vigorous stirring and then kept at this temperature for half an hour. Due to the formation of HCl during the hydrolysis of TiCl4, the starting pH of the colloidal solution was 0. By applying dialysis (3 days) of the obtained solution against water, which was changed daily, the pH increased to pH ~ 3 and slow particle growth was achieved ( ~ 4.5 nm). The final concentration of TiO2 colloids was determined from Ti(IV)-peroxide complex [30, 31].

All the chemicals except for the ones stated otherwise were acquired from Aldrich, Fluka, and used without further purification.

2.2. DSSCs Preparation

Fluorine doped tin oxide (FTO) substrates (Solaronix TCO 22-7, 7 Ω/sq) were cut in size  cm, washed in successive ultrasonic baths of deionized water, acetone, and isopropanol, and dried with N2 gas flow. The TiO2 mesoporous films were deposited by doctor blade technique. The TiO2 paste was made suspending P25 nanoparticles and PEG 2000 in water, adding Triton X-100 to adjust the viscosity and improve adhesion to the substrate. The films were burned at 450°C for 40 minutes. The thickness of the films was measured by step profilometer. The mesoporous films were kept in air, in dark, and prior to colloidal treatment or before dipping in dye for the untreated electrodes; the films were reburned at 450°C for 15 min to remove any moisture. The colloidal treatment of 0.12 M was drop-casted onto the films; after 1 min the excess was removed and the films were left to dry in air. After drying they were sintered and subsequently cooled down to 80°C before being dipped in to 9 mM solution of N3 dye (Solaronix) in ethanol.

The substrates were left overnight in the dye solution in dark, after which they were washed with ethanol and dried for few minutes in air. The counter electrode was a FTO glass substrate coated with platinum precursor solution (Platisol T, Solaronix) which was burned at 450°C for 20 min. The cell was assembled using 60 μm surlyn spacer. Ionic liquid electrolyte consisting of 0.6 M BMII (1-butyl-3-methylimidazolium iodide), 0.1 M LiI, 0.05 M I2, and 0.5 M TBP (4-tert-butylpyridine) in acetonitrile was inserted in to the cell before complete sealing.

To ensure reproducibility, several batches of cells were made, with at least 2 identical cells per batch with the respective posttreatment.

Investigation was also made on cells prepared using a Solaronix AN-50 electrolyte, with mesoporous photoanode thickness around 8 μm. Where stated, a compact TiO2 layer was deposited via spin-coating a precursor solution of 0.25 M TAA (diisopropoxytitanium bis (acetylacetonate) solution) in ethanol. The compact films were formed by burning the coated substrates at 490°C for 1 hour.

2.3. Spectroscopy

Raman spectroscopy measurements were made with a micro-Raman Renishaw 1000 system with  nm in confocal mode. The acquisition time was 40 s in order to achieve a relatively good signal to noise ratio using a power density of  W/cm2. As a control sample we used a TiO2 mesoporous film made from colloidal paste of P25 nanocrystals.

Absorption measurements were performed on dye solution desorbed from films with and without posttreatment using a JASCO V-550 UV-Vis spectrometer. FTO substrates coated with mesoporous TiO2 films of 1 cm2 were posttreated and the films with the same thickness were dipped and left overnight in a 9 mM ethanol solution of N3 dye. After removing the substrates from the solution and washing off the excess dye with ethanol the films were left to dry in dark and then the dye was desorbed from the films placing them in sealed containers with equal volumes of a 0.1 M solution of NaOH in water.

2.4. Morphology

Thickness measurements were conducted using a step profilometer. Investigation of the thickness and roughness change after colloidal treatment and sintering procedure at 150, 350, and 450°C was performed on samples similar to those used in cell configuration, that is, mesoporous TiO2 films of 1 cm2 deposited onto FTO substrates. The thickness was measured before and after the colloidal treatment.

Scanning electron microscope (SEM) imaging was made to study the surface of the films. The experiments were performed using a LEO 1530 FE-SEM, with a Schottky emitter, operated at 10 keV accelerating voltage, equipped with Everhart-Thornley and In-lens detectors for secondary electrons and Oxford INCA EDS X-Ray spectrometer.

2.5. Device Characterization

Current voltage characteristics of the cells were measured with Keithley 236 source-measure unit under simulated AM1.5 illumination of 100 mW/cm2 Abet Technologies Sun 2000 Solar Simulator. The simulator was calibrated using a silicon reference cell with KG5 filter, and the cells were masked with a sample holder which disabled any light piping effects.

Open circuit voltage decay (OCVD) measurements were performed using a Keithley 2400 SourceMeter, exposing the cell to full sunlight for 5 s to achieve steady state; then the illumination was interrupted by closing the shutter; the time interval between points was 50–100 ms.

3. Results and Discussion

Primarily the investigation on the coating of the photoanode led to establishing that the optimal concentration of the colloidal solution was 0.12 M. Increasing the concentration leads to cracking and peeling of the films. The effect of further decoration of the mesoporous films by successive coatings led to similar results. This was a consequence of tightly packed areas of the TiO2 film surface that were acting as a compact layer which when dried, shrank, causes strain between the formed surface film and the rest of the mesoporous matrix which led to cracking and detaching from the substrate.

Employing a posttreatment of the TiO2 mesoporous photoanode films requires a sintering process in order to remove any residual water or impurities from the mesoporous matrix and film surface, to ensure an efficient dye loading. However, to try and understand the effect of the sintering temperature on the size of the colloidal TiO2 nanocrystals, as well as, on the morphology and porosity of the mesoporous films, we performed systematic investigations using profilometric measurements, Raman spectroscopy, and SEM imaging. Furthermore to establish whether the surface treatment was preliminary changing the effective surface area of the mesoporous photoanode UV-Vis absorption spectra were also measured.

To investigate the nanocrystalline size and morphology of the films with regard to the temperature treatment, 0.12 M of TiO2 colloidal solution was drop-casted onto clean glass slides. The samples were sintered on a hot plate in air for 20 min at different temperatures of 150, 350, and 450°C. As a reference (P25@450°C) a film prepared by using the P25 TiO2 paste (see Section 2.2) was used.

Raman measurements were performed to investigate the crystalline size. The data of the Raman spectra are summarized in Table 1. Estimations of the crystalline size were made according to Kelly et al. [32] experimental results. The analysis was done on the basis of the two most intense anatase Eg modes around 145 cm−1 and 640 cm−1. Extracting the values for the full width half maximum (FWHM) of the peaks ( and , resp.), using the available data, we have observed that by increasing the annealing temperature the size of the nanocrystals increases, as a consequence of nanocrystalline coalescence during the burning process. Here we note that the Raman measurement is essentially a measurement of the crystalline core and not the nanoparticle itself, which in turn could be few nanometers larger.

Table 1: Raman shift- and FWHM- of the of the Eg modes around 145 cm−1 and 640 cm−1 nanocrystalline size () dependence on the sintering temperature, estimated from the FWHM.

The colloidal posttreatment of the mesoporous TiO2 photoanodes induces a slight thickness change. For the films between 13 and 15 μm, we observed an increase of 0.2–0.5 μm, depending on the sample. We are reporting on an interval rather than a fixed thickness increase, as a result of multiple measurements on large number of substrates, also taking into account the difficulty of precise measurement on films of 1 cm2 surface with such roughness. In the further investigations this difference in thickness was compensated by using a few tenths of micron ticker films for the untreated photoanode. Additionally the 2D surface profile did not indicate any difference in the roughness of the samples as seen from Figure 1.

Figure 1: Surface profile of the TiO2 film before (black solid line) and after (purple dotted line) the colloidal posttreatment sintered at 450°C.

Figure 2 shows secondary electrons SEM images of the untreated and posttreated photoanode at 450°C. At this resolution we did not observe any difference between the surface morphologies.

Figure 2: Secondary electrons SEM images of mesoporous TiO2 photoanodes: (a) untreated photoanode; (b) posttreated photoanode sintered at 450°C.

Posttreatment of the photoanode with nanoparticles of around 5 nm can impact the surface volume ratio of the mesoporous films. Any change in efficiency of the DSSC could be attributed to the higher or lower dye loading of the photoanodes. To study the effect of the posttreatment of the photoanode at the investigated temperatures we performed absorption measurements. The UV-Vis absorption spectra of the dye solutions desorbed from untreated and posttreated mesoporous films are shown in Figure 3.

Figure 3: Absorbance of aqueous solution of N3 dye desorbed from TiO2 mesoporous films; untreated photoanode (black solid line) and the posttreated photoanodes at 150°C (red dot-dash line), 350°C (green dotted line), and 450°C (blue dashed line).

It can be observed that there is a small increase (around 5%) in the integrated dye absorption of the films treated at 150 and 350°C; in contrast, the film with surface treatment at 450°C does not show practically any difference in dye absorption with respect to the untreated film. This increase could be expected taking into account the smaller nanoparticle size in the coating films sintered at lower temperatures. The surface treatment in this case is increasing the effective surface area of the mesoporous film, hence increasing the dye absorption. We performed absorption measurements on several batches of untreated and posttreated films to substantiate the observed absorption trend. We found that even though the absorption increase for the low temperature sintered films was small (%), the tendency of this increase and the lack of difference between the untreated and films treated at 450°C remained.

According to the performed measurements and investigations on the posttreated TiO2 films, it can be concluded that the surface treatment is only marginally increasing the thickness of the films without changing the surface morphology and slightly increasing the surface/volume ratio (S/V) only for low temperature annealed samples; while for those sintered at higher temperature (450°C) there is no distinction in the S/V with the untreated films.

Electrical investigations were made on complete 1 cm2 dye-sensitized solar cell devices employing posttreated photoanodes annealed at different temperatures. The aim was to understand the effect that the colloidal posttreatment would have on the efficiency of the cell. The current-voltage characteristics of the prepared cells are shown in Figure 4(a). The parameters of the cells in Figure 4(a) are shown in Table 2. The highest conversion efficiency has been observed in DSSC device with the colloidal treatment of the photoanode sintered at 450°C, showing an improvement in efficiency larger than 10% with respect to the bare one. This improvement is mainly associated with the increase in the photocurrent of the cell. The increase in the depends on the light harvesting efficiency (LHE) and/or the collection and injection efficiency [33]. However, the investigation done on the dye absorption of the photoanode indicates that there are no extra dye molecules absorbed to account for an increase of 10%. Furthermore, taking into account only the UV-Vis absorption measurements one would expect to find a slight increase in the photocurrent (about 5%) for the cells with photoanode treatment at 150°C and 350°C, but in fact the efficiency of these cells is slightly lower than for the cells with the untreated photoanode, as seen from Figure 5.

Table 2: Photovoltaic parameters of the DSSCs with curves shown in Figure 4(a).
Figure 4: Photocurrent density-voltage curves measured under (a) AM 1.5 simulated light intensity at 100 mW/cm2 (1 sun); (b) dark conditions, of DSSCs with untreated photoanode (black full square) and posttreated photoanodes with colloidal treatment at 150°C (red full circle), 350°C (green full triangle), and 450°C (blue full inverted triangle).
Figure 5: Box plots of the dependence of the efficiency of the DSSCs on the photoanode posttreatment temperature.

Apparently there is no significant correlation among the increase in the dye absorption (the surface/volume ratio) and the conversion efficiency increase in these cells, allowing us to eliminate the LHE as a reason for the efficiency increase. Furthermore, low sintering temperature can also affect the conductivity of the TiO2 photoanode by slowing down the charge transport probably as a consequence of the low interconnectivity of the surface nanoparticles to the mesoporous matrix. In the case of low temperature annealed photoanodes, these two effects, LHE increase and worse electron transport would compensate each other, and consequently the cells with untreated and the cells with posttreated photoanode have similar conversion efficiency.

If we consider the difference in the dark current shown in Figure 4(b), we can notice a very slight shift of the dark current onset, hence the increase in the of 0.01-0.02 V. According to Ito et al. [28], the suppression of the dark current for the posttreated photoanodes would indicate a decrease of the electron trap sites on the TiO2 surface. This argument would suggest that the photoanode posttreated at 150°C has the smallest surface trap density. However if we take into account the steepness of the slopes, where the steepest slopes indicate lowest series resistance in the cell [34], we can agree with the assumption that, in fact for the 150°C and 350°C treated samples, there is an issue of the electron transport through the photoanode due to interconnectivity of the nanoparticles, which in turn is suppressing the cell efficiency regardless of the higher dye absorption and possibly lower surface trap sites of these photoanodes.

This is only a qualitative notification since the series resistance depends not only on the electron transport in the photoanode but also on the transport in the FTO substrate, electron transfer across the interface of electrolyte/Pt-FTO, and the electrolyte diffusion time [35]. Nevertheless for the means of this investigation, due to the identical construction elements of the cells and changes only in the photoanode surface, we can deem this result relevant. It is reasonable to suggest that the increase in the /efficiency is a result of either change in the collection or injection efficiency.

In order to have an increase in the rate and efficiency of electron injection from the photoexcited dye into the TiO2 one should observe a downward shift of the conduction band which would result in a lower , since the band edge would become closer to the redox potential. This has not been observed in our investigation taking into account the solar cells characteristics. According to Sommeling et al. this downward shift effect could be balanced out if the surface treatment also strongly reduces the recombination rate; hence no change in the would be recorded [26]. In fact this small increase in the can also be attributed to increase in the quasi-Fermi level of the TiO2 which happens as a consequence of reduced density of surface trap states of the titania [25]. Nevertheless, at this point we can rule out the injection efficiency as the dominant contributor to the improvement in the current density.

We recorded the open circuit voltage decay (OCVD) of the solar cells with and without a surface treatment to investigate in-depth mechanism behind the efficiency improvement in using the colloidal treatment and annealing at 450°C. This technique in principle is a large perturbation technique used to extract information on the recombination time and mechanism in the DSSC. The cell is illuminated under steady state conditions and after the light is switched off, the decay is measured. The OCVD technique is a dark measurement, meaning that the recombination with the dye is not registered. Additionally it is important to point out that OCVD measurement time frame in liquid DSSCs is quite long (>50 ms) so only information on the recombination of the electrons with the oxidized electrolyte is measured. Since the electron transport in the TiO2 mesoporous photoanode has been explained vastly by a trapping/detrapping model [3638], Bisquert and coworkers have developed interpretation of the electron lifetime measured by OCVD that considers not only the trapping/detrapping events in the semiconductor but also the different possibilities for interfacial charge transfer [39, 40]. Figure 6(a) shows the decay curves of the cells prepared with and without the colloidal treatment of the photoanode. It can be seen that the of the cell with posttreated photoanode has a slower initial decay, which continues with time to decay in a similar way as the cell with the untreated photoanode. The steeper decay of the cell with untreated photoanode is an indication of faster recombination of the electrons with the oxidized species in the electrolyte. According to the theory [39] the electron lifetime can be derived from the derivative of the decay curve using the following expression: where is the Boltzmann constant, is the absolute temperature, is the elementary charge, and is the elapsed time.

Figure 6: (a) Open circuit voltage decay curves; (b) electron lifetime as a function of the , of DSSC with untreated photoanode (black full square) and posttreated photoanode with colloidal treatment at 450°C (blue full inverted triangle).

The log - curve has 3 characteristic regions, which give information on the electronic states involved in the recombination process. A constant electron lifetime at high indicates recombination via free electrons in the conduction band; a linear increase in the mid region is a sign of trapping/detrapping events where charge transfer is mainly governed through bulk traps, and a region of inverted parabola in the low indicates a change in the trap states responsible for the recombination from bulk to surface states [40].

From the two curves in Figure 6(b) it is evident that there is a very small region of seemingly constant lifetime at high around 0.7 V. In this region there is practically no difference between the two cells. Analyzing the shape of the curves we can notice that there is a more significant difference in the electron lifetime of the two cells in the region where the charge transport is governed by processes of trapping and detrapping. The relatively linear part up to ~ 0.45 V suggests that, at this position of the Fermi level, the transfer occurs mainly through bulk traps in the TiO2. The onset of the parabolic shape of the curve for the cell with the posttreated photoanode is slightly shifted towards lower potentials which signifies the beginning of recombination processes dominated by surface states. Charge transfer is realized through bulk trap states up to lower values of the potential compared to the cell with the untreated photoanode. It would seem that the mechanism of increasing the efficiency of the cell is in fact determined by the decrease of surface trap states. By modifying the surface trap density one can manage to reduce the charge transport through the surface states and increase the electron lifetime of the TiO2 photoanode and consequently reduce the recombination probability. This increase in the electron lifetime can be the reason behind the efficiency increase.

Since there have been reports in the literature that the recombination kinetics between the TiO2 photoanode and the electrolyte might be dependent on the ionic liquid in the electrolyte [41, 42], we have performed OCVD measurements on solar cells with commercially available Solaronix electrolyte, without the intention of investigating how concentration, diffusion coefficient of the triiodide, or different cations affect the recombination, but rather just to confirm that the surface treatment is reducing the surface states of the TiO2 mesoporous film, and in doing so reducing the interfacial recombination regardless of the electrolyte. The cell size, assembly and all other materials and parameters were as described previously in Section 2.2.

In Figure 7(a) we are showing the electron lifetime dependence on the open circuit voltage of these cells. The shape of the curves emphasizes the difference in the recombination mechanism even more significantly. At high the electron transport through the conduction band is demonstrated with the seemingly constant electron lifetime. The exponential increase of the lifetime represented with the straight line in the logarithmic representation follows the same trend of trap-facilitated transport as described from the curves in Figure 6(b). However at < 0.4 V for the untreated electrode there is an onset of parabolic curvature which indicates that recombination through surface traps becomes dominant, whereas for the posttreated electrode this onset begins at around 0.25 V. Because the transport mainly occurs through bulk trap states, the recombination time is prolonged by one order of magnitude considering that the electrons are caught and released much faster from surface than from bulk trap states. This type of lifetime dependence points out that surface traps have been significantly diminished.

Figure 7: Electron lifetime as a function of the of DSSC with untreated photoanode (black full square) and posttreated photoanode with colloidal treatment at 450°C (blue full inverted triangle), with Solaronix electrolyte: (a) without a compact layer; (b) with a compact layer.

In contrast to the () curve shape of the cells with ionic liquid electrolyte presented in Figure 6(b), the curves in Figure 7(a) are quite different. Explicitly this difference is evident in the lower electron lifetime and the more pronounced inverted parabola shape in the low region. The lower electron lifetime can be attributed to the higher thickness of the mesoporous photoanode. Because of the grater surface area and the larger number of grain boundaries, a more intense electron recombination due to a higher surface states density can be expected. The shape of the inverted parabola region is determined mainly by the reorganization energy of the acceptor species in the electrolyte [40]. Furthermore, the combination of different dye and electrolyte components on semiconducting nanocrystals can change the density of surface states [43].

According to Cameron and Peter [44], it is essential to also take into account the recombination with the electrolyte through the substrate when analyzing the OCVD curves. Since no surface treatment is made on the substrate in the preparation of the different photoanodes and the investigation is focused on the surface treatment of the photoanode without changing the electrolyte within the same batch of cells, for the purposes of analyzing the charge transfer through different trap states, we tend not to take into account the back reaction via the substrate, given that the effects of this reaction should be the same in all the cells. Additionally our investigation is not focused on analytically deriving the density of states function but rather extracting information on how the surface treatment influences the electron lifetime; hence we believe that it is appropriate to use the previously discussed methodology [39, 40]. However with the intention of confirming the validity of our results, we have prepared identical cells, to those measured in Figure 7(a), with the only difference of adding a compact TiO2 layer. The results are shown in Figure 7(b). It is evident that using a compact layer does not significantly change the shape of the () curve.

Again, we can confirm that the main difference in the electron lifetime is due to the reduction of the surface state transport. When comparing the shape of the curves presented in Figures 7(a) and 7(b) one can observe that the cells employing a TiO2 compact layer and the ones without the compact layer have almost identical () curve shape.

4. Conclusions

The implementation of TiO2 nanoparticle colloidal solution for posttreatment of the dye-sensitized solar cell photoanode has proven to be favorable in efficiency improvement. We have investigated the posttreatment sintering temperature dependence on the morphological properties of the photoanode films as well as the impact on the photovoltaic properties of the DSSC. Establishing an efficiency improvement of 10% for the photoanode posttreated with the colloidal solution of anatase nanoparticles at 450°C, we further investigated the mechanisms responsible for this efficiency increase. The recorded efficiency increase was mostly a result of an increase in the short circuit current; however we saw no evidence of an increase of the effective surface area of the posttreated photoanode or an increased dye loading. From the conducted investigation by OCVD measurements we can validate that this type of colloidal treatment of the mesoporous photoanode reduces the number of surface traps that can act as recombination centers, hence prolonging the electron lifetime. The posttreatment nanoparticle layer operates in a manner of passivating the surface of the photoanode altering the recombination mechanism by shifting the bulk trap state dominant transport to lower potentials.

The colloidal treatment not only increases the overall cell efficiency similarly to the TiCl4, but also represents a facile method for posttreatment that leads to further cost beneficial manufacturing of the dye-sensitized solar cell.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.


The authors wish to thank Dr. Caterina Soldano and Mr. Paolo Mei for the precious technical contribution. This work was partially supported by Progetto Premiale CNR 2012—Produzione di energia da fonti rinnovabili (Iniziativa CNR per il Mezzogiorno, L. 191/2009 art. 2 comma 44).


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