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0Hindawi Publishing Corporation
Journal of Nanomaterials
Volume 2014, Article ID 357979, 11 pages
http://dx.doi.org/10.1155/2014/357979
Research Article
Solution Processed Silver Nanoparticles in Dye-Sensitized Solar Cells
Marko Berginc, Ursa Opara Krasovec, and Marko Topic
University of Ljubljana, Faculty of Electrical Engineering, Trzaska 25,1000 Ljubljana, Slovenia Correspondence should be addressed to Marko Berginc; marko.berginc@fe.uni-lj.si Received 7 November 2013; Accepted 15 January 2014; Published 24 February 2014 Academic Editor: Jianping Xie
Copyright © 2014 Marko Berginc 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.
A plasmonic effect of silver nanoparticles (Ag NPs) in dye-sensitized solar cells (DSSCs) is studied. The solutions of silver nitrate in isopropanol, ethylene glycol, or in TiO2 sol were examined as possible precursors for Ag NPs formation. The solutions were dip-coated on the top of the porous TiO2 layer. The results of optical measurements confirmed the formation of Ag NPs throughout the porous TiO2 layer after the heat treatment of the layers above 100°C. Heat treatment at 220°C was found to be optimal regarding the formation of the Ag NPs. The porous TiO2 layers with Ag NPs have been evaluated also in DSSC by measuring current-voltage characteristics and the external quantum efficiency of the cells. In addition, the amount of adsorbed dye has been determined to prove the plasmonic effect in the cells. The I-V characterization of the DSSCs revealed an increase of the short circuit current in the presence of Ag NPs although the amount of the attached dye molecules decreased. These results confirm that the performance enhancement is related to the plasmonic effect. However, neither a thin sol-gel TiO2 layer nor poly(4-vinylpyridine) shells provide effective protection for the long term stability of the Ag NPs against the corrosion of I3-/I- based electrolyte.
1. Introduction
In the last decade the processes and new materials for dye-sensitized solar cells (DSSCs) have been extensively researched in order to enhance the performance and the stability of the cells [1-4]. In order to broaden and/or increase the spectral sensitivity of the solar cell several concepts have been considered, for example, the quest for new sensitizers [5-7] or cosensitizers [8-11], different approaches for engineering active layer/electrolyte interface [12], optimizing the thickness of the active layer, or increasing the concentration of the attached dye molecules [13-15]. Absorption has also been improved by increasing the optical path using larger scattering particles or voids in the active layer [14, 16-18]. Furthermore, an undyed layerplacedontop of theactivelayer [13, 14, 19, 20] or a mirror-like Pt counter electrode [21-30] was studied as an internal back reflector. In addition, different materials have also been proposed as external back reflectors placed at the rear side of the DSSCs [31, 32].
In recent years a surface plasmon resonance using metal nanoparticles (NPs) has also attracted much attention and has
been studied for various solar cell technologies [33-37]. The surface plasmon resonance is a light induced coherent oscillation of conduction band electrons on the surface of the metal NPs. The wavelength of resonance peak due to the presence of plasmonic particles greatly depends on factors such as size, shape, and dielectric environment. Two types of enhanced absorption are possible: (1) near-field: a strong electromagnetic field in the vicinity of the NPs around the plasmonic resonance wavelengths greatly enhances the absorption in the active layer and (2) far-field enhancement of the light absorption in the photoactive layer due to the scattering effect.
In the last few years a concept of surface plasmon resonance has been introduced to the dye-sensitized solar cells employing noble metals, mostly Ag [38-48] or Au NPs [42, 47, 49-56]. The scattering, that is, far-field enhancement (arrows in Figure 1) is generally already present in DSSC due to the strong scattering of the porous TiO2 layer. Therefore, the researchers focused mostly on the near-field plasmonic (dashed circles in Figure 1) where the absorbing dye should be close to the NPs and the electromagnetic field around
Figure 1: Near-field (dashed circles) and far-field effect (arrows) in the DSSC.
NPs significantly enhances the absorption of the dye and consequently increases the /SC.
The proof of the concept was firstly presented on two simplified flat structures. The first one contained dyed Ag NPs on compact TiO2 layer placed over the front transparent conductive oxide (TCO) [38,41]. In the studies, a less harmful Co2+/3+ based redox electrolyte was used in order to preserve unprotected Ag NPs. The second structure contained Ag NPs deposited on the front TCO that were protected with a thin compact TiO2 layer, varying in thickness between 2 and 9 nm, covered with a monolayer of dye molecules [39, 40]. The results confirmed that the electromagnetic field related to the near-field plasmonic effect decreases with a power of two by increasing the thickness of the TiO2 shell around NPs, that is, by increasing the distance from the dye molecules and NPs [39, 40]. If the shell was thicker than 2nm the plasmonic effect was hindered. On the other hand, the shell should protect the NPs from aggressive electrolyte; therefore the shell should not be too thin either [43, 55, 57, 58]. The study showed that to fully protect the Ag NPs at least 7.7 nm thick compact crystalline TiO2 layer is needed [39]. The near-field plasmonic enhancement in DSSC was confirmed but the performance of the cells was very low (>0.05%) due to the very thin active layers used in this study.
So far several different locations of NPs and deposition techniques have been proposed to prepare DSSC with plas-monic enhancement.
(i) Location 1: NPs deposited on the front TCO by soaking the front TCO in suspensions containing NPs [49] or by sputtering the NPs [44].
(ii) Location 2: the NPs are formed throughout porous TiO2 layer.
(a) One-step preparation of the active layer with NPs: the metal (core shell) NPs precursors are mixed in a TiO2 paste and the (core shell) NPs are formed after annealing process [43, 48, 50, 53-56].
(b) Two-step preparation of the active layer with NPs: undyed/dyed porous TiO2 layers are (i) immersed into or (ii) spin-coated by a metal salt solution or a solution containing core shell NPs and after additional treatment (e.g., drying,
heat treatment, photocatalitic reduction under UV illumination, etc.), the (core shell) NPs are formed [42, 45, 51, 52, 55, 58].
(iii) Location 3: NPs located at a certain position within the porous TiO2 layer.
A thin metal layer is sputtered on the porous TiO2 layer which created NPs after heat treatment. Afterwards, additional porous TiO2 overlayers have been deposited [46].
(iv) Location 4: NPs located on the top of the porous TiO2. A thin metal layer is sputtered at the back side of the dyed/undyed TiO2 layer which created NPs at the rear side after heat treatment [44, 46,47].
The researchers confirmed a significant effect of the NPs location, concentration, and size on the performance enhancement. Therefore, they have to be carefully optimized according to the DSSCs structures (thickness of the active layer, electrolyte, dye, etc.) in order to achieve the highest plasmonic enhancement. Generally, the highest enhancement is found when the NPs are spread throughout the active layer [42, 53]. Furthermore, larger NPs shift the plasmonic resonance toward longer wavelengths, but the magnitude of the shift strongly depends on the materials used for NPs and the dielectric environment (surrounding material), for example, the resonance peak of the Au NPs in a suspension shifts from 519 nm to 579 nm, when the diameter of the NPs increases from 20 to 80 nm [49]. On the other hand, a parasitic absorption within NPs could significantly hamper the plasmonic effect [45,59] if the NPs exceed optimal size or agglomeration takes place. The simulations showed that the absorption of metal nanoparticles could take up about 2030% of the total absorption of DSSC at visible wavelengths even under the optimized conditions [59].
Some researchers studied the structures containing unprotected NPs [44, 46, 47, 49, 54, 56, 58, 59] but the long term stability remains questionable, since the I3-/I-based electrolyte is very aggressive even to Au NPs [39, 52]. Additionally, the unprotected NPs could act as effective recombination centres [55]; therefore many research focused also on core/shell or even core/shell/shell NPs with Ag or Au cores and TiO2 [42, 43, 45, 48, 50, 53], SiO2 [50, 53, 55], or organic shells [51, 52]. In addition to careful design regarding the location, concentration, and size of the NPs it has been stressed on that the shell should be pinhole free to ensure the protection against electrolyte, but on the other hand the shell should be as thin as possible to utilize the plasmonic effect [39, 40, 45, 52, 57] and to reduce parasitic absorption within a shell. A red shift in plasmonic resonance by increasing the thickness of the shell was also observed [39]. In addition to the plasmonic effect the NPs present in the cell structure could induce different effects influencing the solar cell parameters. The NPs with the TiO2 shell can upward shift the Fermi level of the TiO2, reduce the dark current, and increase the electron lifetime which all increase the VOC [43, 53]. Additionally, the NPs can simultaneously increase the internal surface available for dye loading which additionally increases the /SC [45]. Therefore, the performance
TiO2 shell
enhancement due to the plasmonic effect should be always very carefully examined.
Many researchers significantly improved the conversion efficiency when NPs were incorporated (from 30% up to 140%, relatively) [47,50,52,55,60], but high relative improvements were generally not obtained for the solar cells achieving state-of-the-art efficiency. Nevertheless, some researchers foundremarkableimprovementsalsoinabsoluteterms. Dang et al. [42] found an improvement of the performance from 8.3 to 10.8% when TiO2/Au/TiO2 core/shell/shell NPs were included throughout the active layer of the DSSC. Furthermore, Choi et al. [53] increased the efficiency of DSSC from 9.3% to 10.2% after incorporating Au/SiO2 core/shell NPs, while the ^ increased only to 9.8% when the TiO2 shell was applied.
Herein, the DSSCs containing Ag NPs throughout the active layer are examined in Figure 2. Ethylene glycol and isopropanol were used to prepare silver nitrate solutions that have been used for the impregnation of the porous TiO2 layer. The formation of Ag NPs formed at five different temperatures was examined using optical measurements of the samples deposited on microscope glass. The optimal temperature determined to be 220°C was used for the preparation of the Ag NPs within porous TiO2 layers for DSSCs. The prepared AgISO NPs were afterwards protected with either a thin TiO2 layer or organic shell based on poly(4-vinylpyridine), PVP. In addition, the feasibility of the formation of Ag/TiO2 core/shell NPs in a single step was studied by incorporation of the silver nitrate to the Ti sol.
The porous TiO2 layers with Ag NPs have been tested in the DSSC. To evaluate the plasmonic enhancement external quantum efficiency (EQE), current-voltage characteristics (IV) at standard test conditions and the amount of the adsorbed dye were measured and compared to our reference DSSCs without NPs. Finally, a stability of the Ag NPs against electrolyte in DSSCs is presented by remeasuring the I-V characteristics of DSSCs three months after manufacturing and by exposing the AgISO/TiO2 and AgISO/PVP core shell NPs to I3-/r redox electrolyte and measuring the difference in absorption.
— Dye
— Shell TiO2 0 Ag NPs
Figure 2: Cross section of DSSC with integrated Ag/TiO2 core shell NPs in the active layer.
in isopropanol to obtain the sol with 0.4 M of titanium. To deposit the Ag NPs on porous TiO2 layers the dip-coating method was used (speed 10cm/min). The layers were heat-treated for 1h at different temperatures from 100 to 300°C. After heat treatment the bare Ag NPs (AgISO and AgEG)orAg/ TiO2 core/shell NPs within a porous TiO2 layer were formed (Ag/TiO2).
For the stability tests (Section 3.3) the bare AgISO NPs were coated with either a thin TiO2 or PVP shell. To make a TiO2 shell the Ag-TiO2 layers were additionally dipcoated using the TiO2 sol (speed 10 cm/min) and heat treated at 220° C for 1h. To form a PVP shell around AgISO NPs we soaked the Ag-TiO2 layers for 24 h into a solution containing 0.005 M poly(4vinylpyridine) in acetonitrile.
2. Experimental
2.1. Preparation of the Active Layer. An optimized Pechini sol-gel TiO2 paste (based on P25, Degussa) [61] was applied to the glass substrate using a "doctor blading" technique. For optical measurements a microscope glass was used as substrate while a fluorine-doped SnO2 coated glass (TCO) with a sheet resistance of 8 Q/square was used for the DSSCs' substrate. After deposition, the TiO2 layers were sintered at 450°C for 1 hour.
Three different solutions containing Ag NPs precursors were studied. Solution 1 (AgISO) was 0.004 M AgNO3 in isopropanol, solution 2 (AgEG) was 0.004 M AgNO3 in ethylene glycol, and solution 3 (Ag/TiO2) was AgISO mixed with TiO2 sol in a molar ration 0.4 M/0.004 M. The TiO2 sol was prepared by mixing the Titanium (IV) isopropoxide (Aldrich) with acetyl acetone (Fluka) in molar ratio 1: 1.5
2.2. DSSC Preparation. The TiO2 layers without/with Ag NPs have been immersed in an ethanol solution of a Ruthenium complex based dye (Ru(2,2'bipyridyl-4,4'dicarboxylate)2 (NCS)2, Solaronix) for 12 hours. For the counter electrode, platinum (thickness ~ 5nm) was sputtered onto a TCO glass substrate. Both electrodes were then sealed using a 25 ^m thick polymer foil (Surlyn, DuPont) which also acts as a spacer between the electrodes. Electrolyte was injected through two predrilled holes in the counter electrode. The electrolyte was a binary ionic liquid mixture in a volume ratio 13: 7 of 1-propyl-3-methyl-imidazolium iodide (Iolitec) mixed with 1-ethyl-3-methyl-imidazolium tetracyanoborate (Merck), 0.5 M methyl benzimidazol, and 0.1 M guanidinium thiocyanate. The concentration of I2 was 0.2 M. Three identical DSSCs were assembled for each material combination, each with an active area ranging from 0.58 to 0.72 cm2. Before characterization the cells were stored in the dark for 24 hours to allow the electrolyte to penetrate into the TiO2 pores.
2.3. Characterization. The I-V characterization was performed using an Oriel Class ABA solar simulator equipped with a 1.5 G air mass filter, the spectrum of which closely matches the required AM1.5 spectrum. In accordance with the IEC 60904-3 standard the short-circuit current mismatch parameter was calculated in conjunction with a calibrated c-Si reference solar cell, covered with a KG5 glass filter; the level of standard illumination (1 sun, was deter-
mined. The cells were also masked to leave onlythe active area of the cell exposed, which is stated as the most rigorous condition regarding the cell's efficiency. I-V characteristics of the cells were then measured using a Keithley 238 source meter by applying a voltage and measuring the current. The cells were scanned stepwise (10 mV) from 0 V (short circuit regime) to 0.9 V (beyond VOC).
The UV-vis optical measurements (total transmittance Ttot and reflectance -RTOt) were performed on a Lambda 950 Perkin Elmer spectrophotometer equipped with a 150 mm Ulbricht integration sphere coated with Spectralon. The spectra were recorded from 300 to 800 nm in decrements of 5 nm. Absorption was calculated accordingly to the A = 100% - RTOT - rTOT.
External quantum efficiencies (EQEs) were measured without bias light using an Xe lamp and a monochromator (70525 Arc Lamp Apex Illuminator and Cornerstone 260 Monochromator, Oriel, Newport) at increments of 5 nm from 300 to 800 nm. The monochromatic light was focused so that the beam was smaller than the active areas of both the reference photodetector and the DSSCs. A stable reading was obtained after a 3 s delay between setting the wavelength and taking a current measurement.
The amount of the dye adsorbed on the TiO2 layer was determined with UV-vis spectroscopy. The Ruthenium dye was firstly detached from the TiO2 layers using 0.02 M NaOH (Merck); the dye solution has been diluted with 0.02 M NaOH to 50 mL before obtaining UV-vis spectra. In order to determine the amount of dye adsorbed on the TiO2 layers a calibration curve was made. For the calibration curve and the evaluation of the samples concentration the absorbance peak of the dye at the 500 nm has been considered.
3. Results and Discussion
Herein we present the results of the very simplified integration of the Ag NPs within the porous TiO2 layer. The Ag NPs within the TiO2 layers were prepared using three different solutions, that is, AgISO, AgEG, and Ag/TiO2 (see Section 2). In Section 3.1 the influence of the heat treatment temperature on the formation of Ag NPs by measuring the absorption spectra is presented. The TiO2 layers with Ag NPs were tested also in the DSSCs and the results were compared with the cells without Ag NPs. We have evaluated the DSSCs by measuring the I-V characteristic, EQEs, and the amounts ofthe adsorbed dye (Section 3.2). Section 3.3 deals with the stability of the DSSCs containing Ag NPs. The performance of the DSSCs has been remeasured three months after the manufacturing.
Additionally, the degradation of the TiO2 layers containing AgISO/TiO2 or AgISO/PVP core/shell NPs due to the exposure to the I3-/r electrolyte is presented.
3.1. AgNPs Preparation. The influence of the heat treatment temperature on the formation of Ag NPs was evaluated by optical spectroscopy. The absorption spectra (A = 100% -RTOT - Ttot) of the TiO2 layers (reference) deposited on microscope glass and further impregnated with AgISO, AgEG, and Ag/TiO2 are presented in Figures 3(a), 3(b), and 3(c).
The AgISO NPs within the porous TiO2 layer are formed already at 100°C visible as a homogeneous dark red layer, shown in Figure 3(a). The absorption enhancement (compared to the reference TiO2 layer without NPs) is noticeable above 365 nm reaching the enhancement peak (AA = AAgx -A) around 410 nm. A further increase in the heat treatment temperature up to 220° C gradually increases the absorption without changing the shape of the curve, while a further increase in the temperature to 300°C noticeably decreases the absorption and changes the shape of the curve, that is, the layers become grey. In a further study the heat treatment at 220°Cwas used for the preparation of a TiO2 layer with AgISO NPs. The optimal heat treatment temperature where the enhancement is most pronounced is 220°C.
Similar absorption enhancement and optimal heat treatment temperature at 220°C was found for AgEG NPs (without shell), as shown in Figure 3(b). This is in accordance with our expectation since only the ethylene glycol instead of isopropanol was used in solution 2. In both cases the organic components decompose and reduce the Ag+ to Ag0 while leaving the Ag NPs on the surface of the TiO2. However, the AgEG samples are less homogeneous which is probablyrelated to the different surface tension and viscosity of the ethylene glycol.
The absorption of the Ag/TiO2 core/shell NPs are presented in Figure 3(c). In this case the plasmonic enhancement cannot be compared with the bare TiO2 layer on a microscope glass substrate (black full line in Figure 3(c)) since solution 3 (which includes the TiO2 sol) is expected to form not only Ag/TiO2 core/shell NPs but also a thin overlayer on the porous TiO2 layer. Therefore, a new reference having a thin "shell" TiO2 overlayer has been used; that is, the porous TiO2 layer has been dip-coated into a TiO2 sol (speed 10 cm/min) and heat treated afterwards at 220°C for 1 hour. For Ag/TiO2 NPs the colour of the samples was greyish (Figure 3(c)) showing significantly smaller absorption enhancement. The absorption enhancement can be only found at 220°C while heat treatment at lower or higher temperatures shows even deterioration in absorbance compared to the reference. The minor enhancement might be observed if each studied heat treatment temperature would have its own reference produced at the same temperature. Nevertheless, the 220°C seem to be the optimal heat treatment also for the formation of Ag/TiO2 core/shell NPs.
3.2. DSSCs with AgNPs. The TiO2 layers with Ag NPs formed at 220°C from different precursors have been tested also in DSSC and the results are compared with the DSSC without Ag
V \\ \\ v\ v„ \ W
\ v\ SA
SA \\ X Vs
- Ref.
...... 100°C
---150°C
600 A (nm)
----- 180°C
- 220°C
---- 300° C
- Ref.
---Ref. + s. TiO2
...... 100° C
---150° C
500 600
A (nm)
----------180°C
--220°C
--------300°C
\ \ 1 v 1 a 1 "a I ^ • ^ \ '■ ^ \ \ \\
800 300
500 600
A (nm)
100°C
150°C
180°C 220° C 300° C
800 300
Ref. + s. TiO2 100°C
500 600
A (nm)
---150° C
--- - 180°C - 220°C
Figure 3: (a-c) The absorption (A = 100% - RTOT - Ttot) of the AgISO (a) and AgEG (b) NPs (without shell) and Ag/TiO2 core/shell NPs (c) located within the undyed TiO2 layer on microscope glass substrate heat treated at different temperatures. The absorption of bare TiO2 layer (black full line) and the bare TiO2 layer covered with a thin "shell" TiO2 layer (black dashed line) on a microscope glass substrate are shown for the reference. (d) The same as (c) but dyed porous TiO2 layers.
NPs. The AgISO and AgEG NPs studied in this section were not protected with a sol-gel TiO2 or PVP shell. The TiO2 layers with Ag NPs were immersed into a dye solution. The amount of the dye molecules attached to the TiO2 surface of different layers was evaluated spectroscopically (see Section 2). The results of dye loading are gathered in Figure 4 and regardless of the solution used for Ag NPs preparation the TiO2 layers with Ag NPs show smaller dye loading. The results confirm that the inclusion of the Ag NPs within the porous TiO2
layers reduces the inner surface area available for the dye attachment.
The current-voltage characteristics (I-V) of all DSSCs have been measured. Typical I-V for the reference and for the DSSCs with Ag NPs (AgISO, AgEG, and Ag/TiO2) measured after manufacturing (a) and after keeping the cells in the dark at room temperature for three months (b) are presented in Figure 5. In addition the averaged performance parameters (short circuit current /sc, open circuit voltage VOC, fill factor
3e - 8 -
j| 2e-8
1e - 8 -
Figure 4: The amount of the dye molecules attached to the surface of the active layers containing AgISO, AgEG, or Ag/TiO2 NPs. The Ag NPs were thermally treated at different temperatures as denoted at the top of the columns (values in °C). The results for porous TiO2 layer without NPs (ref) and porous TiO2 layer covered with a "shell" TiO2 layer (ref. + s. TiO2) are shown for reference.
Table 1: Performance parameters (/SC, VOC, FF, and if) of reference DSSCs and DSSCs with Ag NPs (AgISO, AgEG, and Ag/TiO2) measured after manufacturing/after 3 months.
Cell 7sc (mA/cm2) Voc (mV) FF (%) n (%)
Ref. 9.0/9.2 673/708 49/55 3.0/3.6
AglSO 9.4/9.1 687/725 52/58 3.4/3.9
AgEG 5.9/7.0 576/620 53/56 1.8/2.4
Ag/TiO2 8.4/9.2 635/684 51/57 2.7/3.6
FF, and conversion efficiency of three identical cells are gathered in Table 1.
The DSSC with AgISO NPs is the only structure where a small increase in /SC was observed compared to the reference structure. The increase can be related to the plasmonic effect since the DSSCs with AgISO NPs have a smaller amount of dye molecules attached to the TiO2 than the reference DSSCs (see Figure 4).
The DSSCs with Ag/TiO2 have smaller /SC than the reference (which has no additional "shell" TiO2 overlayer), as shown in Table 1. This is according to our expectation since a thin "shell" TiO2 overlayer is formed together with the formation of Ag/TiO2 NPs. It should be mentioned that the formation of a TiO2 overlayer on the top of the porous TiO2 layer significantly decreases the dye loading reaching a half value compared to the reference porous layer (Figure 4). Therefore, the performance of the DSSCs with Ag/TiO2 cannot be directly compared with the reference DSSCs which has no TiO2 overlayer (ref., Table 1). However, we can see that the JSC of Ag/TiO2 is only 7% lower than the reference (9.0 mA/cm2 for the ref. versus 8.4 mA/cm2 for the Ag/TiO2, Table 1) although the amount of the adsorbed dye is halved (Figure 4). This is another indirect proof of the plasmonic effectinthe DSSC. Theresults arewellinaccordance also with the optical measurements presented in Figure 3(d) showing a higher absorption of a dyed porous TiO2 layer containing Ag/
TiO2 core/shell NPs (Figure 3(d), red full line) than a dyed TiO2 layer covered with a thin "shell" TiO2 (black dashed line) although the amount of the attached dye molecules is in both cases similar (1.7 x 10- mol/cm for the reference with a "shell" TiO2 overlayer and 1.6 x 10-8 mol/cm2 for the Ag/TiO2, Figure 4).
The DSSCs with AgEG have significantly smaller JSC than the reference although a comparable /SC to DSSC with AgISO NPs would be expected due to similar absorption enhancement (Figures 3(a) and 3(b)) and a similar amount of the attached dye (Figure 4). The origin for the decrease is unknown. It might be related to the very inhomogeneous deposition of the Ag NPs due to different surface tension of the ethylene glycol compared to the isopropanol and/or poor attachment of the Ag NPs to the porous TiO2 layer. This creates a very low concentration of the AgEG NPs at the edges of the DSSCs and a very high concentration in the centre which increases the parasitic absorption within the NPs and significantly decreases the /SC.
The normalized EQEs of the DSSCs are presented in Figure 6 (the EQEs were normalized to 0.8 at 345 nm). According to the expectation, the EQEs show the same trends as observed for the /SC determined from I-V measurements; that is, the only enhancement is found for DSSCs with AgISO while smaller values were observed for DSSCs with AgEG and Ag/TiO2. The increase or decrease in EQEs is observed above 365 nm which is in agreement with the absorption measurements (Figure 3).
The VOC of the DSSCs are gathered in Table 1. The DSSCs with AgISO NPs have on average 14 mV higher VOC than the reference DSSC which might be related to the upward shift of the Fermi level induced by the Ag NPs [43, 53]. The DSSCs with Ag/TiO2 NPs have 38 mV smaller VOC than the reference. This could be explained by a smaller dye loading which reduces the number of injected electrons in a conduction band of the TiO2. Additionally, the smaller dye loading might leave a larger part of the TiO2 surface exposed to the electrolyte which increases the recombinations. Both effects shift the Fermi level downward and decrease the VOC. A significantly smaller VOC for the DSSCs with AgEG is difficult to explain but might be due to the poor attachment of Ag NPs that act as strong recombination centres.
The FF is practically unaffected by the NPs; therefore the ^ is the outcome of the JSC and VOC. The increase in ^ was found only for the DSSCs with AgISO while the DSSCs with AgEG and Ag/TiO2 NPs show a lower ^ than the reference DSSCs.
3.3. Stability ofAgNPs. The DSSCs have been remeasured 3 months after manufacturing, that is, after keeping the cells in the dark under open circuit conditions for 3 months (Table 1). The DSSC with AgISO NPs is the only structure where a decrease in JSC was observed (-3%) while the other DSSCs showed an increase. The JSC of the reference DSSC increased for 2% while the DSSCs with AgEG and Ag/TiO2 increased for 18% and 9%, respectively. Interestingly, for the JSC of reference, AgISO and Ag/TiO2 DSSCs became practically alike (Figure 5(b)) which might be related to the degradation of
- Ref.
- AgISO
0.4 V (V)
- Ag/TiO2
- Ref.
- AgISO
0.4 V (V)
- Ag/TiO2
Figure 5: The current-voltage (I-V) characteristics of typical reference DSSC and typical DSSCs with Ag NPs (AgISO, AgEG, and Ag/TiO2) that were measured after manufacturing (a) and after 3 months (b).
- Ref.
- AgISO
500 600
A (nm)
- Ag/TiO2
Figure 6: The normalized EQEs of the DSSCs containing AgISO or AgEG NPs or Ag/TiO2 core/shell NPs. The DSSCs without NPs or "shell" TiO2 overlayer is given for reference. The EQEs were normalized to 0.8 at 345 nm.
K\ 1 \ \
k \\ ' \ \
I If \ S 1 : S \ AxX
500 600
A (nm)
AgISO-before el. AgEG-before el. Ag/TiO2-before el.
---AgISO-after el.
AgEG-after el. ---Ag/TiO2 -after el.
Figure 7: The absorption enhancement (AA = A Agx - A ref ) of the undyed TiO2 layers with AgISO, AgEG, and Ag/TiO2 NPs before (full lines) and after being exposed to the I3-/I- electrolyte (dashed lines). All NPs were thermally treated at 220°C.
the Ag NPs. Additionally all cells showed a 5-8% and 1112% increase in the VOC and FF, respectively. These changes cannot be associated with the presence of Ag NPs since similar variations were observed also for reference DSSCs. The ^ increased for 20, 15, 33, and 33%, relatively, for the reference and the DSSCs with AgISO, AgEG, and Ag/TiO2 NPs. The AgISO DSSC has still the highest performance but the differences became less distinctive. The degradation of the Ag NPs in the presence of I3-/I- based electrolyte is not surprising and is in accordance with the literature. A quick degradation of the Ag NPs was found by Lin et al. [46] and
Thanachayanont et al. [58] who also found a decrease in /SC and an increase in VOC and FF during the 10 days stability study.
The changes (especially in /SC) in remeasured DSSCs suggest that the dye molecules produce a certain degree of protection but they cannot prevent the degradation entirely. Therefore, the stability of the Ag NPs upon exposure to the aggressive I3-/I- based electrolyte was studied.
The absorption enhancements (AA = AAgx - Af of the AgISO, AgEG NPs, and Ag/TiO2 core/shell NPs within
(a) (b) (c)
Figure 8: Degradation of the AgISO NPs coated with either a "shell" TiO2 or a PVP shell (a) layer before and (b) immediately after being exposed to the electrolyte, and (c) after 24 hours. The AgISO NPs located within undyed porous TiO2 layer were thermally treated at 220°C.
undyed porous TiO2 layers are presented in Figure 7. The full lines present the AA after production while the dashed lines present the AA after exposure of the layer to the electrolyte for 24 hours under ambient conditions. As expected the AA decrease substantially for the unprotected AgEG and especially AgISO NPs. Surprisingly, a small decrease in AA of the Ag/TiO2 core/shell NPs was also observed which reveals that the thin TiO2 shell does not provide sufficient protection required for long term stability.
Since the Ag/TiO2 core/shell NPs that were formed in a single step do not provide sufficient protection we used a secondary step to protect the AgISO NPs with either a thin sol-gel TiO2 or PVP shell, which should protect the NPs from the electrolyte and allow the dye attachment [52]. The protected NPs were then exposed to the I3-/I- electrolyte and the photographs were taken at different time periods, Figure 8. A substantial degradation of the protected Ag NPs was noticed if the sol-gel TiO2 layer was used. The thin TiO2 layer prepared via sol-gel route has a certain degree of porosity which allows the penetration of the electrolyte. Moreover, in our study the PVP shell did not protect the AgISO NPs although it provided adequate protection for the Au NPs [52]. In addition a few different techniques to prepare TiO2 shells around NPs can be found in the literature. Dang
et al. [42] synthesized core shell NPs before being deposited on the porous TiO2 layer. On the other hand, a compact TiO2 shell around Ag NPs could be formed afterwards by atomic layer deposition [39, 40] or by calcination of the Ag-TiO2 films refluxed with a Titanium (IV) isoproxide in isopropyl alcohol solution [45].
4. Conclusions
A plasmonic effect of Ag NP in the dye-sensitized solar cells (DSSCs) has been confirmed. We used three different solutions containing silver nitrate in isopropanol, ethylene glycol, or isopropanol/TiO2 sol for dip-coating of porous TiO2 layers. The results confirmed the formation of the Ag NPs without/with shells within a porous TiO2 layer. The optimal heat treatment temperature of the dip-coated layers, which gave the most intensive plasmonic enhancements, was 220°C for all three solutions. However, the ethylene glycol solution of silver nitrate gave a very nonhomogeneous distribution of Ag NPs over the TiO2 layers. On the other hand, the results show that the formation of the Ag NPs from the isopropanol solution leads to a uniform formation of the NPs throughout the layer giving also the highest plasmonic enhancement in DSSCs. The incorporation of the Ag NPs in the porous
TiO2 layer decreases the dye loading but increases the short circuit current which is a direct indication of the plasmonic effect. The plasmonic effect has been confirmed also by EQE measurements. Nevertheless, the degradation of Ag NPs was observed in the cells that have been measured again three months after the manufacturing. In addition, the study confirmed that neither a thin sol-gel TiO2 overlayer nor a poly(4-vinylpyridine) can provide sufficient protection for the long term stability of the Ag NPs against the corrosion of the I3-/I- electrolyte.
Conflict of Interests
The authors declare that there is no conflict of interests regarding the publication of this paper.
Acknowledgments
Mateja Hocevar is acknowledged for TiO2 paste and electrolyte preparation and Joze Stepan for his help in fabricating the cells. Marko Berginc would like to acknowledge the Slovenian Research Agency (Contract no. Z2-4189-1538) for the funding. The work was also partially funded by the Slovenian Research Agency under the P2/0197 Program. The authors would especially like to acknowledge the bilateral Project between the Laboratory of Photovoltaics and Optoelectronics and CEA (Contract no. Bt-CEA/Q2-0002).
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