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5 February 2020 Poly(vinyl pyrrolidone)-modified metal oxide anode interlayers for stable organic solar cells
Author Affiliations +
Abstract

A new generation of anode interlayers (AILs) has been introduced in recent years for improving the efficiency and stability of organic solar cell (OSC) devices. Electrode interlayer modification is a simple and effective way of enhancing OSC device performance. We used poly(vinyl pyrrolidone) (PVP) as an AIL modifier to alter molybdenum trioxide (MoO3) and vanadium pentoxide (V2O5) AILs in OSC devices and compared them with pure metal oxide AILs. Using this modification, average power conversion efficiencies were raised from 5.2  %    ±  0.4  %   to 6.0  %    ±  0.3  %   for OSCs with MoO3-based AILs, and from 6.2  %    ±  0.1  %   to 6.8  %    ±  0.3  %   for OSCs with V2O5-based AILs. Moreover, the PVP-metal oxide AILs also improved the overall device quality, producing a nanotextured morphology with good optical properties and favorable chemical composition. Beneficial wetting properties for interfacial adhesion between anode and active layer are observed using contact angle measurements. Overall, devices with PVP-modified metal oxide AILs showed promising results with greater device stability compared to pure metal oxide AIL-based OSC devices.

1.

Introduction

Organic solar cells (OSCs) have recently reached power conversion efficiencies (PCEs) of up to 16%.1 A particularly attractive feature of OSCs is the possibility of developing cost-effective large-scale production methods, as devices can be fabricated using solution-processable materials. The typical structure of an OSC (Fig. 1) includes a bulk heterojunction active layer, consisting of a mixture of donor and acceptor materials. Apart from the active layer, interlayers between the active layer and the electrodes play an important role in the extraction of photogenerated charges, affecting the efficiency of the overall OSC device.

Fig. 1

Schematic of the OSC device structure studied in this work. The AILs used were MoO3, PVP-MoO3, V2O5, and PVP-V2O5.

JPE_10_4_042003_f001.png

In terms of anode interlayers (AILs), poly(3,4-ethylenedioxythiophene)-poly(styrenesulfonate) (PEDOT:PSS) has been almost universally used over the past decade2,3 on top of an indium tin oxide (ITO) anode. However, the negative effects of PEDOT:PSS on active layer morphology have been well documented and can affect device longevity and overall efficiency.46 These problems have been associated with low charge carrier mobilities and nonradiative recombination losses within the device.7 These results suggest that even though PEDOT:PSS has served well as a solution-processable AIL, it is unlikely to be the ultimate AIL material in a future OSC technology.

In recent years, a new generation of AILs has been introduced using materials such as metal oxides,810 conducting polymers,11 graphene-based AILs,12 conductive polyelectrolytes,13 and cross-linkable materials.14 Semiconductor metal oxide interlayers can have consistent long-term stability in high-efficiency OSCs.15,16 Among these metal oxides, molybdenum trioxide (MoO3) and vanadium pentoxide (V2O5) have been widely used to produce AILs processed at low temperatures. The combination of low temperature processing conditions with high PCE motivates the use of metal oxides as AILs in OSC devices.17

Electrode interlayer modification using polymers is known to be a simple and effective way to improve OSC device performance.18,19 For example, metal oxides modified with polymers, such as poly[(9,9-bis(3′-(N,N-dimethylamino)propyl)-2,7-fluorene)-alt-2,7-(9,9-dioctyl)-fluorene] (PFN) and poly(vinyl pyrrolidone) (PVP), have produced reduced surface defects when the polymer was directly mixed with the metal oxide rather than coated on top as a bilayer.20,21 PVP is a widely known nonconjugated polymer, which has been used both as a stand-alone cathode interlayer (CIL) in OSCs and as a CIL in combination with metal oxides.21,22 Most of the interlayer modifications reported so far have involved CILs, especially the use of various polymer composites with zinc oxide (ZnO)23,24 and titanium oxide (TiOx).25 In contrast, there are very few reports on metal oxide AIL modifications with polymers in OSC devices, and those reports have mostly used a metal-oxide/polymer bilayer structure.26 Nanocomposite-based AILs are slowly gaining attention in OSCs due to their structural and optical advantages over pure metal oxide AILs.27,28 Similar to pure metal oxides,29,30 the work function of these nanocomposite AILs can also be tuned to align energy levels for a wide range of donor materials.31 In addition, compared to the complex functionalization methods reportedly required to modify interfacial layers,32 a simple mixture of alcohol-soluble modifier like PVP and the metal oxide precursors would be more beneficial toward cost-effective large-scale printing of next-generation solar cells.33 Most of the polymer-based composites for metal oxide AIL modifications have used only PEDOT:PSS.32,34,35 However, the acidic nature of PEDOT:PSS mixed with water-based metal oxide precursors limits the long-term air stability. Therefore, there is a need for water-free and nonacidic AIL precursors to enhance the air stability along with the efficiency of the OSC devices.

In this work, PVP nanocomposite was used for modification of MoO3 (PVP-MoO3) and V2O5 (PVP-V2O5) AILs. The alcohol-soluble PVP mixed metal oxide interlayers are compared with pure metal oxide interlayers. The influence of the nanocomposite on the physical and chemical properties of the AIL was analyzed using various characterization techniques, and the effect on OSC device performance has been measured. In all devices, the active layer that was used is poly (4,8-bis[(2-ethylhexyl)oxy]benzo[1,2-b:4,5-b′]dithiophene-2,6-diyl3-fluoro-2-[(2-ethylhexyl)carbonyl]thieno[3,4-b]thiophenediyl):[6,6]-phenyl-C71-butyric acid methyl ester (PTB7:PC71BM). PTB7 was chosen due to its expanded absorption spectrum up to the near-infrared wavelength region.36

2.

Experimental Details

2.1.

Materials and Solutions

Prepatterned ITO glass slides with sheet resistance of 15  Ω/cm2 were purchased from Kintec Company. Bis(2,4-pentanedionato)molybdenum(VI) dioxide was purchased from Sigma-Aldrich. Vanadium triisopropoxide (VTIPO) was purchased from Alfa Aesar. PTB7 was purchased from 1-Material Inc. PC71BM was purchased from Nano-C. PVP (Mw 1,300,000 by light-scattering); isopropanol, chlorobenzene, and 1,8-diiodooctane (DIO) were purchased from Sigma-Aldrich. All materials were used without further purification.

A MoO3 precursor solution was freshly prepared by dissolving bis(2,4-pentanedionato)molybdenum(VI) dioxide in isopropanol with a 1:150 w/v ratio. A 0.05 M solution precursor of VTIPO was freshly prepared by dissolving 100  μL of VTIPO in 8 mL of isopropanol. For PVP-MoO3 interlayers, PVP (1  mg/mL) was initially dissolved in isopropanol solvent and ultrasonicated for 10 min until it formed a clear solution. Bis(2,4-pentanedionato)molybdenum(VI) dioxide or VTIPO was then added to the PVP/isopropanol solution at the same concentration as for the pure MoO3 and V2O5 solutions. An active layer solution was prepared by dissolving PTB7 (10 mg):PC71BM (13 mg) in chlorobenzene (1 mL) and stirring inside the glovebox overnight at room temperature. DIO (3 vol%) was added to the PTB7:PC71BM solution and stirred at 60°C for 3 h before the deposition process.

2.2.

Thin-Film Deposition and Device Fabrication

Prepatterned ITO glass substrates were sequentially cleaned by ultrasonication with acetone and isopropanol for 10 min each. The surface of the cleaned substrates was treated with a UV–ozone cleaner (Novascan Technologies, Inc.). MoO3, PVP-MoO3, and V2O5 AIL precursor solutions were deposited on the cleaned ITO substrates by spin coating at 5000 rpm for 30 s in air. PVP-V2O5 was spin-coated at 6000 rpm for 30 s. The resultant thicknesses were 30 nm for MoO3, PVP-MoO3 and V2O5 AILs, and 28 nm for PVP-V2O5. The spin-coated films were annealed at 150°C, and PVP-MoO3 AILs were further treated with a UV–ozone cleaner (Novascan) for 15 min.

After depositing AILs, PTB7:PC71BM blended solutions were spin coated at 1000 rpm for 40 s under nitrogen atmosphere inside a glove box to form a 100-nm thin film without a postdeposition annealing process. The substrates were then transferred to a thermal evaporator to deposit a 1-nm lithium fluoride (LiF) interlayer followed by a 100-nm aluminum (Al) electrode under a base pressure of 3×107  Torr. A mask with a designated active area of 0.1  cm2 was used during the evaporation process. In total, at least six devices were made for each architecture. A schematic for the OSC devices is shown in Fig. 1.

2.3.

Characterization Methods

The surface morphology of AILs and active layers was analyzed using an MFP-3D Origin atomic force microscopy (AFM) in tapping mode under atmospheric conditions. A UV–visible spectrometer (V650, Jasco) was used to measure the transmittance spectra of films. Work function measurements were carried out in air using AC2 photoelectron spectroscopy (RKI Instruments). The surface energy of the films was estimated using contact angle measurements (KSV Instruments Ltd.). The chemical environment and oxidation states were analyzed using X-ray photoelectron spectroscopy (XPS, The Kratos Axis DLD). The photovoltaic device performance was characterized using a 1-kW Oriel solar simulator with an AM 1.5 G filter as the light source in conjunction with a Keithley 2400 source measurement unit. The best performed devices were kept in a dark room in a nitrogen environment to study their stability for 96 h.

3.

Results and Discussion

3.1.

Physical and Chemical Characterization

3.1.1.

AIL surface morphology

Tapping mode AFM was performed for morphological analysis of metal oxide and PVP-metal oxide films. The root mean square roughness (Rrms) for MoO3 was 2.60 nm, increasing to 8.75 nm for untreated PVP-MoO3 AILs and decreasing to 6.91 nm after UV–ozone treatment [Figs. 2(a)2(c)]. For V2O5 and PVP-V2O5 AILs, Rrms was 1.90 and 6.90 nm, respectively [Figs. 2(d) and 2(e)]. As shown in Fig. 2, there is an obvious structural change from a flat surface for a thin layer of metal oxide on top of ITO to a nanotextured surface with the addition of PVP, consistent with previous reports.37,38

Fig. 2

Tapping mode AFM images of thin films of (a) MoO3, (b) PVP-MoO3 without UV–ozone treatment (w/o UVO), (c) PVP-MoO3 after UV–ozone treatment, (d) V2O5, and (e) PVP-V2O5 thin films.

JPE_10_4_042003_f002.png

The presence of nanoscopic voids appearing in between nanoclusters due to rapid solvent evaporation could be a reason for the higher Rrms of PVP-AILs.39 PVP has a well-known influence on synthesized metal oxide morphologies.40 The hydrophobic vinyl groups and hydrophilic carbonyl groups present in PVP can induce shape effects by forming polarized micelles in precursor solutions, leading to the formation of metal oxide nanoclusters.41 The size and self-assembly of these nanoclusters can be controlled by changing the molecular weight of PVP.42 Hence, by choosing PVP with the highest available average molecular weight (1,300,000  g/mol), 5–15 nm metal oxide nanoclusters were obtained in Fig. 2.

The agglomeration of clusters can leave parts of the surface uncovered [Fig. 2(b)]. These surfaces would be PVP-rich, which would be detrimental for OSC device performance. Therefore, after postdeposition annealing, we further treated the PVP-MoO3 AILs with UV–ozone for 15 min to remove the upper layer of PVP and form a more uniform top surface, as shown in Fig. 2(c).21 Unlike untreated PVP-MoO3 AILs, PVP-V2O5 AIL-based devices worked well without performing any PVP surface removal techniques.

Although higher surface roughness can cause local shorts in thin-film devices, it is not a limiting factor for overall device performance. AILs with Rrms as high as 25 nm have been successfully used as hole injection layers for organic electronic devices.43 In fact, nanostructured hole-transporting layers can be beneficial for thin-film solar devices by avoiding electronic losses at the electrode/polymer interface, resulting in an increased fill factor (FF)44,45 and device stability.46 The surface roughness of active layers deposited on different AILs was also analyzed (see Sec. 5.1). The increment in surface roughness which is required to improve internal reflection in the active layer.47

3.1.2.

AIL optical properties

To understand changes in the device performance, the optical transmittance has been analyzed for pure metal oxide AILs with and without the addition of PVP (Fig. 3). A high transmission rate in the visible region could be beneficial for AILs in OSC devices. Figure 3(a) shows that the pure MoO3 layer has slightly less transmittance compared to the PVP-MoO3 composite layers through the visible region. The transmittance of PVP-MoO3 AILs increased after exposure to UV–ozone for 15 min, possibly due to slightly decreased thickness of the layer following removal of the organic layer by UV–ozone treatment. However, the slightly decreased optical transmittance of PVP-MoO3 films below 400  nm could result in the reduction of short-circuit current density (JSC) in OSC devices.48 There is less difference between the optical transmittance in the case of V2O5 and PVP-V2O5 AILs, as shown in Fig. 3(b). In both cases, the highest transmission rate is observed around 500 nm and above, covering most of the solar spectrum. The antireflective effect observed from 330 to 410 nm can be attributed to the formation of smooth surfaces,49,50 which could decrease the extinction and dispersion of light.

Fig. 3

Transmittance spectra for (a) MoO3 and PVP-MoO3, with a detailed view of part of the curve inset, and (b) V2O5 and PVP-V2O5 AILs.

JPE_10_4_042003_f003.png

The photoelectron spectroscopy in air technique was used to determine the work function of the AILs presented in Figs. 4(a) and 4(b). These figures plot the square-root of the counting rate as a function of the photon energy in order to find the photoemission threshold energy. The crossing point of the background and the yield line gives the work function of the material.51,52 The work function for the MoO3 film was determined as 5.7 eV and was decreased to 5.6 eV in the case of PVP-MoO3 AIL [Fig. 4(a)]. The work function was unchanged with and without UV–ozone treatment of AILs. The work function of V2O5 AILs was 5.5 eV [Fig. 4(b)], only 0.17 eV was lower than the HOMO of the donor PTB7 [Fig. 4(c)]. Hence, holes can more easily travel from the donor’s HOMO level to V2O5 and PVP-V2O5 AILs and then pass on to the ITO electrode.53,54 The energy level diagrams shown in Fig. 4(c) were obtained with the values from Figs. 4(a) and 4(b) similar to the previous reports.52,55,56

Fig. 4

Photoelectron spectra for (a) MoO3 and PVP-MoO3, (b) V2O5 and PVP-V2O5, and (c) energy level diagrams for AILs with respect to the PTB7:PC71BM OSC device structure.

JPE_10_4_042003_f004.png

3.1.3.

X-ray photoelectron spectroscopy

XPS core level scans of the Mo 3d region provided an insight into the chemistry of pure and modified MoO3 films. For pure MoO3 [Fig. 5(a)], the intensity is split into two regions that are identified with 3d3/2 and 3d5/2 orbitals (the spin-orbit splitting is 3.3 eV) with an area ratio of 1:0.6, respectively. There are no traces of Mo(V) species. These values are consistent with the Mo(VI) state being present in MoO3 AILs.57

Fig. 5

XPS Mo 3d core level scans for (a) MoO3 and (b) PVP-MoO3 without UV–ozone (top) and with UV–ozone (bottom) AILs.

JPE_10_4_042003_f005.png

For PVP-MoO3 with and without UV–ozone treatment [Fig. 5(b)], additional peaks of Mo(V) appear at lower binding energy (by 1.0  eV) than the Mo(VI) peaks. Similar spectra were previously reported for different ratios of Mo(V) and Mo(VI) at higher annealing temperatures, from 150°C to 250°C.58,59 Both of these studies attributed the presence of Mo(V) to distortion of the molybdenum lattice due to gradual dehydration and organic thermalization at elevated temperatures. Since both MoO3 and PVP-MoO3 AILs were annealed at 150°C, the addition of PVP could be the reason behind the observation of Mo(V) states, indicating that some MoO3 lattice distortion had occurred. With the UV–ozone treatment, these peaks attenuated noticeably, suggesting that the reduced Mo(V) species are forming at the very surface (top 13 molecular layers) of the layer and that the UV–ozone treatment effectively suppresses Mo(V) species in PVP-MoO3 AILs. Since these particular MoO3 AIL samples only possess Mo(V) and Mo(VI) species, the minimum Mo:O stoichiometry can be assessed directly from the known Mo(V):Mo(VI) ratios.58,59 Using ratios obtained from the high-resolution core-level spectra in Fig. 5, the Mo:O stoichiometries of the samples coated on ITO substrates were determined and recorded in Table 1.

Table 1

XPS compositional analysis for MoO3 and PVP-MoO3 AILs. Mo(V):Mo(VI) and Mo:O were calculated using high resolution of Mo 3d and O 1s core level scans.

AILsOxygen (%)Carbon (%)Molybdenum (%)Mo(V):Mo(VI)Mo:O
MoO344.320.820.00.01:3.0
PVP-MoO3 (without UV–ozone)24.442.816.70.21:2.8
PVP-MoO3 (with UV–ozone)43.925.118.20.11:2.9

A quantitative analysis of the composition of the samples is also listed in Table 1. The relative content of oxygen, carbon, and molybdenum was estimated from O1s, C1s, and Mo 3d core level scans, respectively. The MoO3 AIL has a relatively high oxygen content and almost equal carbon and molybdenum content, with stable Mo:O lattice stoichiometry. PVP-MoO3 without UV–ozone treatment contained less oxygen, with relatively high carbon and low molybdenum content. After UV treatment, the PVP-MoO3 sample has relatively low carbon and molybdenum content. As pointed out before, the atomic ratio of Mo(V):Mo(VI) has decreased from 0.2 to 0.1 after UV–ozone treatment. The resulting calculated stoichiometries are PVP-MoO2.8 before UV–ozone treatment and PVP-MoO2.9 after UV–ozone treatment. Previous reports have obtained similar values for solution-processed MoO3 AILs and have shown that low annealing temperatures are more suitable for achieving stable Mo:O stoichiometries with less oxygen deficiencies.60

From the XPS fits in Fig. 6, we can deduce the presence of two vanadium oxidation states in V2O5-based AILs by deconvoluting two peaks from the vanadium V2p3/2 peak. Namely, V(IV) generates a peak between 517 and 516 eV, and V(V) produces a peak at around 518 eV.61 V(IV) occurs as a result of the partial reduction of V(V) after exposure to air for 10 min. Interestingly, the fraction of V(IV) species slightly increased for the PVP-V2O5 films, which indicates that more oxygen vacancies are generated during hydrolysis. This could lead to enhanced electrical conductivity of films.62

Fig. 6

O1s and V2p core level scans for V2O5 (top) and PVP-V2O5 (bottom) AILs.

JPE_10_4_042003_f006.png

The O1s peak is also fitted using two contributing peaks, which are the peaks for O atoms in V2O5 between 530.7 and 530.8 eV,61,63,64 and the undecomposed precursor peak between 531.3 and 531.9 eV.65 The effective oxidation state of vanadium (VOX) can be calculated using the splitting between the O1s and V2p3/2 transition centroids, so that VOX=13.820.68 [O(1s)V(2p3/2)].66 The values of VOX listed in Table 2 are in agreement with V2O5 oxidation states from previous reports.67

Table 2

XPS data obtained for different V2O5-based AILs from high resolution scans.

AILV(V) position (eV)V(IV) position (eV)V(V):V(IV)O1s position in V2O5 (eV)O1s position in undecomposed precursor (eV)VOX
V2O5518.0517.01.71:1530.8531.95.1
PVP-V2O5517.5516.51.32:1530.7531.94.8

3.1.4.

Wettability of AILs

Wettability measurements can provide information on interfacial interactions between the anode and the active layer in an OSC device.68 From Figs. 7(a) and 7(b), the surfaces of the MoO3-based AILs clearly become more hydrophilic after the addition of PVP. There was a corresponding small increase in the contact angle for nonpolar chlorobenzene [Figs. 7(c) and 7(d)], which could produce diminished JSC in an OSC device.69 In contrast, Figs. 8(a) and 8(b) show that water contact angles increased for V2O5 AILs when PVP was added. This suggests that V2O5 is less hydrophobic than PVP-V2O5, which is consistent with the slightly lower contact angles for chlorobenzene on pure V2O5 [Figs. 8(c) and 8(d)].

Fig. 7

(a) and (b) Side-on photographs of droplets of water; (c) and (d) chlorobenzene on the labeled MoO3-based AIL surfaces. Measurements of contact angle are also labeled.

JPE_10_4_042003_f007.png

Fig. 8

(a) and (b) Side-on photographs of droplets of water; (c) and (d) chlorobenzene on the labeled V2O5-based AIL surfaces. Measurements of contact angle are also labeled.

JPE_10_4_042003_f008.png

In previous work on hole transporting layers, Manders et al. and Cho et al. have demonstrated that hydrophobic AILs result in favorable OSC device characteristics compared to hydrophilic surfaces.69,70 Moreover, hydrophilic surfaces coated beneath polymer:PC71BM active layers have resulted in adverse aggregation of PC71BM, which, in turn, resulted in lower PCE.71 The decrease in chlorobenzene contact angle on PVP-V2O5 AILs could therefore lead to strong interfacial cohesion between the anode and the active layer, low series resistance in the OSC device, and consequently enhanced photovoltaic parameters.

3.2.

Photovoltaic Performance and Stability

The photovoltaic performance of OSC devices with PVP composite metal oxide AILs was tested and compared with OSCs, which have pure metal oxide AILs. The four OSC device structures for these experiments are shown, as indicated in Fig. 1. Based on topographical measurements (above), oxide encapsulation of PVP22 seems to be high for PVP-MoO3 AILs, and OSC devices showed diminished performance (PCE=0%) without performing the UV–ozone treatment described previously to remove PVP. Therefore, device analysis for the high efficiency of low band-gap polymer donor PTB7 was carried out only for the best performed AILs; that is, PVP-MoO3 with UV–ozone treatment was studied.

Photovoltaic performance and stability data are presented in Fig. 9 and Table 3. The best efficiency for a single device was obtained with a PVP-V2O5 AIL, with VOC=0.72  V, JSC=14.82  mA/cm2, FF=66%, and a PCE of 7.10%. The slight dip in the current-density in devices with AILs of PVP-MoO3 following UV–ozone treatment, in comparison to devices with MoO3 interlayers, can be explained by the increasing surface roughness (from 2.60 to 6.91 nm), which can lead to the formation of local shorts in the interlayer.18,72 On the other hand, the increment in FF from 0.53 (for MoO3) to 0.60 (for PVP-MoO3) shows improvement in the OSC device quality with the addition of PVP. Also, VOC is enhanced for PVP-MoO3 AILs compared with MoO3 AILs, from 0.70 to 0.72 V. These improvements in FF and VOC can be attributed to efficient hole transportation because of the reduced work function of the PVP-MoO3 AILs. The hydrophilic nature of the PVP-MoO3 AIL surface is also consistent with the decrease in JSC relative to pure MoO3, but this did not offset the increased FF measurement.

Fig. 9

Performance and stability data for the best OSCs with various interlayers. (a) JV curves, (b) JPhVeff characteristics, (c) dark JV curves, and (d) normalized PCE as a function of time.

JPE_10_4_042003_f009.png

Table 3

Photovoltaic parameters for PTB7:PC71BM OSCs with various AILs. Mean and standard deviation values are presented for six devices of each type. Shunt (RSH) and series (RS) resistances were calculated from the J–V curves [Fig. 9(a)].

AILVOC (V)JSC (mA/cm2)FFPCEave (%)PCEbest (%)RSH (Ω.cm2)RS (Ω.cm2)
MoO30.70±0.0215.0±0.70.53±0.035.2±0.45.60714.5015.3
PVP-MoO3 (with UVO)0.72±0.0114.5±0.20.60±0.016.0±0.36.301790.508.1
V2O50.72±0.0114.7±0.30.60±0.026.2±0.16.3212098.4
PVP-V2O50.72±0.0114.8±0.10.66±0.016.8±0.37.1013966.1

Similar enhancement in FF was seen in PVP-V2O5 compared to pure V2O5-based devices. The enhancement in VOC to 0.72 V for V2O5 and PVP-V2O5 compared to MoO3-based devices can be explained by more efficient charge transfer because of the reduced work function of V2O5 layers. Wettability of the AILs seems to have no large effect on the overall device performance although the hydrophobic MoO3 AIL, which could have stronger adhesion with the active layer showed slightly higher JSC.

The PTB7:PC71BM devices were also measured in reverse bias conditions to better understand their performance with respect to the addition of PVP nanocomposite. As shown in Fig. 9(b), the photocurrent density (JPh) increases with effective voltage (Veff)73 and reaches saturation at 2  V, suggesting that most of the electron–hole pairs are dissociated into free carriers at this potential. Since the photocurrent generation mechanism is dependent on the quality of charge carrier injection and extraction rates, at any given point in the device only a certain number of electron–hole (e–h) pairs can dissociate and transfer to appropriate electrodes. For the maximum power output condition (Veff=0.2  V), JPh/JSat is 0.85, 0.90, 0.87, and 0.96 for the best-performed MoO3, PVP-MoO3, V2O5, and PVP-V2O5 AIL OSC devices, respectively. The high values of VOC and FF observed for PVP-V2O5 AIL-based OSC devices can be partly attributed to efficient charge extraction at the AIL/active layer interface, with suppressed nongeminate recombination leading to an improved collection of charge carriers at the respective electrodes.74

In Fig. 9(c), the lowest leakage current of 1.87×104  mA/cm2 was obtained for a PVP-MoO3 device. This is one order of magnitude less than the leakage current for the best-performed pure MoO3 and PVP-V2O5 AIL-based devices. This result is consistent with the high shunt resistance (RSH) of 1790.5  Ω.cm2 and the moderately low series resistance (RS) of 8.10  Ω.cm2 recorded in Table 3 for PVP-MoO3 AIL devices.

Stability was also studied for PTB7:PC71BM solar cell devices with the various AILs [Fig. 9(d)]. After 96 h, MoO3 and PVP-MoO3 AIL devices had decreases in JSC of 20% and 17%, and in FF of 5.6% and 4.9%, respectively. This led to efficiency retention of 81% and 91% for MoO3 and PVP-MoO3 OSC devices, respectively. The V2O5 AIL-based device showed a 9.5% reduction in JSC and a 4.5% reduction in FF, retaining 79% of its initial PCE. For the PVP-V2O5 device, JSC decreased 10.5% and only 1.8% in FF, with 91% retention of PCE. Overall, the PVP nanocomposite metal oxide AIL devices had better efficiency retention than pure metal oxide AIL devices. This enhanced stability is likely to be due to the nonacidic nature of the PVP-modified metal AILs.

4.

Conclusion

In summary, the results have demonstrated that solution-processible PVP nanocomposite metal oxide AILs showed distinctive nanotextured morphology with higher transmittance compared to pure metal oxide AILs. Both PVP mixed metal oxides also showed favorable chemical composition, thereby producing improved photovoltaic performance compared to pure metal oxide AILs. They exhibited greater stability (higher efficiency retention) and better shunt resistance (RSH) with lower leakage currents. The results suggest that charge extraction within OSC devices was more efficient for the PVP nanocomposites. This photovoltaic performance in conjunction with the optical, chemical, and interfacial properties suggest that the PVP nanocomposite metal oxide AILs could give not only unperturbed diode characteristics but could also improve the photovoltaic parameters of OSC devices. Indeed, the clear increase in FF for PVP-based AILs indicates an enhancement in the overall device quality. Thus, PVP-metal oxide mixtures provide promising AILs. One of the reasons to extend this study to PVP-V2O5 was to avoid UV–ozone treatment, which was necessary for removal of a surface organic layer on PVP-MoO3 AILs, and therefore to achieve enhanced photovoltaic performance without this additional fabrication procedure. These results demonstrate the potential for AILs processed at moderate annealing temperatures with simple fabrication procedures to improve the overall quality and stability of OSC devices.

5.

Appendix

5.1.

Surface Morphology of Active Layers

The differences in surface roughness for the active layer were comparatively small for devices with MoO3 AILs [Figs. 10(a)10(c)]. Rrms for PTB7:PC71BM coated on pure MoO3 was 2.40 nm. This increased to 2.85 nm for coating on untreated PVP-MoO3 and increased slightly further to 2.90 nm for coating on UV–ozone treated PVP-MoO3. An increase in the surface roughness of active layers was consistently observed with the addition of PVP to the V2O5 AILs. For active layers deposited on V2O5 AIL, the Rrms value was 2.84 nm and this increased to 4.85 nm for PVP-V2O5 layers [Figs. 10(d) and 10(e)]. Rough surfaces of PTB7:PC71BM layers can improve the internal reflection in the active layer, which can lead to increased device efficiency.47

Fig. 10

AFM images of PTB7:PC71BM active layers coated on (a) MoO3, (b) PVP-MoO3 without UV–ozone treatment (w/o UVO), (c) PVP-MoO3 after UV–ozone treatment, (d) V2O5, and (e) PVP-V2O5.

JPE_10_4_042003_f010.png

Acknowledgments

This work was supported by New Zealand’s Ministry of Business, Innovation and Employment (Contract UOAX0911), the Faculty of Science at the University of Auckland, and a Universitas 21 Graduate Research Project grant. The authors thank Dr. Yiran An for providing technical support with AFM and Dr. Krishnachary Salikolimi for providing photoelectron spectroscopy measurements. The authors wish to thank Dr. Jegadesan Subbiah and Dr. David Jones at the University of Melbourne for providing facilities and expert advice for some parts of this research.

References

1. 

B. Fan et al., “Achieving over 16% efficiency for single-junction organic solar cells,” Sci. China Chem., 62 (6), 746 –752 (2019). https://doi.org/10.1007/s11426-019-9457-5 Google Scholar

2. 

F. Zhang et al., “Polymer photovoltaic cells with conducting polymer anodes,” Adv. Mater., 14 (9), 662 –665 (2002). https://doi.org/10.1002/(ISSN)1521-4095 ADVMEW 0935-9648 Google Scholar

3. 

S.-I. Na et al., “Efficient and flexible ITO-free organic solar cells using highly conductive polymer anodes,” Adv. Mater., 20 (21), 4061 –4067 (2008). https://doi.org/10.1002/adma.v20:21 ADVMEW 0935-9648 Google Scholar

4. 

M. F. Al-Mudhaffer et al., “The origin of performance limitations in miniemulsion nanoparticulate organic photovoltaic devices,” Sol. Energy Mater. Sol. Cells, 175 77 –88 (2018). https://doi.org/10.1016/j.solmat.2017.09.007 SEMCEQ 0927-0248 Google Scholar

5. 

F. Liu et al., “Understanding the morphology of PTB7:PCBM blends in organic photovoltaics,” Adv. Energy Mater., 4 (5), 1301377 (2014). https://doi.org/10.1002/aenm.201301377 ADEMBC 1614-6840 Google Scholar

6. 

M. Jørgensen, K. Norrman and F. C. Krebs, “Stability/degradation of polymer solar cells,” Sol. Energy Mater. Sol. Cells, 92 (7), 686 –714 (2008). https://doi.org/10.1016/j.solmat.2008.01.005 SEMCEQ 0927-0248 Google Scholar

7. 

A. Uddin and X. Yang, “Surface plasmonic effects on organic solar cells,” J. Nanosci. Nanotechnol., 14 (2), 1099 –1119 (2014). https://doi.org/10.1166/jnn.2014.9017 JNNOAR 1533-4880 Google Scholar

8. 

Y. Sun et al., “Solution-processed small-molecule solar cells with 6.7% efficiency,” Nat. Mater., 11 (1), 44 –48 (2012). https://doi.org/10.1038/nmat3160 NMAACR 1476-1122 Google Scholar

9. 

M. Y. Ameen et al., “Solution processed transition metal oxide anode buffer layers for efficiency and stability enhancement of polymer solar cells,” Opt. Mater., 75 491 –500 (2018). https://doi.org/10.1016/j.optmat.2017.11.006 OMATET 0925-3467 Google Scholar

10. 

W. Qiu et al., “Ultrathin ammonium heptamolybdate films as efficient room-temperature hole transport layers for organic solar cells,” ACS Appl. Mater. Interfaces, 6 (18), 16335 –16343 (2014). https://doi.org/10.1021/am504606u AAMICK 1944-8244 Google Scholar

11. 

J. E. Yoo et al., “Directly patternable, highly conducting polymers for broad applications in organic electronics,” Proc. Natl. Acad. Sci. U. S. A., 107 (13), 5712 –5717 (2010). https://doi.org/10.1073/pnas.0913879107 Google Scholar

12. 

Y. J. Jeon et al., “Moderately reduced graphene oxide as hole transport layer in polymer solar cells via thermal assisted spray process,” Appl. Surf. Sci., 296 140 –146 (2014). https://doi.org/10.1016/j.apsusc.2014.01.061 ASUSEE 0169-4332 Google Scholar

13. 

H. Zhou et al., “Conductive conjugated polyelectrolyte as hole-transporting layer for organic bulk heterojunction solar cells,” Adv. Mater., 26 (5), 780 –785 (2014). https://doi.org/10.1002/adma.201302845 ADVMEW 0935-9648 Google Scholar

14. 

A. W. Hains et al., “Anode interfacial tuning via electron-blocking/hole-transport layers and indium tin oxide surface treatment in bulk-heterojunction organic photovoltaic cells,” Adv. Funct. Mater., 20 (4), 595 –606 (2010). https://doi.org/10.1002/adfm.v20:4 AFMDC6 1616-301X Google Scholar

15. 

Y. Sun et al., “Efficient, air-stable bulk heterojunction polymer solar cells using MoOx as the anode interfacial layer,” Adv. Mater., 23 (19), 2226 –2230 (2011). https://doi.org/10.1002/adma.v23.19 ADVMEW 0935-9648 Google Scholar

16. 

Z. Yin et al., “Interface control of semiconducting metal oxide layers for efficient and stable inverted polymer solar cells with open-circuit voltages over 1.0 volt,” ACS Appl. Mater. Interfaces, 5 (18), 9015 –9025 (2013). https://doi.org/10.1021/am402175m AAMICK 1944-8244 Google Scholar

17. 

K. Zilberberg et al., “Low-temperature, solution-processed MoOx for efficient and stable organic solar cells,” ACS Appl. Mater. Interfaces, 4 (3), 1164 –1168 (2012). https://doi.org/10.1021/am201825t AAMICK 1944-8244 Google Scholar

18. 

H. Pan et al., “MoO3Au composite interfacial layer for high efficiency and air-stable organic solar cells,” Org. Electron., 14 (3), 797 –803 (2013). https://doi.org/10.1016/j.orgel.2012.12.020 OERLAU 1566-1199 Google Scholar

19. 

X. Jia et al., “A low-cost and low-temperature processable zinc oxide-polyethylenimine (ZnO:PEI) nano-composite as cathode buffer layer for organic and perovskite solar cells,” Org. Electron. Phys. Mater. Appl., 38 150 –157 (2016). https://doi.org/10.1016/j.orgel.2016.08.012 Google Scholar

20. 

N. Wu et al., “Zinc oxide: conjugated polymer nanocomposite as cathode buffer layer for solution processed inverted organic solar cells,” Sol. Energy Mater. Sol. Cells, 141 248 –259 (2015). https://doi.org/10.1016/j.solmat.2015.05.039 SEMCEQ 0927-0248 Google Scholar

21. 

C. E. Small et al., “High-efficiency inverted dithienogermole-thienopyrrolodione-based polymer solar cells,” Nat. Photonics, 6 (2), 115 –120 (2012). https://doi.org/10.1038/nphoton.2011.317 NPAHBY 1749-4885 Google Scholar

22. 

H. Sun et al., “Investigating the multiple roles of polyvinylpyrrolidone for a general methodology of oxide encapsulation,” J. Am. Chem. Soc., 135 (24), 9099 –9110 (2013). https://doi.org/10.1021/ja4035335 JACSAT 0002-7863 Google Scholar

23. 

S. Shao et al., “Enhanced performance of inverted polymer solar cells by using poly(ethylene oxide)-modified ZnO as an electron transport layer,” ACS Appl. Mater. Interfaces, 5 (2), 380 –385 (2013). https://doi.org/10.1021/am302408w AAMICK 1944-8244 Google Scholar

24. 

J. Liu et al., “Printable highly conductive conjugated polymer sensitized ZnO NCs as cathode interfacial layer for efficient polymer solar cells,” ACS Appl. Mater. Interfaces, 6 (11), 8237 –8245 (2014). https://doi.org/10.1021/am501001v AAMICK 1944-8244 Google Scholar

25. 

Z. Yin et al., “Solution-derived poly(ethylene glycol)-TiOx nanocomposite film as a universal cathode buffer layer for enhancing efficiency and stability of polymer solar cells,” Nano Res., 8 (2), 456 –468 (2015). https://doi.org/10.1007/s12274-014-0615-8 1998-0124 Google Scholar

26. 

Y. Guo et al., “Organic solar cells based on a Cu2O/FBT-TH4 anode buffer layer with enhanced power conversion efficiency and ambient stability,” J. Mater. Chem. C, 5 (32), 8033 –8040 (2017). https://doi.org/10.1039/C7TC02566A Google Scholar

27. 

J. Cheng et al., “Pre- and post-treatments free nanocomposite based hole transport layer for high performance organic solar cells with considerably enhanced reproducibility,” Nano Energy, 34 76 –85 (2017). https://doi.org/10.1016/j.nanoen.2017.02.021 Google Scholar

28. 

Z. Huang et al., “All-room-temperature solution-processed new nanocomposites based hole transport layer from synthesis to film formation for high-performance organic solar cells towards ultimate energy-efficient fabrication,” Nano Energy, 47 26 –34 (2018). https://doi.org/10.1016/j.nanoen.2018.02.019 Google Scholar

29. 

A. L. F. Cauduro et al., “Crystalline molybdenum oxide thin-films for application as interfacial layers in optoelectronic devices,” ACS Appl. Mater. Interfaces, 9 (8), 7717 –7724 (2017). https://doi.org/10.1021/acsami.6b14228 AAMICK 1944-8244 Google Scholar

30. 

X. Li et al., “MoOx and V2Ox as hole and electron transport layers through functionalized intercalation in normal and inverted organic optoelectronic devices,” Light Sci. Appl., 4 e273 (2015). https://doi.org/10.1038/lsa.2015.46 Google Scholar

31. 

L. Dou et al., “25th anniversary article: a decade of organic/polymeric photovoltaic research,” Adv. Mater., 25 (46), 6642 –6671 (2013). https://doi.org/10.1002/adma.201302563 ADVMEW 0935-9648 Google Scholar

32. 

D. Konios et al., “Highly efficient organic photovoltaic devices utilizing work-function tuned graphene oxide derivatives as the anode and cathode charge extraction layers,” J. Mater. Chem. A, 4 1612 –1623 (2016). https://doi.org/10.1039/C5TA09712F Google Scholar

33. 

A. Rajagopal, K. Yao and A. K. Y. Jen, “Toward perovskite solar cell commercialization: a perspective and research roadmap based on interfacial engineering,” Adv. Mater., 30 1800455 (2018). https://doi.org/10.1002/adma.201800455 ADVMEW 0935-9648 Google Scholar

34. 

L. Chen et al., “Efficient bulk heterojunction polymer solar cells using PEDOT/PSS doped with solution-processed MoO3 as anode buffer layer,” Sol. Energy Mater. Sol. Cells, 102 66 –70 (2012). https://doi.org/10.1016/j.solmat.2012.03.027 SEMCEQ 0927-0248 Google Scholar

35. 

S. Shao et al., “In situ formation of MoO3 in PEDOT:PSS matrix: a facile way to produce a smooth and less hygroscopic hole transport layer for highly stable polymer bulk heterojunction solar cells,” Adv. Energy Mater., 3 (3), 349 –355 (2013). https://doi.org/10.1002/aenm.201200609 ADEMBC 1614-6840 Google Scholar

36. 

A. Iwan et al., “Electrochemical and photocurrent characterization of polymer solar cells with improved performance after GO addition to the PEDOT:PSS hole transporting layer,” Sol. Energy, 146 230 –242 (2017). https://doi.org/10.1016/j.solener.2017.02.032 Google Scholar

37. 

C. V. Subba Reddy et al., “Characterization of MoO3 nanorods for lithium battery using PVP as a surfactant,” J. Solid State Electrochem., 13 (12), 1945 –1949 (2008). https://doi.org/10.1007/s10008-008-0741-x JSSEFS 1432-8488 Google Scholar

38. 

P. Gouma, K. Kalyanasundaram and A. Bishop, “Electrospun single-crystal MoO3 nanowires for biochemistry sensing probes,” J. Mater. Res., 21 (11), 2904 –2910 (2006). https://doi.org/10.1557/jmr.2006.0353 JMREEE 0884-2914 Google Scholar

39. 

X. Orignac et al., “Influence of solvent concentration on the microstructure of SiO2-TiO2 sol-gel films,” J. Sol-Gel Sci. Technol., 8 (1–3), 243 –248 (1997). https://doi.org/10.1023/A:1026497826255 Google Scholar

40. 

Z. Gou et al., “Morphology-controllable synthesis and gas-sensing properties of α-MoO3,” J. Mater. Sci. Mater. Electron., 24 (3), 1018 –1023 (2013). https://doi.org/10.1007/s10854-012-0869-4 JSMEEV 0957-4522 Google Scholar

41. 

D. W. Su, S. X. Dou and G. X. Wang, “Hierarchical orthorhombic V2O5 hollow nanospheres as high performance cathode materials for sodium-ion batteries,” J. Mater. Chem. A, 2 (29), 11185 –11194 (2014). https://doi.org/10.1039/c4ta01751j Google Scholar

42. 

Y.-T. Wang, W.-T. Whang and C.-H. Chen, “Hollow V2O5 nanoassemblies for high-performance room-temperature hydrogen sensors,” ACS Appl. Mater. Interfaces, 7 (16), 8480 –8487 (2015). https://doi.org/10.1021/am509182s AAMICK 1944-8244 Google Scholar

43. 

J. Meyer et al., “MoO3 films spin-coated from a nanoparticle suspension for efficient hole‐injection in organic electronics,” Adv. Mater., 23 (1), 70 –73 (2011). https://doi.org/10.1002/adma.201003065 ADVMEW 0935-9648 Google Scholar

44. 

J. He et al., “Realization of 13.6% efficiency on 20  μm thick Si/organic hybrid heterojunction solar cells via advanced nanotexturing and surface recombination suppression,” ACS Nano, 9 (6), 6522 –6531 (2015). https://doi.org/10.1021/acsnano.5b02432 ANCAC3 1936-0851 Google Scholar

45. 

P. Yu et al., “13% Efficiency hybrid organic/silicon-nanowire heterojunction solar cell via interface engineering,” ACS Nano, 7 (12), 10780 –10787 (2013). https://doi.org/10.1021/nn403982b ANCAC3 1936-0851 Google Scholar

46. 

N. K. Elumalai et al., “Enhancing the stability of polymer solar cells by improving the conductivity of the nanostructured MoO3 hole-transport layer,” Phys. Chem. Chem. Phys., 15 6831 –6841 (2013). https://doi.org/10.1039/c3cp50994j PPCPFQ 1463-9076 Google Scholar

47. 

M. V. Srinivasan et al., “Performance evaluation of PTB7:PC71BM based organic solar cells fabricated by spray coating method using chlorine free solvent,” RSC Adv., 5 (69), 56262 –56269 (2015). https://doi.org/10.1039/C5RA04760A Google Scholar

48. 

S. R. Hammond et al., “Low-temperature, solution-processed molybdenum oxide hole-collection layer for organic photovoltaics,” J. Mater. Chem., 22 (7), 3249 (2012). https://doi.org/10.1039/c2jm14911g JMACEP 0959-9428 Google Scholar

49. 

X. Bao et al., “Simple O2 plasma-processed V2O5 as an anode buffer layer for high-performance polymer solar cells,” ACS Appl. Mater. Interfaces, 7 (14), 7613 –7618 (2015). https://doi.org/10.1021/acsami.5b00091 AAMICK 1944-8244 Google Scholar

50. 

S.-I. Na et al., “Evolution of nanomorphology and anisotropic conductivity in solvent-modified PEDOT:PSS films for polymeric anodes of polymer solar cells,” J. Mater. Chem., 19 (47), 9045 –9053 (2009). https://doi.org/10.1039/b915756e JMACEP 0959-9428 Google Scholar

51. 

M. M. Y. A. Alsaif et al., “Exfoliation solvent dependent plasmon resonances in two-dimensional sub-stoichiometric molybdenum oxide nanoflakes,” ACS Appl. Mater. Interfaces, 8 (5), 3482 –3493 (2016). https://doi.org/10.1021/acsami.5b12076 AAMICK 1944-8244 Google Scholar

52. 

C. Chen, Y. Chen and S. Chuang, “High‐performance and highly durable inverted organic photovoltaics embedding solution‐processable vanadium oxides as an interfacial hole‐transporting layer,” Adv. Mater., 23 (33), 3859 –3863 (2011). https://doi.org/10.1002/adma.201102142 ADVMEW 0935-9648 Google Scholar

53. 

M. T. Greiner et al., “Universal energy-level alignment of molecules on metal oxides,” Nat. Mater., 11 (1), 76 –81 (2012). https://doi.org/10.1038/nmat3159 NMAACR 1476-1122 Google Scholar

54. 

Z. Tan et al., “High-performance inverted polymer solar cells with solution-processed titanium chelate as electron-collecting layer on ITO electrode,” Adv. Mater., 24 (11), 1476 –1481 (2012). https://doi.org/10.1002/adma.201104863 ADVMEW 0935-9648 Google Scholar

55. 

F. Liu et al., “Efficient polymer photovoltaic cells using solution-processed MoO3 as anode buffer layer,” Sol. Energy Mater. Sol. Cells, 94 (5), 842 –845 (2010). https://doi.org/10.1016/j.solmat.2010.01.004 SEMCEQ 0927-0248 Google Scholar

56. 

F. Cheng et al., “Enhancing the performance and stability of organic solar cells using solution processed MoO3 as hole transport layer,” RSC Adv., 7 37952 –37958 (2017). https://doi.org/10.1039/C7RA06511F Google Scholar

57. 

NIST, “NIST X-ray photoelectron spectroscopy database, NIST standard reference database 20, version 4.1,” (2017) http://srdata.nist.gov/xps/Default.aspx Google Scholar

58. 

J. J. Jasieniak et al., “A solution-processed MoOx anode interlayer for use within organic photovoltaic devices,” Adv. Funct. Mater., 22 (12), 2594 –2605 (2012). https://doi.org/10.1002/adfm.201102622 AFMDC6 1616-301X Google Scholar

59. 

J. Xiong et al., “High alcohol-soluble MoOx gel for interfacial layer in organic solar cells,” Curr. Appl. Phys., 17 (8), 1021 –1028 (2017). https://doi.org/10.1016/j.cap.2017.04.014 1567-1739 Google Scholar

60. 

B. Li et al., “Room-temperature, solution-processed MoOx thin film as a hole extraction layer to substitute PEDOT/PSS in polymer solar cells,” ACS Photonics, 1 (2), 87 –90 (2014). https://doi.org/10.1021/ph4000168 Google Scholar

61. 

Y. Suchorski et al., “Evolution of oxidation states in vanadium-based catalysts under conventional XPS conditions,” Appl. Surf. Sci., 249 (1), 231 –237 (2005). https://doi.org/10.1016/j.apsusc.2004.11.083 ASUSEE 0169-4332 Google Scholar

62. 

H. Cong et al., “A facile approach to prepare a vanadium oxide hydrate layer as a hole transport layer for high-performance polymer solar cell,” ACS Appl. Mater. Interfaces, 9 (21), 18087 –18094 (2017). https://doi.org/10.1021/acsami.7b02164 AAMICK 1944-8244 Google Scholar

63. 

D. Briggs, “Auger and X-ray photoelectron spectroscopy,” Practical Surface Analysis, John Wiley & Sons, Chichester (1983). Google Scholar

64. 

J. Crane et al., “The application of electric fields to aerosol assisted chemical vapor deposition reactions,” J. Electrochem. Soc., 158 (2), D67 (2011). https://doi.org/10.1149/1.3519870 JESOAN 0013-4651 Google Scholar

65. 

G. Beamson and D. Briggs, The Scienta ESCA 300 Database, Wiley, Chichester (1992). Google Scholar

66. 

G. W. Coulston, E. A. Thompson and N. Herron, “Characterization of VPO catalysts by X-ray photoelectron spectroscopy,” J. Catal., 163 (1), 122 –129 (1996). https://doi.org/10.1006/jcat.1996.0311 JCTLA5 0021-9517 Google Scholar

67. 

K. Zilberberg et al., “Solution processed vanadium pentoxide as charge extraction layer for organic solar cells,” Adv. Energy Mater., 1 (3), 377 –381 (2011). https://doi.org/10.1002/aenm.v1.3 ADEMBC 1614-6840 Google Scholar

68. 

T. H. Lai et al., “Properties of interlayer for organic photovoltaics,” Mater. Today, 16 (11), 424 –432 (2013). https://doi.org/10.1016/j.mattod.2013.10.001 MATOBY 1369-7021 Google Scholar

69. 

J. R. Manders et al., “Solution-processed nickel oxide hole transport layers in high efficiency polymer photovoltaic cells,” Adv. Funct. Mater., 23 (23), 2993 –3001 (2013). https://doi.org/10.1002/adfm.201202269 AFMDC6 1616-301X Google Scholar

70. 

S. P. Cho et al., “Brush painted V2O5 hole transport layer for efficient and air-stable polymer solar cells,” Sol. Energy Mater. Sol. Cells, 132 196 –203 (2015). https://doi.org/10.1016/j.solmat.2014.08.019 SEMCEQ 0927-0248 Google Scholar

71. 

J. S. Kim et al., “Control of the electrode work function and active layer morphology via surface modification of indium tin oxide for high efficiency organic photovoltaics,” Appl. Phys. Lett., 91 (11), 112111 (2007). https://doi.org/10.1063/1.2778548 APPLAB 0003-6951 Google Scholar

72. 

J. E. Houston et al., “Molecular design of interfacial layers based on conjugated polythiophenes for polymer and hybrid solar cells,” Polym. Int., 66 (10), 1333 –1348 (2017). https://doi.org/10.1002/pi.5397 PLYIEI 1097-0126 Google Scholar

73. 

V. D. Mihailetchi et al., “Photocurrent generation in polymer-fullerene bulk heterojunctions,” Phys. Rev. Lett., 93 (21), 216601 (2004). https://doi.org/10.1103/PhysRevLett.93.216601 PRLTAO 0031-9007 Google Scholar

74. 

J. Subbiah et al., “A green route to conjugated polyelectrolyte interlayers for high-performance solar cells,” Angew. Chem. Int. Ed., 56 (29), 8431 –8434 (2017). https://doi.org/10.1002/anie.201612021 Google Scholar

Biographies of the authors are not available.

© 2020 Society of Photo-Optical Instrumentation Engineers (SPIE)
Hima A. Kavuri, Shinji Kihara, Duncan J. McGillivray, and Geoff R. Willmott "Poly(vinyl pyrrolidone)-modified metal oxide anode interlayers for stable organic solar cells," Journal of Photonics for Energy 10(4), 042003 (5 February 2020). https://doi.org/10.1117/1.JPE.10.042003
Received: 27 August 2019; Accepted: 19 December 2019; Published: 5 February 2020
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