# Ambient Air and Hole Transport Layer Free Synthesis: Towards Low Cost CH3NH3PbI3 Solar Cells

Authors: Muhammad Imran Ahmed; Hareema Saleem; Ahmed Nawaz Khan; Amir Habib
Journal: Journal of Nanomaterials
 (2016)

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## Abstract

Perovskite absorbers have witnessed a remarkable efficiency increase in last couple of years. To meet the commercialization challenge, reduced cost and improved efficiency are the two critical factors. We report on a hole transport layer free device synthesized under ambient air conditions of high humidity of 50% using TiO2-graphene oxide nanocomposite as electron selective contact. The devices achieved a power conversion efficiency of 5.9%. We introduce a novel synthesis route for TiO2-graphene oxide (GO) composite allowing superior charge transport properties. Incorporation of GO in TiO2 allows achieving higher power conversion efficiencies while working under ambient air conditions. Ambient air synthesis with hole transport free architecture has the potential to reduce the cost of this technology leading to commercial viability.


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## Body

## 1. Introduction

Ability to harness energy has ushered in the current age of development. Intricate interdependence of our ecosystem has resulted in considerable damage to environment by our use of fossil fuels. Depleting resources and ever increasing costs have reinvigorated the efforts to find sustainable alternatives. Heralded as a major scientific breakthrough in 2013, perovskite absorbers based solar cells have achieved major milestones in a span of few years on the back of intense research effort with a certified efficiency at 20.1% [1]. Perovskite absorbers have all the right ingredients, high extinction coefficient [2, 3], charge carrier mobility [4], long diffusion lengths [5], ambipolar charge transport properties [6], earth abundant materials, and, to cap it all, low temperature solution processability, to make them the green technology of tomorrow.Developed as a solid state Dye-Sensitized Solar Cell (DSSC) [7, 8], perovskites have evolved as a new class of solar cell. Mesoporous [9], mesostructured [6], and planer architecture [10] have been explored. Scaffolds of TiO2 were replaced by inert Al2O3 and then by zirconia demonstrating the ability to transport electrons by perovskite absorbers [11–13]. Electron beam induced current studies have concluded that hole diffusion length is longer than electron diffusion lengths for devices with TiO2 as electrons selective contact [14]. The ability to transport holes was established by demonstrating devices employing only one selective contact for electrons [15]. Processing has evolved from one-step spin coating [16] to two-step sequential deposition [17], vapor assisted [9], coevaporated [18] and numerous other techniques to achieve the optimum film morphology. Efforts have also been directed at evolving methods for processing under ambient conditions of high relative humidity with considerable success [17]. TiO2 has been a material of choice for electron selective contact applications. A wide band gap semiconductor has been extensively investigated owing to its low cost, electrochemical stability, and facile processing [19]. An important aspect of improving efficiency in these devices is to improve the charge carrier mobility by modifying TiO2 by substitutions with Y3+, Al3+, or Nb5+ into TiO2 [20–22] or by using titania nanorods and nanowires and ZnO nanorods [23–25].Electron transport shortcoming of TiO2 can be addressed by employing graphene owing to its remarkable electron transport properties. Thermal stability, optical transparency and outstanding conductivity, and charge carrier mobility afford the possibility of improving the optoelectronic devices in all aspects [26–29]. GO and reduced GO (rGO) have been investigated for wide ranging applications in memory devices [30], transistors [31], biosensors, and solar cells [32]. Several studies have concluded the effectiveness of utilization of GO and rGO for optimization of DSSCs [33–35]. A recent report has established that incorporation of graphene in TiO2 reduces the series resistance and improves the energy scheme in planar geometry solar cells [36].Hole selective contact free device geometry has the potential to afford reduced cost by avoiding the expensive Hole Transport Materials (HTMs). High certified efficiencies for this configuration bode possibility to develop this technology for commercial application [37–39]. One limiting point is the stringent requirement of environmental control needed to process these devices. Thus obtaining hole transport layer (HTL) free devices while processing under ambient air conditions of high humidity could open the possibility of reduced cost commercial viability of this technology.Here we combine HTL free architecture with ambient air synthesis of high relative humidity to afford a possibility of manufacturing cost optimization. The architecture used a TiO2 electron transport layer with CH3NH3PbI3 absorber resulting in an efficiency of 5.9%. Impedance spectroscopy was employed to evaluate the series and shunt resistance values. Graphene was incorporated into TiO2, using a novel synthesis technique to synthesize a nanocomposite for electron selective contact. Incorporation of this composite reduces series resistance and improves the shunt resistance increasing both Fill Factor (FF) and efficiency. Incorporation of GO in titania composite had an added advantage of improving the stability of the device. Since titania interface with CH3NH3PbI3 is reported to be detrimental due to titania activation under Ultraviolet (UV), red shifting the titania band gap can help offset this deterioration. Effect of temperature on the performance of solar cell was investigated by conducting impedance spectroscopy at elevated device temperature of 40°C and 60°C.


## 2. Experimental Methods

### 2.1. Materials

All the chemicals except CH3NH3I were purchased from sigma Aldrich and were used without further processing. CH3NH3I, (MAI) was sourced from Dysol (MS101000-50). Indium doped tin oxide (ITO) was used as front contact. At 10 mm × 10 mm it had a resistivity of 15 Ω/cm. ITO coated slides were detergent cleaned, washed with flowing ultrapure water, and ultrasonicated in ethanol for 20 min. They were subsequently dipped for one minute in piranha solution, rinsed in flowing ultrapure water, and dried by blowing hot air.


### 2.2. Experimental Details

Titania nanoparticles were synthesized by sol gel route. Titanium isopropoxide (<97%), 2-methoxyethanol (99.9+%), and ethanolamine (99+%) were mixed in 1 : 4 : 0.5 molar ratio. The mixture was refluxed in a three-necked flask in an inert environment and stirred at room temperature for 1 hr and 80°C for 1 hr and finally the temperature was raised to 120°C for 2 hr under constant stirring. Light yellow color of the sol indicated the dissolution of isopropoxide precursor in methoxyethanol solvent aided by ethanolamine as linker. Modified hummers method [40] was used to synthesize graphene oxide from graphite flakes average + 100 mesh (≥75% min).Devices were synthesized by spin coating titania over precleaned ITO coated glass slides at 2500 rpm for 20 s. TiO2 coated slides were dried in oven at 500°C for 2 hr with a heating rate of 10°C per min and were allowed to cool in furnace. CH3NH3PbI3 was deposited by a modified two-step solution processing method. Lead iodide was dissolved in dimethylformamide (DMF) to obtain a 1 M solution. MAI was dissolved in isopropanol at 7 mg/mL. Lead iodide solution was spin-coated on TiO2 coated slides at 3000 rpm for 20 s. Lead iodide coated slides were annealed for 3 min at 40°C and then at 100°C for 5 min. They were removed from oven and then mounted on spin coater and MAI was coated at rpm of 3000 for 20 s. Slides were again annealed for 3 min at 40°C and 5 min at 100°C in laboratory oven. Au was thermally evaporated by a mask to define an active area for device of 0.11 cm2.


### 2.3. Characterization

Microstructure and film morphologies were investigated using scanning electron microscope (JEOL JSM6490A) and atomic force microscope JEOL SPM 5200. X-ray diffraction (XRD) studies were done on STOE Stadi MP inθ-2θ mode using Cu Kα source under tube acceleration voltage of 40 KV and tube current of 20 mA. Measurements were recorded with a step size of 0.04° and dwell time of 3 s for each step. ECOPIA HMS-5000 system was used for Hall effect measurements employing Van der Pauw principle. Contacts were made with silver paste on the samples and gold coated spring loaded contacts were used for measurements. Nanovea PS 50 optical profilometer was used to determine the film thicknesses employing Mountains 2D software suite. Cyclic Voltammetry (CV) and impedance spectroscopy were performed using Bilogic EC Lab work station. For CV measurements, platinum counter electrode was used with saturated calomel as reference electrode while the test sample made the working electrode. EC Lab V10.40 software was used for simulation of impedance data. J
-
V parameters were obtained on Keithley 2400 source meter. Newport 67005 solar simulator with AM 1.5 G filter was used at an irradiance intensity of 100 mW/cm2. Voltage step was 10 mV with a step time of 40 ms.


## 2.1. Materials

All the chemicals except CH3NH3I were purchased from sigma Aldrich and were used without further processing. CH3NH3I, (MAI) was sourced from Dysol (MS101000-50). Indium doped tin oxide (ITO) was used as front contact. At 10 mm × 10 mm it had a resistivity of 15 Ω/cm. ITO coated slides were detergent cleaned, washed with flowing ultrapure water, and ultrasonicated in ethanol for 20 min. They were subsequently dipped for one minute in piranha solution, rinsed in flowing ultrapure water, and dried by blowing hot air.


## 2.2. Experimental Details

Titania nanoparticles were synthesized by sol gel route. Titanium isopropoxide (<97%), 2-methoxyethanol (99.9+%), and ethanolamine (99+%) were mixed in 1 : 4 : 0.5 molar ratio. The mixture was refluxed in a three-necked flask in an inert environment and stirred at room temperature for 1 hr and 80°C for 1 hr and finally the temperature was raised to 120°C for 2 hr under constant stirring. Light yellow color of the sol indicated the dissolution of isopropoxide precursor in methoxyethanol solvent aided by ethanolamine as linker. Modified hummers method [40] was used to synthesize graphene oxide from graphite flakes average + 100 mesh (≥75% min).Devices were synthesized by spin coating titania over precleaned ITO coated glass slides at 2500 rpm for 20 s. TiO2 coated slides were dried in oven at 500°C for 2 hr with a heating rate of 10°C per min and were allowed to cool in furnace. CH3NH3PbI3 was deposited by a modified two-step solution processing method. Lead iodide was dissolved in dimethylformamide (DMF) to obtain a 1 M solution. MAI was dissolved in isopropanol at 7 mg/mL. Lead iodide solution was spin-coated on TiO2 coated slides at 3000 rpm for 20 s. Lead iodide coated slides were annealed for 3 min at 40°C and then at 100°C for 5 min. They were removed from oven and then mounted on spin coater and MAI was coated at rpm of 3000 for 20 s. Slides were again annealed for 3 min at 40°C and 5 min at 100°C in laboratory oven. Au was thermally evaporated by a mask to define an active area for device of 0.11 cm2.


## 2.3. Characterization

Microstructure and film morphologies were investigated using scanning electron microscope (JEOL JSM6490A) and atomic force microscope JEOL SPM 5200. X-ray diffraction (XRD) studies were done on STOE Stadi MP inθ-2θ mode using Cu Kα source under tube acceleration voltage of 40 KV and tube current of 20 mA. Measurements were recorded with a step size of 0.04° and dwell time of 3 s for each step. ECOPIA HMS-5000 system was used for Hall effect measurements employing Van der Pauw principle. Contacts were made with silver paste on the samples and gold coated spring loaded contacts were used for measurements. Nanovea PS 50 optical profilometer was used to determine the film thicknesses employing Mountains 2D software suite. Cyclic Voltammetry (CV) and impedance spectroscopy were performed using Bilogic EC Lab work station. For CV measurements, platinum counter electrode was used with saturated calomel as reference electrode while the test sample made the working electrode. EC Lab V10.40 software was used for simulation of impedance data. J
-
V parameters were obtained on Keithley 2400 source meter. Newport 67005 solar simulator with AM 1.5 G filter was used at an irradiance intensity of 100 mW/cm2. Voltage step was 10 mV with a step time of 40 ms.


## 3. Results and Discussion

As-synthesized GO was investigated for quality of exfoliation. XRD profile in Figure S1 in Supplementary Material available online athttp://dx.doi.org/10.1155/2016/8947597 shows peak shifts from 2θ value of 26.47° for graphite to 11.8° for graphene indicating increase in interplaner spacing d from 3.37 Å of graphite to 7.5 Å of graphene due to imbedding of oxygen atoms in graphite lattice [41]. Minor peak broadening at 11.8° reflects good retention of graphite honey comb lattice in exfoliated sheets [42]. Scanning Electron Microscopy (SEM) study revealed exfoliation of graphite into single and multilayer sheets with lateral dimensions in tens of micrometers. Taping mode atomic force microscopy (AFM) images (Figure S2) provided evidence for the quality of exfoliation. Dispersions of GO on silicon wafer were studied to avoid any distortion induced by plain glass slide in height profile along z-axis. Average roughness in the range of 0.3 nm and step height of 0.4–1 nm in the z direction on a flat silicon wafer demonstrates that single sheets of GO have been achieved during the exfoliation process.Anatase titania nanoparticles were synthesized via sol gel route [43]. The sol was spin-coated on glass slides and studied under SEM and AFM. Uniform particle size distribution was achieved giving compact pin hole free blocking layers. Average particle size was estimated at 20 nm with a mean square roughness of 0.182 nm (Figure S3). Film thickness was determined at about 200 nm (Figure S5) XRD profile in Figure 1 of as-pristine titania confirmed anatase phase with sharp peaks attributed to (101), (004), (200), (105), (211), and (204) planes as outlined in JCPDS 21-1272. Obtained pattern confirms highly crystalline nature of the nanoparticles and the absence of rutile phase [44]. Diffraction patterns were also recorded for TiO2-GO composites with different weight fractions but no additional peak could be observed by addition of GO. By very small quantity of GO in the composite and the fact that diffraction peak for GO is at 25.0°, it may be masked by strong diffraction for anatase phase at the same 2θ.Figure 1
(a) AFM micrograph and (b) XRD pattern of TiO2 film.
(a)
(b)Synthesis of titania GO composite was tried by mixing GO in titania sol and aging it for 24 hr and ultrasonication for 30 min before spin coating. The results thus achieved were less than perfect, the sol would form gel during the aging process, and when it did age the film formation was nonuniform. Extensive studies under SEM and AFM revealed that the GO in the composite was not covered by the titania nanoparticles but would appear as an agglomerate on the film (Figure S4). Electrical characterization by four-probe Van der Pauw method did not register any improvements in film parameters. We devised a new method whereby to incorporate GO in required weight fraction at the start of the sol gel reaction as against dispersing GO in the already prepared slurry. This afforded the possibility of incorporation of GO in the sol as a constituent and offers good linking between thin GO films and the particle matrix. SEM micrograph in Figure2 confirms that the films obtained from the sol prepared by this method were pin hole free and homogeneous and with uniform particle size distribution. GO appeared completely imbedded in the particle matrix with even nanoparticle coverage on the sheets.Figure 2
SEM micrographs of TiO2-GO composite prepared byin situ incorporation of GO in sol gel reaction.Complete dispersion of GO in TiO2 has resulted in improvement in resistivity over pristine TiO2 films. These improvements are attributed to superior charge carrier properties of GO, reducing interfacial resistance between TiO2 nanoparticles. GO provides a two-dimensional conductive framework for anchoring of nanoparticles. Though higher GO concentrations resulted in greater reduction of resistivity, the films formed were of poor quality with delamination at GO titania interface resulting in shortening of the devices. Best quality films were obtained with 0.4 wt% of GO in TiO2 and were subsequently used for further studies. This concentration corresponds to the reported optimum for obtaining best GO sheet surface coverage with TiO2 nanoparticles [36]. Resistivity values are tabulated in Table 1 and are in good agreement with reported values [45].Table 1
Resistivity values of TiO2-GO composites.
Sample
Resistivity (Ω·m)
0 wt% GO in TiO2
3.59 × 105
0.1 wt% GO in TiO2
2.76 × 105
0.2 wt% GO in TiO2
2.04 × 105
0.3 wt% GO in TiO2
7.87 × 104
0.4 wt% GO in TiO2
7.33 × 104
0.5 wt% GO in TiO2
3.62 × 104Efforts to reproduce the reported procedure [17] for synthesis of CH3NH3PbI3 under ambient conditions in our lab could not result in uniform films (Figure S8). Modifications were tried and the one being reported resulted in complete surface coverage of the devices with uniform pin hole free morphology. Lead iodide at 1 M solution in DMF was heated to 70°C and was spin-coated on a substrate heated to 50°C under ambient conditions at 3000 rpm for 20 s and subsequently annealed at 40°C for 3 min and 100°C for 5 min. The lead iodide coated films were then mounted on a spin coater and 20 μL of isopropanol was added while the sample was spinning followed by drop-wise addition of MAI solution in isopropanol. During this step the sample was spun at 3000 rpm for 20 s. The films acquired a light brown color. Subsequent to this step MAI solution in isopropanol was added on the slide and was given a soaking time of 20 s and then spun at 3000 rpm for 20 s again. While the sample rotated it was dried with hot air blown on it by a hair dryer. This resulted in rapid crystallization and the film acquired a blackish texture and was further annealed in oven at 40°C for 3 min followed by 100°C for 5 min.Study of lead iodide films (Figure3(a) and Figure S6) reveled a needle like morphology which was transformed to CH3NH3PbI3 upon wetting with MAI solution in isopropanol. The grains grew and the morphology evolved from a needle like structure to a cuboid morphology with grains ranging in submicron size in lateral dimensions. Large area low magnification scan in Figures 3(b) and 3(c) reveals the efficiency of the developed synthesis technique. AFM micrographs in Figure S7 exhibited a surface roughness of 14.5 nm with average grain of the size in microns, thus showing that the grains grow more rapidly in lateral dimension than vertical. Large grain size and large area uniform coverage correspond well with reported observations that humidity has a beneficial effect in grain growth allowing grain boundary creep resulting in larger and uniform coverage [46, 47]. Smaller overall grain boundary surface area avoids energetic disorders allowing reliable photovoltaic performance from ambient air synthesized devices.Figure 3
(a) AFM micrographs of PbI2 film, (b) needle like morphology transformed to cuboids by wetting with CH3NH3I as is evident from AFM image, and (c) low magnification large area SEM micrograph. Scale bars in (a) and (b) represent 2 μm.
(a)
(b)
(c)Strong diffraction intensities at 14.0, 24.3, 28.4, 40.5, 43.0, and 50.3° in Figure4 correspond to reflections from (110), (202), (220), (224), (314), and (404) planes confirming tetragonal phase of absorber [37, 48–50]. Intensities of the signals are an indication of crystallinity of film. In addition to these peaks, peaks for lead iodide can also be observed in the pattern suggestive of residual lead iodide in the films.Figure 4
XRD profile of CH3NH3PbI3.This residual PbI2 is not detrimental to the photovoltaic performance of the devices as residual lead iodide at the boundaries and interfaces has been reported to improve the carrier properties of the films by improved carrier life times and reducing recombination by electrons from titania and holes from CH3NH3PbI3.Optimum titania GO composite was used to prepare complete devices. A 200 nm thick blocking layer was deposited by spin coating. Absorber layer at a thickness of about 400 nm was deposited followed by thermal evaporation of 100 nm Au electrode. Cross section FE SEM image at Figure5(c) demonstrates the device architecture. Current voltage curves for device based on TiO2 only and TiO2-GO blocking layer are presented in Figure 5(a) along with tabulated performance parameters. Performance enhancement for TiO2-GO based devices can be attributed to energetically favorable energy scheme (Figure 5(b)) where GO provides an intermediate step between CH3NH3PbI3 and TiO2. Higher mobility of GO also provides improved conductivity over TiO2 only devices. Higher FF for these devices over TiO2 only devices is an indication of reduced series resistance.Figure 5
(a)J
-
V curves for TiO2 and TiO2-GO based solar cells. (b) Schematic of complete device along with energy levels overlaid on completed device. (c) SEM image of cross section profile of complete device.
(a)
(b)
(c)Quantifiable evidence for the decrease in series resistance and other device parameters was provided by impedance spectroscopy. Impedance spectroscopy (IS) is a very versatile technique and has been extensively employed for analysis of photovoltaic (PV) device including DSSC and polymeric solar cells [51–55]. It affords the opportunity to model and evaluate performance of solar cells in terms of equivalent circuit offering an opportunity to improve the performance by addressing target components in terms of equivalent resistance values. IS was obtained for the prepared devices from a frequency range of 1 MHz to 500 mHz at bias voltage between 100 mV and 800 mV and oscillation potential amplitude of 20 mV. Simulated circuit element values are presented in Figures 6 and 7 while Nyquist plots are depicted in Figure 8. They reflect a typical feature characteristic for solar cells commonly described using a transmission line model [56].Figure 6
R
s, R
s
c, and R
r
e
c plots for TiO2 and TiO2-GO based devices, with equivalent circuit.Figure 7
R
s, R
s
c, and R
r
e
c plots for TiO2 and TiO2-GO based devices obtained at different temperatures. Legend along each plot indicates the test conditions.Figure 8
Nyquist plots for TiO2 and TiO2-GO based devices; (a), (b), and (c) are plots at 25, 40, and 60°C, respectively.
(a)
(b)
(c)Two RC elements with a series resistanceR
s have been used as equivalent circuit to model the experimental results. Resistances associated with ITO and circuit wires are demonstrated by R
s and an additional RC component models the contribution due to shunt resistance and the capacitance of the active layer. Constant phase elements are used instead of ideal capacitors for better data fit. They are part of an equivalent circuit depicted in Figure 6.Nyquist plots present two characteristic arcs, one low frequency and an intermediate frequency arc. While the intermediate frequency arc is associated with recombination in the active layer, the source of low frequency arc is debated. Some associate it with ferroelectric domain wall controlled charge accumulation [57] while others have attributed it to the trap state distribution in CH3NH3PbI3 [51]. Another thought is for the difference in electron affinities at the perovskite interfaces being the source of this feature [58]. Some have even postulated that it has no bearing on the device physics and have left it out of the curve fitting process [25]. In DSSCs, this low frequency feature was associated with ion migration in liquid electrolyte; evidence of ionic mobility in CH3NH3PbI3 has been presented [59, 60] and can be the source of this low frequency feature in CH3NH3PbI3 based devices.Graphical trend for the values ofR
s,  R
s
c, and R
r
e
c is depicted in Figure 6. R
s and R
s
c contribute to the total series resistance [58] and the addition of GO in TiO2 matrix results in lowering of the total series resistance. Since IS measurements are not sensitive to the photocurrent, only FF and V
o
c are the parameters that can be attributed to the calculated values [56]. The decrease in series resistance is the cause of increased FF for devices with titania GO composites.Recombination rate in the active layer can be demonstrated by the variation of the recombination resistance with bias voltage.R
r
e
c is calculated from the intermediate frequency feature of the Nyquist plot [58]. The higher the recombination resistance, the lower the recombination rate and vice versa. Recombination rates dictate the value of  V
o
c; thus lower recombination rate translates into higher V
o
c. Slope of R
r
e
c presents an idea of the FF of the devices; lower slope represents a higher FF. With the addition of GO in TiO2, the value of R
r
e
c is increased for the composite validating the observation of higher V
o
c for the devices based on nanocomposite electron selective contact.Capacitance values associated with intermediate frequency arc are associated with charge accumulation or separation with the absorber interfaces. The values do not change with the changing potential and remain almost constant for the entire potential range at the order of 10−9 F cm−2. Variation of bias voltage results in increasing carrier densities and the invariance of capacitance with this increasing density is another manifestation of the long diffusion lengths for CH3NH3PbI3 absorbers [61].In order to evaluate the performance of devices at elevated temperatures, impedance measurements were repeated by heating the samples at 40°C and at 60°C. A decreasing trend ofR
s and R
s
c with an increase in R
r
e
c with the increase of temperature to 40°C can be inferred as an evidence of the increase in the photovoltaic performance of the devices under study. Increasing the temperature to 60°C results in sharp increase in R
s and R
s
c along with decay in the value of R
r
e
c. This trend demonstrates a decreasing performance of devices at 60°C. This decrease in performance can be associated with phase change of CH3NH3PbI3 from tetragonal phase to cubic phase at 55°C [62]. Additionally, the difference in the coefficient of thermal expansion mismatch can have a deleterious effect with increasing temperatures [63]; this increased mismatch increases the defect states which associated with higher recombination rates at the interface effects the density of states. Increase of recombination rate is manifested by a decrease of R
r
e
c values in impedance plot and the interfacial mismatch and increased defect densities resulting in increase of series resistance by increasing R
s
c.Devices were stored under ambient air conditions for 1000 hr without encapsulation and tested again; devices retained 73% of original efficiency. Enhanced stability can be explained by the band gap modification of TiO2 with incorporation of GO causing a shift to the visible spectrum [64]. Titania is a wide band gap semiconductor and affords efficient electron uptake from active layer with high mobility and solution processability under ambient conditions. A band gap of 3.2, photoexcitation, is achieved in UV range and is typically employed as photocatalyst for oxidation of organic matter [65].Degradation mechanism for CH3NH3PbI3 at the interface of titania is postulated as [66](1a)
2
I
-
⟷
I
2
+
2
e
-
at the interface between
TiO
2
and
CH
3
NH
3
PbI
3
(1b)
3
CH
3
NH
3
+
⟷
3
CH
3
NH
2
↑
+
3
H
+
(1c)
I
-
+
I
2
+
3
H
+
+
2
e
-
⟷
3
HI
↑Titania acts as an oxidizing agent for I
-, at the interface, resulting in the loss of perovskite crystal structure by forming lead iodide and CH3NH2, which is rapidly lost due to its low bp of 17°C. Systematic studies have addressed the issue of UV sensitivity by using interfacial layer of Sb2S3, UV filters, employing zirconia or alumina scaffolds and aluminosilicate shells around titania particles [67–69]. UV sensitivity of this interface can be addressed if the absorption edge of titania can be shifted to visible range. It has been demonstrated that the absorption edge of titania can be shifted to visible range due to electronic coupling between p states of the imbedded graphene and the titania conduction band [70].Band gap of titania GO composite in our work was investigated using CV (Figure S9) and HOMO/LUMO levels were calculated by the following equations:(2a)
E
HOMO
=
-
E
ox
onset
-
4.8
eV
(2b)
E
LUMO
=
-
E
red
onset
-
4.8
eV
.Band gaps obtained with changing GO concentrations are tabulated (Table 2). Shift in band gap can be a possible source for improved efficiency of the devices addressing the degradation mechanism at titania CH3NH3PbI3 interface.Table 2
Band gaps for different concentrations of TiO2-GO composite.
Composition
Band gap (eV)
Titania
3.18
0.1 wt% GO
3.11
0.2 wt% GO
3.05
0.3 wt% GO
2.99
0.4 wt% GO
2.95Planer geometry CH3NH3PbI3 cells have been associated with hysteresis in J
-
V curves. Low hysteresis observed in our devices may be because of the low efficiencies as compared to the extremely efficient cells with record efficiencies. Another thought can be because of the interface engineering effects at the electron selective contact and CH3NH3PbI3 and TiO2 interface with TCO because of the addition of GO that can be attributed to this reduction in hysteresis [46, 71, 72]. A potential barrier to electron transfer exists at CH3NH3PbI3 TiO2 interface as demonstrated by Xing et al. [73, 74] and any improvement in the charge collection efficiency at this interface can result in improved photovoltaic performance and reduced hysteresis. Jena and coworkers have presented conclusive evidence that hysteresis observed in these devices not only is because of the bulk properties of the CH3NH3PbI3 like ion migration and ferroelectric behavior but also is strongly affected by the interfaces associated with the bulk of the material [75]. A missing interface at CH3NH3PbI3 HTL junction has the advantage of reducing hysteresis combined with modified electron selective contact at the other interface. Any modification of TiO2 which reduces the trap states effects the buildup of capacitance at the interfaces by allowing rapid charge collection. Also band alignment of TiO2 at the TCO and CH3NH3PbI3 end can affect the band bending during forward and reverse scan directions. Passivation of the trap states, enhanced electron mobility, and suitable band alignments are all the benefits associated with TiO2-GO nanocomposite, which can be a possible reason for low J
-
V hysteresis in studied devices.


## 4. Conclusions

We demonstrated a CH3NH3PbI3 solar cell using TiO2-GO nanocomposite as electron selective contact in a hole transport layer free architecture. Ambient air synthesis route was adopted and PCE of 5.9% was achieved. Novel technique is introduced to obtain TiO2-GO nanocomposite byin situ incorporation of GO during the sol gel reaction. Band gap was engineered for higher stability of the devices. Incorporation of GO had a synergetic effect by passivation of the trap states in TiO2. This along with band gap engineering may be responsible for reduced hysteresis effects. Enhanced stability, reduced hysteresis, and an ambient air synthesis route with hole transport layer free geometry have the potential to reduce cost and enhance commercial viability of this technology.



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