Facile Preparation, Characterization of Flexible Organic Solar Cells Using P3HT-MWCNTS Composite Photoactive Layer ()
1. Introduction
Recently, organic electronics based on conducting polymers (CPs) has been increasingly interesting because CPs have many advantages, such as they can be easily prepared in thin films, their bandgap (the gap between the Lowest Unoccupied Molecule Orbital (LUMO) and the highest occupied Molecule Orbital (HOMO) can be adjusted by chemical methods. CPs have been applied in organic light-emitting diodes (OLEDs), Organic Gas Sensors (OGS), Organic Solar Cells (OSC), etc. [1] [2] [3] [4] [5]. Among the CPs, poly(3-hexylthiophene) (P3HT) is mostly used for OGSs and OSCs because P3HT possesses a rather narrow energy bandgap (1.93 - 1.95 eV [6] ) enabling it to absorb a large solar energy spectrum. P3HT is served as an electron donor material [7], while [6,6]-phenyl C61-butyric acid methyl ester (PCBM) is used as an electron acceptor one [8]. Comparing to c-Si cells, the production for both the materials and devices of OSCs requires less expensive equipment: instead of the crystal growth, the liquid-phase epitaxy and the ion implantation, simple techniques like spin coating or sol-gel dip coating can be used for making thin films of the P3HT-based photoactive layer. However, the photoelectrical conversion efficiency (PCE) of OSCs is much lower than that of c-Si cells. This is mainly due to the strong decay of the excitons or electron-hole pairs (EHPs), that is generated in the donors/acceptors junctions owing to the solar radiation. A way to eliminate the probability of the EHPs recombination is embedding inorganic particles into the photoactive layer to form a nanocomposite material, resulting in so-called charge separation. Thomas et al. [9] and Liu et al. [10] have shown that the PCE can be enhanced by the use of composite photovoltaic materials. We have also demonstrated that using a nanocomposite P3HT + nc-TiO2 as the photoactive layer, the PCE of OSCs has maintained value as large as 1.2% at a temperature of 130˚C due to the enhancement of the thermal endurance [11]. It is well-known that carbon nanotubes (CNTs) possess remarkable properties for applications in molecular electronics, energy storage, sensors, new composites for solar cells, etc. Cai et al. [12] have used a composite of P3HT and bamboo-structured CNTs for the efficient hole transport layer (HTL) in CH3NH3PbI3I-based perovskite solar cells. The PCE of the cells increased in more two times (namely from 3.6% for pristine P3HT to 8.3% for P3HT + CNT). Mombrú et al. [13] have used multiwalled carbon nanotube (MWCNT) mixed with poly(3,4-ethylene dioxythiophene): poly(styrene sulfonate) composites (PEDOT: PSS-MWCNTs) for electrodes in solar cell applications. The authors showed that the large out-of-plane conductivity of the devices was much improved due to the addition of MWCNTs in the PEDOT: PSS films. Kuila et al. [14] pointed out that both the HOMO and LUMO energy levels of the P3HT+CNTs material served as the photoactive layer were lowered comparing with those of pristine P3HT. Jun et al. [15] fabricated OSCs using reduced graphene oxide (rGO)/P3HT: PCBM as a photoactive layer. The authors denoted that the PCE of the device can be much enhanced by both the charge selectivity and effective charge transport of rGO in P3HT polymer. The largest PCE was found to be of 4.5% for the OSCs using rGO doped with 5.0 wt% of nitrogen. However, for producing the devices, ITO-coated glass served as the transparent conducting electrode (TCE) and PEDOT-PSS—as the HTL were used. Recently [16], we prepared rGO-P3HT films with electrical and optical properties suitable to TCEs using for optoelectrical devices, especially OSCs.
In this work, we present a facile method for producing MWCNTs-P3HT: PCBM-based OSCs without ITO-coated glass substrate and PEDOT-PSS layer. The absorption and photoluminescence properties of the composite photoactive layer as well as the photoelectrical conversion performances of the devices were also presented.
2. Experiment and Method
The photoactive films were prepared by spin coating method that was described elsewhere [11]. To compare the photoactive properties of a pristine P3HT and a P3HT + MWCNTs composite (abbreviated to P3CT) as well as the performance parameters of the devices, pristine P3HT and P3CT films were prepared with the same technological conditions. The MWCNTs of 30 - 50 nm in diameter and rGO of 99.9% purity were supplied by the Institute of Materials Science, Vietnamese Academy of Science and Technology (VAST). rGO-P3HT-coated PET (transparent conducting substrate), further called GPP, was used as an anode. These GPP flexible substrates (with a sheet resistance of ca. 50 Ω and a transmittance of ca. 85%) were produced following the procedure as described in [16]. The aluminum (Al) coating was used for a cathode and also for a reflecting mirror. P3HT solutions were prepared by dissolving 8 mg of P3HT powders in 1 ml of chlorobenzene. To prepare P3HT-MWCNTs composites, MWCNTs were mixed in P3HT solution by a MWCNTs/polymer weight ratio of 0.015 to 0.030 and 0.050 (namely 1.0, 3.0 and 5.0 wt%). Further, the devices with the additive of 1.5, 3.0 and 5.0 wt% MWCNTs are abbreviated to P3CT-15, P3CT-30 and P3CT-50, respectively. Uniform distribution and a complete dispersion of MWCNTs in P3HT were obtained by magnetically stirring the solutions for 12 h. Next step, pristine P3HT and P3CT solutions were spin-coated onto the GPP substrates according to conditions: a delay time of 120 s, a rest time of 30 s, a spin speed of 1500 rpm, and an acceleration of 500 rpm, and finally a drying time of 2 min. All the sample then were annealed in an exceed nitrogen pressure (namely 1.05 at) at a temperature ranging from 120˚C to 180˚C for 8 h. The thickness of P3HT and P3CT layers deposited in our experiments has a value of 100 nm. For photoluminescence and UV-Vis measurements, P3HT and P3CT films of the same thickness were coated onto corning-247 glass substrates. A 50 nm-thick fullerene derivative 1-(3-methoxycarbonyl) propyl-1-phenyl[6,6]C61 (PCBM) served as the acceptor layer was then deposited onto both photoactive layers (namely P3HT and P3CT). Finally, LiF/Al electrodes (served as the shallow contact [11] ) was successively evaporated (30 nm for LiF and 70 nm for Al) onto PCBM layer, using a mask with windows of 5.0 mm × 5.0 mm in size (the active area of the cells was of 0.25 cm2). Thus, two types of OSCs with a structure of GPP/P3HT/PCBM/LiF-Al and GPP/P3CT/PCBM/LiF-Al were prepared. The structure of a typical of the composite device is presented in Figure 1. The thickness of all the functional layers (anode, photoactive film, PCBM and cathode) is of ~350 nm that is negligible comparing to the PET substrate (i.e. 350 nm compared to 350 μm). Thus the device thickness can be seen as the thickness of the PET substrate.
The surface morphology pictures MWCNTs and composite samples were made by using a High-Resolution Transmittance (HR-TEM) and Field-Emission
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Figure 1. Schematic drawing of a PET/rGO-P3HT/P3CT/PCBM/LiF/Al device made from the functional layers with shown thicknesses.
Scanning Electron Microscopy (FE-SEM), respectively (“Hitachi” Ltd.). The photoluminescence (PL) spectra and the ultraviolet-visible absorption spectra of the samples were carried out on a HORIBA “FL3-2” spectrophotometer and a JASCO UV-VIS-Nir “V570”, respectively. The photocurrent density-voltage (J-V) characteristics of the two types of the OCSs were measured on the current-voltage unit under radiation of 100 mW/cm2 (or AM1.5) taken from “Sol 1A” Newport solar simulator source.
3. Results and Discussion
3.1. Morphology, Photoluminescence and UV-Vis Analysis
Figure 2 shows the surface morphology of MWCNTs and P3CT film with a percentage of 3.0 wt% MWCNTs. This figure demonstrates that the MWCNTs were well embedded in the polymer. The heat treatment at the above-mentioned temperatures not much affected on the morphology of the films, thus negligible differences in the morphology of the sample were observed when annealed at Ta of 120˚C to 160˚C and 180˚C. From preliminary measurements of the current-voltage (I-V) characteristics, it was found that the samples annealed at 160˚C exhibited the best I-V performance. Thus, for further investigations all the samples concerned were annealed at 160˚C for 8 h.
Prior to choose an appropriate composition in the composites used for photoactive layers, we investigated photoluminescent properties of both the pristine polymer and composite films, namely P3HT and P3CT mixed with different concentrations of MWCNTs. The aim of the investigation is searching for the composite which has the strongest photoluminescence quenching effect which indicates the largest possibility of the charge separation in the photoactive layer. The PL spectra of the samples measured at an excitation wavelength of 470 nm are presented in Figure 3.
Strong luminous quenching of the samples was observed at wavelengths around 580 nm (corresponding to π-π* bonding in P3HT). The effect of the luminous quenching proves the electrons transport from the LUMO band of P3HT to the LUMO band of PCBM, and holes—from HOMO band of P3HT to the HOMO of MWCNT through the P3HT/PCBM and P3HT/MWCNT heterojunctions in the nanocomposite, respectively. The quenching efficiency can be
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Figure 2. (a) TEM image MWCNTs and (b) FE-SEM micrograph a composite film with the MWCNTs/P3HT ratio is 3.0 wt% annealed at 160˚C, for 8 h.
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Figure 3. PL spectra of a pristine P3HT (a) and composite films with the MWCNTs additive of 1.5 wt% (b), 3.0 wt% (c) and 5.0 wt% (d). The excitation wavelength λ = 470 nm.
qualitatively estimated by a relative quenching coefficient (χ, %) that is calculated by following equation.
(1)
where Ip and Ic are the intensities of the PL peak of polymers and composites, respectively.
Taking values of Ip and Ic from Figure 3 and applying Equation (1), χ was found to be of 18%, 72% and 47%, respectively for 1.5, 3.0 and 5.0 wt% MWCNTs embedded in P3CT films. Thipperudrappa et al. [17] showed that the fractional intensity Ip/Ic is given by the product of both static and dynamic quenching. The authors also denoted that instantaneous or static quenching occurs if the quencher substances are very near to, or in contact with fluorescent molecules at the moment of its excitation. In other words, the electron-hole pairs generated at the heterojunctions (i.e. P3HT/MWCNTs interfaces) are not recombined; they are separated from each other, resulting in the luminous quenching of polymeric composite thin films. This is a specific property that is desired for designing an OSC with the large PCE. The fact that the quenching is closely involved to the charge separation proves that the luminous quenching can be considered as a useful factor for choosing a combination of conducting polymers and inorganic nanoparticles used for devices fabrication. Thus, in our experiments, the P3HT with an additive of 3.0 wt% MWCNTs (i.e. P3CT-30 sample) possessing the largest χ (72%) can be used for making photoactive layer in P3HT-MWCNT based solar cells.
Next, the absorption spectra of both P3HT/glass the P3HT-30/glass samples wre characterized. To eliminate the glass absorption, the absorption spectra of both the pristine P3HT and P3CT-30 films were measured under a baseline regime. The measured results are presented in Figure 4(a), showing a clear difference in absorption related to π-π* bonding for two samples, at the wavelength around 550 nm, in particular. At this wavelength, comparing to the P3HT, the composite film much stronger absorbed, namely the absorption coefficient of the composite sample is nearly 30% larger than the one of the pristine P3HT. The π-π* absorption peak of the pure P3HT and P3CT-30 composite film is located at 555 nm and 545 nm, respectively. This blue-shift was attributed to the more disordered chain conformation in P3HT embedded with MWCNTs [14]. The authors pointed out that the disordered conformation in the P3HT chain results in a more amorphous structure in the composite film.
To determine the gap between HOMO and LOMO of a conducting polymer that is similar to the energy bandgap (Eg) of the inorganic semiconductors, one can use data obtained by UV-Vis spectra measurements. It is known that the relationship between the bandgap and absorption coefficient of the semiconducting materials are expressed by the following formula [18]:
(2)
where h is Planck’s constant, ν is the frequency of the incident UV-Vis radiation, A is a constant and n is 1/2 for direct band semiconductors and 2 for indirect bandgap semiconductors.
For both the P3HT and P3CT samples, n = 2 is the best fit. The hν-dependences of (αhν)1/2 of the samples are plotted in Figure 4(b). Extending the linear hν-dependence of (αhν)1/2 to cross the abscissa, the value of Eg of the P3HT and P3CT-30 films was found to be 1.95 eV and 1.93 eV, respectively. The first value
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Figure 4. UV-Vis spectra of a pristine P3HT and a P3CT-30 films (a) and the plots of (αhν)2 vs. photon energy (hν) for their Eg determination (b).
is rightly Eg value as reported by Ren et al. [6] when P3HT was prepared for the hybrid solar cells. The smaller value in the bandgap of the composite film (1.93 eV) is explained by the lowering LUMO energy level of the polymer due to the presence of the MWCNTs [14]. The absorption of the P3CT films in the wavelengths range from 400 nm to 600 nm is much larger comparing to the pristine P3HT film. This fact proves the advantage in the solar energy absorption of the composite-based photoactive layer in comparison with the pristine polymer.
3.2. Characterization of Device Performance
Performance parameters of a PV device such as open-circuit voltage (Voc), short-circuit current density (Jsc) and the fill factor (FF) were determined from experimental data obtained from voltage dependence of the current density, namely J-V characteristics. Figure 5 shows the J-V curves of the two devices, pristine P3HT and P3CT-30, under illumination with a power density of 100 mW/cm2.
The FF of the devices is calculated from the following formula:
(3)
where (J × V)max is the largest value from all the J ´ V. The photoelectrical conversion efficiency, PCE, denoted as η, can be determined by:
(4)
where Pin is the density of the illuminating power, in mW/cm2. In our experiments Pin = 100 mW/cm2). All the values of the performance parameters determined from J-V curves and Equations (3) and (4) are listed in Table 1.
Comparing to the pristine-polymer device, the Voc of the P3CT-30 is negligibly smaller (0.87 V compared to 0.89 V), but the Jsc is much larger (5.05 mA/cm2 to 4.1 mA/cm2). The fact that the FF of the P3CT is larger than that of P3HT based OSC proves that the intrinsic resistance of the composite device is smaller than the one of the pristine-polymer device. This is due to: 1) the presence of rGO in the TCE and 2) MWCNTs in P3HT polymer. Using a scheme of the energy levels demonstrated in Figure 6 that is built up from the data of the energy bandgap structure of the single components in the photovoltaic cell (shown f.i. in [14] and [19] ), one can explain the increase in the Jsc of the P3CT-30 device.
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Table 1. Experimental data of performance parameters of pristine-polymer and composite-based OSCs.
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Figure 5. “a” is the J-V characteristic of a pristine P3HT-based device and “b”—J-V of the P3CT-30 based device.
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Figure 6. Scheme of the energy levels of single components of the composite solar cell embedded with MWCNTs. The dashed and solid arrows indicate hole and electron movement directions, respectively.
From Figure 6 one can see that due to a high value (namely 5.1 eV) of the work function, MWCNTs favor holes injection from the polymer blend to the nanotubes. This results in a fast extraction of them to the electrode. Indeed, as reported in [20], acting as the exciton dissociation sites, MWCNTs embedded in P3HT have contributed to a considerable increase in the power conversion efficiency of the composite device. Although the flexible GPP used for the anode in the device has a transmittance lower than that of the standard ITO-coated glass, the PCE of the composite OSC attained a value as large as 2.35% that is still small in comparison to the PCE of the inorganic solar cells. Taking advantage of the facile preparation of large-area OSCs, one can expect potential applications of the flexible TCE and MWCNTs-additive photoactive layer for solar power production.
4. Conclusions
MWCNTs were embedded with an optimum percentage of 3.0 wt% in conducting polymer, P3HT, for the photoactive layer in the flexible solar cells PET/rGO-P3HT/P3CT/PCBM/LiF-Al. Characterization of the UV-Vis absorption spectra of the photoactive films as well as the current-voltage curves of the devices showed that the composite OSCs exhibited a much larger photoelectrical conversion efficiency in comparison with the polymeric solar cell. Under illumination of light with a power density of 100 mW/cm2, the following parameters of the cells were obtained: Voc = 0.87 V, Jsc = 5.05 mA/cm2, FF = 0.54, PCE = 2.35%.
The obtained results suggest further useful applications of the flexible solar cells for effective solar power conversion, in terms of rolled large-area photovoltage panels.
Acknowledgements
We thank Dr. Bui Hung Thang (Institute of Materials Science, VAST) for supplying us with pure MWCNTs and rGO materials. The authors (from ARGD) express sincerely thanks to VNU-University of Engineering and Technology (VNU-UET) for the financial support under project number CN20.05.