Self-assembled Materials

Liquid crystals in photovoltaics: a new generation of organic photovoltaics

  • Polymer Journal volume 49, pages 85111 (2017)
  • doi:10.1038/pj.2016.109
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This article presents an overview of the developments in the field of organic photovoltaics (PVs) with liquid crystals (LCs). A brief introduction to the PV and LC fields is given first, followed by application of various LCs in organic PVs. Details of LCs used in bilayer solar cells, bulk heterojunction solar cells and dye-sensitized solar cells have been given. All the liquid crystalline materials used in PVs are structured and the efficiency of solar cells is tabulated. Finally, an outlook into the future of this newly emerging, fascinating and exciting field of self-organizing supramolecular LC PV research is provided.


For the sustainable growth of the global economy, availability of cheap energy is essential. Our energy demand is increasing continuously to improve our lifestyle. At present, fossil energy sources are the primary sources for most of the world’s current energy requirements and only a little is provided by hydropower, nuclear energy and biomass. The exponential growth of carbon dioxide level in the atmosphere owing to the burning of fossil fuels is leading to the threat of a universal climate change. Moreover, there will be limited availability of conventional energy sources in the long term. Future energy demand cannot be met with conventional sources of energy. Nuclear energy sources are one of the promising energy sources, but owing to their associated hazardousness and cost effectiveness, these energy sources does not appear to be socially acceptable universally. Moreover, nuclear fuel is also limited to tackle gigantic demand of energy. Despite several efforts, the problem of energy provision around the world remains unsolved, and there is a great need of finding alternative clean energy sources. To solve the energy crisis of the globe, exploitation of solar energy is undoubtedly the best answer. It is the most abundant inexhaustible source of regenerative energy. It is known since the evolution of life on the Earth that Mother Nature generates chemical energy from solar energy via photosynthesis. The supply of energy by Sun on Earth in an hour is more than that we use in a year. Therefore, only a fraction of solar energy is required to overcome our all energy requirements, if it can be converted to electric energy efficiently. The device that is developed to convert solar energy into electrical energy is known as photovoltaic (PV) solar cell.

During the past 60 years, PV energy has been used as a promising candidate for energy devices because it is abundant, inexhaustible, cheap, straight to production ability and pollution-free that does not raise the green-house gases. The PV effect involves the generation of a photocurrent and photovoltage on absorption of light photons in a semiconductor. The three-step process, which is an important process for the conversion of light to electrical or chemical energy, includes the light-induced exciton (electron–hole pair) generation, separation and migration of electrons and holes in outer circuit. Inorganic semiconductors, such as Si, GaAs, CdSe and so on, have often been used owing to their high charge-carrier mobility and stability. High cost of these electronic-grade materials and processability are the main concerns in utilizing inorganic semiconductors. Therefore, recently organic semiconductors have attracted much attention for solar cell materials owing to their low cost processing, fabrication on both hard and flexible substrates, large-area application and the availability of unlimited variety of organic molecules with different opto-electronic properties.

Organic semiconducting materials is a field of intense scientific activity because of their potential application in electronic and opto-electronic devices, such as field effect transistors, light-emitting diodes, sensors and PV cells.1, 2, 3, 4, 5, 6 During the past decade, organic solar cells have attracted considerable attention owing to their outstanding characteristics, such as potential low-cost fabrication, utilize high throughput, light weight, flexibility and easy processability with efficiency upto 10 %.7, 8, 9, 10, 11 Organic PVs (OPVs) has been the subject of enormous scientific interest and therefore has been covered in many reviews, special issues and books.12, 13, 14, 15, 16, 17, 18, 19, 20, 21, 22 Significant attention has been given to overcome technological and materials problems in order to develop these OPV devices, which can perform better than inorganic PV devices. In recent years, several researches are conducted to improve the efficiency of organic solar cells and thereby realized applications, such as lightweight or flexible power sources.8 Organic solar cells have better potential than conventional solar cells owing to their easy fabrication with the common vacuum evaporation technique, spin-coating, inkjet printing, doctor-blading, drop-casting, screen printing and roll-to-roll printing. In addition to that, they can be readily processed on flexible substrates and devices could be translucent.

The operation mechanism of light conversion in OPV cells is based on charge generation at the interface between two different organic semiconductors, followed by their separation and migration toward opposite electrodes. These cells are known as heterojunction solar cells.9 In these heterojunction solar cells, the transportation of the holes and electrons is conducted through organic p-type and n-type semiconductors and the spontaneous charge flow produces electricity. The concept of heterojunction was first introduced using bilayer structures5 where a layer stacking of donor and acceptor molecules with a planar interface (Figure 1) is realized. This provides a spatially uninterrupted pathway for the photogenerated charge carriers to the respective electrodes.23 However, creating an organic bilayer structure is not easy and economical, and therefore the concept of bulk heterojunction (BHJ) is realized. Figure 1 represents the device structures of bilayer heterojunction (a), BHJ (b) and the fundamental steps occurring in donor–acceptor heterojunction solar cells with the highest occupied molecular orbital/lowest unoccupied molecular orbital (HOMO/LUMO) electronic band gap structure (c). In a bilayer heterojunction solar cell, both donor and acceptor materials are separately layered with cathode and anode while in BHJ a nanoscale blend of both donor (D) and acceptor (A) is used as active layer. The nanometer domain sizes of this blend allowing the excitons with short lifetimes to reach at an interface and dissociate owing to the large donor–acceptor interfacial area. An energy-level diagram and the conversion process are given in Figure 1c to illustrate the principle of operation of the conversion of energy. The ionization potential of the D is low and has high EHOMO, whereas the A has a high electron affinity (EA) and low ELUMO. When the light incidents on the surface, excitons (electron–hole pair) are formed in the material (1), these photogenerated excitons diffuse to the interface (2), electrons and holes are separated; electrons migrate to acceptor (3) and holes migrate toward anode (4). Charge separation is energetically favorable when

Figure 1
Figure 1

Device structure of (a) bilayer heterojunction, (b) bulk heterojunction, (c) device working principle with electronic HOMO/LUMO structure and (d) schematic illustration of charge separation at donor–acceptor interface ((1) exciton formation, (2) diffusion of exciton to interface, (3) dissociation and (4) charge transport in the active layer of organic photovoltaic solar cell). A full color version of this figure is available at the Polymer Journal online.

Many different types of organic materials have been used in OPVs, for example, small molecules, polymers, oligomers, dendrimers, organic dyes and liquid crystals (LCs). Owing to the paucity of space, it is not possible to cover the developments happened in all types of OPV cells; therefore, this article deals only with the use of LCs in OPVs.

A brief overview of LCs

LCs, also referred to as mesophases, are materials that have the properties of both crystals and liquids. These materials show order and mobility at molecular, supramolecular and macroscopic levels. LCs are accepted as the fourth state of matter after the three classical states of matter: solid, liquid, and gas. LCs are ubiquitous in everyday life in the form of LC display devices, thermal sensors and so on. They are not only important in materials science but also in living systems and in biology.24 Several bio-molecules, such as DNA, lipids and proteins, form various liquid crystalline phases under appropriate conditions.24 The appearance of mesomorphism in DNA fragments (nano DNAs) has been related to the significant role of LCs in the evolution of life in the prebiotic world.25

LCs are classified in various ways, such as: depending on the molar mass of the constituent molecules, low molar mass (monomeric and oligomeric) and high molar mass (polymeric) LCs; depending on the process by which the liquid crystalline phase is obtained, whether by adding solvent (lyotropic) or by changing the temperature (thermotropic); depending on the nature of the constituent molecules (organic, inorganic, ionic, organometallic); depending on the geometrical shape of the molecules (rod-like, disc-like); and depending on the arrangement of the molecules in the liquid crystalline phase (nematic, smectic, columnar, helical, B phases and so on). The most common class of LCs commonly known as calamitic LCs are derived from rod-like molecules.26 They have primarily been exploited for their applications in LC displays.27 Calamitic LCs were discovered more than a century ago in 1888 when Reinitzer28 noticed an unusual double melting behavior of cholesterol benzoate. For about 90 years, it was believed that only rod-like (calamitic) molecules can form LCs when Chandrasekhar et al.29 synthesized and realized the LC phases of disk-like molecules. These are now commonly referred to as discotic LCs (DLCs). Both calamitic and discotic mesogens exhibit nematic (having only long-range orientational order) or higher order smectic and columnar phases (Figure 2).

Figure 2
Figure 2

Schematic representations of nematic-, smectic- and columnar-phase formation by calamitic and discotic mesogens.

Another variety of LCs in which usually two calamitic molecules are joined via a central bent unit is classified as banana or bent-core LCs.30 Though they were known in literature as calamitic LCs since 1929,31 their ferroelectric properties owing to the formation of chiral mesophase are realized only in 1996.32 Although bent-core LCs have not been much studied for PV properties, both calamitic and DLCs are explored to fabricate PV solar cells. As the story of LC PVs started with DLCs, we begin our discussion with these systems.

Discotic LCs

The self-organization of disc-like or plate-like molecules leads to the formation of DLCs. A majority of DLCs are composed of polycyclic aromatic cores, such as triphenylene (TP), anthraquinone, phthalocyanine (Pc) and so on, surrounded by plural number of flexible aliphatic chains.33, 34 The strong π–π interactions between aromatic cores favor columnar stacking of the molecules. The columnar mesophase is formed owing to the self-assembly of rigid disc-shaped aromatic cores, which consists usually 6–8 peripheral molten aliphatic chains with mobility. The separation between core–core (intracolumnar) is generally of the order of 0.35 nm while the separation between neighboring columns (intercolumnar) is in the range of 2–4 nm. This assembly of molecules gives more interaction between neighboring molecules within the same column compared with the neighboring column. In this columnar arrangement of aromatic cores, each column acts as a molecular wire where the electrons or holes migrate efficiently along the columns in quasi one dimension (Figure 3). Owing to this unidirectional arrangement, the electrical conductivity along the columns have been observed to be many orders of magnitude greater than that in perpendicular direction.35 Because of this behavior, DLCs could be used in opto-electronic devices, such as PV solar cells, light-emitting diodes and gas sensors. Owing to the technological applications and fundamental importance of DLCs, they have received much attention of the scientists around the globe thtat has been reviewed in several articles.33, 34, 36, 37, 38, 39, 40, 41, 42, 43, 44, 45, 46, 47, 48, 49, 50, 51

Figure 3
Figure 3

One-dimensional charge migration in DLCs.

In comparison to other organic semiconducting materials such as single crystals and conducting polymers, DLCs possess many advantages. Both p-type and n-type DLCs can be easily designed and synthesized, their optical and electronic properties can be tuned via proper chemical modifications, they can be easily obtained in very high purity, they can be aligned parallel to the electrode surface (homeotropic alignment) for better one-dimensional charge migration (Figure 3), they display self-healing of structural defects owing to their fluid nature, they are soluble in common organic solvents and possess low melting point and therefore can be economically processed.52

Long exciton diffusion length and high charge-carrier mobility are the key factors to realize efficient OPV solar cells. Some DLCs exhibit very good exciton diffusion length (~70 nm) and very high charge-carrier mobility (~1 cm2 V−1 s−1).53 The simulated defect-free DLC assembly was reported to have the mobility in excess of 10 cm2 V−1 s−1.54 The charge-carrier mobility in organic materials may be correlated with the molecular structure and packing of constituting molecules. In DLCs, the charge-carrier mobility is expected to improve upon the close stacking of the columns, and the molecular order could be enhanced by enlarging the size of polycyclic aromatic core as a result of intense π–π interactions. A speculative relationship between charge mobility and core size has been proposed,55 Several large polycyclic aromatic hydrocarbon cores, defined as ‘nano-graphenes’ have been explored by Müllen and co-workers to build various DLCs.39, 45, 56 The dispersion of large-size discotics in archetypal DLCs is reported to improve physical properties of the system significantly owing to complimentary polytopic interactions.57 In another innovative approach, we realized that the conductivity of DLCs can be enhanced by several orders of magnitude by dispersing a very small amount of metallic, semiconducting or carbon nanoparticles.58, 59, 60, 61, 62, 63, 64, 65, 66, 67

Since the discovery of DLCs, there has been tremendous interest in utilizing these materials as one-dimensional semiconductors. Conducting and photoconducting properties of DLCs have been studied extensively.50, 68 Owing to their excellent charge-transport property, DLCs have been applied to prepare bilayer and BHJ solar cells.6 They have also been used as additives in solar cells69, 70, 71, 72 and also as electrolyte in dye-sensitized solar cell (DSSC).73 DLCs derived from porphyrin, Pc, TP, hexabenzocoronene and decacyclene have been used as hole-transporting layer while crystalline and liquid crystalline perylene derivatives and C60 derivatives have commonly been used as electron-transporting materials.

Gregg et al.74 and Petritsch et al.75 were the first ones to demonstrate the PV effect in porphyrin- and Pc-based DLCs. However, the seminal work of Schmidt-Mende et al.6 on well-defined discotic PV solar cell prepared from a hexa-peri-hexabenzocoronene (HBC)-based DLC, reported in 2001, generated tremendous interest in this field. Therefore, we open this section with HBC-based DLCs in PVs.

Hexabenzocoronene DLCs in PVs

HBC is one of the largest and highly symmetrical all-benzenoid polycyclic aromatic hydrocarbons that has recently been realized to function as a core fragment for generating DLCs by Müllen and co-workers.76 HBC-based DLCs show columnar phases with remarkably high mesophase breadth and charge-carrier mobilities.77, 78 They act as donor materials (p-type, hole-transporting semiconductors) in electronic devices. Schmidt-Mende et al.6 prepared an OPV device using a HBC-based DLC, HBC-PhC12, 1a (Figure 4) in combination with an organic soluble electron-accepting perylenediimide (PDI) dye, 2a (Figure 5) to produce thin films with vertically segregated perylene and hexabenzocoronene with large interfacial surface area.

Figure 4
Figure 4

Chemical structure of HBC DLCs used in OPV.

Figure 5
Figure 5

Chemical structure of perylene-based electron acceptors used in OPV.

Power-conversion efficiency (PCE) upto 2% was achieved with a small incident irradiance <1 mW cm−2. However, it degrades at higher intensities and reaches to 0.22% under 1 Sun illumination at AM 1.5G.79 Simple solution-processing steps are used to fabricate these OPV devices. Intermolecular and macroscopic ordering was reported to be responsible for the high performance of fabricated devices. For compound HBC-PhC12, the calculated HOMO level was 5.25 eV and LUMO level was 2.64 eV, with a large band gap of 2.61 eV. Similarly, HOMO and LUMO energies for perylene were 5.32 and 3.29 eV, respectively. From HBC-PhC12 to perylene, which has a high electron affinity as a result of the electron-withdrawing diimide bridges, there is 0.65 eV LUMO step and 0.07 eV HOMO step. The devices showed high external quantum efficiencies (EQEs; Figure 6), which is due to the large interfacial area within the bilayer structure, and possibly owing to the high exciton diffusion ranges in the separated HBC-PhC12 and perylene regions. The short circuit current (JSC) and open circuit voltage (VOC) were −33.5 μA cm−2 and 0.69 V, respectively, and the fill factor (FF) was 40% (Figure 6). Later, they tried several other HBC-based DLCs (Figure 4) to prepare PV solar cells.80, 81 However, none of these devices could cross the PCE of the above-mentioned first device. PCE of some of the HBC-based DLCs used in PV solar cells are presented in Table 1. In all tables, Cr=crystals; LC=liquid crystal; Colh=columnar hexagonal; Colp=columnar plastic; N=nematic and SmA=smectic A.

Figure 6
Figure 6

(a) EQE action spectra for a 40:60 HBC-PhC12:perylene diimide blend (solid line) and the fraction of absorbed light in an HBC-PhC12 film (dashed line), a perylene film (dotted line) and a 40:60 blend film (dash-dotted line). (b) Current–voltage characteristics for this device in the dark and under illumination at 490 nm. The JSC and VOC under illumination are −33.5 μA cm−2 and 0.69 V, respectively, and the FF is 40%. The diode has a rectification ratio of 8.3 × 102 at 2 V. (c,d) Normalized EQE action spectra taken under illumination through the ITO and Al electrodes, respectively, corrected for the absorption of the contacts and glass. Reproduced with permission from Schmidt-Mende et al.6 Copyright 2001 American Association for Advancement of Science.

Table 1: Photovoltaic parameters of some best-performing HBC DLC-based solar cells

Device prepared using chiral HBC derivative 1b (Figure 4) and perylene derivative 2a (Figure 5) exhibits ISC, 3.3 μA cm−2, VOC 0.46 V, FF 32.5% and PCE of 0.1% at 490 nm. Compared with the above-mentioned HBC-PhC12/perylene device, it gives very poor results. This has been attributed to different film-forming properties and film morphologies of HBC derivative 1b.80 In this case, vertical segregation of HBC and perylene layer was not observed in the spin-coated blends. A combination of 1a or achiral 1b with perylene acceptor 2a gives very poor PCE.81 Efforts have also been made to attach perylene dye covalently to HBC discotic as shown in structure 1n to realize phase-segregated donor–acceptor structure. However, this device exhibits very poor PCE.82 Replacing the perylene dye 2a by other perylene dyes such as 2b2d (Figure 5) also did not improve the efficiency.81, 82

Jung et al.83 added a photoconducting carbazole-based polymer in the HBC/perylene solar cell to improve its efficiency. It was observed that the PCE of the device is dependent on the morphology of film. An addition of the photoconducting polymer improves the device performance, albeit only for experiments performed in vacuum.

The PV properties of three HBC derivatives were investigated with respect to the influence of the alkyl side chains (Figure 4, structure 1d, 1f and 1g) by Li et al.84 For the devices fabricated from 1d compound, the VOC is 0.52 V and the PCE is 1.5% with EQE values of 12%, which is much higher than the EQE of 6% and 4% in 1f and 1g, respectively. This is due to the shielding effects of the alkyl chains, which reduces the HOMO level on increasing side chain length. HBC derivative 1c with normal dodecyl peripheral chains exhibits EQE of 29.5%.85

The effect of chemical structure and self-assembly of HBC discotics were studied by Hesse and co-workers.79, 86 Various phenyl-substituted HBCs (Figure 4, structure 1h, 1i, 1j, 1k and 1l) as electron donor blended with PDI, 2a were studied. They investigated the effect on the device performance by means of different parameters, such as different alkyl chain lengths (6, 8, 12 and 16) of carbon atoms, introduction of a triple bond linker between HBC core and residual phenyl group and a swallow-tailed dialkylphenyl chain. It was also observed that by increasing the side chain length of the HBC molecule the layered structure is disrupted, which results to disordered structure. PCE up to 0.24% was realized in these devices.79, 86

Wong et al.87, 88 prepared a number of fluorenyl-substituted HBC (FHBC) and their thiophene dendrimers (Figure 4, structure 1m, 1o, 1p, 1q, 1r and 1s). Formation of columnar structures is reported in these materials by X-ray diffraction studies. BHJ solar cells with the structure ITO/PEDOT:PSS/FHBC/PC61BM (1:2 w/w)/TiOx/Al were fabricated and PCE up to 2.5% was observed in these devices (Table 1).87, 88 In these devices, [6,6]-phenyl-C61-butric acid methyl ester (PC61BM) and [6,6]-phenyl-C71-butric acid methyl ester (PC71BM) have been used as electron acceptor. Addition of HBC-based amphiphilic interface modifier improves the PCE of the device made of compound 1o and PC61BM by 20%.89

Kang et al.90 demonstrated the self-assembled molecular structure of p–n junction of HBC discotic 12-c-HBC, 1t (Figure 4) and PC70BM. The PCE is increased up to 2.41% upon addition of 10% donor material with 10:90 wt% of 21:PC70BM. The solution-processed fabricated device showed the VOC 1 V and JSC 6.37 mA cm−2.90 The enhancement to the PCE is due to the formation of ball-and-socket packing nest structure of 12-c-HBC molecules into PC70BM, which results in the formation of well-defined molecular p–n junctions.

Porphyrin DLCs in PVs

Porphyrins are considered as ‘pigments of life’ owing to their biochemical involvement in various vital processes in the living systems.91 Porphyrin derivatives, such as hemes, chlorophylls, cytochromes, peroxidases, myoglobins, catalases and so on, are some important biological representatives. They are the primary light-harvesting molecules in natural photosynthesis.92, 93 Porphyrin derivatives absorb light up to the red region of the visible spectrum with high extinction coefficients. A number of porphyrin derivatives have been successfully used in DSSCs, bilayer and BHJ solar cells.94, 95, 96, 97

The use of DLC porphyrin in OPV was first realized by Gregg et al.98 who prepared an unusual PV cell using a DLC porphyrin, zinc octakis(8-octyloxyethy1)porphyrin 3a (Figure 7), sandwiched in between two symmetrical indium tin oxide (ITO) electrodes in 1990. It was proposed that ‘the illuminated electrode interface possesses much higher concentration of excitons than at the counter electrode owing to strong absorption of incident light by the porphyrin. The exciton dissociation at the porphyrin/ITO interface was inherently asymmetric, and this leads to a significant and persistent PV effect’.98

Figure 7
Figure 7

Chemical structure of porphyrin DLCs used in photovoltaics.

BHJ solar cells incorporating porphyrin discotic molecules 3b and 3c (Figure 7) with PC61BM electron acceptor were prepared by Li and co-workers that showed PCE upto 0.222%.99, 100 These porphyrin have high absorption range over solar spectrum and align homeotropically for efficient charge transport. Both bilayer heterojunction and BHJ devices were fabricated with the cell structure of ITO/PEDOT:PSS/DLC/PC61BM/Ca-Al. An active layer of 80-nm porphyrin was spin-coated from its chlorobenzene solution and a 30-nm-thick PC60BM layer was thermally deposited under vacuum to construct bilayer solar cells. On the other hand, BHJ devices were prepared from a blend of porphyrin and PC60BM (1:1 w/w, 230–250-nm thick). It has been observed that thermal annealing of these devices induced alignment of discotic molecules in the photoactive layers, leading to a factor of 4–5 higher PCE. PV parameters of these devices are tabulated in Table 2 along with Pc discotics.

Table 2: Photovoltaic parameters of some best-performing porphyrin and phthalocyanine DLC-based solar cells

Although porphyrin DLCs exhibit many attractive features, such as broad absorption spectrum, low gap between HOMO and LUMO energy levels, facile homeotropic alignment, high charge-carrier mobility and resemblance with natural photosynthetic antenna, surprisingly, out of >200 DLCs derived from porphyrin nucleus only 2 DLCs have been so far used to fabricate real solar cell. Therefore, it would be quite interesting to further explore these interesting intriguing materials.

Pc DLCs in PVs

Pcs are closely related to porphyrins and are also known as tetrabenzo tetraazaporphyrins. Pcs are macrocyclic compounds with an alternative carbon atom–nitrogen atom ring structure, which acts as a tetradentate ligand. They have found applications in bio and electronic industries.101 Pcs can act both as p-type and n-type semiconductors depending on peripheral substitutions.102 Piechocki et al.103 discovered columnar mesophase properties of Pc LCs in 1982, and since then, about 400 Pc-based DLCs have appeared in the literature.34 Pc-based DLCs have been extensively studied for their conducting and photoconducting properties and charge-carrier mobility up to 0.71 cm2 V−1 s−1 has been realized.49 Several Pc-based DLCs have been used to fabricate solar cells. Chemical structures of these DLCs are presented in Figure 8 and their PV parameters are tabulated in Table 2.

Figure 8
Figure 8

Chemical structure of phthalocyanine-based DLCs used in photovoltaics.

Petristch et al.104 utilized discotic liquid crystalline Pc in organic solar cells in 1999. They investigated a double-layer PV device comprising a discotic Pc derivative 4a (Figure 8) as electron donor and a perylene derivative 2e (Figure 5) as electron-acceptor material. Compound 4a was heated to its isotropic temperature (292 °C) and cooled slowly to room temperature. Then a thin layer of perylene as electron acceptor and Al as top contact electrode were deposited. The device exhibits EQE of 1%. They also prepared a blended OPV device based on Pc 4a as donor and perylene derivative 2a as acceptor105 that shows EQE upto 1% with VOC of 0.1 mV and 25% FF.

Levitsky et al.106 demonstrated a solar cell based on n-type nanoporous Si (PSi) filled with copper Pc (CuPc) and its discotic derivatives 4b (Figure 8). The fabricated device shows the PCE upto 2%. Such organic filled nanoporous inorganic matrices may lead to the fabrication of hybrid PV systems with efficient photoinduced charge transfer and charge migration. Both CuPc and PSi contribute to the photocarrier generation, but the CuPc discotic derivative shows the property of increasing the hole mobility along the quasi-one-dimensional columns. The device was fabricated as ITO/PSi–CuPc/Al architecture followed by the plasma etching of nanoporous Si to ensure the opening of the all pores. PSi was filled by dropping a solution (10−2M) of CuPc. The IV curves of Psi samples that were not treated by plasma etching to open all pores exhibited a ‘kink’ behavior leading to a decrease of the VOC and ISC values. The authors suggested that ‘samples with a poorly developed pore structure or with partially opened pores cannot provide a sufficiently dense filling of CuPc molecules to form a conductive wire for hole transport to the anode. This is consistent with the theoretical model, which indicates that the IV curve degradation occurs as a result of a decrease of the hopping coefficient; poor filling leads to isolation of the CuPc aggregates making them insulated from each other’.106

Fujii and co-workers extensively studied various Pc DLCs in PVs.69, 70, 107, 108, 109, 110, 111, 112, 113 They prepared an OPV device based on Pc derivative 1,4,8,11,15,18,22,25-octahexylphthalocyanine (C6PcH2) 4d (Figure 8) as donor and the fullerene derivative PC61BM as acceptor in 2010.107 High EQE of >70% in the Q-band absorption region of C6PcH2 and a high energy-conversion efficiency of 3.1% were achieved with different compositions of both donor and acceptor materials. The values of VOC is 0.81 V, ISC of 9.6 mA cm−2 and FF of 40% were observed for the solar cell with the C6PcH2:PC61BM composite layer at a weight ratio of 2:1. To improve the FF of the above device, they studied the optimization of the active layer thickness and insertion of buffer layer.108 The optimized active layer thickness was determined to be 120 nm. By inserting a hole-transporting MoO3 buffer layer between cathode and active layer, the PCE was enhanced to 3.2%. Working on the same DLC 4d, they studied the effect of additional additives on the surface morphology.109 By using processing additive 1,8-diiodooctane (0.2% v/v) in various organic solvents, such as toluene, trichloroethylene and chloroform, the performance of BHJ solar cells was markedly improved. The values of VOC of 0.78 V, ISC of 9.1 mA cm−2, FF of 58% and the PCE 4.1% were recorded. Other additives such as 1,8-dichlorooctane and 1,8-dibromooctane also exhibit similar effect. However, increasing the amount of additives decreases the PCE.110 The marked improvement in the PCE has been attributed to distinctly different surface morphology (Figure 9) of the active layer where processing additive separated the donor–acceptor phases.110

Figure 9
Figure 9

AFM images of surface of C6PcH2:PCBM composite thin films: (a) without DIO, (b) with 0.2% v/v of DIO, and (c) with 0.8% v/v of DIO. Reproduced with permission from Dao et al.110 Copyright 2013 Elsevier B.V. A full color version of this figure is available at the Polymer Journal online.

The stability and the degradation mechanism of the solar cell have also been studied.111 Solar cells based on Pc show higher stability than the cells fabricated with the conventional donor material poly(3-hexylthiophene) (P3HT) in the same environment (45 °C temperature and 1 Sun). It was observed that the irradiation of a solar simulator degrade the C6PcH2 molecule by breaking chemical bonds of two pyrrole aza nitrogens as well as the four meso-bridging aza nitrogens with neighboring carbons and this affected the device lifetime. Deposition of various buffer layers between the active layer and counter electrode improve the stability.114, 115

Solar cells with homologous series of 1,4,8,11,15,18,22,25-octahexylphthalocyanine (Figure 8, structure 4c, 4d, 4e, 4f and 4g) were prepared by Dao et al.112 to understand the effects of alkyl chain length on PV parameters. They observed that, ‘by shortening the alkyl substituents length, the columnar structure of the Pc discotic altered from 2D rectangular lattices to pseudohexagonal structures and Davydov splitting at the Q-band of CnPcH2 absorbance spectra decreases, which results in the higher hole mobility and the deeper HOMO energy levels. As a result, the PCE of CnPcH2-based BHJ solar cell is improved from 0.3% to 3.7% by changing the alky substituent length’.112 In this series, the highest PCE was observed in the Pc 4d with hexyl alkyl chain.

Very recently, Dao et al. utilized various Pc–tetrabenzoporphyrin hybrid macrocycles 4i4m to prepare solar cells.113 These compounds were prepared by replacing azo links of Pc 4d by methane groups. Thus non-peripherally substituted octahexyl tetrabenzoporphyrin (C6TBPH2, 4i), tetrabenzomonoazaporphyrin (C6TBMAPH2, 4j) tetrabenzodiazaporphyrins 4k and 4l (C6TBDAPH2, a mixture of cis and trans compounds) and tetrabenzotriazaporphyrin (C6TBTAPH2, 4m) were prepared. These hybrid molecules were reported to exhibit rectangular columnar mesophases. Photovolatiac solar cells were prepared using various Pc–tetrabenzoporphyrin hybrid macrocycles mixed with PC70BM in ITO/MoOx/BHJ/Al structures and solar cell performance was measured under AM 1.5G illumination at an intensity of 100 mW cm−2. PV parameters of these devices are presented in Table 2. The best PCE of 4.7% with VOC of 0.73 V, JSC of 10.8 mA cm−2 and FF of 59% was achieved for the devices prepared from C6TBTAPH2 mixed with PC70BM.

Fujii and co-workers also used Pc DLCs 4d and 4e as additives in classical BHJ thin-film solar cells based on P3HT and [6,6]-phenyl-C61-butyric acid methyl ester (PCBM).69, 70 The PV devices show EQEs of 74, 66 and 47% at a wavelength of 540 nm without CnPcH2, with C6PcH2 and with C7PcH2, respectively. The PCE of the solar cell without CnPcH2 was 2.3% with ISC of 8.6 mA cm−2, VOC of 0.57 V and FF of 48% that improves to 3.0% with ISC of 12.1 mA cm−2, VOC of 0.56 V and FF of 44% with C6PcH2. However, the addition of C7PcH2 does not show much improvement in PCE.

Jurow et al.116 synthesized a mixture of various thioalkyl-substituted Pc derivatives 4h. Number of thioalkyl-substitution was estimated in between 3 and 10. Some of these mixtures were reported to be discotic liquid crystalline. Solar cells prepared from these materials exhibit PCE in between 0.06% and 0.15%.

TP discotics in PVs

TP-based DLCs are the most rigorously studied materials. More than 1000 TP DLCs have been prepared and studied for various physical properties.117, 118, 119 Because of their good photoconducting and charge-carrier mobility behavior, it was obvious to look for their use in PV solar cells.50 Chemical structures of TP DLCs used in PVs are presented in Figure 10. PV parameters of some best-performing devices are tabulated in Table 3. The first report appeared in 2005 when Oukachmih et al.120 prepared two-layered devices using TP ether 5a (Figure 10) as a hole-transporting material and perylene derivatives 2d, 2f and 2g (Figure 5) as electron-transporting materials. These devices showed EQE of around 3%. They studied the effect of UV–ozone and argon plasma treatment of ITO on the solar cell efficiency of these devices. On UV–ozone treatment, the work function of ITO increases while it decreases on argon plasma treatment. The VOC depends both on the organic–organic interface as well as on the electrode–organic interface. The UV–ozone treatment of ITO decreases VOC, whereas it increases on the argon plasma treatment.121

Figure 10
Figure 10

Chemical structure of triphenylene-based DLCs used in photovoltaics.

Table 3: Photovoltaic parameters of some best-performing TP DLC-based solar cells

In 2010, Jeong et al.71 used TP discotics as an additive to well-established P3HT:PC61BM BHJ OPV device to realize the effect on PCE. The devices configured with P3HT:PC61BM (1:1.2 w-w) layer doped with 2,3,6,7,10,11-hexaacetoxytriphenylene (3 wt%) exhibit an average PCE of 3.97% after thermal annealing. In comparison, the reference cells display only 3.03% PCE. Two derivatives of TP, namely, 2,3,6,7,10,11-hexaacetoxytriphenylene 5b and 2,3,6,7,10,11-hexamethoxytriphenylene 5c were used to fabricate OPV devices. However, it may be noted that both these compounds do not show any thermotropic mesomorphism.

A year later, Zheng et al.122 reported the use of a well-known DLC, namely, 2,3,6,7,10,11-hexabutoxytriphenylene (HAT4) 5d (Figure 10) as an additive to improve the PCE of P3HT:PC61BM-based solar cells. The TP discotics (HAT4) disperse in the active layer to form a more efficient pathway for charge carriers. The influence of charge-carrier mobility with annealing and insertion of HAT4 discotic were studied. The hole and electron mobilities of the pristine P3HT:PC61BM blended system devices were recorded as 7.86 × 10−6 and 5.35 × 10−5 cm2 V−1 s−1, respectively, after thermal annealing. On dispersion of HAT4, hole and electron mobilities increase to 4.50 × 10−5 and 2.32 × 10−4 cm2 V−1 s−1, respectively. They demonstrated that both JSC and FF were increased without changing the VOC. PCEs up to 3.5% were realized in these devices. The improvement in JSC and FF was attributed owing to efficient photoinduced charge transfer in BJH solar cells by inserting HAT4. The AFM (atomic-force microscopy) images of HAT4 film surface before and after annealing are shown in Figures 11a and b. The sectional morphology of the device after thermal annealing is shown in Figures 11c and d.

Figure 11
Figure 11

Tapping-mode AFM surface image of HAT4 film, (a) before annealing and (b) after annealing; the inset shows a simplified diagram of the π–π stacking configuration in HAT4. (c, d) SEM images of the sectional morphology of the device with HAT4. Reproduced with permission from Zheng et al.122 Copyright 2011 Elsevier B.V. A full color version of this figure is available at the Polymer Journal online.

We further explored the use of HAT4 as an additive in classical OPV cells.72 A conventional device was fabricated with cell structure of ITO/PEDOT:PSS/HAT4-PCBM:P3HT/Al and its PV parameters were compared with the device without HAT4. The PCE was improved 63% after addition of the DLC. A significant improvement in JSC from 7.4 to 10.3 mA cm−2 was observed. This enhancement could be due to the increased charge-separation efficiency in active layer owing to HAT4. Thickness of DLC layer have important role in the device. When the thickness of the layer was 10–20 nm, the maximum value of JSC and PCE was achieved. Further enhancement in the layer thickness decreases JSC and PCE. On increasing thickness beyond a certain length, traps are created owing to the dislocation of columns. Annealing of the device is also crucial for getting high PCE. On annealing, traps get healed resulting in improved JSC and efficiency of the devices with DLC increased to 12.9 mA cm−2 and 2.27%, respectively. The device without DLC in it did not affect the PCE on annealing. Insertion of molybdenum oxide as a buffer layer between ITO and active layer also gives similar results.123

We also developed BHJ solar cells based on composites of copolymer poly [N-90-heptadecanyl-2,7-carbazole-alt-5,5-(40,70-di-2-thienyl-20,10,30-benzothiadiazole)] (PCDTBT) and the fullerene derivative PC71BM with an inserted layer of HAT4.124 Two different materials, poly (3,4 ethylenedioxythiophene)-poly (styrenesulfonate) (PEDOT: PSS) and molybdenum trioxide (MoO3) were used as buffer layers between ITO and DLC layers. All the devices with inserted DLC layer exhibited better performance compared with reference cells. PV solar cells containing 30-nm thick HAT4 layer display 5.14% PCE under 1 Sun condition. This is a significant improvement in the PCE compared with earlier reports.

TP DLCs as a moiety to form self-assembly with diblock polythiophene on side chains were used by Chen et al.125 They synthesized diblock copolymers P3HT-block-poly[3-(10-(2,3,6,7,10-pentakis(hexyloxy)triphenylene)decyloxy)thiophene] (P3HT-b-P3TPT) 5f (Figure 10) having a TP liquid crystalline pendant. The copolymers form an extremely well-defined highly ordered nanowires owing to the presence of LCs that enhance the charge transport. Diblock copolymers of P3HT/P3TPT with molar ratios of 3:1, 6:1 and 9:1 termed H3P1, H6P1 and H9P1 were synthesized. The thin films were solution coated on ITO substrate and annealed. The morphology change to the thin film structures and self-assembly was studied by AFM. Different treatments were given to the thin films, such as as-cast, slow film growth (SA), thermal annealing (TA) and ortho-dichlorobenzene (o-DCB) vapor annealing followed by thermal annealing (SA+TA). The OPV device based on the SA+TA-treated H9P1/PC61BM blend exhibits the best performance with a PCE of 1.54%, JSC of 6.51 mA cm−2, VOC of 0.601 V and FF of 39.4%, whereas the device based on its analogous block copolymers H6P1 and H3P1 only shows PCE values of 0.99% and 0.24%, respectively. The improved PCE results from the interaction between the TP moieties. The SA+TA treatment can easily drive interchain π–π interactions to develop the fine formation of crystalline lamellar aggregation favoring an optimized morphology of the active layer. Similarly, a DLC block poly(2,3,6,7,10-pentakis(hexyloxy)-11-(oct-7-en-1-yloxy)triphenylene) (P3HT-b-PTP) 5g (Figure 10) was used to configure PV device structure of P3HT-b-PTP):PCBM)/LiF/Al.126 The highest PCE of 4.03% is achieved when the concentration of P3HT-b-PTP is 5%, with a JSC of 10.36 mA cm−2 and an FF of 64.91%.

They further prepared dye-sensitized nanoarrays (NAs) with DLC interlayer for high-efficiency inverted polymer solar cells. Inverted polymer solar cells were fabricated with well-aligned and highly uniform one-dimensional ZnO nanoparticles with organic ditetrabutylammonium cis-bis(isothiocyanato)bis(2,2′-bipyridyl-4,4′-dicarboxylato) ruthenium(II) (N719) dye and 3,6,7,10,11-pentakis(hexyloxy)-2-hydroxytriphenylene 5e (Figure 10).127 The N719 shell and N719/LC double-shells were introduced to modify the interface between the active organic layer and ZnO NAs. The self-organization of DLC facilitate the active layer components to rearrange, leading to a more orderly nanomorphology of active layer and consequently reduces the probability of electron/hole recombination at the interface donor/acceptor materials. The best PCE of the device with only dye-coated NAs was 7.3%, which increases to 8% when the NAs were coated with dye and DLC.

Chen et al.128 extended their work by synthesizing DLC ligands dithiol-functionalized TP (TP-S) 5h modified ZnO nanoparticles (TP-S@ZnO). Hybrid solar cells based on a blend of P3HT and TP-S@ZnO were prepared and characterized. They reported that ‘DLC ligands improve the compatibility between P3HT polymer and ZnO nanoparticles, which is beneficial for enhanced charge separation and transfer efficiency. DLC molecular interface modification can provide a viable and interesting method to promote the compatibility and a large interfacial area between polymers and nanocrystals, which improve the performance of the device. The self-assembly of TP-S ligands tends to provide a better pathway for electrons and holes for transporting in the active layer’.128 Solar cells with a conventional device configuration ‘ITOPEDOT:PSS/active layer/LiFAl’ were prepared. The BHJ devices based on P3HT/ZnO film showed a PCE of 0.46%, which improves to 0.51% on directly grafting the ligand TP-S onto ZnO NPs and annealing the sample at 130 °C. The device based on TP-S@ZnO/P3HT showed an improvement with a PCE of 0.70%, which further improves to 0.95% on annealing the sample at 130 °C.

Perylene DLCs in PVs

Perylene tetracarboxylic acid bisimides commonly known as perylenebisimides are among the best n-type organic semiconductors known to date. Many non-LC perylenebisimide derivatives have been used as electron acceptor in PV solar cells. Upon appropriate peripheral substitution, perylene derivatives exhibit columnar mesophases and the use of these liquid crystalline materials in PVs is presented here. Kim and Bard129 prepared an organic donor/acceptor heterojunction PV devices based on a non-LC zinc Pc (ZnPc) as donor and a liquid crystalline perylene diimide, N,N-diheptyl-3,4,9,10-perylenebiscarboximide (PTCDI) 6a (Figure 12) as acceptor with the cell configuration ITO/ZnPc/PTCDI/Ga:In. The device with D and A thickness of 100 nm generated FF of 22%, with a JSC value of 0.40 mA cm−2 and VOC of 0.60 V. The FF was improved by 40% with a JSC value of 1.58 mA cm−2 and VOC of 0.60 V (Table 4) by lowering the donor and acceptor thickness to 25 nm. The better performance of thin active layer device was attributed to the efficient separation of excitons and facile transport of free charges in thin layer.

Figure 12
Figure 12

Chemical structure of perylene-based DLCs used in photovoltaics.

Table 4: Photovoltaic performance of perylene, decacylene and other DLCs

In another study, Archambeau et al.130 used a benzoperylene LC 6b as an electron donor in conjunction with another perylene-based acceptor 2f (Figure 2). Compound 6b is actually a mixture of four regioisomers, which exhibit a columnar mesophase at ambient temperature and clears at 180 °C. The device exhibits an FF value of 48% with low VOC of 0.4 V.

Decacyclene DLCs in PVs

1,7,13-Trialkanoyloxydecacyclene DLCs exhibit very interesting physicochemical properties and can be prepared easily by direct Friedel–Crafts acylation of parent hyderocarbon.131 Owing to the presence of keto groups, they act as electron-deficient molecules. Hirota et al.132 utilized discotic liquid crystalline 1,7,13-heptanoyldecacyclene (C7DC) 7 (Figure 13) as an electron-accepting layer in a [2-methoxy-5-(2′-ethylhexyloxy)-1,4-phenylenevinylene] (MEH-PVV)-based solar cell. The PV device with ITO|PEDOT:PSS|MEH-PVV|C7DC|LiF/Al structure was prepared by spin-coating PEDOT:PSS and MEH-PVV/C7DC on ITO/glass substrate followed by vacuum deposition of LiF/Al. Crystal-like C7DC domains buried in MEH-PVV were observed in AFM images of active layer. Poor miscibility of C7DC and MEH-PVV resulted in distinct phase separation between MEH-PVV and C7DC. The PV cell showed JSC of 3.6 μA.cm2, VOC of 1.3 V and FF was 32% with PCE of 0.14%, which increased to 0.30% upon annealing the device at 100 °C.

Figure 13
Figure 13

Chemical structure of 1,7,13-heptanoyldecacyclene.

Benzo[o]ditriphenyleno[2,1,12,11-efghi:11′,12′,1′,2′-uvabc]ovalene DLCs in PVs

Müllen and co-workers explored the ‘bottom-up’ approach to build DLCs derived from large polycyclic aromatic hydrocarbon cores, defined as ‘nano-graphene’ structures formed by π–π stacking. With appropriate flexible alkyl chains, these larger aromatic cores lead to DLCs with enhanced columnar stability and supramolecular order with improved charge-carrier transport owing to the more extended p-orbital overlap.133 DLCs with three swallow-tailed alkyl substituted (benzo[o]bistriphenyleno[ 2,1,12,11-efghi:2′,1′,12′, 11′-uvabc] ovalene, 8 (Figure 14), were prepared and utilized to fabricate solar cells. Crystalline PDI 2a (Figure 2) was used as an electron acceptor. Scanning electron microscopic investigations revealed homogeneous bicontinuous phase across the thickness with PDI crystals evenly dispersed in the liquid crystalline matrix. This morphology could be favorable for hole and electron migration in donor and acceptor domains. PV devices with ITO/DLC-PDI/Ag structure were fabricated by spin-coating from a chloroform solution of a mixture of donor and acceptor materials. The highest device efficiency was observed for blends with donor and acceptor ratio of 4:6. EQE up to 19% was achieved at 490 nm for these graphene discotics.

Figure 14
Figure 14

Chemical structure of benzo[o]ditriphenyleno[2,1,12,11-efghi:11′,12′,1′,2′-uvabc]ovalene DLCs.

Dibenzo[a,c]phenazine DLCs in PVs

Lee et al.134 attached a 2,3,6,7-tetra-6-hexyloxydibenzo[a,c]phenazine-11-carboxylic acid discotic monomer to polyacrylamide. The resultant polymer (DLC-PAM) 9 (Figure 15) exhibits a hexagonal columnar mesophase. It was used to prepare a conventional P3HT/PCBM cell with an active layer of DLC-PAM. The optimized thickness of the PAM-DLC layer was 90 nm to enhance the charge transport. The JSC and VOC values of 5.18 mA cm−2, and 0.60 V, respectively, with 51% FF and 1.60% PCE were achieved in this device.

Figure 15
Figure 15

Chemical structure of polymer DLC-PAM.

Calamitic LCs in PVs

Calamitic or rod-like LCs have primarily been explored in display devices and conducting impurities are considered as ‘black sheep’ in these materials. However, as the dark conductivity and photoconductivities of nematic, smectic and cholesteric materials were measured in 1969,135 calamitic LCs also became interesting materials for semiconducting applications.135 Kamei et al.136 studied the PV effect in the nematic LC (NLC) in 1972 and observed the maximum VOC of 0.5 V. Kelly and co-workers, in a series of papers,137, 138, 139, 140 reported the preparation of real PV devices from various calamitic LCs. PV parameters of some best-performing calamitic LC-based solar cells are presented in Table 5. Nematic gel template is formed from a mixture of polymerizable mesogen 10a and non-polymerizable mesogen 10b (Figure 16), which contains phase-separated droplets of LC in crosslinked polymer. Compound 10a with terminal double bonds is a reactive mesogen that forms a nematic glass at room temperature on cooling. Compound 10b exhibits a monotropic nematic phase stable down to room temperature. These materials have an ionization potential of 5.31 eV, so that they are suitable for use as an electron-donating species in the gel. Compound 11a is an electron-withdrawing perylene derivative having fluorene groups. In the thin film of compound 11a, rapid quenching introduces a glassy state. It has a high EA of 3.94 eV and therefore can be used as an electron-accepting material. From ionization potential and EA data, it is clear that charge separation at the interface is thermodynamically favorable in these donor–acceptor couples. A mixture of 10a and 10b in the ratio 1:2 forms a gel, which displays a nematic phase that remained stable at room temperature for a long period. A PV device with cell structure of ITO/PEDOT:PSS/LC gel/LiF/Al was fabricated that exhibits EQE of 5.3% and PCE of 0.6%.

Table 5: Photovoltaic parameters of some best-performing calamitic LC-based solar cells
Figure 16
Figure 16

Chemical structure of fluorene-thiophene donors and perylene-based acceptors.

They extended their work by taking four different perylene-based electron acceptors having similar EAs but different thermotropic phases and two fluorene–thiophene LCs 10c and 10d (Figure 16). 138 Best results are obtained when the nematic donor is mixed with an amorphous acceptor to give a super-cooled nematic glass at room temperature. AFM reveals phase separation on a nanometer scale with a broad distribution of domain sizes. PV device with a blend of donor 10c and acceptor 11a showed the best PCE of 0.9%.138, 139

In another study, they prepared organic bilayer PV cell with an insoluble electron-donating layer formed by crosslinking a nematic reactive mesogen.140 In a nematic reactive mesogens, a planar alignment with the long molecular axis aligned on the substrate plane can be achieved upon crosslinking.141 The performance of the device is limited by the charge-carrier mobility of the acceptor material, which can be enhanced by the electron-donating layer formation by mesogens.

A number of PDI-based crystalline and liquid crystalline acceptors having fluorine or carbazole moieties were prepared (Figure 16). Bilayer solar cells prepared from crosslinkable donor 10d and acceptors 11a, 11c, 11e and 11f exhibit PCEs in between 0.42% and 0.93%. It was observed that crosslinking of the monomer 10d by irradiation with UV light to obtain an insoluble layer does not degrade device performance

Kekuda et al.142 demonstrated the effect of donor–acceptor interface on the performance of BHJ device. They reported performance of a device based on a commercially available liquid crystalline polymer poly(9,9′-dioctylfluorene-cobithiophene) (F8T2) 10e (Figure 16). The conventional device configuration ITO/PEDOT:PSS/F8T2/C70/Al showed a PCE of 3.4% after annealing the polymer LC films at 200 °C.

Sun et al.143 used liquid crystalline poly(2,5-bis(3-alkylthiophen-2-yl)thieno[3,2-b]thiophene) (PBTTT) 12 (Figure 17) to fabricate a bilayer device (Figure 18) composed of the active layer of PBTTT:PCBM (1:2)/MDMO-PPV:PC70BM (1:4) and compared the results with single layer (PBTTT:PCBM or MDMO-PPV:PC70BM) devices. The exact nature of the mesophase has not been revealed in this paper. The bilayer device exhibited a VOC of 0.59 V, JSC values of 10.1–10.7 mA cm−2, FF of 50% and PCE values of 3.0–3.2%, which were significantly (by a factor of 2) higher than single-layer devices.

Figure 17
Figure 17

Chemical structure of calamitic LCs used in photovoltaics.

Figure 18
Figure 18

(a) A schematic representation of the device configuration (up) of a bulk heterojunction solar cell based on PBTTT:PCBM (1:3 wt %) and the associated energy level diagram (bottom). (b) JV characteristics of the ITO/PEDOT/PBTTT:PCBM (1:3 wt %)/Al solar cells at different substrate temperatures. The inset shows the PCE values as a function of the substrate temperature. (c) JV characteristics of the ITO/PEDOT/PBTTT:PCBM/Al solar cells with different weight ratios of PBTTT to PCBM at the substrate temperature of 50 °C. The inset shows the JSC and PCE values of the devices as a function of the PBTTT:PCBM weight ratio. (d) Topographical (up) and phase (bottom) AFM images of pure PBTTT films and PBTTT:PCBM (1:3 wt %) films on the ITO/PEDOT substrate. Reproduced with permission from Sun et al.143. Copyright 2009, American Chemical Society. A full color version of this figure is available at the Polymer Journal online.

Hindson et al.144 used liquid crystalline triphenylamine-based poly(azomethine)s as hole-transport materials in typical ITO/PEDOT:PSS/TPA/PCBM/Al devices. 4,4′-Diaminotriphenylamine (TPA) was polymerized with either terephthalaldehyde (TPA-14Ta), 2,5-thiophenedicarboxaldehyde (TPA-25Th) or 1,3-isophthalaldehyde (TPA-13Iso) to yield various polymers. Structure of one of these polymers 13 is shown in Figure 17. The HOMO and LUMO energy levels of these polymers were in the range of 5.0–5.3 and 2.4–3.3 eV. PV devices show the best PCE value of 0.12%, with VOC of 0.41 V, JSC of 1.23 mA cm−2and FF of 24% after annealing the composite at 200 °C.

Chen and co-workers used various calamitic LCs to prepare PV solar cells.126, 145, 146, 147, 148, 149, 150, 151, 152 An electron-donor material poly[3-(6-(4-cynaobiphenyloxy)-hexyl) thiophene](P3HbpT) 14 (Figure 17) having well-known LC cyanobiphenyl was prepared by attaching 4’-hydroxycyanobipheny to 3-(6-bromohexyl)thiophene followed by nuclear bromination of thiophene ring and its polymerization. It shows liquid crystalline property with order morphology and microstructure.145 ZnO nanoparticles were dispersed in it and a hybrid BHJ device was prepared with the active layer of P3HbpT/ZnO. PCE of 0.61% was achieved.

The work was extended by the synthesis of a new donor–acceptor-type liquid crystalline copolymer, poly[3-(6-(cyanobiphenyoxy)thiophene)-alt-4,7-(benzothiadiazole)] (P3HbpT-BTD) 15 (Figure 17).146 This liquid crystalline copolymer was reported to have good optical absorption abilities and spontaneous organizational properties on thermal annealing. The devices based on P3HbpT-BTD and ZnO nanoparticles show the PCE of 1.98% after annealing the composites at 180 °C. The reason to the better performance could be ascribed owing to the self-assembly of mesogens, which induce the ZnO nanoparticles to form a well-dispersed and highly orientated region that resulted in better hole and electron transport.

In continuation to their work on thiophene-based LC donors, they prepared novel copolymer systems PBbTTT-T 16 and PBbTTT-TT 17 with high crystallinity and photocrosslinkable building blocks for p–p intermolecular interactions by copolymerization of 2,5-bis(3- bromododecylthiophen-2-yl)thieno[3,2-b]thiophene (BbTTT) monomer with thiophene and thieno[3,2-b]thiophene.147 The solar cell device that consist of PBbTTT-TT:PC71BM in 1:3.5 ratio shows the PCE of 2.57%. This could be ascribed owing to the high order and crystallinity of the LC material and also to the enhanced stability owing to the photocrosslinkable bromine-functionalized unit.

In another study, they demonstrated the OPV device based on P3HT/ZnO hybrid system by employment of liquid crystalline ligands 4-(5-(1,2-dithiolan-3-yl)pentanoate)-4′-(hexyloxy)-terphenyl 18 (HTph-S) at interface to induce the compatibility, charge separation and transfer efficiency enhancement and optimized micro-morphology.148 The device configuration was ITO/PEDOT:PSS/HTph-S@ZnO/P3HT. The effect of modification of active layer and annealing of layer was demonstrated. The unmodified ZnO/P3HT showed a JSC of 2.01 mA cm−2, VOC of 0.57 V and an FF of 41% with low 0.47% PCE, but the device containing active layer of HTph-S@ZnO/P3HT gives the JSC of 3.77 mA cm−2, VOC of 0.64 V and an FF of 51%, resulting in PCE of approximately 1.23%. Similarly, ZnO nanoparticles passivated by a layer of 4,7-diphenyl-2,1,3-benzothiadiazole-based LC molecules 19 were prepared149 and used in P3HT/ZnO hybrid PV devices. The LC-ZnO layer acts as an electron-acceptor layer in hybrid solar cells and also enhances the order and crystallinity of P3HT chains. Moreover, the order of the P3HT/LC-ZnO blend morphology is significantly enhanced after thermal annealing at 160 °C, which improves PCE by 1.8-fold compared with the device based on P3HT/ZnO. PCE up to 0.89% was realized in these devices.

Liquid crystalline calamitic molecules DPBT-S 19 and PBTTT 12 were also used to prepare CdS nanocrystals for PV solar cells.150 A solution of LC and CdS precursor in chlorobenzene was spin-casted and annealed at different temperatures to decompose the CdS precursor to generate CdS nanoparticles embedded in LC matrix. The efficient charge transfer in the LC/CdS nanocomposites makes these materials suitable to be used as an active layer in PV solar cells. PV devices with inverted architecture (glass/ITO/ZnO/CdS interface layer/active layer/MoOx/Ag) were fabricated and the best PCE of 1.2% was realized.

They also synthesized P3HT-based liquid crystalline rod-coil block copolymers, that is, rod-like LC block poly(4-(dodecyloxy)-4′′-(oct-7-en-1-yloxy)-1,10:4′,1′′-terphenyl), 20 (P3HT-b-Pterph).126 The configured device architecture ITO/PEDOT:PSS/P3HT-b-Pterp exhibit PCE of 0.34–0.44%, which improve to 0.56% for P3HT-b-Pterph after annealing at 200 °C. Corresponding PV devices with DLC block poly(2,3,6,7,10-pentakis(hexyloxy)-11-(oct-7-en-1-yloxy)triphenylene), (P3HT-b-PTP) show better performance than those based on P3HT:PCBM:P3HT-b-Pterph. It has been attributed that ‘the DLC block in P3HT-b-PTP is more favorable in interpenetrating networks and also more compatible with the fullerene acceptors. This is because liquid crystalline state annealing promotes the orientation of mesogens to induce polythiophene backbone packing with higher ordering, which further enhances the charge-carrier mobility and improves the JSC’.126

Chen et al.151 also demonstrated that ionic LCs (ILCs) can be self-assembled with conjugated polymer as an interlayer to achieve high PCE via rapid LC-induced dipole orientation in polymer-based solar cell. The ILCs 3-((2′-(4″-cyanobiphenyl-4-yloxy)ethyl)dimethylammonio)propanesulfonate 21 (CbpNSO) with zwitterionic charges were blended with cationic conjugated polyelectrolyte (CPE) poly[3-(6-trimethylammoniumhexyl)-thiophene] 22 (PTNBr) to afford a novel CPE−ILC complex. It has been pointed out that ‘the spontaneous orientation of LC favors more ordered structural arrangement in CPE−ILC complexes. LC-assisted electrostatic assembly can improve the orientation of dipole moments at cathode interface, which significantly reduces the work function of ITO. Compared with pure PTNBr CPE as electron transport layer (ETL), CPE−ILC complex increases the efficiency of P3HT:PCBM cell by 37%. Solar cell prepared with donor poly(4,8-bis(5-(2-ethylhexyl)thiophene-2-yl)-benzo[l,2-b:4,5-b′]dithiophene-alt-alkylcarbonyl-thieno[3,4-b]thiophene) (PBDTTT-C-T) and acceptor PC70BM in the presence of PTNBr-CbpNSO exhibits PCE of 7.49%’.151

Recently, they also synthesized LC-conjugated polyelectrolytes poly[9,9-bis[6-(4-cyanobiphenyloxy)-hexyl]−fluorene−alt-9,9-bis(6-(N,N-diethylamino)-hexyl)-fluorene] 23 (PF6Ncbp) and poly[9,9-bis[6-(4-cyanobiphenyloxy)-hexyl]−fluorene−alt-9,9-bis(6-(N-methylimidazole)-hexyl]-fluorene] 24 (PF6lmicbp) (Figure 17) by covalently linking cyanobiphenyl mesogen with conjugated polyelectrolytes.152 It has been pointed out that ‘after deposition of a layer of LC-conjugated polyelectrolytes on ZnO interlayer, the spontaneous orientation of LC groups can induce a rearrangement of dipole moments at the interface, which leads to the better energy-level alignment’. The orientation of dipoles can be successfully improved without interference and can also induce the upper active layer to form better crystallization morphology, which facilitate the electron extraction and transportation. Significant PCE of 7.6% can be achieved by deposition of LC polyelectrolytes PF6Ncbp and PF6lmicbp on ZnO as ETL.

Shin et al.153 observed PV properties of diketopyrrolopyrrole (DPP)-based mesomorphic small-molecules, 3,6-bis{5-(4-alkylphenyl)thiophen-2-yl}-2,5-di(2-ethylhexyl)-pyrrolo[3,4-c]-pyrrole-1,4-diones 25 (DPP-TP6 and DPP-TP12, Figure 19). DPP-TP6 with hexyl terminal chains exhibits LC properties while the higher homolog DPP-TP12 was found to be non-mesomorphic. BHJ PV solar cells were fabricated using DPP-TP6 and DPP-TP12 as an electron donor and PC71BM as an acceptor with a typical device structure; ITO/PEDOT:PSS/donor:PC71BM blend/LiF/Al. Solar cells with DPP-TP6:PC71BM films show a PCE as high as 4.3% with a VOC of 0.93 V and an FF of 55%, while only 1.2% PCE could be realized for DPP-TP12 (Figure 20). This clearly demonstrates that molecular organization induces the self-assembly, which is auspicious to fabricating high-performance solution-processable solar cells.

Figure 19
Figure 19

Chemical structure of DPP-TP6 and DPP-TP12.

Figure 20
Figure 20

(a) JV characteristics under 1 sun illumination (inset: dark JV curves) and (b) IPCE spectra for BHJ solar cells based on DPP-TP6:PC71BM (1:1, w/w) blend as-cast and after thermal annealing at 140 °C for 10 min. Reproduced with permission from Shin et al.153 Copyright 2013, American Chemical Society. A full color version of this figure is available at the Polymer Journal online.

Recently, Sun et al.154 synthesized a new molecular donor NLC benzodithiophene terthiophene rhodanine 26 (Figure 21) and fabricated a device (Figure 22), which shows the promising PCE of 9.3% with FF of 77%, which is rare in OPV devices. They attributed that the donor phase in OPV is well ordered, which favors the exciton diffusion length for efficient charge separation. Interestingly, thick solar cells with active layer of thicknesses up to 400 nm also exhibits high FF of ~70% and high PCE of ~8%.

Figure 21
Figure 21

Chemical structure of BTR.

Figure 22
Figure 22

Device architecture and photovoltaic performances. (a) Schematic diagram of a normal cell architecture used in this study. (b) JV characteristics of BTR:PC71BM BHJ solar cells with or without THF solvent vapor annealing tested in air under 98 mW cm−2 AM 1.5G illumination. Inset: dark current plotted in a semi-log scale of the two solar cells. (c) EQE spectra of optimized BTR-based solar cells with or without THF SVA treatment. (d) JV curve of the most efficient BTR:PC71BM BHJ solar cell after 15 s of THF SVA measured by an independent research institute in nitrogen atmosphere under an illumination of 100 mW cm−2. Reproduced with permission from Sun et al.154 Copyright 2015, Nature Publishing Group. A full color version of this figure is available at the Polymer Journal online.

Calamitic LCs as additives in PVs

Similar to DLCs, the effect of doping calamitic LCs on the PV performance of classical solar cells have been studied.155, 156, 157, 158 Canli et al.155 investigated the effect of a chiral smectic LC namely (S)-5-octyloxy-2-[{4-(2-methylbuthoxy)-phenylimino}-methyl]-phenol 27a (Figure 23) in a P3HT/PCBM BHJ organic solar cell. The charge-carrier mobility of the composites increased on addition of the LC material. The addition of LC in P3HT:PCBM solar cells increases JSC from 4.1 to 11.2 mA cm−2 and result in substantial improvement of PCE from 1.1% to 2.9%. The LC forms a nanomorphology between donor and acceptor phases owing to the higher degree of order of films, which leads to the improved photocurrent, larger IPCE values and higher PCE. They extended their work on another smectic LC, namely, 5-(10-undecenyloxy)-2-[[[4-hexylphenyl]imino]methyl]phenol 27b (Figure 23).156 The addition of LC improves the crystallinity of the P3HT layer, the JSC from 0.53 to 3.68 mA cm−2 and PCE from 0.008% to 0.27%.

Figure 23
Figure 23

Chemical structure of calamitic LCs used as additives in photovoltaics.

Jeoung et al.157 incorporated classical NLCs 4-cyano-4’-pentylbiphenyl 28a (5CB) and 4-cyano-4’-octylbiphenyl 28b (8CB) in a typical P3HT:PC61BM solar cells. They reported that ‘the incorporation of NLC additives led to a higher absorbance in blend thin film, a higher crystallinity of P3HT, closer P3HT chains, larger PC61BM domains and enhanced hole/electron mobilities even without postthermal annealing’. The non-annealed cell with 4 wt% 8CB additives showed an increase in all parameters, resulting in PCE of 3.72% compared with 2.14% of the reference device without NLC additives. The JSC is strongly dependent on the absorption intensity derived from the crystallinity of P3HT and the charge-transport properties of networks in PV blend films, hence the blending of the LC in blend enhance the absorption peak improving the spectral overlap with solar emission at 603 nm for the P3HT and this further leads to closer π–π stacking of the P3HT and lower to the band energy.

Shi et al.158 used 4-octyloxy-4’-cyanobiphenyl 28c (8OCB), another classical NLC to evaluate the performance of P3HT:PCBM solar cell. Pristine P3HT:PCBM device and the devices with the LC weight ratios of 3, 6 and 10 wt% exhibited a JSC of 8.11, 9.10, 10.08 and 6.36 mA cm−2, respectively. The device performance depends on doping percentage of NLC, too much additives led to a lower JSC because of the decreased crystallinity and the phase separation in large scale, which were unfavorable for charge transport. The performance was better after mixing 6% 8OCB and annealed at 70 °C, which gives the JSC of 10.08 mA cm−2 and high FF of 54.9%. The annealing temperature of 70 °C in liquid crystalline transitions facilitated the formation of an optimized phase separation in P3HT:PCBM:8OCB system (Figure 24). PCE up to 3.5% was realized.

Figure 24
Figure 24

AFM images of P3HT:PCBM:8OCB films with 8OCB weight ratio of 3 wt% (a), 6 wt% (b) and 10 wt% (c) after annealing at 70 °C for 20 min, and the films with 8OCB weight ratio of 6 wt% without (d) or with annealing (e) at 130 °C for 10 min, respectively. Reproduced with permission from Shi et al.158 Copyright 2014, Springer-Verlag Berlin Heidelberg. A full color version of this figure is available at the Polymer Journal online.

LCs in DSSCs

DSSCs are highly promising candidates for the next-generation PVs owing to their low fabrication cost and good PCE. After the pioneering work of O’Regan and Grätzel,159 huge interest has been developed in these PV devices and PCE values up to 13% has been achieved.160 A schematic structure of a DSSC is shown in Figure 25. DSSC differs from both BHT and bilayer solar cell by its basic construction and operational process. A DSSC basically consists of a sandwich structure of nanocrystalline TiO2/dye-electrolyte between transparent anode and counter cathode. As shown in Figure 25, the light photons are absorbed by the dye adsorbed over TiO2 nanocrystals that provides larger surface area for absorption. In this process, the dye molecules absorb the photons and excited electrons flow into TiO2 and become oxidized. Electrons travel to anode, external load and finally to the cathode, where it transferred to electrolyte usually containing I/I3. The electrolyte works as brokers between cathode and TiO2. The oxidized dye receives electrons from I ion redox, and the iodide is oxidized into I3. The process continues and the circuit is completed.

Figure 25
Figure 25

Schematic representation of a typical DSSC. A full color version of this figure is available at the Polymer Journal online.

As ionic conductivity is quite important in DSSC, early efforts have been made to use ILCs in these devices.161, 162 Yamanaka et al.161 synthesized a new ILC, 1-dodecyl-3-methylimidazolium iodide 29 (C12MImI, Figure 26), and used in DSSC cells as a hole transport layer to enhance the JSC and PCE. The bilayer structure of interdigitated alkyl chains of the imidazolium cations in ILC with the smectic A phase localized the I and I3 between the smectic A layers. The exchange reaction can be promoted by the presence of localized high concentration of I and I3 ions. The higher conductivity of the LC-conjugated electrolyte leads to high value of JSC compared with non-liquid crystalline ionic liquid electrolyte.161 The higher conductivity of ILC is attributed to the enhancement of the exchange reaction between iodide species, which was supported by the large exchange reaction-based diffusion coefficients.162 They utilized these ILCs to prepare a quasi-solid-state DSSC by incarcerating a low molecular weight gelator. Furthermore, improvement to the PCE could be achieved on addition of 5.0 g l−1 gelator to ILC, which also increase JSC owing to the enhancement of the conductivity of the liquid crystalline gel electrolyte.162 The device exhibits JSC value of 7.7 mA cm−2. Full characterization of these devices has not been revealed.

Figure 26
Figure 26

Chemical structure of LCs used in DSSCs.

Similar to LC additives in BHJ solar cells, efforts have also been made to evaluate the performance of DSSC by adding LCs. The embedded LC induced a diffusing pathway, which may increase the ordering strength in the electrolyte and enhance the transportation of redox species in the quasi-solid-state DSSCs. Kim et al.163 mixed the classical LC mixture E7 in a polymer electrolyte and demonstrated the effect of the function of the concentration rate of the LC on the PCE and the FF of the DSSC. The polymer electrolyte consists of ethylene carbonate, propylene carbonate, acetonitrile, tetrabutylammonium iodide, iodine, 1-propyl-3-methylimidazolium iodide and polyacrylonitrile (PAN). The quasi-solid-state DSSCs with optimized concentration of LC as 10 wt% exhibit the best PCE of 4.52% (Table 6).

Table 6: Photovoltaic performance of quasi-solid state DSSCs with liquid crystals

They further studied the effects of LC E7 or ML-0249 addition in PAN-based electrolyte composed of I/I3 redox species.164 The high order and molecular arrangement of the LC incarcerated in polymeric electrolyte molecules creates the transport pathway of redox species. This high mobility and transportation of carriers improved the photocurrent density and also the PV performance. The devices based on ML-0249:PAN (1:1) was fabricated and showed a VOC of 0.703 V, JSC of 13.57 mA cm−2, FF of 66.8% and PCE of 6.29% and E7:PAN (3:1) device showed a VOC of 0.719 V, JSC of 13.27 mA cm−2, FF of 65.1% and PCE of 6.21% at 1 Sun. It has been revealed that ‘the higher ionic conductivity of the LC embedded in polymeric electrolytes leads to enhancement in both JSC and FF of the quasi-solid-state DSSCs, which significantly improved the PV performance’.164

Karim et al.165 prepared solar cells with device configuration of SnO2:F|TiO2|N719|polymer LC electrolyte|pt where the polymer electrolyte was composed of iodine, tetrabutylammoniumiodide,1-propyl-3-methylimidazolium iodide, ethylene carbonate/propylene carbonate (EC/PC, 3/1 as weight ratio), PAN or click polymers as a polymer matrix, LC (ML-0249) as a plasticizer and acetonitrile. Click polymers (Figure 26) were prepared from 2,7-diazido-9,9-dioctylfluorene and 2,7-diethynyl-9,9-dioctylfluorene, respectively, using CuI-catalyzed (P1) and non-CuI-catalyzed (P2) click polymerization. The liquid electrolyte was trapped in the polymer matrix to generate polymer electrolyte. The DSSCs without ML-0249 (LC) showed a PCE of 3.53% for PAN-based electrolyte. The highest PCE of 4.70% and 4.78% were resulted for the DSSCs devices for P1:ML-0249 (1:3) and PAN:ML-0249 (1:3), respectively. The PAN:ML-0249 (1:3) system showed the highest PV performance with a PCE of 4.78%. It has been described that ‘by using LC, the viscosity of the electrolyte became low, which provided high diffusion properties of the I3 ion. As a result, the performance of the DSSC was improved’.165

Wang et al.166 used the classical NLC, 4-cyano-4’-n-heptyloxybiphenyl (7CB), into the poly(vinylidenefluoride-co-hexafluoropropylene) (PVDF)-based polymeric gel electrolyte for quasi-solid-state DSSC. The device architect FTO|TiO2|C106|LC-PVDF|Pt were fabricated, DSSC with the PVDF electrolyte shows a JSC of 14.89 mA cm−2, VOC of 685 mV, FF of 74% and an PCE of 7.54% upon adding of the LC was into the PVDF-based polymeric gel electrolyte, no change in the VOC, a decrease in FF and a remarkable increase (from 14.89 to 17.20 mA cm−2) in the JSC were obtained with higher PCE of 8.01%. This change is attributed to ‘the light trapping scheme formed by the addition of LC, the optical path of incident light is enhanced and consequently the light harvesting efficiency, which benefit the generation of photoelectron. Therefore, the electron diffusion coefficients and diffusion length of the DSSC were enlarged as well as photocurrent density, which offsets the lower FF and results in higher PCE’.166

Ahn et al.167 developed DSSCs composed of LC-embedded electrospun polymer gel electrolyte. Two types of solar cells having electrospun poly(vinylidene fluoride-co-hexafluoropropylene) (e-PVdF-co-HFP) polymer gel electrolyte were fabricated; first with doping of E7 LC and, in another device, without doping with the LC E7 and with a liquid electrolyte. DCCS containing the E7-embedded e-PVdF-co-HFP polymer gel electrolyte show a much higher PCE of 6.82% than that of an e-PVdF-co-HFP nanofiber (6.35%) with VOC of 0.72 V, JSC of 14.62 mA cm−2 and FF of 64.8% values.

In DSSC, the use of iodine solution is highly problematic owing to its corrosive nature. Recently, we demonstrated the use of discotic mesogenic molecules, hexahexylthiotriphenylene 31 (HHTT) and hexahexyloxytriphenylene 32 (HAT6) as iodine-free redox electrolyte in DSSCs (Figure 27).73 The cell shows VOC of 0.95 V, JSC of 0.534 mA cm−2, FF of 88.24% and overall PCE of 0.45% in a typical fluorine-doped tin oxide/TiO2/N719/HHTT/Pt DSSC configuration. The discotic material acts as charge carrier and mediator in these solar cells.

Figure 27
Figure 27

The geometry of DSSC with discotic electrolytes. A full color version of this figure is available at the Polymer Journal online.

Guldi et al.168 demonstrated the effect of LC phases in solid-state DSSCs. They synthesized novel imidazolium-based ILCs, which shows 3-D self-assembled motifs in LC phase. The devices with compound 33 showed JSC of 8.3 mA cm−2, VOC of 0.46 V and PCE upto 1.5% at 40 °C temperature under 1 Sun illumination. In solid crystalline phase, efficiency increases linearly owing to the decrease in viscosity, which leads to the better electrode/dye/LC contact. A good balance between dye and hole transport is accumulated by the presence of liquid crystalline phase, which gives rise to the stability of the device.

Very recently, Kato et al.169 developed nanostructures of liquid crystalline electrolytes 34-36 (Figure 26) to prepare DSSCs. They demonstrated two types of electrolyte assemblies, first as non-covalent assemblies of two-component mixtures consisting of I2-doped imidazolium ionic liquids and carbonate-terminated mesogenic compounds and second as single-component mesogenic compounds covalently bonded with an imidazolium moiety doped with I2 (Figure 28). The fabricated device with components 34 shows PCEs of 5.8±0.2%, with VOC of 0.65 V, JSC of 14.6 mA cm−2 and FF of 60% in the liquid crystalline smectic phase at 30 °C. The PCE decreases to 0.9±0.1% in the isotropic phase at 120 °C. DSSC prepared from 35 exhibits PCE of 2.4% in the smectic phase at 90 °C. The efficiency decreases both in the crystalline phase at 30 °C to 1.6% as well as in the isotropic phase at 120 °C to 1.4%. However, in the covalent-type electrolyte 36, the PCE increases with temperature in the smectic phase. It shows PCE of 0.2% at 30 °C in the SmA phase, which increases to 2.4% at 120 °C in the same LC phase. These liquid crystalline DSSCs have been reported to exhibit excellent stability over 1000 h.

Figure 28
Figure 28

The schematic illustration of the assembly of LC electrolytes into layered smectic A phases and an LC-based dye-sensitized solar cell. Blue areas represent insulating parts, and red areas show ion conductive parts. FTO, fluoride-doped tin oxide. Reproduced with permission from Högberg et al.169 Copyright 2016, American Chemical Society. A full color version of this figure is available at the Polymer Journal online.

Summary and outlook

Past few years have witnessed tremendous development in the field of OPVs owing to the predicted limited availability of fossil fuels and the impact of burning of these hydrocarbons on environment. The potential inexpensive fabrication, lightweight, flexible, semitransparency and so on of solar cells made of organic materials make them one of the most promising candidates for environmentally acceptable and commercially viable energy devices. A number of organic monomeric, oligomeric and polymeric materials have been prepared to make bilayer and BHJ solar cells. Recently, LCs have been introduced in OPVs to impart order in active layers. LC state represents a fascinating state of matter that combines both order and mobility at molecular level to macroscopic levels. The use of LCs in OPVs is currently a subject of great importance. In this paper, we have given an overview of the development of liquid crystalline materials in OPV devices. Both calamitic and DLCs have been used in bilayer, BHJ and DSSCs.

Discotic derivatives of HBC, porphyrins, Pcs, TP, perylene and decacylene have been used both as donor and acceptor as well processing additives for bilayer and BHJ solar cells. PCE exceeding 4% has been achieved in discotic PV devices. In some cases, columnar phase forming DLCs have been deployed as facilitating additives in the active layer of conventional polymer solar cells to dramatically enhance their efficiencies. Among these derivatives, HBC and TP derivatives showed significant improvement to PCE. The highest efficiency was achieved using a TP derivative 5h, which showed PCE of 8%, with enriched JSC of 16.4 mA cm−2, VOC of 0.73 V and 65% FF. PCE of 5.14% was achieved for PV solar cells containing HAT4 layer of 30-nm thickness as an inserted layer. Porphyrin derivatives showed PCE upto 4.1% while Pcs derivative-based devices performed upto 4.7% PCE.

Among the calamitic LCs, LC-conjugated polyelectrolytes poly[9,9-bis[6-(4-cyanobiphenyloxy)-hexyl]−fluorene−alt-9,9-bis(6-(N,N-diethylamino)-hexyl)-fluorene] 23 (PF6Ncbp) and poly[9,9-bis[6-(4-cyanobiphenyloxy)-hexyl]−fluorene−alt-9,9-bis(6-(N-methylimidazole)-hexyl]-fluorene] 24 (PF6lmicbp) used in device fabrication showed PCE upto 7.6%. A molecular-donor NLC benzodithiophene terthiophene rhodanine 26 have been employed to fabricated a device that shows the promising PCE of 9.3% with FF of 77%, which is rare in OPV devices. This is the highest reported PCE among calamitic-based OPV devices.

Various LCs have been employed in dye sensitizers as well as in solid-state dye sensitized solar cells. The NLC 4-cyano-4′-n-heptyloxybiphenyl (7CB) into thePVDF-based polymeric gel electrolyte for quasi-solid-state DSSC showed a remarkable increase (from 14.89 to 17.20 mA cm−2) in the JSC with higher PCE of 8.01%. PCE of 5.8% has been achieved in the liquid crystalline SmA phase of LC polyelectrolytes.

The field of liquid crystalline PVs is relatively young, but it has made significant advances during the past decade. With the help of LCs, the efficiency of OPV devices has reached to about 10%, which is considered essential for the commercial viability of solar cells. However, at present, these experiments are only at the ‘proof of concept’ stage and more rigorous efforts are required to move forward. Despite the promising properties of LCs, they have not yet been explored well and more efforts have to be made to realize their full potential. Porphyrins are natural light-harvesting antennas and hundreds of porphyrin-based LCs have been realized, but, surprisingly, only a few are used in OPVs. Hardly 0.01% of total known LCs have so far been explored in OPV field. No doubt LCs will have more prevalent roles in OPVs in the near future. However, there are several difficulties associated with LCs in OPV systems, such as proper alignment, stability, proper matching of energy levels and so on, which have to be solved to materialize their application. LCs may find significant role in next-generation advanced functional and/or engineered materials for OPV application that can only be realized as the field progresses.


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  1. Soft Condensed Matter Group, Raman Research Institute, Bengaluru, India

    • Manish Kumar
    •  & Sandeep Kumar


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The authors declare no conflict of interest.

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Correspondence to Sandeep Kumar.