Deposit and Characterization of Semiconductor Films Based on Maleiperinone and Polymeric Matrix of (Poly(3,4-Ethylenedioxythiophene) Polystyrene Sulfonate)

: The development of small semiconductor molecules such as the maleiperinone, have gained importance due to their applications in optoelectronics. In this work semiconductor ﬁlms composed by a polymer matrix of PEDOT:PSS (poly(3,4-ethylenedioxythiophene) polystyrene sulfonate) and maleiperinone were manufactured. The ﬁlms used in the studies were deposited by vacuum evaporation and spin-coating techniques. Atomic force microscopy (AFM), scanning electron microscopy (SEM), thermogravimetric analysis (TGA) and Infrared spectroscopy were used for the analysis of morphological and structural ﬁlms. The fundamental and the onset of the direct and indirect band gaps were also obtained by UV-vis spectroscopy. The band-model theory and the Density-functional theory (DFT) calculations were applied to determine the optical parameters. The dipole moment is 3.33 Db, and the high polarity gives a signal of the heterogeneous charge distribution along the structure of maleiperinone. Simple devices were made from the ﬁlms and their electrical behavior was subsequently evaluated. The presence of the polymer decreased the energy barrier between the ﬁlm and the anode, favoring the transport of charges in the device. Graphene decreased the absorption and its ohmic behavior make it a candidate to be used as a transparent electrode in optoelectronic devices. Finally, the MoO 3 provides a behavior similar to a dielectric.


Introduction
Due to their low-temperature processing, relatively easy production and for being lightweight and flexible, organic semiconductors (OSCs) have received considerable attention [1][2][3][4][5][6]. Even though OSCs are known for their unique properties, the origin of the electronic and optical properties in organic materials is unexplored. The afore mentioned represents a drawback to the application of OSCs in optoelectronics. Unlike inorganic semiconductors, OSCs are not atomic solids, instead they form conjugated bonds constituted by a system of π delocalized orbitals. Therefore, important parameters of these systems are the band gap (E g ) and the position of the frontier molecular orbitals HOMO and LUMO [7]. An advantage of OSCs is the ability to precisely tune those parameters by molecular design, and small modifications of the chemical structure can lead to large changes in the electrical and optoelectronic behavior [7]. In the OSCs these values depend on structural factors such as their π-conjugated system, planarity, the presence of electroacceptor or electrodonor groups and the aromaticity of the rings. Therefore, important work in molecular engineering has been done to control E g and the position of the frontier molecular orbitals. Two main categories of OSCs have been established: small molecules and polymer materials. Small molecules possess defined molecular structure and molecular weight; these features facilitate their fabrication and reproducibility. Furthermore, small molecules exhibit the tendency to form ordered systems affording high charge carrier mobilities [5,6]. Thus, small molecules have received considerable attention as promising alternatives to polymeric materials [1]. Additionally, the monocrystals of small molecules show remarkable charge transport properties thanks to the strong coupling of their delocalized π system in the crystalline state [8].
The use of thin films of small molecules reduces the amount of semiconductor material needed for the fabrication of electronic devices, which also decrease the cost [9]. Most of the small molecules can be deposited by physical vapor deposition (PVD) under high vacuum [10], to form semiconductor films, both amorphous and polycrystalline [8]. During PVD, the small molecules, generally in the form of a powder, are heated until evaporation/sublimation, and then the formation of high thermal gradients between the vapor and the substrates promotes the condensation of the molecule followed by its depot. Within the different techniques of PVD, vacuum evaporation/sublimation technique is a very appropriate choice for the deposition of thin films based on small molecules [3,11]. A vacuum of <10 −6 torr is applied to reduce contaminants such as oxygen and water [3], one of its main advantages. Furthermore, this technique produces homogeneous films of high purity and quality. Its main disadvantage lies in the loss of material (from 70 to 80%) that is not only deposited on the substrates, but also throughout the evaporation chamber. On the other hand, the spin-coating technique has also been used to deposit small molecules, using a simple device known as a spin-coater and a solution of the semiconductor to be deposited. This technique consists of depositing an excess of the material of interest on the substrate; subsequently, it is rotated at high speeds, to achieve uniform distribution of the material on it, thanks to the action of centrifugal force. One of the main advantages of the deposit by spin-coating in optoelectronics is the simplicity of the process, cost and handling of the device. The main disadvantages inherent to this technique are the inefficient use of the material to be deposited and the size of the substrate, since it is only possible to deposit films with dimensions of about 25 × 76 mm [12]. During the deposit by spin-coating, only a small portion (from 2 to 5%) of the material placed on the substrate is required for the manufacture of the film, while the rest of the material is removed by rotating the substrate [12].
The small molecules to be used in the depot of semiconductor films by vacuum evaporation and spin-coating must meet a series of requirements such as: high thermal and chemical stability, possess conjugated bonds and be capable to form molecular blocks and conduction channels for the charges transport. Currently there are small molecules such as porphyrins, phthalocyanines and the acene-based derivatives [1][2][3][4][5][6][9][10][11], that have been widely studied as semiconductor films. However, the accelerated development of the organic electronics requires the synthesis and evaluation of new semiconductor molecules that allow for competing against inorganic semiconductors widely used in the manufacture of devices. Thus, in the present work, the fabrication of films based in maleiperinone (MP) is proposed. MP (Figure 1a) is a flat molecule that has several fused aromatic rings, which has a rigid conjugated structure and an expanded π surface, favoring intermolecular interactions. These characteristics in the MP will benefit the adoption of an orderly structure in solid state. Additionally, the presence of nitrogen atoms in the polyaromatic system generates a decrement in the energy of the HOMO-LUMO orbitals, which translates into greater stability of the molecule. MP (10H-pyrrolo[2,1-a]perimidin-10-one) is a fused heterocyclic compound that has shown luminescent properties due to its π-electron structure that confers amphoteric properties as a result of the coexistence of the π-donor (naphthalene ring) and π-acceptor (heteroring) system [13]. Pyrrolo [1,2-a]perimidin-10-one is an integral part of the structure of some compounds that has traditionally been used as dyes and pigments [14]. On the other hand, materials containing pyrroloperimidine have contributed to the remarkable growth of interest in white light-emitting materials and other optoelectronic devices [15,16]. In recent years, perinones based on naphthalene benziimidazole [17] and trans-perinone [18] have been used as electron acceptor materials in organic electronic devices. Because these compounds have a much larger π-electron plane, incorporating perinone-like structures into materials can improve stacking intermolecular in organic solids. Maleiperinone presents a C=C bond within the five-membered ring, thus converting this molecule into a completely conjugated rigid structure, whereas other perinones without C=C bond in the five-membered ring do not show the charge transfer such as succinylperinone or tetrahydrophtaloperinone. Also, naphthalene rings in maleiperinone have shown to improve both HOMO/LUMO electron densities and high efficiency solar light absorption, making these systems suitable for applications as donors in organic solar cells [19]. In the present work, the fabrication of pristine and hybrid semiconductor films based on MP is proposed. This work started with the depot of films of pristine MP, then their chemical and structural characterization was carried out. The E g value was obtained considering direct and indirect electronic transitions, and the results were compared with the theoretically obtained by Density-functional theory (DFT). Subsequently, hybrid semiconductor films composed by a polymer matrix of PEDOT:PSS (poly(3,4-ethylenedioxythiophene) polystyrene sulfonate) ( Figure 1b) and MP were manufactured. It is intended to manufacture films with dispersed heterojunction, in which a greater contact surface and greater charge transport are generated between the PEDOT:PSS and the electronic donor MP. It is important to consider that dispersed heterojunction PEDOT:PSS/MP can also have the drawback of not having well-defined regions for the selective filtration of charge carriers towards the electrodes in electronic devices. Nevertheless, the use of PEDOT:PSS in this work is due to the fact that this polymer is one of the most important polymers in organic electronics, in the manufacture of hybrid films. The PEDOT:PSS can be used in different optoelectronic devices as an electrode [20,21], as a hole injector layer [21], as a carrier layer for holes or electrons [22,23] and as an active layer [24]. The study comprises the films: MP/PEDOT:PSS and hybrid films PEDOT:PSS/MP doped with graphene and molybdenum oxide (MoO 3 ). Graphene and MoO 3 have been selected in this work, because the electrical properties of PEDOT:PSS can be improved by graphene or MoO 3 doping [21,[25][26][27][28]. Thanks to the π-π stacking interactions, the conjugated aromatic chains of PEDOT:PSS can be stably fixed on graphene or MoO 3 structures [21,25,26]. Finally, the films were characterized optical and electrically, considering the interaction of the MP particles with the dopants. Composite and hybrid films have gained importance in optoelectronics since they combine the electrical properties of small molecules with the properties of the polymeric matrix where they are embedded [28][29][30].

Materials and Methods
All reagents and solvents were obtained from commercial suppliers (Sigma-Aldrich, Saint Louis, MO, USA), and used without further purification. MP (10H-pyrrolo[2,1-a]perimidin-10-one) was synthesized according to the method described by Likhatchev [13] from maleic anhydride and 1,8-diaminonaphthalene. The MP was deposited by vacuum evaporation and spin-coating techniques. The thin films fabricated by evaporation technique, were deposited through a high-vacuum thermal evaporation system (HVTE) using tantalum crucibles. The MP was heated to 570 K, sublimated at a vacuum pressure of 5 × 10 −6 Torr and the deposit speed was 11.4 Å/s. The thickness of each film was monitored using a microbalance quartz crystal monitor, connected to a thickness sensor (Intercovamex, S.A. de C.V., Cuernavaca, Morelos, Mexico). For the spin-coating technique, a Smart Coater 200 equipment (Laurell Technologies Corporation, North Wales, PA, USA) was used. The dispersion used for the manufacture of the films consisted of 6 mL of (i) poly(3,4-ethylenedioxythiophene)poly(styrenesulfonate) (PEDOT:PSS) from a dilution of 2.8 wt% in H 2 O or (ii) 0.2 mg/mL graphene/PEDOT:PSS hybrid dispersion in dimethylformamide or (iii) 0.8 wt% crystalline Molybdenum trioxide/PEDOT:PSS (MoO 3 /PEDOT:PSS) with 2 mg/mL of MP. The mixture was dispersed using the G560 shaker of Scientific Industries Vortex-Genie (Bohemia, New York, NY, USA). The dispersion was later deposited on the substrate and the equipment was operated at a constant angular speed of 900 rpm during 20 s and an acceleration of 302 rpm/s, then dried at 80 • C for 3 min. Thin films were deposited in monocrystalline n-type silicon wafers (c-Si), quartz and indium tin oxide (In 2 O 3 ·(SnO 2 ) x ) coated glass (glass-ITO) substrates. It is important to consider that the quartz and the glass-ITO substrates were at first sequentially washed in an ultrasonic bath with dichloromethane, methanol, and acetone. The silicon substrate was washed with a "p" solution (10 mL HF, 15 mL HNO 3 , and 300 mL H 2 O), to remove surface oxide. Thermogravimetric analysis (TGA) was performed on films by using TA Instruments Q50 Analyzer (Waters Corporation, New Castle, DE, USA). All samples were performed under nitrogen purge and were heated from 25 to 600 • C at a heating rate of 20 • C/min. FTIR spectroscopy analysis was performed for the compounds as KBr pellets and for the films using a Nicolet iS5-FT (Thermo Fisher Scientific Inc., Waltham, MA, USA) spectrometer at a wavelength range of 4000 to 500 cm −1 . The absorbance and transmittance of the powders and films were obtained in the 200-1100 nm wavelength range, on a UV-Vis 300 Unicam (Thermo Fisher Scientific Inc., Waltham, MA, USA) spectrophotometer. Topographic characteristics of films were investigated in contact mode with a Nanosurf Naio AFM (Nanosurf, Liestal, Switzerland) and morphologic characteristics were studied with a JEOL JSM-IT100 Scanning Electron Microscope (JEOL de Mexico, CDMX, Mexico). SEM conditions were: 10 kV beam current and working distance 12 mm and samples were examined in low-vacuum mode, with SEM chamber pressure set at 40 Pa. In order to characterize the electrical behaviour of the films, simple devices were fabricated using ITO as anode and silver as cathode. For the evaluation of the electrical behavior of the devices a programmable voltage source, a sensing station with lighting and temperature controller circuit from Next Robotix (Comercializadora K Mox, CDMX, Mexico) and an auto-ranging Keithley 4200-SCS-PK1 pico-ammeter (Tektronix Inc., Beaverton, OR, USA) were employed.

Theoretical Calculations
All geometries were optimized using a pure DFT method for energy evaluations, applying Becke's gradient corrections [31] for exchange and Perdew-Wang's for correlation [32]. This is the scheme for the B3PW91 method that forms part of the Gaussian 09 Package [33]. All calculations were performed using the 6-31 G** basis set. Frequency calculations were carried out at the same level of theory to confirm that the optimized struc-tures were at a minimum of the potential surfaces. The hydrogen bonds were studied taking advantage of the Grimme function (G3) implemented in the Gaussian09 package [34].

Deposit and Characterization of Pristine Maleiperinone Film
In order to study the optical and electrical behavior of thin films of MP as well as its possible application in optoelectronic devices, MP was initially deposited by vacuum evaporation. The topography and morphology are known to have a great influence on the optical and electrical properties exhibited by the MP thin films and depend on the preparation parameters of the film deposition. To study the surface roughness and topographical features of the prepared film an AFM was carried out. The 3D AFM image of the thin film is depicted in Figure 2a, and some voids are observed on the surface, although the film completely covers the substrate. In pristine MP film, the root mean square (RMS) roughness and the thickness values are recorded in Table 1. The RMS is in the order of 16.95 nm, indicating a relatively smoot surface. The SEM micrograph at 250× of MP film in Figure 2b shows a smooth and homogeneous surface with the formation of elongated structures randomly dispersed in the film. These structures are caused by the preferential directions in the growth process of some nuclei formed on the film initially deposited [10,12,13,35]. On the other hand, Figure 2c, shows the FTIR spectra of MP film, the bands appearing at 1710, 1639, 1588 and 1413 cm −1 are attributed to νC=O, νC=N, γ-heterocyclic system and νC-N bonds, respectively. The MP film spectrum was compared to the KBr pellet spectrum of the MP (see Figure 2c). The similarity between the two spectra is an indication of the ability of MP to form thin films, without undergoing chemical degradation. One of the main drawbacks of the use of organic semiconductors, with respect to inorganic ones such as silicon, is the low thermal stability [1][2][3][4][5][6]. Apparently, MP is a small molecule with high potential to compose uniform films by evaporation under vacuum.  Figure 3a shows the absorption spectra of MP film in the spectral range 280-1000 nm. The absorption spectrum shows strong transition in the visible region (450-550 nm) and in the UV region (280-315 nm). A maximum around 297 nm is observed in the spectrum, correspondent to the electronic transition n→π* towards the aromatic ring of naphthalene and an absorption band at 483 nm because of the charge transfer complex of the π electrons of the endocyclic double bond of the MP towards the heterocyclic ring [36]. Advanced UV-vis spectrum study of the prepared film was undertaken to determine the optical band gap (E g ). UV-vis spectrum data was used for point-by-point refinement of the absorption coefficient, α and the photon energy, hν [37,38]. The absorption coefficient is obtained by means of: α = −ln(T|d), where: T is the transmittance of the film (see Figure 3b), and d, is the thickness. The photon energy is obtained through: hν = hc/λ, where h is the Planck constant, c represents the speed of light and λ is the wavelength. From α and hν values, E g was obtained for direct and indirect transitions and based on the results it was determined whether the MP can be considered either as an indirect or direct band semiconductor.
To obtain information about direct or indirect interband transitions, the fundamental absorption edge data can be analyzed within the framework of the one-electron theory of Bardeen et al. [38]. Indirect and direct transitions versus hν (see Equation (1)), are plotted in the Bardeen equation, which is depicted in Figure 3c [39,40], where the factor α 0 depends on the transitions probability and can be assumed to be constant within the optical frequency range [37] and n is a number which describes the type of transition process, for direct transitions, n = 1 2 , and for indirect transitions n = 2 [38,41,42]. Thus, the optical band gap for both transitions could be determined by the extrapolation to zero of the linear regions of the (αhυ) 2 = f (hν) and (αhυ) 1 2 = f (hν) curves, E g d and E g i , respectively (Figure 3c) [38]. The extrapolation of this dependence to zero absorption yields a value of the E g at the photon energy axis [37]. The obtained values of the fundamental band gap and onset band gap were determined and summarized in Table 1. The fundamental gap is the energy gap between valence band, π and conduction band π* whereas the onset gap corresponds to the onset of optical absorption and formation of Frenkel excitation [41,43]. The band gap of 2.71 and 2.06 eV for direct and indirect transitions, respectively, places the MP in the range of small semiconductor molecules. The dominant transitions are the indirect type, which is related to a predominantly amorphous character in the film. The thermal gradients during the deposition of the film, between the temperature of the MP and the temperature of the substrates, are responsible for the amorphous structure in the semiconductor film.

Theoretical Study
The electronic behavior of this compound is illustrated by the nature of its frontier molecular orbitals. Figure 4a shows HOMO and LUMO. The energy gap calculated between HOMO and LUMO is 2.721 eV, a result that suggests a semiconductor behavior. In addition, the value of this theoretical band gap is in the interval obtained for the experimental band gap (see Table 1). In other hand, there are important factors that influence the transport properties of the MP such as the dipole moment of the small molecule that according to the DFT calculations is 3.33 Db. This high polarity gives a signal of the heterogeneous charge distribution along the structure of MP. In Figure 4b the electrostatic potential mapped onto electron density is observed, the red zone represents the strong electronegative pole, one localized on the homocyclic region of the MP. The value of dipole moment arises from the interaction of this region with those electropositive shown in green-blue or blue colors. The presence of this negative charge density deserves an explanation because it seems to be stronger than those arising from the carbonyl group, the inductive effect caused by the nitrogen atoms found as heteroatoms in the aromatic framework gives place to this particularly negative region. The ring directly receiving the excess of electronic charge shows the nitrogenated substituent in para position with respect to the final negative charged region, therefore it is possible to consider that the sum of the inductive effect of this electron release group and the positive mesomeric effect of the oxygen group induces a strong electronic current that ends in the red zone of Figure 4b. A comparison is made with a model molecule where such a nitrogen atom was substituted by a methyl group, Figure 4c shows this case and the electrostatic potential mapped onto the electronic density shows the negative electronic densities on the oxygen and lateral nitrogen regions.

Deposit and Characterization of Hybrid Semiconductor Films
The evaluation of the electrical behavior took place in a simple device made from MP film. The ITO was used as anode, while the Ag was deposited as cathode. The current (I) vs. voltage (V) of the pristine MP was estimated in the presence of radiation of different wavelengths between the IR and the UV of the electromagnetic spectrum. According to Figure 5a, it is expected to generate a device with ohmic contact, where different phenomena can take place. After the electrons are displaced from the HOMO to the LUMO of the MP, they will be injected-extracted towards the Ag. On the other hand, the hollow created in HOMO will be transferred to the ITO without the generation of energy barriers that hinder the charge injection-extraction process. The MP behaves as a p-type semiconductor or hole transporter, and its HOMO level with respect to the ITO work function allows for easy injection and high mobility of holes. According to the graph of Figure 6a, the behavior of the device ITO/MP/Ag is basically ohmic and there is no dependence between the current transported, and the wavelength irradiated to the device. In order to enhance the electrical behavior of the MP, hybrid films were deposited using the PEDOT:PSS as a matrix. Figure 5b shows how the polymer, with a work function of 5.1 eV [44], behaves as a kind of hole injector layer [21], and it is expected to favor the transport of charges between the MP that acts as a p-type semiconductor and the ITO. Additionally, the MP/PEDOT:PSS film was treated with the dopant's graphene and MoO 3 . The presence of dopants is intended to facilitate the transport of charges in the device [21,[25][26][27][28]. Figure 6b shows the ln I-V graph for the film of pristine PEDOT:PSS, it is observed that in a similar way to the device made with the MP (Figure 6a), the polymer shows ohmic behavior under different lighting conditions; furthermore, it shows insulating behavior in dark conditions or lack of radiation. These results will allow to compare the effect of both MP and polymer in the hybrid films.   Figure 7a shows the AFM image, while the Table 1 shows the RMS and the thickness values for the film PEDOT:PSS/MP, and additionally for the films doped with graphene ( Figure 7b) and MoO 3 (Figure 7c). The difference in topography between the three films is evident, and RMS values in Table 1 [46]. Since the substrates and deposit conditions of the films were the same for the three different types of film, it is evident that the presence of the doping particles influences the structure of these films.   Figure 9a shows the absorbance spectrum for each hybrid film. Comparing this figure with the spectrum in Figure 3a, the presence of PEDOT:PSS decreases the absorption of the MP, over all in the region around 483 nm, correspondent to the band generated by the transfer of the π electrons of the double endocyclic bond, towards the heterocyclic ring [36]. This effect is more significant when graphene is used (see Figure 9a), since this film does not present absorption in its spectrum. The decrease in absorption in these two films may be due to the type and morphology of dispersed heterojunction formed. By supplementing this information with the transmittance spectra in Figure 9b, it is observed that the film PEDOT:PSS/MP transmitted more than 73% of light in the wavelength region of 400-1000 nm. Nevertheless, PEDOT:PSS/MP/graphene film does not show optical behavior. The film containing graphene shows a suppressed transmittance [26]. On the other hand, when MoO 3 is the chosen dopant (see Figure 9a), the band is kept at 297 nm corresponding to the transitions n→π* towards the aromatic ring of the naphthalene. Transmission spectra of PEDOT:PSS/MP/MoO 3 is shown in Figure 9b. The transmittance at 400 nm is 77% and decrease throughout the visible range [25]. Due to the good optical transparency of the PEDOT:PSS/MP and PEDOT:PSS/MP/MoO 3 films, they would be an effective option to use in the field of organic electronics [25][26][27]. The band gap values for indirect and direct transitions, are reported in Table 1  Regarding the electrical features, Figure 10a-c show that in a similar way to the optical behavior, the electrical properties are completely modified in the films. Figure 10a illustrates the ln I-V characteristics of ITO/PEDOT:PSS/MP/Ag at different electromagnetic radiation. The results show that the curves have the same ln I-V behavior and the current increases under natural or normal illumination condition. Two distinct regions characterize these curves indicating two different conduction mechanisms. At V < 0.65 V the current increases exponentially with the applied voltage, while at V ≥ 0.65 V, the current is deviated due to a voltage drop across the resistance associated with the neutral region of a semiconductor and interface states [47]. In the Figure 10b, corresponding to the device ITO/PEDOT:PSS/MP/graphene/Ag, the same behavior is present in all the curves. At applied V < 0.1 V, the logarithm of the current increases linearly with increasing applied voltage; this indicates that thermionic emission conduction is the predominant conduction mechanism [48]. For the device ITO/PEDOT:PSS/MP/MoO 3 /Ag the behavior can be studied only, in the curve obtained under normal lighting conditions and it is an exponential behavior. The rest of the curves show a linear behavior at V ≥ 0.6 V. The incorporation of the PEDOT: PSS in the films of the devices, reduces the energy barrier between the ITO and the maleiperinone and modifies the electrical behavior in the devices. Additionally, the presence of the dopants graphene and MoO 3 , generated particular behaviors in the devices. On the one hand, graphene decreased the absorption in the film and added to its ohmic behavior, giving it the potential to be used as a transparent electrode in optoelectronic devices. In the case of the hybrid film doped with MoO 3 , the effect is less significant, because it decreases the transport of charges in the device by several orders of magnitude. This film could function as a dielectric material in organic transistors. The surface resistance results are shown in Table 2 for normal lighting conditions at 0.5 and 1 V. Films with graphene and MoO 3 dopants are the ones with the least resistance and are more likely to be used in optoelectronic devices.  Finally, Figure 11 shows the thermogram of MP pristine, PEDOT:PSS/MP/graphene, PEDOT: PSS/MP/MoO 3 , and PEDOT:PSS/MP films. Thermogravimetric analysis of the MP pristine film shows that MP decomposes into a single phase and begins to lose weight after its melting point at 130 • C. PEDOT: PSS/MP/graphene, PEDOT:PSS/MP/MoO 3 , and PEDOT:PSS/MP films compared to pristine MP film show weight losses greater than 250 • C, which indicates proper operating ranges, this is important for many optoelectronics applications. In these films, the weight losses less than 150 • C are attributed to the water absorbed by PEDOT:PSS, while weight losses greater than 250 • C are attributed to the breakdown of the sulfonate group of PSS. The steepest weight loss was observed at 400 • C, which is attributed to the degradation of the polymer backbone and the oxidation of graphene, in addition the film containing MoO 3 is the one with the best thermal stability.

Conclusions
Initially, pristine maleiperinone was deposited using the high-vacuum thermal evaporation technique. The band gap obtained for direct electronic transitions (2.82 eV), and for indirect ones (2.09 eV), places maleiperinone within the family of organic semiconductors. Additionally, the DFT analysis found a high polarity and a heterogeneous charge distribution in maleiperinone. The band gap calculated is in the range obtained experimentally. With the semiconductor maleiperinone, composite films were deposited using PEDOT:PSS as a matrix and additionally, films were made with the dopants graphene and MoO 3 . The presence of the polymer decreased the energy barrier between the semiconductor film and the anode, favoring the transport of charges in the device. Graphene decreased the absorption of the film and its ohmic behavior make it a candidate to be used as a transparent electrode in optoelectronic devices. The MoO 3 in the hybrid film provides a behavior similar to a dielectric. Thermogravimetric analysis of the films shows that the film containing MoO 3 is the one with the best thermal stability.