In the latter half of the 20th century the first active environmentalist movements such as Greenpeace and the International Energy Agency were born and initiated a gradual rethinking of environmental awareness. Against all expectations the sole agency under international law for climate protection policy, called the United Nations Framework Convention on Climate Change, was formed 20 years later. Today the awareness of sustained, regenerative and environmental policies permeates throughout all areas of life, science and industry. But energy provision is the most decisive topic, especially since the discussions concerning the phase out of nuclear power where the voices calling for alternative energy sources have become much more vociferous. In addition the depletion of fossil fuels is expected to occur in the not too distant future. All new energy generation methods are required to meet the present and future energy demands, need to be ecological and need to exhibit the same or significantly lower cost expenditure than current energy sources. Unfortunately mankind is confronted with the problem that current commercial alternative energies are more expensive and not yet remotely as efficient as the present energy sources. Although energy provision based on water, wind, sun and geothermal sources have a huge potential because of their continuous presence, unfortunately, they are plagued by inefficient energy conversion caused by the state of technology i.e. the conversion of sun light into electricity loses energy through heat emission, reflection of the sun light, the inability of the material to absorb the entire sun spectrum and the ohmic losses in the transmission of electric current. The sun power is the most exhaustless resource and moreover through photovoltaic action, one of the most direct and cleanest source for use in energy conversion. Presently incoming sun light is not transformed in its entirely, as much degradation occurs during photon absorption and electron transfer processes. A number of other innovative possibilities have also been researched. With respect to cost and efficiency one of the most promising devices is injection solar cells (ISC). By dint of the dye sensitised solar cell (DSSC) Grätzels findings provided the foundations for much research into this type of solar cell where the light absorbing molecule employed in is a dye.[1] The current is obtained through charge separation in the dye, which is initiated through the connection between the dye and a metal oxide on the one hand and a matched redox couple on the other. In a variant of the DSSC the charge separation processes can also occur between a nanoporous metal oxide and nanoparticles giving rise to a quantum dot sensitised solar cell (QDSSC).[2] The use of nanoparticle (NP) properties can be utilized for the harvesting of solar energy, as demonstrated by Kamat and coworkers[3] who were able to exploit these findings subsequently and prepare a number of nanoparticle based solar cells. Nanoparticle research has comprised a wide field of science and nanotechnology for a number of years. As the size of a material approaches dimensions on the nm scale the surface properties contribute proportionally more to the sum of the properties than the volume due to the increase in the surface to volume ratio. These dimensions also constitute a threshold in which quantum physical effects need to be taken into account. Hence the properties of devices or materials in this size regime are inevitably size dependent. The basic principles can be described by two different theories, one of which is based on molecular orbital theory in which the particle is treated as a molecule. For this reason n atomic orbitals with the same symmetry and energy can build up n molecular orbitals through their linear combination based on the LCAO method (Linear Combination of Atomic Orbitals).[4] In the case of solids the orbitals build up energy bands, where the unoccupied states form the quasi continous conduction band (CB) and the occuppied states form the quasi continous valence band (VB). The energy \"forbidden\" area in between these two bands is called the band gap. The band gap is a fixed material property for bulk solids but depends on size in the case of the nanoparticles. In contrast to the LCAO method, simplified solid state theory will be used throughout the present work, the theoretical background of which is provided by the effective mass approximation.[5] When an absorption of a photon occurs, an exciton (electron-hole pair) can be generated. By promoting an electron (e-) from the valence band into the conduction band a hole (h+) may be said to remain in the valence band. By comparison to bulk solids, in a small particle the free charges can sense the potential barrier i.e. the edges of the nanoparticle. Analogous to the particle in a box model this potential barrier interaction results in an increase in the band gap as the particle size decreases. In a solar cell NPs with a particle size which possess a band gap energy in the near infrared (NIR) may be utilised and therefore the NPs will be able to absorb in this spectral region. However NPs also have the ability to absorb higher energy photons due to the continuum present in their band structure, so that almost the entire sun spectral range from the NIR up to UV wavelengths may be absorbed just by using the appropriate NP material and size. Suitable NPs are metal chalcogenides e.g. MX (where M = cadmium, zinc or lead and X = sulfur, selenium or tellurium) because of their bandgap size[6–10] and their relative band positions compared to those of the semiconductor oxide states. Both the TiO2/CdSe[11–14] and TiO2/CdTe[15–18] systems have already been successfully fabricated and many of the anomalies reported.[3] Much interest in the lead chalcogenides has been generated by reports that they may feature the possibility to exhibit multiple exciton generation (MEG) where the absorption of one high energy photon can result in more than one electron-hole pairs.[19–25] Currently electrochemical impedance spectroscopy (EIS) is being used more and more to clarify processes at polarisable surfaces and materials such as nanoparticles. Likewise this method has been rediscovered in photovoltaic research and its use in the characterisation of DSSCs has been discussed in the literature.[26–31] In a number of publications the evaluation of nanoporous and porous structures has been quite extensively explored.[28,29,32–34] Since the mid-20th century Jaffé’s[35] theoretical work concerning the steady- state ac response of solid and liquid systems lead to the formation of the basics of EIS. Further developments in the measurement technology have lead to a broader range of analysis becoming possible. Nevertheless the most challenging part still remains the interpretation of the results and especially to merge the measured data with the theoretical model. EIS quantifies the changes in a small ac current response at electrode electrolyte interfaces i.e. the rate at which the polarized domain will respond, when an ac potential is applied. In this way dielectric properties of materials or composites, such as charge transfers, polarization effects, charge recombination and limitations can be measured as a function of frequency and mechanistic information may be unveiled. Hence EIS allows one to draw a conclusion concerning chemical reactions, surface properties as well as interactions between the electrodes and the electrolyte. Other very useful tools that may be employed for quantifying electron transfer processes and their time domains are intensity modulated photocurrent spectroscopy (IMPS) and intensity modulated photovoltage spectroscopy (IMVS). IMPS permits the generation of time-resolved plots of particular photo-processes in the system, each of which may be specifically addressed through varying the excitation wavelength. For the IMPS technique a sinusoidal wave with a small amplitude is applied, analogous to that of electrochemical impedance spectroscopy, but in this case the modulation is applied to a light source and not to the electrochemical cell as in EIS.[35] The current response is associated with the photogenerated charge carriers which flow through the system and finally discharge into the circuit. The amount of generated and discharged charge carriers is often different due to the presence of recombination and capture processes in surface or trap states. Ultimately the phase shift and magnitude of these currents reveal the kinetics of such processes. The only processes that will be addressed will be those that occur in the same frequency domain or on the same time scale as that of the modulated frequency of the illuminated light. In the literature some explanation of the kinetics of simple systems can be found and basic theories and introductive disquisitions may be found elsewhere.[36–38] Furthermore in solar cell research a multiplicity of studies are available which give an account of IMPS measurements on TiO2 nanoporous structures. Such studies permitted proof for the electron trapping and detrapping mechanism in TiO2 surface states.[39,40] An analysis of TiO2 electrodes combined with a dye sensitization step was established in the work of Peter and Ponomarev.[41–43] Hickey et.al.[44,45] have previously published kinetic studies on CdS nanoparticle (NP) modified electrodes. A theory was presented which allows for the IMPS data to be the interpreted in the case of CdS NP based electrodes. The back transfer, recombination and surface states have been demonstrated to be important as was determined from their inclusion in the theory. Similar attempts to explain the kinetics of CdS quantum dots are described by Bakkers et.al.[46]. In the present work the most important questions concern the behaviour of the photovoltaic assembly. Such assemblies can be equated with an electrode in contact with an electrolyte. Preliminary remarks about such electrodes as components of an electrochemical cell will be introduced in the first part of chapter 2. Thereafter the properties of electrodes in contact with the electrolyte and under illuminated conditions are illustrated. This is followed by a description of the important electrochemical and opto-electrochemical methods which have been employed in these studies. In particular, two separate subsections are dedicated to the methods of EIS and IMPS and the experimental section which are then linked to the theoretical section. The synthesis of all substances used and the preparation of the solar cell substrates are also dealt with in this section as will the equipment used and the instrument settings employed. The optical response of the working photoactive electrode is not only dependent on the substances used but also on their arrangement and linkage. The substrate which was employed in chapter 3 consists of a nanoporous ZnO gel layer upon which an organic linker has been placed in order to connect the oxide layer with the light absorbing component, the PbS NPs. Chapter 3 deals with the linker dependence on the ZnO layer and reports the typical optical characteristics and assembly arrangements of six different linkers on the ZnO layer which is an important intermediate stage in the fabrication of an ISC. The questions concerning how the type of linking affects the photo response and other electrochemical interactions of the complete solar cell substrate will be outlined in chapter 4. Further an examination of the electrochemical and opto-electrochemical behaviours of the samples will be presented similar to that presented in chapter 3. The most interesting substrate resulting from the investigations as described in chapter 3 and 4 will be used for a more in-depth characterisation by EIS in chapter 5. A suitable model and the results of the calculation of the ISC and the intermediate stages will be presented. The potential dependence, the dependence on the illuminated wavelength and also the size dependence of the PbS nanoparticles will be discussed. It will be revealed that ZnO is chemically unstable in contact with some of the linkers. For that reason the same linker study has been repeated with the more stable TiO2 employed as the wide band metal oxide. Comparisons between the different semiconductor metal oxides are made in chapter 6. In addition a number of open questions which previously had remained unanswered due to the instability of the ZnO can now be answered. In chapter 7 another highly porous structure different from that of the ZnO gel structure has been studied to determine its suitability as an ISC substrate. The structure arises from the electrodeposition of a ZnO reactant in the presence of eosin Y dye molecules. In the end the desorption of the dye provides a substrate with a high degree of porosity. Compared to the ZnO gel which was prepared and used for measurements in chapter 3 and 4, the electrodeposited ZnO is of a higher crystallinity and possesses a more preferential orientation. This results in a lower amount of grain boundaries which in turn results in fewer trap processes and subsequently yields a higher effective diffusion of the electron through the layer.[47,48] Optical and (opto-)electrochemical methods have been used for the basic characterisation of the untreated ZnO/Eosin Y and all other materials used in the fabrication of the ISC and a comparison with the ZnO gel used in chapter 3 and 4 will be made. Finally in chapter 8 an alternative metal oxide structure will be discussed. The background to this last chapter is to examine the influence of the ISC where the oxidic layer is present as a highly periodic arrangement, known as a photonic crystal. The TiO2 metal oxide which was also used in chapter 6 has been structured to form an inverse opal. First preparative findings and the first illustration of the (opto-)electrochemical results are presented. Consequently suggestions for improvements will be made. It is envisaged that the information gathered and presented here will help to achieve a deeper understanding of solar cells and help to improve the device efficiency and the interplay of the materials. Elementary understanding paves the way for further developments which can also contribute to providing devices for more efficient energy conversion.

This thesis discusses vacuum deposited organic solar cells. It focuses on the investigation of new donor molecules blended with the standard electron acceptor C60. These donor-acceptor heterojunctions form the photoactive system of organic solar cells. In addition, the influence of the processing conditions on the morphology of the blend layers is investigated, as the morphology is crucial for an efficient generation of free charge carriers upon photon absorption. Bulk heterojunction solar cells with the donor DTDCTB are deposited at different substrate temperatures. We identify three substrate temperature regimes, discriminated by the behavior of the fill factor (FF ) as a function of the blend layer thickness. Devices deposited at RT have a maximum FF between 50 and 70 nm blend thickness, while devices deposited at 110 °C have a monotonically decreasing FF. At Tsub=85 °C, the devices have an S-kinked current-voltage curve. Grazing incidence wide angle X-ray scattering measurements show that this peculiar behavior of the FF is not correlated with a change in the crystallinity of the DTDCTB, which stays amorphous. Absorption measurements show that the average alignment of the molecules inside the blend also remains unchanged. Charge extraction measurements (OTRACE) reveal a mobility for the 110 °C device that is an order of magnitude higher than for the RT device. The difference in mobility can be explained by a higher trap density for the RT samples as measured by impedance spectroscopy. Despite slightly higher carrier lifetimes for the RT device obtained by transient photovoltage measurements, its mobility-lifetime product is still lower than for the 110 °C devices. Based on DTDCTB, three new donor materials are designed to have a higher thermal stability in order to achieve higher yields upon material purification using gradient sublimation. For PRTF, the thermal stability is increased demonstrated by a higher yield upon sublimation. However, all new materials have a reduced absorption as compared to DTDCTB, which limits the short current density, and the FF is more sensitive to an increase of the blend layer thickness. The highest power conversion efficiency is achieved for a PRTF:C60 solar cell with 3.8%. Interestingly, PRTF:C60 solar cells show exceptionally low nonradiative voltage losses of only 0.26 V. Another absorber molecule is the push-pull chromophore QM1. Scanning electron microscope (SEM) measurements show a growth of the molecule in nanowires on several substrates. The nanowires have lengths up to several micrometers and are several tens of nanometers wide. The formation of the nanowires is accompanied by a strong blue shift (650 meV) of the thin film absorption spectrum in comparison to the absorption in solution, which is attributed to H-aggregation of the molecules. Furthermore, the thin film absorption onset reaches up to 1100 nm, making the material a suitable candidate for a near infrared absorber in organic solar cells. For a solar cell in combination with C60, a power conversion efficiency of 1.9% was achieved with an external quantum efficiency of over 19% for the spectral range between 600 and 1000 nm. The method of “co-evaporant induced crystallization” as a means to increase the crystallinity of blend layers without increasing the substrate temperature during the deposition is investigated. Mass spectrometry (LDI-ToF-MS) measurements show that polydimethylsiloxane (PDMS), which is used as a co-evaporant, decomposes during the evaporation and only lighter oligomers evaporate. Quartz crystal microbalance (QCM) measurements prove that the detection of PDMS saturates at higher amounts of evaporated material. LDI-ToF-MS measurements show further that the determination of the volatilization temperature by QCM measurements is highly error prone. The method was applied to zinc phthalocyanine (ZnPc) :C60 solar cells, accepting the insertion of PDMS into the blend layer. Diffraction (GIXRD) measurements show a large increase in crystallinity. ZnPc:C60 solar cells produced by applying the method reveal a similar behavior as solar cells processed at a higher substrate temperature.

The demand for electrical energy is steadily increasing. Highly efficient organic solar cells based on mixed, strongly absorbing organic molecules convert sunlight into electricity and, thus, have the potential to contribute to the worlds energy production. The continuous development of new materials during the last decades lead to a swift increase of power conversion efficiencies (PCE) of organic solar cells, recently reaching 12%. Despite these breakthroughs, the usage of highly complex organic molecules blended together to form a self-organised absorber layer results in complicated morphologies that are poorly understood. However, the morphology has a tremendous impact on the photon-to-electron conversion, affecting all processes ranging from light absorption to charge carrier extraction. This dissertation studies the role of phase-separation of the self-organised thin film blend layers utilized in organic solar cells. On the molecular scale, we manipulate the phase-separation, using different molecule combinations ranging from the well-known ZnPc:C 60 blend layers to highly efficient oligothiophene:C60 blend layers. On the macroscopic scale, we shape the morphology by depositing the aforementioned blend layers on differently heated substrates (in-vacuo substrate temperature, Tsub). To characterise the manufactured blend layers, we utilize high resolution microscopy techniques such as photoconductive atomic force microscopy, different electron microscopic techniques, X-ray microscopy etc., and various established and newly developed computational simulations to rationalise the experimental findings. This multi-technique, multi-scale approach fulfils the demands of several scientific articles to analyse a wide range of length scales to understand the underlying optoelectronic processes. Varying the mixing ratio of a ZnPc:C60 blend layer from 2:1 to 6:1 at fixed in vacuo substrate temperature results in a continuous increase of surface roughness, decrease of short-circuit current, and decrease of crystallinity. Additionally performed density functional theory calculations and 3D drift-diffusion simulations explain the observed crystalline ZnPc nanorod formation by the presence of C60 in the bulk volume and the in turn lowered recombination at crystalline ZnPc nanorods. Moving to oligothiophene:C60 blend layers used in highly efficient organic solar cells deposited at elevated substrate temperatures, we find an increase of phase-separation, surface roughness, decrease of oligothiophene-C60 contacts, and reduced disorder upon increasing Tsub from RT (PCE=4.5%) to 80 °C (PCE=6.8%). At Tsub =140 °C, we observe the formation of micrometer-sized aggregates on the surface resulting in inhomogeneous light absorption and charge carrier extraction, which in turn massively lowers the power conversion efficiency to 1.9%. Subtly changing the molecular structure of the oligothiophene molecule by attaching two additional methyl side chains affects the thin film growth, which is also dependent on the substrate type. In conclusion, the utilized highly sensitive characterisation methods are suitable to study the impact of the morphology on the device performance of all kinds of organic electronic devices, as we demonstrate for organic blend layers. At the prototypical ZnPc:C60 blend, we discovered a way to grow ZnPc nanorods from the blend layer. These nanorods are highly crystalline and facilitate a lowered charge carrier recombination which is highly desirable in organic solar cells. The obtained results at oligothiophene: C60 blends clearly demonstrate the universality of the multi-technique approach for an in-depth understanding of the fragile interplay between phase-separation and phase-connectivity in efficient organic solar cells. Overall, we can conclude that both molecular structure and external processing parameters affect the morphology in manifold ways and, thus, need to be considered already at the synthesis of new materials.

This thesis investigates the electrical and electrochemical properties and the long-term stability of anodes of the solid oxide fuel cell (SOFC). A model is suggested, which describes the impedance spectra of symmetrical anode cells. According to this, the series resistance in the spectra is caused by the resistance of the electrolyte (YSZ), ohmic parts of the anodes, which are described as porous electrodes, and by the partial contacting of the anodes. A major contribution to it is provided by the nickel matrix in the anodes. The high frequency relaxation in the spectra is assigned to the transfer reaction, the low frequency to a gas diffusion inhibition along the gas supply channels. The degradation of the symmetrical anode cells, which has been observed in long-term experiments, is ascribed to a degradation of the electrolyte material, of the transfer reaction, of the nickel matrix in the anodes and of the contact resistance between the anodes and the current collecting nickel grids. The degradation rate of the last two depends on the gas composition. A model for the observed behaviour in time is presented. / Diese Arbeit untersucht die elektrischen und elektrochemischen Eigenschaften und die Langzeitbeständigkeit der Anoden von Festoxid-Brennstoffzellen (SOFC). Ein Modell wird vorgestellt, mit dem die Impedanzspektren symmetrischer Anodenzellen beschrieben werden können. Demnach ist der Serienwiderstand in den Spektren verursacht durch den Widerstand des Elektrolyten (YSZ), ohmsche Anteile in den Anoden, die als poröse Elektroden beschrieben werden, und durch die partielle Kontaktierung der Anoden. Maßgebliche Beiträge liefert hier die Nickelmatrix in den Anoden. Die hochfrequente Relaxation in den Spektren wird der Durchtrittsreaktion, die niederfrequente einer Gasdiffusionshemmung entlang der Gasversorgungskanäle zugeordnet. Die in Langzeitversuchen beobachtete Degradation der symmetrischen Anondenzellen wird zurückgeführt auf eine Degradation des Elektrolytmaterials, der Durchtrittsreaktion, der Nickelmatrix in den Anoden und des Kontaktwiderstandes zwischen den Anoden und den stromabnehmenden Nickelnetzen. Die Degradation der beiden letzteren ist in ihrer Rate abhängig von der Gaszusammensetzung. Ein Modell für das beobachtete zeitliche Verhalten wird vorgestellt.

Etwa die Hälfte aller Solarzellen weltweit wird aus blockerstarrtem Silizium hergestellt. Derartige Blöcke weisen in ihren Außenbereichen eine verringerte Diffusionslänge der Minoritätsladungsträger auf. Um die Ursache dafür im Fall des bodennahen Bereichs zu bestimmen wurden zwei Spezialblöcke (ein Block mit reduzierter Bor-Dotierung und ein Block mit Phosphor-Dotierung) - u. a. mittels DLTS und FTIR - auf Kristalldefekte untersucht. Zusätzlich zu Dotierelementen (B, P, Al, As) wurden im Bodenbereich folgende Defekte nachgewiesen: <u>Metalle</u>: Fe, Cr <u>Sauerstoffhaltige Defekte</u>: Interstitieller Sauerstoff, Thermische Donatoren (TD), O1, O2 <u>Stickstoffhaltige Defekte</u>: NN-Paar, NNO-Komplex, Shallow Thermal Donors (STD) <u>Ausgedehnte Defekte</u>: Versetzungen, Ausscheidungen, Korngrenzen. Die Verteilung der flachen Donatoren (P, TD, STD, As) und Akzeptoren (B, Al) bestimmt den Widerstandsverlauf im bodennahen Bereich des Phosphor dotierten Spezialblocks. Das dortige Diffusionslängenprofil kann im Rahmen der Shockley-Read-Hall-Statistik erst durch eine Erhöhung des Minoritätseinfangquerschnitts für das Cr-Niveau (Faktor 5) bzw. für das STD-Niveau (Faktor 10) nachgezeichnet werden. Eisen, Versetzungen und Korngrenzen haben hier keinen wesentlichen Einfluss. In den untersten Millimetern des Spezialblocks müssen weitere Defekte hinzukommen, die die Diffusionslänge zusätzlich reduzieren; Thermische Donatoren und O1 und eventuell Ausscheidungen kommen dazu in Frage. Die sinngemäße Übertragung der Konzentrationsverläufe aus den beiden Spezialblöcken auf einen Block mit einer produktionsüblichen Dotierung ([B]≈10^{<small>16</small>}/cm^{<small>3</small>}) ergibt, dass in diesem Fall verschiedene Defekte (TD, STD, CrB und FeB) einen Beitrag zur Diffusionslängenreduktion im bodennahen Blockbereich liefern.

Organic transistors are a core component for basically all relevant types of fully organic circuits and consumer electronics. The Organic Permeable Base Transistor (OPBT) is a transistor with a sandwich geometry like in Organic Light Emitting Diodes (OLEDs) and has a vertical current transport. Therefore, it combines simple fabrication with high performance due its short transit paths and has a fairly good chance of being used in new organic electronics applications that have to fall back to silicon transistors up to now. A detailed understanding of the operation mechanism that allows a targeted engineering without trial-and-error is required and there is a need for universal optimization techniques which require as little effort as possible. Several mechanisms that explain certain aspects of the operation are proposed in literature, but a comprehensive study that covers all transistor regimes in detail is not found. High performances have been reported for organic transistors which are, however, usually limited to certain materials. E. g., n-type C60 OPBTs are presented with excellent performance, but an adequate p-type OPBT is missing. In this thesis, the OPBT is investigated under two aspects: Firstly, drift-diffusion simulations of the OPBT are evaluated. By comparing the results from different geometry parameters, conclusions about the detailed operation mechanism can be drawn. It is discussed where charge carriers flow in the device and which parameters affect the performance. In particular, the charge carrier transmission through the permeable base layer relies on small openings. Contrary to an intuitive view, however, the size of these openings does not limit the device performance. Secondly, p-type OPBTs using pentacene as the organic semiconductor are fabricated and characterized with the aim to catch up with the performance of the n-type OPBTs. It is shown how an additional seed-layer can improve the performance by changing the morphology, how leakage currents can be defeated, and how parameters like the layer thickness should be chosen. With the combination of all presented optimization strategies, pentacene OPBTs are built that show a current density above 1000 mA/cm^2 and a current gain of 100. This makes the OPBT useful for a variety of applications, and also complementary logic circuits are possible now. The discussed optimization strategies can be extended and used as a starting point for further enhancements. Together with the deep understanding obtained from the simulations, purposeful modifications can be studied that have a great potential. / Organische Transistoren stellen eine Kernkomponente für praktisch jede Art von organischen Schaltungen und Elektronikgeräten dar. Der “Organic Permeable Base Transistor” (OPBT, dt.: Organischer Transistor mit durchlässiger Basis) ist ein Transistor mit einem Schichtaufbau wie in organischen Leuchtdioden (OLEDs) und weist einen vertikalen Stromfluss auf. Somit wird eine einfache Herstellung mit gutem Verhalten und Leistungsfähigkeit kombiniert, welche aus den kurzen Weglängen der Ladungsträger resultiert. Damit ist der OPBT bestens für neuartige organische Elektronik geeignet, wofür andernfalls auf Siliziumtransistoren zurückgegriffen werden müsste. Notwendig sind ein tiefgehendes Verständnis der Funktionsweise, welches ein zielgerichtetes Entwickeln der Technologie ohne zahlreiche Fehlversuche ermöglicht, sowie universell einsetzbare und leicht anwendbare Optimierungsstrategien. In der Literatur werden einige Mechanismen vorgeschlagen, die Teile der Funktionsweise betrachten, aber eine umfassende Untersuchung, die alle Arbeitsbereiche des Transistors abdeckt, findet sich derzeit noch nicht. Ebenso gibt es einige Veröffentlichungen, die Transistoren mit hervorragender Leistungsfähigkeit zeigen, aber meist nur mit Materialien für einen Ladungsträgertyp erzielt werden. So gibt es z.B. n-typ OPBTs auf Basis von C60, für die bisher vergleichbare p-typ OPBTs fehlen. In dieser Arbeit werden daher die folgenden beiden Aspekte des OPBT untersucht: Einerseits werden Drift-Diffusions-Simulationen von OPBTs untersucht und ausgewertet. Kennlinien und Ergebnisse von Transistoren aus verschiedenen Parametervariationen können verglichen werden und erlauben damit Rückschlüsse auf verschiedenste Aspekte der Funktionsweise. Der Fluss der Ladungsträger sowie für die Leistungsfähigkeit wichtige Parameter werden besprochen. Insbesondere sind für die Transmission von Ladungsträgern durch die Basisschicht kleine Öffnungen in dieser nötig. Die Größe dieser Öffnungen stellt jedoch entgegen einer intuitiven Vorstellung keine Begrenzung für die erreichbaren Ströme dar. Andererseits werden p-typ OPBTs auf Basis des organischen Halbleiters Pentacen hergestellt und charakterisiert. Das Ziel ist hierbei die Leistungsfähigkeit an die n-typ OPBTs anzugleichen. In dieser Arbeit wird gezeigt, wie durch eine zusätzliche Schicht die Morphologie und die Transmission verbessert werden kann, wie Leckströme reduziert werden können und welche Parameter bei der Optimierung besondere Beachtung finden sollten. Mit all den Optimierungen zusammen können Pentacen OPBTs hergestellt werden, die Stromdichten über 1000 mA/cm^2 und eine Stromverstärkung über 100 aufweisen. Damit kann der OPBT für eine Vielzahl von Anwendungen eingesetzt werden, unter anderem auch in Logik-Schaltungen zusammen mit n-typ OPBTs. Die besprochenen Optimierungen können weiterentwickelt werden und somit als Startpunkt für anschließende Verbesserungen dienen. In Verbindung mit erlangten Verständnis aus den Simulationsergebnissen können somit aussichtsreiche Veränderungen an der Struktur des OPBTs zielgerichtet eingeführt werden.

Broadening the spectrum available to solar cells towards infrared wavelengths is one way to increase efficiency of organic solar devices. This thesis explores the possibilities of these organic heterojunction devices and two different material classes in thin films and organic solar devices: tin phthalocyanines (SnPcs) and aza-bodipys. To estimate the efficiency reachable under sunlight, model calculations are done for single and tandem cells. These calculations include a distinction between the optical gap and the electrical gap and the splitting of the quasi-Fermi levels. With a number of assumptions, e.g. a fill factor (FF) and an external quantum efficiency (EQE) within the absorption range of 65%, the resulting efficiencies are 15% in a single cell and of 21% in a tandem cell. Halogenation is known to lower the energy levels of molecules without chang-ing the optical band gap. Three different fluorinated and chlorinated SnPcs are investigated and compared to the neat SnPc. While chlorination of SnPc worsens the transport properties of the active layer leading to a lowered FF, the fluorina-tion of SnPc results in the intended increase in VOC and, consequently, efficiency for planar heterojunctions. In bulk heterojunction, however, fluorination does not change the efficiency probably due to the unstably bound fluorine. One method to modify the ionization potential (IP) and the absorption of the second material class, the aza-bodipys, is the annulation of the benzene ring. The energy levels determined by CV and UPS measurement and DFT-calculation show very good agreement and can be linked to a decrease in VOC: The Ph4-bodipy (not benzannulated) device has an efficiency of 1.2% with an EQE reaching up to 800nm and a VOC of almost 1V. The Ph2-benz-bodipy device shows a Voc of 0.65V and an efficiency of 1.1%, the EQE reaching up to 860nm. The variation of the molecule’s end groups to vary their IP is successfully employed for three different benz-bodipys: The variation results in a decrease of the optical gap from 1.5eV for the phenyl group, to 1.4eV for the MeO group, and 1.3eV for the thiophene group with the effective gap and the VOC following this trend. Efficiencies of 1.1% and 0.6% in combination with C60 can be reached in mip-type devices. Ph2-benz-bodipy is then optimized into a single cell with an efficiency of 2.9%. In a tandem cell with DCV6T-Bu4:C60, a Voc of 1.7V, a FF of 57% and an efficiency of 5% is reached. / Die Erweiterung des verfügbaren Spektrums in den Infrarotbereich ist eine Möglichkeit, die Effizienz organischer Solarzellen zu erhöhen. Diese Arbeit erkundet das Potential dieser Heteroübergänge und zwei Materialklassen in dünnen Schichten und Bauelementen: Zinnphthalozyanine (SnPc) und aza-Bodipys. Um die potentielle Effizienz abzuschäötzen, werden Modellberechnungen für Einzel- und Tandemzellen durchgeführt, unter Berücksichtigung des Unterschieds von optischer und elektrischer Bandlücke und der Quasiferminiveauaufspaltung. Mithilfe einiger Annahmen (z.B. Füllfaktor (FF) und externe Quanteneffizienz (EQE) gleich 65%) lässt sich die Einzelzelleffizienz auf 15%, die Tandemzelleffizienz auf 21% abschätzen. Halogenierung kann die Energieniveaus organischer Moleküle herabsetzen, ohne die optische Bandlücke zu verändern. Drei verschiedene chlorierte und fluorierte SnPcs werden mit dem reinen SnPc verglichen. Während die Chlorierung die Transporteigenschaften der aktiven Schicht und den FF verschlechtern, erhöht die Fluorierung wie erwartet Leerlaufspannung (VOC) und Effizienz im flachen Übergang, nicht jedoch in der Mischschicht, vermutlich aufgrund des nicht stabil gebundenen Fluors. Ein Weg, Ionisationspotential (IP) und Absorption der aza-Bodipy zu verändern, ist die Anelierung des Benzenrings. Die durch CV und UPS ermittelten und mittels DFT errechneten Energieniveaus stimmen gut überein und führen zu einer Verringerung der VOC: Die Zelle mit nichtaniliertem Ph4-bodipy zeigt eine Effizienz von 1.2%; das EQE reicht bis 800nm, die VOC beträgt fast 1V. Die Ph2-benz-bodipy-Zelle zeigt eine VOC von 0.65V und eine Effizienz von 1.1%, das EQE reicht bis 860nm. Der Austausch der Endgruppen zur Vergrößerung des IP, erfolgreich angewandt auf drei Benz-Bodipy-Verbindungen, führt zu einer Verringerung der optischen Bandlücke: von 1.5eV (Phenyl) über 1.4eV (MeO) zu 1.3eV (Thiophen); effektive Bandlücke und Voc folgen diesem Trend. Effizienzen von 1.1% und 0.6% in Kombination mit C60 werden in mip-Zellen erreicht. Ph2-benz-bodipy zeigt in einer optimierten nip-Zelle sogar eine Effizienz von 2.9%. Eine Tandemzelle mit DCV6T-Bu4:C60 zeigt eine Voc von 1.7V, einen FF von 57% und eine Effizienz von 5%.