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In the present review, the main degradation mechanisms occurring in the different layer stacking (i.e. photoactive layer, electrode, encapsulation film, interconnection) of polymeric organic solar cells and modules are discussed. Bulk and interfacial, as well as chemical and physical degradation mechanisms are reviewed, as well as their implications and external or internal triggers. Decay in I-V curves in function of time is usually due to the combined action of sequential and interrelated mechanisms taking place at different locations of the device, at specific kinetics. This often makes the identification of specific root causes of degradation challenging in non-model systems. Additionally, constant development and refinement in terms of type and combination of materials and processes render the ranking of degradation mechanisms as a function of their probability of occurrence and their detection challenging. However, it clearly appears that for the overall stability of organic photovoltaic devices, the actual photoactive layer, as well as the properties of the barrier and substrate (e.g. cut of moisture and oxygen ingress, mechanical integrity), remain critical. Interfacial stability is also crucial, as a modest degradation at the level of an interface can quickly and significantly influence the overall device properties.

The three main strategies for dispersing carbon nanotubes (NTs) into a polymer matrix to get conductive nanocomposites are described, and illustrated with some appealing examples. The direct mixing of the NTs and the polymer is the 'simplest' concept to achieve this goal. Other approaches concern the modification of either the polymer matrix or the NT walls in order to improve the wetting of the filler with the matrix material, and thus promote the incorporation of the NTs into the polymer matrix. Most promising results seem to be obtained upon the addition of a third component. The basic concept is the generation of a stable colloidal system containing both a suspension of NTs stabilized by surfactant molecules in water, and polymer latex. After removal of the water, the resulting powder can be processed into the desired shape. This versatile and environmentally benign concept offers low percolation thresholds and relatively high conductivity levels.

In this paper we demonstrate that the sonication-driven exfoliation of aggregates and bundles of single-wall carbon nanotubes (SWNTs) in an aqueous surfactant solution can be easily monitored by UV-vis spectroscopy. The different stages of the exfoliation process were directly visualized by cryogenic temperature transmission electron microscopy, showing an excellent correspondence with the spectroscopic data: the maximum achievable exfoliation (which does not mean that 100% of the NTs are effectively exfoliated) corresponds to the maximum UV-vis absorbance of the NT solution. Moreover, it has been observed that NTs produced by the arc-discharge technology (Carbolex NTs) require less energy to achieve maximum exfoliation than NTs produced by chemical vapor deposition (HiPCO NTs). This difference is attributed to weaker van der Waals attraction between Carbolex NTs in the bundles and aggregates.

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During nonisothermal crystallization of highly dispersed polypropylene/carbon nanotube (CNT) composites, considerable heterogeneous nucleation is observed to an extent scaling with the CNT surface area. Saturation occurs at higher loadings, reaching a plateau value for the crystallization onset which is 15 °C higher than in the unfilled matrix. Polymorphic behavior does not occur, as revealed from wide-angle X-ray diffraction. Upon subsequent heating, an increase in the melting temperature is observed due to increased crystalline perfection in the presence of CNTs. The complex multiple melting behavior is interpreted in terms of recrystallization phenomena. A study at varying heating and cooling rates reveals that CNTs affect the chain segment mobility of the matrix and largely inhibit recrystallization upon heating. TEM observation of the nanocomposite morphology evidences the occurrence of a transcrystalline layer around the CNTs. A structure model is presented, in which individually dispersed CNTs are separated from a bulklike polymer phase by a highly ordered crystalline interface with reduced polymer mobility.

We present a detailed study of the influence of carbon nanotube (CNT) characteristics on the electrical conductivity of polystyrene nanocomposites produced using a latex‐based approach. We processed both industrially‐produced multi‐wall CNT (MWCNT) powders and MWCNTs from vertically‐aligned films made in‐house, and demonstrate that while the raw CNTs are individualized and dispersed comparably within the polymer matrix, the electrical conductivity of the final nanocomposites differs significantly due to the intrinsic characteristics of the CNTs. Owing to their longer length after dispersion, the percolation threshold observed using MWCNTs from vertically‐aligned films is five times lower than the value for industrially‐produced MWCNT powders. Further, owing to the high structural quality of the CNTs from vertically‐aligned films, the resulting composite films exhibit electrical conductivity of 103 S m−1 at 2 wt% CNTs. On the contrary, composites made using the industrially‐produced CNTs exhibit conductivity of only tens of S m−1. To our knowledge, the measured electrical conductivity for CNT/PS composites using CNTs from vertically‐aligned films is by far the highest value yet reported for CNT/PS nanocomposites at this loading.

The crystallization behavior of isotactic polypropylene (iPP) in the vicinity of single-wall and multiwall carbon nanotubes (SWCNTs and MWCNTs) has been studied. Combined DSC and transmission electron microscopy (TEM) investigations of bulk composite materials reveal that CNTs nucleate iPP when crystallizing from the quiescent melt and that iPP crystals form a transcrystalline layer of aligned iPP lamellar crystals around the nucleating CNT. The pronounced nucleation effect and the formation of a transcrystalline layer is observed also for ultrathin film CNT/iPP samples. Corresponding diffraction studies show that in bulk as well as in the case of the ultrathin film samples only the α-phase of iPP exists. The transcrystalline layer is highly oriented around the nucleating CNTs, and the crystallographic c-axes of the lamellae are oriented perpendicular to the long axis of the nucleating CNT, which is in contradiction to assumptions done in other studies. This crystallization behavior is discussed and a possible explanation is provided based on iPP macromolecules wrapped around rather than aligned along the CNTs prior to formation of the nucleus.