Finally, we can determine the mobilities for charge transport along individual lattice di-rections by fitting the linear regions in Fig. according to eqn. (2). The mobility is given here by the slope of the linear fit. We calculate the electron mobilities as µ a = 6.4 cm 2 /Vs, µ b = 8.1 • 10 4 cm 2 /Vs, and µ c = 0.3 cm 2 /Vs. Again, the mobility along the polymer chains is much higher than in the other two directions. Although intra-chain charge transport is expected to be faster than between different chains, the inter-chain charge transfer between backbones is known to be crucial for transport in a real polymeric system since macroscopic transport cannot only be provided by single chains. The mobilities along the latter two directions are already at the lower end of the range where the picture of band-like charge transport is valid. Such anisotropic behavior has also been experimentally observed for polythiophene-based polymers. For instance, a high mobility anisotropy of µ ∥ /µ ⊥ ≈ 1000 (where µ ∥ and µ ⊥ is the field-effect mobility along and orthogonal to the backbone orientation direction, respectively) was reported for highly oriented films of poly[2,5bis(3-tetradecylthiophen-2-yl)thieno [3,2-b]thiophene] (PBTTT). A similar anisotropy of the mobility of 4 × 10 3 was found in poly(3-octylthiophene) (P3OT) single crystals. Yu et al. reported a mobility of up to 2.3 cm 2 /Vs along the π-stacking direction of mesocrystalline poly(3-hexylthiophen-2,5-diyl) (P3HT). Luo et al. measured inter-chain mobilities along the π-π stacking direction of 1-2 cm 2 /Vs for highly oriented nanocrystalline thiophene-based polymers. Overall, the agreement of our results with recent experimental values shows that a band-like description is able to explain the charge transport in well-ordered polymer systems.