Continuum descriptions of dislocation transport are inherently non-local when long-range interactions are considered. In contrast, classical crystal plasticity theories are local, meaning the plastic response depends only on fields at a given point. As a result, length-scale effects, such as grain size, must be artificially introduced into local theories rather than emerging naturally, limiting their predictive capability at the macroscale. Ideally, such effects should be an outcome of multiscale simulations. However, the computational cost of solving large-scale simulations using continuum dislocation dynamics is significant in terms of both time and memory. In this study, we present a crystal plasticity formulation that incorporates long-range dislocation interactions. Transport of the dislocation density tensor simulated leading to development of slip bands. The computational framework has been implemented within a finite element scheme, where it is possible to introduce precipitates and study computationally interactions with the dislocation field. In this investigation, we have considered two-phase alloy microstructure representative of a γ′-strengthened nickel-based superalloy for disc applications. The model predicts length-scale effects arising from dislocation-precipitate and dislocation-grain boundary interactions. Furthermore, back stresses are predicted to develop as a result of the heterogenous distribution of the dislocation field. These numerical results are used to develop a crystal plasticity framework where such length-scale effects arise as emergent behaviour.