We have observed a systematic nucleation of misfit dislocations at the InGaN/GaN heterointerface. This occurs when InGaN films are grown on an epitaxially laterally overgrown GaN substrate with a reduced dislocation density. The misfit dislocations are aligned along 〈1100〉 directions forming a symmetric hexagonal array. Potential wurtzite slip systems were analysed by extending the Matthews-Blakeslee model to include Peierls forces. Due to an inactive basal plane in the c-growth direction, non-basal slip is necessary for plastic relaxation. The active slip system was identified to be {1122} 〈1123〉. The possibility of activation of other slip systems is also discussed. However, such a periodic nucleation of misfit dislocations has not been observed in InGaN alloys. These materials undergo strain relaxation usually by forming the so-called V-defects, which nucleate from the threading dislocations in the GaN substrate [4]. Misfit dislocations are observed for higher indium compositions ([In] > 1 0%), but these are random and do not provide a systematic strain relief. Lattice strain can severely affect the properties of InGaN [5] and it is important to obtain a clear understanding of strain relaxation mechanisms.In this work, we have observed a systematic strain relief in InGaN by growing the films on GaN substrates with reduced dislocation density. To our knowledge this is the first such observation in these materials. This was achieved by using epitaxially laterally overgrown GaN (ELOG) substrates. The formation of the misfit dislocations for various slip systems is analysed by extending the MatthewsBlakeslee model [1] to include the effect of Peierls forces. The active slip system was identified to be {1122}〈1123〉. We show that in the c-plane heteroepitaxy configuration the basal-plane glide is inactive. Under these conditions, non-basal glide along {1122} slip planes is activated. The possibility of other slip systems being activated is also discussed.