In　this　study,　we　investigate　the　movement　of　dislocations　in　Ni-based　superalloys　under　the　influence　of　lattice　misfit　stresses　between　the　ordered　gamma＇-cuboids　and　the　disordered　gamma-matrix　during　thermal　exposure　in　the　absence　of　an　applied　load.　This　study　focuses　on　a　different　condition　than　the　conventional　creep　testing,　and　thus　offers　a　unique　opportunity　to　study　the　intrinsic　behavior　of　the　alloy.　The　dislocation　density　increases　substantially　with　time　during　thermal　exposure,　leading　to　the　formation　of　various　configurations　of　dislocation　networks　on　the　{100}(gamma/gamma＇)　interfaces,　including　＜110＞　diamond-shaped,　＜110＞/＜100＞　mixed　polygon-shaped　and　＜100＞　square-shaped　networks.　During　thermal　exposure,　the　b　=　l/2＜110＞　native　dislocations　first　move　and　evolve　into　60　mixed　dislocations　along　the　＜110＞　directions　on　the　{100}(gamma/gamma＇)　interfaces,　forming　the　＜110＞　diamond-shaped　dislocation　networks.　In　the　case　of　longer　thermal　exposures,　the　dislocations　further　evolve　into　pure　edge　dislocations　along　the　＜100＞　on　the　{100}(gamma/gamma＇)　interface,　leading　to　the　evolution　of　the　＜110＞　diamond　shaped　dislocation　networks　into　＜100＞　square-shaped　networks,　with　the　mixed　＜1104＜100＞　dislocation　networks　as　an　intermediate　stage　during　the　transition.　These　movements　occur　by　sweep　glide　in　the　{111}　planes　and　diagonal　climb　on　the　{100}　planes　for　the　edge　and　mixed　dislocations　and　by　cross-slip　for　the　screw　dislocations.　The　driving　force　for　all　of　these　movements　is　the　interaction　between　the　normal　misfit　stresses　and　the　edge　components　of　the　Burgers　vectors　of　the　dislocations　to　relax　the　misfit　stresses.　An　analysis　based　on　the　elastic　strain　energy　considerations　is　presented　to　explain　the　driving　forces　for　the　dislocation　movements.　(C)　2016　Acta　Materialia　Inc.　Published　by　Elsevier　Ltd.　All　rights　reserved.