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By means of the measurement of creep curves and microstructure observation, the creep behavior and influencing factors of FGH95 nickel-base superalloy has been investigated. Results show that after the solution treatment at 1150 oC and aging, some coarse g ￠ precipitates are discontinuously distributed in the grain boundary region and around them is the depleted zone of the finer g ￠ phase. However, after the solution treatment at 1165 oC and aging, the grains are obviously grown up, and the films of the carbide are continuously precipitated along the boundaries. After the solution treatment at 1160 oC and aging, the coarse g ￠ phase in the alloy is fully dissolved, the finer g ￠ phase is dispersedly distributed within the grains, and some particles of (Nb,Ti)C phase are discontinuously precipitated in the grains and along the boundaries, which is thought to be the main reason for better creep resistance due to the pinning effect of them to restrain the boundaries slipping. The deformation mechanism of the alloy during creep is the dislocation shearing or bypassing the g ￠ phase. In the later creep stage, the deformation features of the alloy are the single-orientation and double-orientations slipping of dislocations activated in the alloy, which brings out the stress concentration to promote the initiation and propagation of the micro-cracks along the boundaries, and it is thought to be the fracture mechanism of the alloy during creep