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Inconel 617 (IN617), a candidate alloy for applications in the Next Generation Nuclear Plant, derives its oxidation resistance and strength at temperatures above 900°C from both solid solution strengthening and the precipitation of carbides [1]. Cr-rich carbides (usually M 23 C 6 ) reside primarily on grain boundaries, while Mo-rich carbides (usually M 6 C) tend to be within grains [1][2][3][4]. Both intragranular and intergranular carbides play an important role in the creep behavior of the alloy [1]. During creep, intragranular carbides can dissolve and re-precipitate at grain boundaries, especially on boundaries in tension [1]. While the precipitate distribution before and after creep deformation has been investigated, the role of grain boundary character has not been included in the analysis.IN617 was creep tested at both 900 and 1000°C at stresses between 18 and 41 MPa. Microstructural characterization using integrated electron backscatter diffraction (EBSD) and energy dispersive spectroscopy (EDS) was done for both gauge (applied stress > 0) and grip (applied stress ~ 0) sections (see Figure 1). Customized algorithms allowed for analysis of precipitate type, precipitate location, grain boundary character and grain boundary alignment with respect to the stress axis.During creep, the fraction of precipitates on the boundaries increases in the gauge section (σ > 0, Figure 2). The increase in the grain boundary precipitates is due to an increase in the fraction of Mo-rich carbides on grain boundaries with little change in Cr-rich precipitate locations. The influence grain boundary character (i.e., low-angle, general high-angle, or twin boundary (Σ3)) has on precipitate location was also investigated. Figure 3 shows that, for most specimens, the majority of precipitates were found on general grain boundaries, despite general boundaries making up less than half of all boundaries. No differences are observed between grip (σ = 0) and gauge (σ > 0) sections. Finally, the precipitate distribution was analyzed in terms of the angle between the grain boundary trace and the stress axis (θ). If precipitates preferentially reside on boundaries in tension, the distribution should be shifted toward θ = 90°. Figure 4 shows the distribution of precipitates for one specimen in which the Cr-rich precipitates show a strong redistribution in the gauge section. By gathering EBSD and EDS data simultaneously, new insights can be gained on the role of grain boundary character, boundary alignment, and precipitate composition that would not be possible without the integrated data offered by these two methods.