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Specimen ID Temperature Stress Minimum Creep Rate Time to Rupture Elongation RA T-49 900 170 7.4x10-7 3 1.3 5 T-61 1000 41 –a > 3000 –a –a T-60 1000 51 2.2x10-10 1876 0.2 0 T-62 1000 51 8.9x10-10 294 1.8 0 T-58 1000 58 3.7x10-9 111 0.5 0 T-59 1000 61 2.1x10-9 122 0.1 0 T-53 1000 68 3.4x10-9 142 0.3 0 T-52 1000 78 –b 107 –b 0 T-51 1000 88 7.8x10-8 6.7 0.5 0 T-56 1000 92 2.9x10-9 33 0.4 0 T-34 1000 100 –b 18 –b 0 T-57 1000 100 1.7x10-8 15.5 0.2 0 T-55 1000 107 2.6x10-8 8.2 0.2 0 a Test terminated prior to failure b No strain data due to extensometer malfunction From a mechanical property standpoint, the following can be concluded concerning the suitability of coarse-grained MA 754 for use in a supercritical CO2 loop. Table 4-3. Apparent Stress Exponents and Threshold Stresses for High Temperature Creep Temperature oC Apparent Stress Exponent, n Threshold Stress, MPa Longitudinal 800 41 185 900 30 145 1000 29 115 Transverse 800 24 N/A 900 9.3 N/A 1000 4.9 N/A Despite the weakness of the transverse orientation, the stress-rupture behavior of coarse-grained MA 754 still compares favorably with other high-temperature engineering alloys that are being considered for use as tubing or heat exchangers in advanced power plants. Figure 4-5 compares the stress- rupture behavior of MA 754 at 800 and 1000°C with that of three prototypic wrought high-temperature alloys: a solid solution Ni-base alloy (INCONEL® 617), a solid-solution Fe-Ni-Cr alloy (INCONEL® 800H), and a precipitation-hardened Ni-base superalloy (NIMONIC® 105). Even in the weaker transverse orientation, MA 754 is stronger than both solid solution alloys at both 800 and 1000°C. While the strengthened alloy NIMONIC® 105 is stronger at 800°C than MA 754 in both orientations, it is weaker at 1000°C for rupture lives greater than 1000 hr, reflecting the inherent high-temperature stability of the yttria dispersion with respect to precipitates. 60PDF Image | Development Of A Supercritical Carbon Dioxide Brayton Cycle
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