Thermo-Mechanical Fatigue Crack Growth of RR1000
Abstract
:1. Introduction
2. Experimental Procedure
3. Results and Discussion
3.1. Preliminary Waspaloy Isothermal Tests
3.2. Thermal Profiling
3.3. RR1000 Isothermal Testing
3.4. TMFCG Testing
- Pre-machined notch region;
- Room temperature pre-cracking;
- Test temperature (IF) or temperature at which maximum stress is experienced (TMF) pre-cracking;
- IF or TMF test where the crack is grown to about 2 mm.
4. Conclusions
- Induction heating appears to have no effect in terms of crack tip heating or interference with DCPD crack monitoring techniques, and the combination of the two therefore appears satisfactory both for IF crack growth and TMFCG load control tests.
- Time dependence plays a significant role when comparing ‘fast’ and ‘slow’ cycle IF tests at temperatures higher than 500 °C.
- IP conditions result in faster crack growth rates than OOP, due to the high stress and high temperature regime being more damaging in terms of creep and oxidation, giving rise to intergranular failure compared to the more transgranular-dominated failure with OOP.
- Diamond cycles are sensitive to loading direction, as shown by the 90° OOP, with slightly increased growth rates resulting from the ACW cycles.
- A theory has been tested to determine if oxidation rates are responsible for the change in damage mechanism between the two. Early signs suggest that this theory holds such that a fast moving crack at high temperatures oxidises less than a dormant crack in the same temperature range (right hand side of Figure 16) which results in transgranular failure in the former and a more brittle intergranular dominated failure in the latter.
- Oxygen films have been found to build up on the upper and lower surfaces of the crack, particularly during the highly oxidising CW and 500 s ACW cycles, resulting in crack tip blunting and thus retarded crack growth rates.
- Further work is required to confirm the effect of oxygen under these test conditions. Vacuum tests and dwell tests would be useful to identify and confirm if oxidation is the main factor involved in the intergranular aspect of failure in the diamond cycles.
Acknowledgments
Author Contributions
Conflicts of Interest
References
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Alloy | Ni | Cr | Co | Mo | Ta | Al | Ti | Hf | C | B | Zr |
---|---|---|---|---|---|---|---|---|---|---|---|
Waspaloy | bal | 19.5 | 13.5 | 4.3 | – | 1.3 | 3.0 | – | 0.08 | 0.006 | – |
RR1000 | bal | 15.0 | 18.5 | 5.0 | 2.0 | 3.0 | 3.6 | 0.5 | 0.03 | 0.02 | 0.06 |
Isothermal/TMF | Cycle | Mean No. of Cycles to 2 mm | Mean Time to 2 mm (Hours) |
---|---|---|---|
IF | 700 °C Slow | 1180 | 26 |
700 °C Fast | 2450 | 3 | |
500 °C Slow | 8700 | 193 | |
500 °C Fast | 19,500 | 22 | |
300 °C Slow | 36,000 | 800 | |
300 °C Fast | 45,000 | 50 | |
TMF | IP | 2800 | 62 |
90° OOP CW | 9300 | 207 | |
90° OOP ACW | 8000 | 178 | |
90° OOP ACW Long | 6700 | 931 | |
180° OOP | 14,600 | 324 |
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Pretty, C.J.; Whitaker, M.T.; Williams, S.J. Thermo-Mechanical Fatigue Crack Growth of RR1000. Materials 2017, 10, 34. https://doi.org/10.3390/ma10010034
Pretty CJ, Whitaker MT, Williams SJ. Thermo-Mechanical Fatigue Crack Growth of RR1000. Materials. 2017; 10(1):34. https://doi.org/10.3390/ma10010034
Chicago/Turabian StylePretty, Christopher John, Mark Thomas Whitaker, and Steve John Williams. 2017. "Thermo-Mechanical Fatigue Crack Growth of RR1000" Materials 10, no. 1: 34. https://doi.org/10.3390/ma10010034