Creep–fatigue–oxidation interactions in a 9Cr–1Mo martensitic steel. Part III: Lifetime prediction

Fournier, Benjamin; Sauzay, Maxime; Caës, Christel; Noblecourt, Michel; Mottot, Michel; Bougault, Annick; Rabeau, Véronique; Man, Jiří; Gillia, O.; Lemoine, P.; Pineau, A.

doi:10.1016/j.ijfatigue.2008.02.006

Cited by 67 publications

(36 citation statements)

References 60 publications

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“…In this case, the fatigue life in vacuum was longer than that in air (1 -2 × 10 4 cycles in air and 4 × 10 4 cycles in vacuum at Δε t = 0.5 %, 3 -4 × 10 3 cycles in air and 1 -2 × 10 4 cycles in vacuum at Δε t = 0.7 %), which was explained by the lower crack propagation rate in vacuum than in air due to (almost) no oxidation effects. The fact that the fatigue life in air was longer than in vacuum in the present study was opposite phenomena against the fatigue life reduction in those previous reports, which was generally explained by the oxidation-enhanced fatigue crack initiation and propagation mechanism [15][16][17][18]20]. On the other hand, based on the fact that the difference in the fatigue life of the RB-7 specimen between in air and in vacuum was not so large, which did not exceed the scatter range of a factor of 2 of the regression curve of the room temperature test shown in Fig.…”

Section: Resultscontrasting

confidence: 79%

“…3. However, according to the previous reports [15][16][17][18][19], the fatigue life of the 9-12Cr martensitic steels obtained in vacuum was longer than that Fig. 3 Relationship between total strain range (Δε t ) and number of cycles to failure (N f ) of RB-1 specimen tested at R.T. in air [1] and tested at 550…”

Section: Resultsmentioning

confidence: 77%

“…• C in vacuum and in air, which has a similar microstructure to the F82H-IEA [15,16]. In this case, the fatigue life in vacuum was longer than that in air (1 -2 × 10 4 cycles in air and 4 × 10 4 cycles in vacuum at Δε t = 0.5 %, 3 -4 × 10 3 cycles in air and 1 -2 × 10 4 cycles in vacuum at Δε t = 0.7 %), which was explained by the lower crack propagation rate in vacuum than in air due to (almost) no oxidation effects.…”

Section: Resultsmentioning

confidence: 99%

See 2 more Smart Citations

High Temperature Fatigue Life Evaluation Using Small Specimen

Nogami

Hisaka

Fujiwara

et al. 2017

Plasma and Fusion Research

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For developing the high temperature fatigue life evaluation method using small specimen, the effect of specimen size and test environment on the high temperature fatigue life of the reduced activation ferritic/martensitic steel, F82H-IEA, was investigated at 550• C under the total strain range of 0.5 -1.2 % using a new high temperature low cycle fatigue testing machine for the small round-bar specimen. No significant effect of the test environment (oxidation) on the fatigue life was observed in the standard-size specimen, whereas the slight reduction of the fatigue life due to that was indicated in the small-size specimen, especially at the final fracture stage of the test. It could be concluded that the new high temperature low cycle fatigue testing machine of the present study could satisfy the minimum requirements for the high temperature low cycle fatigue life evaluation using small specimen because the fatigue life data obtained using this testing machine could be acceptable based on the comparison with the previous studies data. To improve the reliability and the applicability of this test technology, further evaluations under the wider test temperature and strain conditions are expected in future.

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Section: Resultscontrasting

confidence: 79%

Section: Resultsmentioning

confidence: 77%

Section: Resultsmentioning

confidence: 99%

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High Temperature Fatigue Life Evaluation Using Small Specimen

Nogami

Hisaka

Fujiwara

et al. 2017

Plasma and Fusion Research

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“…Totemeier et al [20] defined failure as a further 20% reduction in stress ratio from the point of crack initiation for INCONEL617; Fournier et al [21] defined the loss of 50% of the maximum stress as the fatigue lifetime for P91 steel; Whereas, Shankar et al [22] took the cycle number corresponding to a drop of 20% from the half-life stress as fatigue life for P91steel. In order to appropriately define the failure criterion of P92 steel, a new life end criterion was adopted, as described in Figure 1 (b).…”

Section: Analysis Of Data and Parameter Definitionmentioning

confidence: 99%

Characterization of Low Cycle Fatigue Performance of New Ferritic P92 Steel at High Temperature: Effect of Strain Amplitude

Wang

Gong

Zhao

et al. 2015

steel research int.

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Low cycle fatigue (LCF) tests were performed at various strain amplitudes ranging from 0.2 to 0.8% to investigate the effects of strain amplitude on cyclic softening behavior and LCF lifetime of new ferrtic P92 steel. LCF tests were conducted under strain controlled in fully reversed manner with strain rate of 1.0 Â 10 À3 s À1 at high temperature of 650 8C. A novel fatigue life end criterion was adopted in this analysis. The effects of strain amplitude on the cyclic softening behavior, the evolution of plastic strain amplitude, hysteresis loop area and the fatigue life were discussed. Similar softening curves were achieved except for the strain amplitude of 0.2%. The evolution of hysteresis loop areas at the smaller strain range amplitude (less than 0.4%) is contrary to the larger ones. A modified life prediction model was proposed based on Coffin-Manson model and energy-based model, comparison of predicted lifetime and experimental data shows that the model gives a good estimation. In order to better understand the basic stress-strain behavior, time-independent cyclic plasticity model was used to represent the cyclic mechanical behavior of this steel. Comparison of the simulated and experimental results shows that the proposed model can give a reasonable prediction of stress-strain hysteresis loop for P92 steel at high temperature.

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“…In such circumstances, mean stress changes are not limited by reverse plasticity effects. Certain steels can exhibit lower cyclic/hold test endurances due to compressive hold times but this is more typically due to crack initiation in consequential surface oxide layers during subsequent transients into tension [14]. The contribution of oxidation should also be considered for Ni based superalloys as growing oxide layers can provide also a further source of crack initiation sites.…”

Section: Cyclic/hold Test Resultsmentioning

confidence: 99%

Creep-fatigue interactions in equiaxed and single crystal Ni-base superalloys

Vacchieri

Costa

Riva

et al. 2014

MATEC Web of Conferences

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Abstract. Ni-base superalloys are employed as structural materials for the most critical hot gas path components of gas turbines. The current market requirement is to cycle the machine every day, providing energy when it is most needed. It is therefore important to understand how creep and fatigue damages interact in these components. Starting from a significant knowledge base of mechanical and microstructural behaviour established from standard tests of the equiaxed and single crystal superalloys, creep-fatigue tests have been performed to evaluate how the two damage conditions develop together. The creep-fatigue testing conditions represent the maximum temperature and strain at the critical locations in real components, while the position of hold-time has been varied from tensile to compressive to understand the effect on reduction in crack initiation endurance with respect to standard LCF tests and on the microstructural mechanisms. The experimental test results have been explained in terms of microstructural evolution and they have been correlated to that observed at critical locations in real components.

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Creep–fatigue–oxidation interactions in a 9Cr–1Mo martensitic steel. Part III: Lifetime prediction

Cited by 67 publications

References 60 publications

High Temperature Fatigue Life Evaluation Using Small Specimen

High Temperature Fatigue Life Evaluation Using Small Specimen

Characterization of Low Cycle Fatigue Performance of New Ferritic P92 Steel at High Temperature: Effect of Strain Amplitude

Creep-fatigue interactions in equiaxed and single crystal Ni-base superalloys

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