High-temperature tensile-hold crack-growth behavior of HASTELLOY® X alloy compared to HAYNES® 188 and HAYNES® 230® alloys

Lee, S. Y.; Lu, Yu‐Lin; Liaw, Peter K.; Choo, Hahn; Thompson, Scott; Blust, J.W.; Browning, P.F.; Aurrecoechea, José M.; Klarstrom, D. L.

doi:10.1007/s11043-008-9049-6

Cited by 25 publications

(9 citation statements)

References 11 publications

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“…The decrease in fatigue life with the addition of a hold time is associated with a transition in crack initiation and propagation mode from transgranular in continuous-cycle fatigue to intergranular when a hold time is incorporated. It is generally accepted that intergranular crack propagation is faster than transgranular crack propagation at high temperatures in a number of alloys [3,6,16], a characteristic that has also been observed for nickel solid solution alloys [8,9]. The driving force for this change in fracture mode and the increased rates of crack propagation (based on metallography of the interrupted specimens) will be addressed in a manner that accounts for the reduction in cyclic performance with the addition of a hold.…”

Section: Discussionmentioning

confidence: 99%

“…There has been little work on the specific evolution of each of these two mechanisms during very high temperature creep-fatigue deformation. Increased rates of intergranular crack propagation during cycling coupled with a hold time have been observed by numerous authors [6][7][8][9][10]. Attributing the increase of crack growth rates directly to creep cavitation is difficult at high temperatures, however, where oxidation also plays a significant role.…”

Section: Introductionmentioning

confidence: 99%

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The development of microstructural damage during high temperature creep–fatigue of a nickel alloy

Carroll

Cabet

Carroll

et al. 2013

International Journal of Fatigue

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Section: Discussionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

The development of microstructural damage during high temperature creep–fatigue of a nickel alloy

Carroll

Cabet

Carroll

et al. 2013

International Journal of Fatigue

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“…The crack length was measured by the compliance method using the crack-opening-displacement gauge. The stress-intensity factor, K, was obtained: [20] K where P = applied load, B = thickness, W = width, a = a/W, a = crack length for a CT specimen, and DK = K max -K min (K max and K min are the maximum and minimum stress-intensity factors, respectively). When the crack length reaches 15.3 mm, a single tensile overload, 13,189 N, which is 133 pct of P max , is applied.…”

Section: Methodsmentioning

confidence: 99%

Neutron and X-ray Microbeam Diffraction Studies around a Fatigue-Crack Tip after Overload

Lee

Barabash

Chung

et al. 2008

Metall Mater Trans A

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An in-situ neutron diffraction technique was used to investigate the lattice-strain distributions and plastic deformation around a crack tip after overload. The lattice-strain profiles around a crack tip were measured as a function of the applied load during the tensile loading cycles after overload. Dislocation densities calculated from the diffraction peak broadening were presented as a function of the distance from the crack tip. Furthermore, the crystallographic orientation variations were examined near a crack tip using polychromatic X-ray microdiffraction combined with differential aperture microscopy. Crystallographic tilts are considerably observed beneath the surface around a crack tip, and these are consistent with the high dislocation densities near the crack tip measured by neutron peak broadening.

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“…Usually, the fine grain size facilitates the time-dependent FCP and SLCG of superalloys, and consequently it reduces the cracking resistance under the time-dependent condition. [22,32,33] To understand these testing results, all specimens were broken into two halves after testing, and SEM fractographic analyses were conducted. The SEM observations of fracture surfaces indicate that the accelerated time-dependent FCP rates caused by an introduction of hold time are associated with fracture mode change.…”

Section: A Fractographymentioning

confidence: 99%

“…However, no literature data exist on the systemic comparison of the FCP behavior of both alloys under both cyclic and hold time fatigue conditions at increased temperature ranges. [20][21][22] In this study, crack propagation tests under cyclic fatigue, hold time fatigue, and sustained loading conditions were performed on INCONEL 617 and HAYNES 230 to explore the crack propagation behavior using compact-tension (CT) specimens in air at 873 K, 973 K, and 1073 K (600°C, 700°C, and 800°C) under a constant K-controlled mode. The time-dependent FCP behavior of the experimental alloys was identified and their FCP rates were compared.…”

Section: Introductionmentioning

confidence: 99%

Time-Dependent Fatigue Crack Propagation Behavior of Two Solid-Solution-Strengthened Ni-Based Superalloys—INCONEL 617 and HAYNES 230

Roy

Hasan

et al. 2011

Metall Mater Trans A

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The fatigue crack propagation (FCP) as well as the sustained loading crack growth (SLCG) behavior of two solid-solution-strengthened Ni-based superalloys, INCONEL 617 (Special Metals Corporation Family of Companies) and HAYNES 230 (Haynes International, Inc., Kokomo, IN), were studied at increased temperatures in laboratory air under a constant stressintensity-factor (K) condition. The crack propagation tests were conducted using a baseline cyclic triangular waveform with a frequency of 1 3 Hz. Various hold times were imposed at the maximum load of a fatigue cycle to study the hold time effect. The results show that a linear elastic fracture mechanics (LEFM) parameter, stress intensity factor (K), is sufficient to describe the FCP and SLCG behavior at the testing temperatures ranging from 873 K to 1073 K (600°C to 800°C). As observed in the precipitation-strengthened superalloys, both INCONEL 617 and HAYNES 230 exhibited the time-dependent FCP, steady SLCG behavior, and existence of a damage zone ahead of crack tip. A thermodynamic equation was adapted to correlate the SLCG rates to determine thermal activation energy. The fracture modes associated with crack propagation behavior were discussed, and the mechanism of time-dependent FCP as well as SLCG was identified. Compared with INCONEL 617, the lower crack propagation rates of HAYNES 230 under the time-dependent condition were ascribed to the different fracture mode and the presence of numerous W-rich M 6 C-type and Cr-rich M 23 C 6 -type carbides. Toward the end, a phenomenological model was employed to correlate the FCP rates at cycle/time-dependent FCP domain. All the results suggest that an environmental factor, the stress assisted grain boundary oxygen embrittlement (SAGBOE) mechanism, is mainly responsible for the accelerated timedependent FCP rates of INCONEL 617 and HAYNES 230.

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High-temperature tensile-hold crack-growth behavior of HASTELLOY® X alloy compared to HAYNES® 188 and HAYNES® 230® alloys

Cited by 25 publications

References 11 publications

The development of microstructural damage during high temperature creep–fatigue of a nickel alloy

The development of microstructural damage during high temperature creep–fatigue of a nickel alloy

Neutron and X-ray Microbeam Diffraction Studies around a Fatigue-Crack Tip after Overload

Time-Dependent Fatigue Crack Propagation Behavior of Two Solid-Solution-Strengthened Ni-Based Superalloys—INCONEL 617 and HAYNES 230

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