Characterization of high temperature tensile and creep–fatigue properties of Alloy 800H for intermediate heat exchanger components of (V)HTRs

Kolluri, M.; Pierick, P. ten; Bakker, Theo C. M.

doi:10.1016/j.nucengdes.2014.12.017

Cited by 27 publications

(16 citation statements)

References 16 publications

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“…It showed that, at temperatures above 473 K, the load serrations in Incoloy800H superalloy occurred over a wide range of strain rates. The tensile and creep-fatigue properties of Incoloy800H superalloy at a high temperature were investigated [13]. It was observed that the combined creep fatigue damage at 800˝C decreased with the decreasing total strain.…”

Section: Introductionmentioning

confidence: 99%

Continuous Casting of Incoloy800H Superalloy Billet under an Alternating Electromagnetic Field

Wang

Zhang

Deng

et al. 2015

Metals

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Abstract:We experimentally investigate the influence of an alternating electromagnetic field on the surface and internal qualities of Incoloy800H superalloy billets. The electromagnetic continuous casting experiments for Incoloy800H superalloy were successfully conducted and the billets (0.1 mˆ0.1 mˆ1.2 m) were obtained. We figure out that the high frequency (20.4 kHz) electromagnetic field which is applied in the mould region can improve the surface quality of Incoloy800H superalloy billet remarkably; the depth of oscillation mark decreases from 1.2 mm (without electromagnetic field) to 0.3 mm (with electromagnetic field). The internal quality of the billet was studied using a variety of characterization techniques. The low frequency (5 Hz) electromagnetic field which is applied in the second cooling region can improve the internal quality; the region of the equiaxed grain increases from 2.45% (without electromagnetic field) to 41.45% (with electromagnetic field). Furthermore, macro-and micro-segregation are suppressed and the TiN inclusion number is decreased as well.

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Section: Introductionmentioning

confidence: 99%

Continuous Casting of Incoloy800H Superalloy Billet under an Alternating Electromagnetic Field

Wang

Zhang

Deng

et al. 2015

Metals

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“…However, for some tests at higher total strain ranges, the cumulative creep-fatigue damage fraction was found to be greater than one (>1). It is worth noting that the D f is more severe at higher total strain ranges [19]. It was also observed that the D c for most of the tests were higher than the ASME-accepted critical value (D c ) of 0.1, which indicates the potential suitability of this alloy for applications beyond 900 • C. In spite of the observed interaction diagram, Figure 13 shows that all of the test results are within the ±2 scatter band of the linear damage equation according to the Campbell diagram [22,26].…”

Section: Discussionmentioning

confidence: 99%

“…From this graph, it is found that the additional inelastic strain was introduced by means of transformation from elastic strain, caused by the reduction of stress generated during the holding time. Based on this behavior it can be assumed that there would be creep deformation at high temperature [10,19]. 1 Cycle number was determined from a 20% drop in the stress ratio.…”

Section: Creep-fatigue Propertiesmentioning

confidence: 99%

“…Based on this behavior it can be assumed that there would be creep deformation at high temperature [10,19]. Figure 8 shows the stress relaxation curves for 60, 180, and 300 s hold time of base metal and weldments, respectively.…”

Section: Creep-fatigue Propertiesmentioning

confidence: 99%

“…In the ASME Code, Section III, Subsection NH, creep-fatigue life is evaluated by a linear summation of fractions of cyclic damage and creep damage, schematically reported in some studies [19][20][21][22][23][24]. Thus, the creep-fatigue criterion is given by: …”

Section: Linear Damage Summationmentioning

confidence: 99%

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High-Temperature Creep-Fatigue Behavior of Alloy 617

Dewa

Park

Kim

et al. 2018

Metals

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This paper presents the high-temperature creep-fatigue testing of a Ni-based superalloy of Alloy 617 base metal and weldments at 900 • C. Creep-fatigue tests were conducted with fully reversed axial strain control at a total strain range of 0.6%, 1.2%, and 1.5%, and peak tensile hold time of 60, 180, and 300 s. The effects of different constituents on the combined creep-fatigue endurance such as hold time, strain range, and stress relaxation behavior are discussed. Under all creep-fatigue tests, weldments' creep-fatigue life was less than base metal. In comparison with the low-cycle fatigue condition, the introduction of hold time decreased the cycle number of both base metal and weldments. Creep-fatigue lifetime in the base metal was continually decreased by increasing the tension hold time, except for weldments under longer hold time (>180 s). In all creep-fatigue tests, intergranular brittle cracks near the crack tip and thick oxide scales at the surface were formed, which were linked to the mixed-mode creep and fatigue cracks. Creep-fatigue interaction in the damage-diagram (D-Diagram) (i.e., linear damage summation) was evaluated from the experimental results. The linear damage summation was found to be suitable for the current limited test conditions, and one can enclose all the data points within the proposed scatter band.

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Thermal Deformation Characteristics and Dynamic Recrystallization Mechanism of Incoloy 800H Alloy under Different Deformations

Jia,

Zhang,

Wang

et al. 2023

Adv Eng Mater

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Incoloy 800H alloy has excellent high‐temperature mechanical properties and broad application prospects. However, the dynamic recrystallization (DRX) behavior of this alloy at different deformations has been little studied. The thermal deformation characteristics and DRX mechanisms of Incoloy 800H alloy are studied by thermal compression tests. Quantitative analysis of grain size, DRX fraction, misorientation distribution, and twin boundaries under different deformation degrees is conducted using electron‐backscattered diffraction. Furthermore, the evolution characteristics of dislocations and grains are observed through transmission electron microscopy. It is found that the proportion of DRX improves with increasing deformation significantly. In the DRX process, discontinuous DRX (DDRX) is the main nucleation mechanism, while continuous DRX (CDRX) serves as an auxiliary nucleation mechanism. As the deformation increases, the CDRX + DDRX mechanisms can also be observed simultaneously in the high‐density dislocation region near the grain boundary. In addition, the ratio of ∑3 boundaries first decreases and then increases as the deformation increases. The initial twins gradually disappear due to the increase in deformation, and new twins are formed within the DRX grains. Twins can promote grain boundary bulging, provide more nucleation sites for DRX, and have a significant promoting effect on DRX.

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Characterization of high temperature tensile and creep–fatigue properties of Alloy 800H for intermediate heat exchanger components of (V)HTRs

Cited by 27 publications

References 16 publications

Continuous Casting of Incoloy800H Superalloy Billet under an Alternating Electromagnetic Field

Continuous Casting of Incoloy800H Superalloy Billet under an Alternating Electromagnetic Field

High-Temperature Creep-Fatigue Behavior of Alloy 617

Thermal Deformation Characteristics and Dynamic Recrystallization Mechanism of Incoloy 800H Alloy under Different Deformations

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