Development of potential low activation ferritic and austenitic steels

Tamura, Manabu; Hayakawa, Hiroshi; Tanimura, Masayuki; Hishinuma, A.; Kondô, Tatsuo

doi:10.1016/0022-3115(86)90144-3

Cited by 184 publications

(82 citation statements)

References 2 publications

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“…These systems are desired to operate at relatively high temperatures up to 650 С. RAFM steels possess exceptional thermal conductivity and low thermal expansion among other steels while being strongly resistant to void swelling. The RAFM steels such as Eurofer97, F82H and Rusfer were developed in Europe [4,5], Japan [6], and Russia [7], respectively. Their composition lies in the following range: Fe-(7.5-12)Cr-(1.1-2)W-(0.15-0.25)V, in weight percent.…”

Section: Introductionmentioning

confidence: 99%

Surface modification and deuterium retention in reduced-activation steels under low-energy deuterium plasma exposure. Part I: undamaged steels

et al. 2016

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Section: Introductionmentioning

confidence: 99%

Surface modification and deuterium retention in reduced-activation steels under low-energy deuterium plasma exposure. Part I: undamaged steels

et al. 2016

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“…Steel of F82H [1][2][3] is planned to use for a Japanese ITER test blanket module. 4) According to the trial design the test blanket is fabricated by mainly hot isostatic pressing and tungsten inert gas welding 5) and the total mass of a unit module exceeds 2 ton.…”

Section: Introductionmentioning

confidence: 99%

Creep Behavior of Double Tempered 8%Cr-2%WVTa Martensitic Steel

Tamura

Nowell²,

Shinozuka

et al. 2006

Mater. Trans.

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Creep testing was carried out at around 650 C for a martensitic 8Cr-2WVTa steel (F82H), which is a candidate alloy for the first wall of the fusion reactors of the Tokamak type. Rupture strength of the double tempered steel (F82HD) is lightly higher than that of simply tempered steel (F82HS). On the other hand, creep rate of F82HD is obviously smaller than that of F82HS in acceleration creep, though creep strain of F82HD in transition creep, where creep rate decreases with increasing strain, is larger than that of F82HS. Hardness of the crept F82HD decreases with increasing creep strain, which corresponded with the transmission electron microscopy (TEM) observation. On the contrary, X-ray diffraction and electron back-scattered diffraction pattern measurements show that fine sub-grains are created during transition creep. The creep curves were analyzed using an exponential type creep equation and the apparent activation energy, the activation volume and the pre-exponential factor were calculated as a function of creep strain. Then, these parameters were converted into two parameters, i.e. equivalent obstacle spacing (EOS) and mobile dislocation density parameter (MDDP). While EOS decreases with increasing creep strain, MDDP increases with increasing strain during transition creep. The decrease in EOS and the increase in either EOS or MDDP are rate-controlling factors in transition and acceleration creep, respectively. On the other hand, in case of F82HS, EOS increases and MDDP decreases during transition creep. In this case, the decrease in MDDP controls the creep rate during transition creep of F82HS. It is concluded that both EOS and MDDP are representative parameters of the change in substructure during creep.

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“…The steel was produced by NKK Corporation under the sponsorship of Japan Atomic Energy Research Institute and was heattreated by normalizing at 1313 K for 0.5 h and tempering at 1013 K for 2 h [5].…”

Section: Material Specimen Geometry and Tensile Testmentioning

confidence: 99%

Measurement of Residual Stresses around the Notch of Tensile Specimens of the High-Cr Tempered Martensitic Steel F82H-Mod

Ilchuk¹,

Spätig²,

Davydov³

et al. 2013

KEM

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Abstract. Residual elastic strains were measured by neutron diffraction using POLDI materials science diffractometer at PSI-Switzerland on pre-loaded notched flat tensile specimens made of the high-chromium tempered martensitic steel F82H-mod steel. To calculate the residual stresses using Hooke's equation, three perpendicular components of the residual strain field were determined. The measured residual strains and stresses were compared with those deduced from finite element simulation calculations. A very good agreement was found for the strains in the loading plane of the specimen while a somewhat larger discrepancy was observed for the out-of-plane residual strain, which was tentatively attributed to an uncertainty in the initial lattice spacing in that direction.

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Development of potential low activation ferritic and austenitic steels

Cited by 184 publications

References 2 publications

Surface modification and deuterium retention in reduced-activation steels under low-energy deuterium plasma exposure. Part I: undamaged steels

Surface modification and deuterium retention in reduced-activation steels under low-energy deuterium plasma exposure. Part I: undamaged steels

Creep Behavior of Double Tempered 8%Cr-2%WVTa Martensitic Steel

Measurement of Residual Stresses around the Notch of Tensile Specimens of the High-Cr Tempered Martensitic Steel F82H-Mod

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