Accumulation of engineering data for practical use of reduced activation ferritic steel: 8%Cr2%W0.2%V0.04%TaFe

Yamanouchi, N.; Tamura, Manabu; Hayakawa, Hiroshi; Hishinuma, A.; Kondô, Tatsuo

doi:10.1016/0022-3115(92)90587-b

Cited by 85 publications

(33 citation statements)

References 6 publications

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“…Truly 'low-activation' steels proved impossible, because the steels are limited by the decay of radioactive products from transmutation of the iron atoms. 'Reduced-activation' materials were considered possible, and in the mid-1980s and early 1990s, fusion reactor materials research programs in Japan, Europe, and the United States [10][11][12][13][14][15][16][17][18][19][20][21][22][23][24][25][26][27][28]. For reduced-activation steels, activity decays in a relatively short time, thus allowing for shallow land burial as opposed to deep geological storage for disposal of decommissioned plant components.…”

Section: Fusion Reactor Studiesmentioning

confidence: 99%

Ferritic/martensitic steels for next-generation reactors

Klueh

Nelson

2007

Journal of Nuclear Materials

769

255

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Section: Fusion Reactor Studiesmentioning

confidence: 99%

Ferritic/martensitic steels for next-generation reactors

Klueh

Nelson

2007

Journal of Nuclear Materials

769

255

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“…[10][11][12][13][14][15][16][17][18][19][20][21][22][23][24][25][26][27][28] The development evolved from calculations to determine which elements must be replaced in conventional Cr-Mo steels to obtain a rapid decay of induced radioactivity after irradiation in a fusion reactor. 9,10 Such calculations indicated that the typical steel-alloying elements Mo, Nb, Ni, Cu, and N must be eliminated or minimized to obtain "reduced activation."…”

Section: Fusion Reactorsmentioning

confidence: 99%

Elevated temperature ferritic and martensitic steels and their application to future nuclear reactors

Klueh¹

2005

International Materials Reviews

485

176

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In the 1970s, high chromium (9-12%Cr) ferritic/martensitic steels became candidates for elevated temperature applications in the core of fast reactors. Steels developed for conventional power plants, such as Sandvik HT9, a nominally Fe-12Cr-1Mo-0 . 5W-0 . 5Ni-0 . 25V-0 . 2C steel (composition in wt-%), were considered in the USA, Europe and Japan. Now, a new generation of fission reactors is in the planning stage, and ferritic, bainitic and martensitic steels are again candidates for in-core and out-of-core applications. Since the 1970s, advances have been made in developing steels with 2-12%Cr for conventional power plants that are significant improvements over steels originally considered. The present study will review the development of the new steels to illustrate the advantages they offer for the new reactor concepts. Elevated temperature mechanical properties will be emphasised. Effects of alloying additions on long-time thermal exposure with and without stress (creep) will be examined. Information on neutron radiation effects will be discussed as it applies to ferritic and martensitic steels.

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“…[13][14][15][16][17] 2. Experimental Procedure A 15 mm mill production plate of F82H 18) was used. Chemical composition of the plate is shown in Table 1.…”

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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Accumulation of engineering data for practical use of reduced activation ferritic steel: 8%Cr2%W0.2%V0.04%TaFe

Cited by 85 publications

References 6 publications

Ferritic/martensitic steels for next-generation reactors

Ferritic/martensitic steels for next-generation reactors

Elevated temperature ferritic and martensitic steels and their application to future nuclear reactors

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

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