JPH1088289A - Chromium-manganese austenitic sintered steel with high corrosion resistance and high strength, its production, and its use - Google Patents

Chromium-manganese austenitic sintered steel with high corrosion resistance and high strength, its production, and its use

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Publication number
JPH1088289A
JPH1088289A JP8241586A JP24158696A JPH1088289A JP H1088289 A JPH1088289 A JP H1088289A JP 8241586 A JP8241586 A JP 8241586A JP 24158696 A JP24158696 A JP 24158696A JP H1088289 A JPH1088289 A JP H1088289A
Authority
JP
Japan
Prior art keywords
less
steel
grain size
reactor
austenitic
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
JP8241586A
Other languages
Japanese (ja)
Inventor
Masahiko Arai
将彦 新井
Tatsumi Hirano
辰己 平野
Yasuhisa Aono
泰久 青野
Takahiko Kato
隆彦 加藤
Yasuo Kondo
保夫 近藤
Masatoshi Inagaki
正寿 稲垣
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Hitachi Ltd
Original Assignee
Hitachi Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Hitachi Ltd filed Critical Hitachi Ltd
Priority to JP8241586A priority Critical patent/JPH1088289A/en
Publication of JPH1088289A publication Critical patent/JPH1088289A/en
Pending legal-status Critical Current

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Classifications

    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E30/00—Energy generation of nuclear origin
    • Y02E30/10—Nuclear fusion reactors
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E30/00—Energy generation of nuclear origin
    • Y02E30/30—Nuclear fission reactors

Abstract

PROBLEM TO BE SOLVED: To provide a Cr-Mn austenitic steel excellent in corrosion resistance, strength, and radiation exposure damage resistance and its production and also to provide a nuclear reactor, a nuclear fusion reactor, and their component parts, by uniformly refining crystalline grain size into superfine state. SOLUTION: The Cr-Mn austenitic sintered steel with high corrosion resistance and high strength is a steel containing, by weight, <=0.1% C, <=1% Si, <=0.4% N, 9-25% of (Mn+Ni) under the condition that Mn is >2 to 15%, and 14-20% Cr and having <=1μm average crystalline grain size and >=90vol.% of austenitic phase or a steel further containing, besides the above, at least one kind among <=3% Mo, <=1.0% Ti, <=2.0% Zr, and <=1.0% Nb and having the above characteristics. These steels are used for a structure in a nuclear reactor and a part, to be subjected to neutron irradiation and brought into contact with high temp. water, of a nuclear fusion furnace, etc.

Description

【発明の詳細な説明】DETAILED DESCRIPTION OF THE INVENTION

【０００１】[0001]

【発明の属する技術分野】本発明は新規なオースナテナ
イト鋼に係り、特に、腐食環境，高応力負荷環境下で使
用するに好適な構造用Ｃｒ−Ｍｎ系オーステナイト鋼と
その製造法，用途に関する。本発明は新規なオーステナ
イト鋼に係り、特に原子炉炉心等の放射線照射環境下で
使用するに好適な構造用Ｃｒ−Ｍｎ系オーステナイト鋼
とその製造法，用途に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a novel austenite steel, and more particularly to a structural Cr-Mn austenitic steel suitable for use in a corrosive environment or a high stress load environment, and a method of manufacturing and using the same. . The present invention relates to a novel austenitic steel, and more particularly to a structural Cr-Mn austenitic steel suitable for use in a radiation irradiation environment such as a nuclear reactor core, and a method of manufacturing and using the same.

【０００２】[0002]

【従来の技術】オーステナイト系ステンレス鋼は、耐食
性，加工性，経済性の面から構造材料として好適な特性
を具備しており、構造部品の材料として広く用いられて
いる。しかし、他の構造用鋼と比較して強度が十分でな
い欠点を有している。オーステナイト鋼の合金組成を変
えずに、耐食特性を維持し、強度を向上させる方法とし
て、変形抵抗となる粒界を材料中に多数導入する所謂結
晶粒径微細化法がある。結晶粒界は異なる結晶方位を持
つ単結晶間の境界であり、粒内の整然とした原子配列の
結晶格子とは相違して乱れた結晶構造を有する。変形を
担う転位は応力下で粒内を運動して変形を起こすが、粒
界の存在は転位との相互作用を引き起こし、転位が乱れ
た粒界を通過する時に大きな抵抗を生む。この変形抵抗
は結晶粒径の関数として結晶粒径の−１／２乗に比例し
て増加し、所謂ホール・ペッチの法則に従うことがよく
知られている。2. Description of the Related Art Austenitic stainless steel has characteristics suitable as a structural material in terms of corrosion resistance, workability, and economy, and is widely used as a material for structural parts. However, there is a disadvantage that the strength is not sufficient as compared with other structural steels. As a method for maintaining the corrosion resistance and improving the strength without changing the alloy composition of the austenitic steel, there is a so-called crystal grain refinement method in which a large number of grain boundaries serving as deformation resistance are introduced into the material. A crystal grain boundary is a boundary between single crystals having different crystal orientations, and has a disordered crystal structure unlike a crystal lattice having an ordered atomic arrangement in a grain. Although the dislocations responsible for the deformation move within the grains under stress to cause the deformation, the existence of the grain boundaries causes the interaction with the dislocations and generates a large resistance when the dislocations pass through the disturbed grain boundaries. It is well known that this deformation resistance increases in proportion to the -1/2 power of the crystal grain size as a function of the crystal grain size, and follows the so-called Hall-Petch law.

【０００３】近年、圧延プロセスでオーステナイト鋼に
対し加工誘起マルテンサイト変態および高温での逆変態
を起こさせ、オーステナイト結晶粒径をサブミクロンサ
イズまで微細化させた研究が進展中であり、例として製
造方法等が鉄と鋼，日本鉄鋼協会，第８０巻，１９９４
年，５２９−５３５ページ及び日本金属学会会報，第２
７巻，第５号，１９８８年，４００−４０２ページに報
告されている。[0003] In recent years, research has been underway to reduce the austenite crystal grain size to a submicron size by causing work-induced martensitic transformation and reverse transformation at high temperature in an austenitic steel in a rolling process. The method is iron and steel, The Iron and Steel Institute of Japan, Vol. 80, 1994
Year, pp. 529-535 and the Bulletin of the Institute of Metals, Japan, No. 2.
7, No. 5, 1988, pp. 400-402.

【０００４】オーステナイト鋼は、耐食性のＣｒを含有
し、腐食環境下に対する抵抗を有していることから、例
えば原子炉内で使用する構造部品の製造用として多く用
いられている。しかし、軽水炉炉心のオーステナイト鋼
部材は使用中に被る長期の放射線照射により、不純物の
結晶粒界への偏析あるいは延性の低下等の機械的性質が
低下することが知られている。例えば、通常の溶体化熱
処理で結晶粒径を数十μｍ程度の多結晶としたオーステ
ナイト系ステンレス鋼では、炉心部で照射量で４×１０
25ｎ／ｍ2 以上の中性子照射を受けた場合、均一延びが
１％以下になる。このような照射下での強度劣化現象の
金属学的メカニズムは、照射によって導入される空孔，
格子間原子等の素欠陥が集合して形成される二次欠陥の
存在により変形抵抗が増大すると説明されている。[0004] Austenitic steel contains corrosion-resistant Cr and has resistance to a corrosive environment, and is therefore often used, for example, for manufacturing structural parts used in nuclear reactors. However, it is known that mechanical properties such as segregation of impurities to crystal grain boundaries or reduction of ductility are reduced by a long-term irradiation of austenitic steel members of a light water reactor core during use. For example, in the case of austenitic stainless steel which is made of polycrystal having a crystal grain size of about several tens of μm by ordinary solution heat treatment, the irradiation amount is 4 × 10
When irradiated with neutrons of 25 n / m 2 or more, the uniform elongation becomes 1% or less. The metallurgical mechanism of such strength degradation phenomenon under irradiation is that vacancies introduced by irradiation,
It is described that the deformation resistance increases due to the presence of secondary defects formed by collecting elementary defects such as interstitial atoms.

【０００５】[0005]

【発明が解決しようとする課題】しかし製造方法で、一
般的な傾向として溶体化材が一気に圧延される工程であ
る逆変態熱処理工程あるいは熱加工工程では、結晶粒径
は、強い加工性の影響、すなわち圧延方向及び厚さ方向
の加工度に強く依存して方向に対して不均一となり易
い。また本方法では加工度に上限があり、サブミクロン
からナノスケールまでの超微細結晶化はより困難であ
る。However, in the production method, in general, in the reverse transformation heat treatment step or the heat processing step in which the solution heat-treating material is rolled at once, the crystal grain size is affected by the strong workability. In other words, it tends to be non-uniform in the rolling direction and in the thickness direction, depending on the degree of work in the thickness direction. In addition, in the present method, there is an upper limit in the degree of processing, and it is more difficult to crystallize ultrafine crystals from submicron to nanoscale.

【０００６】ナノ結晶を有するオーステナイト系ステン
レス鋼は、組成の持つ耐食性に加えて、結晶粒の超微細
化のために高強度が達成され、また超微細結晶であるが
故に粒界での不純物の希釈効果および特に照射損傷によ
る組織変化にも抵抗性がある利点を有する。[0006] Austenitic stainless steel having nanocrystals achieves not only the corrosion resistance of the composition, but also a high strength due to ultra-fine crystal grains, and because of the ultrafine crystals, impurities at the grain boundaries can be eliminated. It has the advantage of being resistant to dilution effects and especially to tissue changes due to radiation damage.

【０００７】オーステナイト鋼組成を有するナノ結晶化
バルク材の製造には以下の課題がある。結晶粒径のナノ
スケール化には、低温でオーステナイト相をより強加工
するプロセスが必要である。また結晶粒径の均一化には
強い圧延組織が残存する溶体化した部材の強圧延以外の
方法の選択が必要である。以上の課題に対して期待でき
る製造方法として機械的グラインディング法の活用があ
る。このプロセスでは、素材粉は圧延法よりもより微細
な加工誘起マルテンサイト相に変態され、そのため加工
粉末の固形化熱処理でも粗大化が抑制されて、ナノ結晶
化され易い。また本法では加工粉末の固形化熱処理およ
びそれに続く組織調整のための高温での加工熱処理でも
結晶粒径の不均一性は圧延プロセスに比べて十分に小さ
いことが期待される。[0007] The production of a nanocrystalline bulk material having an austenitic steel composition has the following problems. In order to reduce the crystal grain size to a nano-scale, a process for further processing the austenite phase at a low temperature is required. Further, in order to make the crystal grain size uniform, it is necessary to select a method other than the strong rolling of a solution-formed member in which a strong rolled structure remains. As a manufacturing method that can be expected for the above problems, there is utilization of a mechanical grinding method. In this process, the raw material powder is transformed into a finer work-induced martensite phase than the rolling method, so that the solidification heat treatment of the processed powder suppresses coarsening and is likely to be nanocrystallized. Also, in this method, it is expected that the non-uniformity of the crystal grain size is sufficiently smaller than that of the rolling process even in the heat treatment for solidification of the working powder and the subsequent working heat treatment at a high temperature for texture adjustment.

【０００８】本発明の目的は、結晶粒径を均一に超微細
化することにより、耐食性，強度，耐放射線照射損傷に
優れたＣｒ−Ｍｎ系オーステナイト鋼、その製造法及び
それを用いた原子炉及び核融合炉とそれらの構成部品を
提供することにある。An object of the present invention is to provide a Cr-Mn austenitic steel excellent in corrosion resistance, strength and radiation damage due to uniform ultrafine crystal grain size, a method for producing the same, and a nuclear reactor using the same. And fusion reactors and their components.

【０００９】[0009]

【課題を解決するための手段】本発明は、重量で、Ｃ
０.１％以下，Ｓｉ１％以下，Ｎ０.４％以下，Ｍｎ２％
を越え１５％以下の範囲で（Ｍｎ＋Ｎｉ）９〜２５％及
びＣｒ１４〜２０％を含有し、平均結晶粒径が１μｍ以
下であり、９０体積％以上のオーステナイト相を有する
ことを特徴とする高耐食性高強度Ｃｒ−Ｍｎ系オーステ
ナイト焼結鋼にある。SUMMARY OF THE INVENTION The present invention provides a C
0.1% or less, Si 1% or less, N 0.4% or less, Mn 2%
High corrosion resistance characterized by containing (Mn + Ni) 9 to 25% and Cr 14 to 20% in a range exceeding 15% and an average crystal grain size of 1 μm or less and having an austenite phase of 90% by volume or more. High strength Cr-Mn austenitic sintered steel.

【００１０】更に、本発明は上述の合金に、Ｍｏ３％以
下，Ｔｉ１.０％以下，Ｚｒ２.０％以下，Ｎｂ１.０％
以下の１種又は複数の元素をＴｉ，Ｚｒ及びＮｂの総量
で2.0％以下を含むものである。Further, the present invention relates to the above alloys, in which Mo 3% or less, Ti 1.0% or less, Zr 2.0% or less, Nb 1.0%.
It contains one or more of the following elements in a total amount of Ti, Zr and Nb of 2.0% or less.

【００１１】また、本発明は重量で、Ｃ０.１％以下，
Ｓｉ１％以下，Ｎ０.４％以下，Ｍｎ２％を越え１５％
以下の範囲で（Ｍｎ＋Ｎｉ）９〜２５％及びＣｒ１４〜
２０％含有する鋼粉又はこれにＭｏ３％以下，Ｔｉ１.
０％以下，Ｚｒ２.０％以下，Ｎｂ１.０％以下の少なく
とも１種又はＴｉ，Ｚｒ，Ｎｂの複数の元素を２.０％
以下を含有する鋼粉に結晶粒径２０ｎｍ以下でかつ加工
誘起マルテンサイト変態相を有する加工粉末を形成する
工程と、加工粉末を１０００℃以下の温度で熱間静水圧
焼結又は熱間押し出し加工を施す工程とを有することを
特徴とする高耐食性高強度Ｃｒ−Ｍｎ系オーステナイト
焼結鋼にある。[0011] The present invention also relates to the present invention in which C 0.1% or less by weight,
Si 1% or less, N 0.4% or less, Mn more than 2% and 15%
(Mn + Ni) 9 to 25% and Cr 14 to
Steel powder containing 20% or Mo3% or less, Ti1.
0% or less, Zr 2.0% or less, Nb 1.0% or less at least one kind or a plurality of elements of Ti, Zr, Nb 2.0%.
Forming a working powder having a crystal grain size of 20 nm or less and a work-induced martensitic transformation phase in a steel powder containing: hot isostatic sintering or hot extrusion of the working powder at a temperature of 1000 ° C. or less And a step of applying high corrosion resistance and high strength Cr-Mn austenitic sintered steel.

【００１２】本発明は、重量で、Ｃ０.１％以下，Ｓｉ
１％以下，Ｐ０.０４５％以下，Ｓ０.０３％以下，Ｎ
０.４％以下，Ｍｎ２％を越え１５％以下の範囲で（Ｍ
ｎ＋Ｎｉ）９〜２５％及びＣｒ１４〜２０％を含有する
オーステナイト鋼で、加工誘起マルテンサイト相を含む
機械的加工粉末を用いて７００℃〜１０５０℃の温度で
固形化熱処理、あるいは固形化熱処理とそれに続く該固
形化物の加工熱処理を実施し、室温の体積率で９０％以
上がオーステナイト相であり、該相の平均結晶粒径が１
０ｎｍ〜１０００ｎｍであることを特徴とする高耐食性
高強度Ｃｒ−Ｍｎ系オーステナイト焼結鋼にある。According to the present invention, C 0.1% or less by weight, Si
1% or less, P 0.045% or less, S 0.03% or less, N
In the range of not more than 0.4% and not less than 2% and not more than 15% (M
n + Ni) Austenitic steel containing 9-25% and Cr 14-20%, using a mechanically processed powder containing a work-induced martensite phase at a temperature of 700 ° C. to 1050 ° C. for heat treatment for solidification or heat treatment for solidification. Subsequently, the solidified product is subjected to a working heat treatment, and at least 90% of the austenite phase has a volume fraction at room temperature, and the average crystal grain size of the phase is 1%.
A high corrosion resistance, high strength Cr-Mn austenitic sintered steel characterized by having a thickness of 0 nm to 1000 nm.

【００１３】本発明は前述と同様にＭｏ，Ｔｉ，Ｚｒ及
びＮｂを含むものである。The present invention includes Mo, Ti, Zr and Nb as described above.

【００１４】本発明は、重量で、Ｃ０.１％以下，Ｓｉ
１％以下，Ｎ０.４％以下，Ｍｎ２％を越え１５％以下
の範囲で（Ｍｎ＋Ｎｉ）９〜２５％及びＣｒ１４〜２０
％を含有する鋼粉又はこれにＭｏ３％以下，Ｔｉ１.０
％以下，Ｚｒ２.０％以下，Ｎｂ１.０％以下の少なくと
も１種でＴｉ，Ｚｒ，Ｎｂの複数の元素を合計で２.０
％以下を含有する鋼粉をアトマイズ粉末あるいは総体と
して該組成を満たす混合粉末を１００℃以下で３０〜１
００時間アトライタあるいはボールミルを用いて機械的
にグラインディングまたは合金化処理し、結晶粒径が１
５ｎｍ以下の加工誘起マルテンサイト変態相を有する加
工粉末を形成する工程と、該加工粉末を熱間静水圧焼結
または熱間押し出し法にて７００℃〜１０５０℃の温度
範囲で固形化熱処理あるいは固形化熱処理とそれに続く
温度域での最終加工熱処理をすることにより室温の体積
率で９０％以上がオーステナイト相となり、１０ｎｍ〜
1000ｎｍの範囲で平均結晶粒径を調整することを特徴と
する高耐食性高強度Ｃｒ−Ｍｎ系オーステナイト焼結鋼
の製造方法にある。The present invention relates to a method for manufacturing a semiconductor device, comprising:
In a range of 1% or less, N 0.4% or less, Mn 2% or more and 15% or less, (Mn + Ni) 9 to 25% and Cr 14 to 20
% Or less than Mo 3%, Ti 1.0%
%, Zr 2.0% or less, and Nb 1.0% or less at least one of a plurality of elements of Ti, Zr, and Nb in total of 2.0.
% Or less as an atomized powder or a mixed powder satisfying the composition as a whole at 100 ° C. or less.
Mechanical grinding or alloying treatment using an attritor or a ball mill for 00 hours.
Forming a working powder having a work-induced martensitic transformation phase of 5 nm or less, and subjecting the working powder to solidification heat treatment or solidification in a temperature range of 700 ° C to 1050 ° C by hot isostatic sintering or hot extrusion. By performing the chemical heat treatment and the final working heat treatment in the subsequent temperature range, 90% or more of the volume ratio at room temperature becomes an austenite phase, and
The present invention relates to a method for producing a high corrosion-resistant, high-strength Cr-Mn-based austenitic sintered steel characterized by adjusting the average crystal grain size in the range of 1000 nm.

【００１５】本発明は、重量で、Ｃ０.１％以下，Ｓｉ
１％以下，Ｎ０.４％以下，Ｍｎ２％を越え１５％以下
の範囲で（Ｍｎ＋Ｎｉ）９〜２５％及びＣｒ１４〜２０
％を含有するＣｒ−Ｍｎ系オーステナイト焼結鋼又はこ
れにＭｏ３％以下，Ｔi１.０％以下，Ｚｒ２.０％以
下，Ｎｂ１.０％以下の少なくとも１種でＴｉ，Ｚｒ，
Ｎｂの複数の元素を合計で２.０％ 以下を含有するＣｒ
−Ｍｎ系オーステナイト焼結鋼よりなることを特徴とす
る原子炉内部材にあり、他前述したＣｒ−Ｍｎ系オース
テナイト鋼によって構成される。The present invention relates to a method for manufacturing a semiconductor device, comprising:
In a range of 1% or less, N 0.4% or less, Mn 2% or more and 15% or less, (Mn + Ni) 9 to 25% and Cr 14 to 20
% Of Cr-Mn-based austenitic sintered steel containing at least one of Mo 3% or less, Ti 1.0% or less, Zr 2.0% or less, and Nb 1.0% or less.
Cr containing a total of 2.0% or less of a plurality of elements of Nb
-An inner member of a nuclear reactor characterized by being made of sintered Mn-based austenitic steel, and constituted by the above-mentioned Cr-Mn-based austenitic steel.

【００１６】本発明は、重量で、Ｃ０.１％以下，Ｓｉ
１％以下，Ｎ０.４％以下，Ｍｎ２％を越え１５％以下
の範囲で（Ｍｎ＋Ｎｉ）９〜２５％及びＣｒ１４〜２０
％を含有するＣｒ−Ｍｎ系オーステナイト焼結鋼又はこ
れにＭｏ３％以下，Ｔi１.０％以下，Ｚｒ２.０％以
下，Ｎｂ１.０％以下の少なくとも１種でＴｉ，Ｚｒ，
Ｎｂの複数の元素を合計で２.０％ 以下を含有するＣｒ
−Ｍｎ系オーステナイト焼結鋼よりなることを特徴とす
る締結部材にあり、他前述のＣｒ−Ｍｎ系オーステナイ
ト鋼によって構成される。According to the present invention, C 0.1% or less by weight, Si
In a range of 1% or less, N 0.4% or less, Mn 2% or more and 15% or less, (Mn + Ni) 9 to 25% and Cr 14 to 20
% Of Cr-Mn-based austenitic sintered steel containing at least one of Mo 3% or less, Ti 1.0% or less, Zr 2.0% or less, and Nb 1.0% or less.
Cr containing a total of 2.0% or less of a plurality of elements of Nb
-A fastening member characterized by being made of a Mn-based austenitic sintered steel, and constituted by the above-mentioned Cr-Mn-based austenitic steel.

【００１７】本発明は、水と接触し、中性子照射を受け
るＣｒ−Ｍｎ系オーステナイト鋼からなる構造部材で、
該部材は平均結晶粒径が１μｍ以下であることを特徴と
する高耐食性高強度構造部材にある。The present invention relates to a structural member made of a Cr-Mn austenitic steel which is in contact with water and subjected to neutron irradiation,
The member is a high-corrosion-resistant high-strength structural member characterized by having an average crystal grain size of 1 μm or less.

【００１８】本発明は、原子炉圧力容器内に中性子源パ
イプ，炉心支持板，中性子計装管，制御棒挿入パイプ，
シュラウド，上部格子板，燃料集合体用被覆管及びチャ
ンネルボックスの各構造部品を備えた原子炉で、該原子
炉の構造部品の少なくとも一つを前述の本発明に係わる
Ｃｒ−Ｍｎ系オーステナイト鋼又は中性子照射を受け高
温高圧水に接する表面を前述の本発明の鋼によって構成
したことを特徴とする原子炉及びその原子炉内構成部品
にある。The present invention provides a neutron source pipe, a core support plate, a neutron instrumentation pipe, a control rod insertion pipe,
A nuclear reactor equipped with a shroud, an upper grid plate, a cladding tube for a fuel assembly, and a channel box, wherein at least one of the structural components of the nuclear reactor is made of the above-described Cr-Mn austenitic steel or the austenitic steel according to the present invention. A nuclear reactor and a component in the nuclear reactor characterized in that a surface which is in contact with high-temperature and high-pressure water after being irradiated with neutrons is constituted by the above-mentioned steel of the present invention.

【００１９】本発明は、原子炉圧力容器内に中性子源パ
イプ，炉心支持板，中性子計装管，制御棒挿入パイプ，
シュラウド，上部格子板，燃料集合体用被覆管及びチャ
ンネルボックスの各構造部品を備えた原子炉用構成部品
で、構造部品の少なくとも一つが全オーステナイト組織
を有する前述のＣｒ−Ｍｎ系オーステナイト鋼によって
構成される。The present invention provides a neutron source pipe, a core support plate, a neutron instrumentation pipe, a control rod insertion pipe,
A component for a nuclear reactor including structural components such as a shroud, an upper lattice plate, a cladding tube for a fuel assembly, and a channel box, wherein at least one of the structural components is made of the above-described Cr-Mn austenitic steel having a full austenitic structure. Is done.

【００２０】本発明は、原子炉圧力容器内に収納された
原子燃料によって得られた熱出力で蒸気タービンを回
し、蒸気タービンの回転によって発電機を駆動し、それ
によって電気出力を得る原子力発電プラントで、原子炉
の熱出力が３２００ＭＷ以上，原子炉圧力７.０ＭＰａ
以上，原子炉水温度２８８℃以上、電気出力が１１００
ＭＷ以上であり、原子炉圧力容器内に設けられた中性子
源パイプ，炉心支持板，中性子計装検出管，制御棒挿入
パイプ，シュラウド及び上部格子板の各構成部品の少な
くとも一つを３０年以上無交換で使用でき、稼働質を８
５％以上としたことを特徴とする原子力発電プラントに
ある。。The present invention relates to a nuclear power plant in which a steam turbine is turned by a heat output obtained by nuclear fuel contained in a reactor pressure vessel, and a generator is driven by rotation of the steam turbine, thereby obtaining an electric output. The reactor has a thermal output of 3200 MW or more and a reactor pressure of 7.0 MPa.
As described above, the reactor water temperature was 288 ° C or higher, and the electric output was 1100.
At least one of the neutron source pipe, reactor core support plate, neutron instrumentation detection tube, control rod insertion pipe, shroud and upper lattice plate installed in the reactor pressure vessel for 30 years or more Can be used without replacement, operating quality is 8
Nuclear power plant characterized in that it is set to 5% or more. .

【００２１】本発明は、原子炉圧力容器内に収納された
原子燃料によって得られた熱出力で蒸気タービンを回
し、該蒸気タービンの回転によって発電機を駆動し、そ
れによって電気出力を得る原子力発電プラントで、原子
炉の熱出力が４３００ＭＷ以上，原子炉圧力が７.２Ｍ
Ｐａ以上，原子炉水温度２８８℃以上,電気出力が1500
ＭＷ以上の稼働率を８５％以上及び１２ケ月運転後の定
検期間を１回当り５０日以内としたことを特徴とする原
子力発電プラントにある。[0021] The present invention provides a nuclear power plant that rotates a steam turbine with a thermal output obtained by a nuclear fuel contained in a reactor pressure vessel, and drives a generator by rotating the steam turbine, thereby obtaining an electrical output. At the plant, the thermal power of the reactor is over 4300MW and the reactor pressure is 7.2M
Pa or more, reactor water temperature 288 ° C or more, electric output 1500
The nuclear power plant is characterized in that an operation rate of MW or more is 85% or more, and a regular inspection period after 12 months operation is within 50 days per operation.

【００２２】本発明における原子炉及び原子力発電プラ
ントは前述のＣｒ−Ｍｎ系オーステナイト鋼との組合せ
は勿論である。更に、原子力発電の高効率化には蒸気条
件を高めることが必須であり、そのためには原子炉によ
って得た蒸気をガスタービンとの複合サイクルとし、そ
の排熱を用いて３００℃〜５００℃の蒸気とする過熱蒸
気を得ることによって達成される。The nuclear reactor and the nuclear power plant according to the present invention can be used in combination with the above-mentioned Cr-Mn austenitic steel. Furthermore, it is essential to increase the steam conditions in order to increase the efficiency of nuclear power generation. For that purpose, the steam obtained by the nuclear reactor is used as a combined cycle with a gas turbine, and the exhaust heat is used to reduce the temperature to 300 ° C to 500 ° C. This is achieved by obtaining superheated steam as steam.

【００２３】本発明は、水冷構造を有する真空容器内に
プラズマ側にセラミックスタイルが設けられ水冷構造を
有するダイバータ、およびプラズマ側にセラミックスタ
イルが設けられ水冷構造を有する第一壁を備えた核融合
炉で、該核融合炉の構成部品の少なくとも一つ、さら
に、水冷構造を有する真空容器，セラミックスタイルが
設けられ水冷構造を有するダイバータ、およびプラズマ
側にセラミックスタイルが設けられた水冷構造を有する
第一壁の少なくとも一つを、前述の本発明に係るＣｒ−
Ｍｎ系オーステナイト鋼によって構成したこと、又は中
性子照射を受け高温高圧水に接する表面を前述の本発明
の鋼によって構成したことを特徴とする核融合炉又は核
融合炉内構成部品にある。According to the present invention, there is provided a divertor having a water-cooled structure provided with a ceramic style on a plasma side in a vacuum vessel having a water-cooled structure, and a nuclear fusion provided with a first wall having a water-cooled structure provided with a ceramic style on a plasma side. At least one of the components of the fusion reactor, a vacuum vessel having a water-cooled structure, a diverter provided with a ceramic style and having a water-cooled structure, and a second water-cooled structure having a ceramic style provided on the plasma side. At least one of the walls is made of the Cr-
A nuclear fusion reactor or a component in a nuclear fusion reactor, characterized in that it is made of a Mn-based austenitic steel, or that the surface in contact with high-temperature and high-pressure water which is irradiated with neutrons is made of the above-mentioned steel of the present invention.

【００２４】本発明の鋼は室温における耐力が３００Ｍ
Ｐａ以上，伸び率０.５％ 以上が好ましく、特に、耐力
４００〜６００ＭＰａ，伸び率１０〜３０％が好まし
い。The steel of the present invention has a proof stress of 300 M at room temperature.
It is preferably at least Pa and an elongation of at least 0.5%, particularly preferably at a yield strength of 400 to 600 MPa and an elongation of 10 to 30%.

【００２５】本発明に係る鋼を前述のＢＷＲ原子炉内構
造物に用いることにより原子炉内構造物を交換すること
なく３０年以上使用することができ、特に４０年間同様
に使用できる。更に、原子炉として熱出力３２００ＭＷ
以上,原子炉圧力７.０ＭＰａ以上，温度２８８℃以上で
ある大容量に対して長期にわたる使用で有効である。更
に、本発明に係る鋼を同様に用いたＡＢＷＲ原子炉では
熱出力４３００ＭＷ以上，炉圧力７.２ＭＰａ 以上，温
度２８８℃以上とし、電気出力を１５００ＭＷ以上の大
容量化が達成できるものである。更に、このＡＢＷＲで
も前述の構造材を無交換で３０年以上の使用が可能とな
るものである。By using the steel according to the present invention for the above-mentioned BWR reactor internal structure, it can be used for 30 years or more without replacing the reactor internal structure, and particularly, it can be used similarly for 40 years. Furthermore, the thermal power of the reactor is 3200MW
As described above, it is effective for long-term use for a large capacity with a reactor pressure of 7.0 MPa or more and a temperature of 288 ° C. or more. Further, in an ABWR reactor similarly using the steel according to the present invention, a heat output of 4300 MW or more, a furnace pressure of 7.2 MPa or more, a temperature of 288 ° C. or more, and a large electric capacity of 1500 MW or more can be achieved. Further, even with this ABWR, the above-mentioned structural material can be used for 30 years or more without replacement.

【００２６】特に、本発明に係る鋼を用いることにより
定検時被曝量を２０ｍＳＶ／人年以下，定検期間を３０
月以内，稼働率９０％以上，熱効率３５％以上，ボイド
係数−２.８〜−４.２％，取出燃焼度４５〜７０ＧＷｄ
／ｔとすることが可能である。In particular, by using the steel according to the present invention, the radiation dose at the time of regular inspection is 20 mSV / person year or less and the period of regular inspection is 30 minutes.
Within a month, operation rate 90% or more, thermal efficiency 35% or more, void coefficient -2.8 to -4.2%, extraction burnout 45 to 70GWd
/ T.

【００２７】本発明が解決しようとする耐食性に優れた
オーステナイト鋼の高強度化は、結晶粒径の超微細化に
より解決できる。このことは、結晶粒界が塑性変形を担
う転位のすべり運動の障害物になることから粒界の密度
を極限まで高めることで塑性変形抵抗性が飛躍化できる
ことで説明される。The high strength of the austenitic steel excellent in corrosion resistance to be solved by the present invention can be solved by making the crystal grain size ultra-fine. This is explained by the fact that the plastic deformation resistance can be increased by increasing the density of the grain boundaries to the limit, since the crystal grain boundaries become obstacles to the sliding motion of the dislocations responsible for the plastic deformation.

【００２８】ナノスケールまでのオーステナイト鋼結晶
粒の超微細化は、加工によるオーステナイト系ステンレ
ス鋼の加工誘起マルテンサイト変態および高温でのオー
ステナイト相への逆変態の性質を応用するのがより効率
的である。従来加工法の圧延法では加工度に上限があ
り、微細な加工誘起マルテンサイトが十分蓄積されな
い。超微細化には粉末冶金法を適用して、極めて強加工
が達成でき、合金化プロセスの併用が可能な機械的グラ
インディングを活用するのがよい。粉末素材の強加工に
は加工粉末の量産が期待できるアトライタあるいは遊星
型ボールミルが適している。加工により初期結晶構造が
面心立方構造のオーステナイト相（γ）である粉末を体
心立方構造のマルテンサイト相（α′）に変態させる
が、逆変態で少なくとも数十ｎｍ粒径の超微細γ相を得
るには粒径が少なくとも１５ｎｍ以下のα′とするのが
よい。The ultra-fine refining of austenitic steel grains down to the nanoscale is more efficient by applying the properties of the work-induced martensitic transformation of austenitic stainless steel by working and the reverse transformation to austenite phase at high temperature. is there. In the rolling method of the conventional processing method, there is an upper limit in the degree of work, and fine work-induced martensite is not sufficiently accumulated. It is preferable to apply powder metallurgy to ultra-fine processing, and to use mechanical grinding, which can achieve extremely strong working and can use an alloying process together. An attritor or a planetary ball mill, which can be expected to mass-produce the processing powder, is suitable for the strong processing of the powder material. The powder is transformed into a martensitic phase (α ′) having a body-centered cubic structure by processing, and the powder is transformed into a martensitic phase (α ′) having a body-centered cubic structure. In order to obtain a phase, it is preferable that the particle size is α 'of at least 15 nm or less.

【００２９】加工粉末の固形化は現状技術では大型部材
が得やすいＨＩＰあるいは熱間押し出し法が好適であ
る。固形化温度は要求される最終結晶粒径に依存する
が、加工粉末の焼結が可能な温度域以上、すなわち７０
０℃以上が望ましく、特にナノスケール粒径を求める場
合は再結晶温度９００℃以下の条件を付した方がよい。
再結晶温度以上では原子拡散はより活発で、粒径の成長
が生じる。サブミクロンサイズの結晶粒径径を得る時に
は９００℃以上での処理も可能である。加工粉末では、
加工により導入される多量の格子欠陥（点欠陥）の働き
で原子拡散がより低温でも活発である。またこの下限近
くの温度での固形化熱処理で固化物中に未焼結部分が存
在する場合には、その後の下限温度以上の熱間加工でそ
れらを消滅させることが可能である。いずれにしても要
求される最終の結晶粒径に調整および均質な組織とする
ためには、さらに７００℃〜１０５０℃間で圧延等の熱
間加工を実施することが望ましい。棒，板，帯及び管形
状等の種々の形状の部材を製造する場合には、最終粒径
調整工程で加工することが望ましい。In the state of the art, the solidification of the processing powder is preferably carried out by HIP or hot extrusion, in which a large member can be easily obtained. Although the solidification temperature depends on the required final crystal grain size, it is higher than the temperature range in which the processed powder can be sintered, that is, 70 ° C.
0 ° C. or higher is desirable, and in particular, when a nano-scale particle size is determined, it is better to apply a condition of a recrystallization temperature of 900 ° C. or lower.
Above the recrystallization temperature, atomic diffusion is more active and grain size growth occurs. In order to obtain a submicron size crystal grain size, treatment at 900 ° C. or more is also possible. In the processing powder,
Atomic diffusion is active even at lower temperatures due to a large amount of lattice defects (point defects) introduced by processing. Further, when unsintered portions are present in the solidified product by the solidification heat treatment at a temperature near the lower limit, it is possible to eliminate them by hot working at a temperature equal to or higher than the lower limit temperature. In any case, in order to adjust to the required final crystal grain size and obtain a homogeneous structure, it is desirable to further perform hot working such as rolling at 700 ° C to 1050 ° C. When members having various shapes such as rods, plates, strips, and tubes are manufactured, it is desirable to process them in the final particle size adjusting step.

【００３０】本Ｃｒ−Ｍｎ系オーステナイト鋼に関して
は、耐食性，強度，耐照射性等の要求を満たす条件に依
存し、望ましい結晶の平均粒径は、１０ｎｍから１００
ｎｍの範囲にあることであり、特に微細結晶オーステナ
イト鋼の変形挙動によって要求される結晶粒径は三つの
領域に分類される。金属，合金におけるナノスケールま
での結晶粒径と耐力の関係は一般的な傾向として図１に
示されるように耐力のピーク点に対応する粒径Ａを持
つ。粒径の減少と共に耐力が減少し、転位による変形が
起き難い（伸びが小さい）領域、すなわち１０ｎｍから
最大耐力値を示すＡまでの領域Ｉとしたホール・ペッチ
則に従って耐力が増加し、結晶粒内での転位のすべり運
動により変形が進行して比較的塑性伸びを有する粒径領
域、すなわちＡから５００ｎｍまでの領域II及び５００
ｎｍから１０００ｎｍまでの領域III とに分けられる。
領域Ｉの下限１０ｎｍの設定は、最終γ相粒径を得るた
めのα′の微細化が最大に見積っても５ｎｍから１０ｎ
ｍの範囲にとどまることによる。また上限の１０００ｎ
ｍは現状の超微細化技術動向の下限と思われるからであ
る。またこの領域は高温での粒界すべりによる超塑性効
果を持ち、高温での加工性を向上させる利点を有してい
る。領域IIが強度的に最も好適な領域であり、使用強度
の要求が最も望まれる部材に好適である。領域III は靭
性を期待する部材に好適である。With respect to the present Cr-Mn austenitic steel, the average grain size of the desired crystal is preferably from 10 nm to 100 mm, depending on the conditions satisfying requirements such as corrosion resistance, strength and irradiation resistance.
In particular, the crystal grain size required by the deformation behavior of the microcrystalline austenitic steel is classified into three regions. As a general tendency, the relationship between the crystal grain size up to the nanoscale and the proof stress of metals and alloys has a grain size A corresponding to the peak point of the proof stress as shown in FIG. The yield strength decreases as the grain size decreases, and the yield strength increases according to the Hall-Petch rule, which is a region where deformation due to dislocation hardly occurs (small elongation), that is, a region I from 10 nm to A showing the maximum yield value. The deformation proceeds due to the sliding motion of dislocations within the grains, and the grain size region has relatively plastic elongation, that is, regions II and 500 from A to 500 nm.
and a region III from nm to 1000 nm.
The setting of the lower limit of 10 nm of the region I is from 5 nm to 10 n even if the miniaturization of α ′ for obtaining the final γ phase particle size is estimated at the maximum.
By staying in the range of m. The upper limit of 1000n
This is because m is considered to be the lower limit of the current trend of ultrafine technology. In addition, this region has a superplastic effect due to grain boundary sliding at a high temperature, and has an advantage of improving workability at a high temperature. The region II is the most preferable region in terms of strength, and is suitable for a member in which the demand for use strength is most desired. Region III is suitable for a member expecting toughness.

【００３１】上記の範囲のＣｒ−Ｍｎ系オーステナイト
鋼の耐食性は耐食性の化学組成を有する理由以外にも結
晶をより均質化及び微細化することにより達成できる。
機械的グラインディングは、溶融凝固で製造された鋼に
比して、非平衡固溶体の加工粉末の製造と低温での固形
化により腐食に関与する粒内での溶質原子の偏析，析出
が少ない組織とすることができる。これは、溶融過程を
経ないことによる。また腐食性の不純物は結晶粒の微細
化により多数ある格子間隔の拡張した粒界に原子レベル
で保有され、より析出し難い。さらに粒径の微細化は孔
食の形成および数に影響を与え、耐食性を向上させる。The corrosion resistance of the Cr-Mn austenitic steel in the above range can be achieved by making the crystal more homogenous and finer besides having a chemical composition of corrosion resistance.
Mechanical grinding is a microstructure in which less solute atoms segregate and precipitate in grains involved in corrosion due to the production of non-equilibrium solid solution processing powder and solidification at low temperatures compared to steel produced by melt solidification. It can be. This is because it does not go through a melting process. In addition, corrosive impurities are retained at the atomic level in a large number of grain boundaries with an extended lattice spacing due to the refinement of crystal grains, and are more difficult to precipitate. Furthermore, the refinement of the particle size affects the formation and number of pits and improves corrosion resistance.

【００３２】中性子照射による材料損傷に関しては、数
十ｎｍ程度の通常粒径のオーステナイト系ステレンス鋼
で発生する照射誘起拡散に伴う偏析や塑性変形を阻害す
る照射欠陥の蓄積が、結晶粒径を限りなく微小化するこ
とにより改善される。結晶粒の微細化はバルク体積率で
格子間隔の拡張した粒界の占有率を高め、偏析発生を抑
制することができる。また粒径が照射欠陥のサイズによ
り近くなることで、欠陥と粒界との相互作用が大きくな
り粒界での欠陥の消滅頻度が高まることで粒内の塑性変
形を阻害する欠陥量を低減することができる。Regarding material damage due to neutron irradiation, segregation accompanying irradiation-induced diffusion generated in austenitic stainless steel having a normal grain size of about several tens of nanometers and accumulation of irradiation defects that inhibit plastic deformation limit the crystal grain size. It can be improved by miniaturization. The refinement of the crystal grains can increase the occupancy of the grain boundaries having an extended lattice spacing by the bulk volume ratio, and can suppress the occurrence of segregation. Also, as the grain size becomes closer to the size of the irradiation defect, the interaction between the defect and the grain boundary increases, and the frequency of defect disappearance at the grain boundary increases, thereby reducing the amount of defects that inhibit plastic deformation in the grain. be able to.

【００３３】以上のように、材料の結晶粒径を微細化し
て結晶粒界を多数導入することで、強度が増し、また、
耐食，耐応力腐食割れ性を向上させ、さらに、耐放射線
照射損傷性が向上する。本発明は強度を上昇させるとと
もに、割れを防止し、耐腐食性，耐照射損傷性を向上さ
せたＣｒ−Ｍｎ系オーステナイト鋼を提供するにある。As described above, the strength is increased by reducing the crystal grain size of the material and introducing a large number of crystal grain boundaries.
Corrosion resistance and stress corrosion cracking resistance are improved, and radiation damage resistance is also improved. An object of the present invention is to provide a Cr-Mn-based austenitic steel that has increased strength, prevented cracking, and has improved corrosion resistance and irradiation damage resistance.

【００３４】Ｎｉはオーステナイト相を安定にし耐食性
を高めるために７％以上含有させる。高Ｎｉ量は耐食性
を向上させるが、他の部材と同一腐食環境下で使用する
場合には接触部で電気化学反応を生じ、他の部材の腐食
を促進させるので、上限は２３％が好ましく、より１８
％が好ましい。Ni is contained in an amount of 7% or more to stabilize the austenite phase and enhance corrosion resistance. The high Ni content improves the corrosion resistance, but when used in the same corrosive environment as other members, an electrochemical reaction occurs at the contact portion and the corrosion of the other members is promoted, so the upper limit is preferably 23%, Than 18
% Is preferred.

【００３５】Ｍｎは素材粉末鋼の製造の際、脱酸材さら
に脱硫材として添加されている。またＭｎはオーステナ
イト生成元素であり、Ｎｉと置換することが可能であ
る。高Ｍｎ量はσ相を生成させるためＭｎは２％を越え
１５％以下とする。Mn is added as a deoxidizer and a desulfurizer during the production of the raw material powder steel. Mn is an austenite generating element and can be replaced with Ni. A high Mn content causes the σ phase to be generated, so that Mn is more than 2% and 15% or less.

【００３６】耐食性を高めるのにＭｎとＮｉの複合添加
は９％以上が必要である。ＭｎとＮｉ複合添加の上限は
Ｎｉ単独添加にならい２５％が好ましい。In order to enhance the corrosion resistance, the combined addition of Mn and Ni requires 9% or more. The upper limit of the addition of Mn and Ni is preferably 25%, as in the case of adding Ni alone.

【００３７】Ｎはオーステナイト生成元素である。Ｍｎ
１０％を越え、Ｃｒ１５％以上の高Ｍｎ高Ｃｒ鋼になる
とσ相が生成しやすいため、Ｎ添加がσ相の抑制に有効
である。高Ｎ量は製造コストがかかるため０.５％ 以下
が望ましい。低Ｍｎ低Ｃｒの鋼では添加しなくともよ
い。N is an austenite forming element. Mn
When the content exceeds 10% and the Cr content is high and the Cr content is higher than 15%, a σ phase is likely to be generated. Therefore, the addition of N is effective in suppressing the σ phase. Since a high N content requires a manufacturing cost, it is desirable to use 0.5% or less. It is not necessary to add it to low Mn and low Cr steel.

【００３８】Ｃｒは耐食性を向上させるために１４％以
上が必要である。しかし、２０％を越えるとオーステナ
イト相を不安定化し、またσ相を生成させ脆化させるた
め１４〜２０％が好ましい。Cr is required to be 14% or more in order to improve corrosion resistance. However, if it exceeds 20%, the austenite phase is destabilized, and the σ phase is formed and embrittled, so that 14 to 20% is preferable.

【００３９】Ｓｉは素材粉末鋼の製造の際、脱酸剤とし
て添加されている。市販SUS304，SUS316等のＪＩＳ規格
に準じてＳｉは１％以下、特に、０.２〜０.５％が好ま
しい。Si is added as a deoxidizing agent in the production of powdered steel. According to JIS standards such as commercially available SUS304 and SUS316, the content of Si is preferably 1% or less, particularly preferably 0.2 to 0.5%.

【００４０】Ｐ，Ｓは素材粉末の製造時に含有され、耐
食性に悪い効果を有している。市販SUS304，SUS316等の
ＪＩＳ規格に準じてＰは０.０４５％以下、Ｓは０.０３
％以下が好ましい。P and S are contained during the production of the raw material powder and have an effect on the corrosion resistance. According to JIS standards such as commercially available SUS304 and SUS316, P is 0.045% or less and S is 0.03%.
% Or less is preferable.

【００４１】Ｍｏは耐食性及び固溶強化型添加元素であ
る。しかし３％を越えて添加するとσ相を生成させ、材
料の脆化を引き起こすので、良好な耐食性及び強度を付
与するには３％以下、２〜３％の添加が好ましい。Mo is an additive element of the corrosion resistance and solid solution strengthening type. However, if added in excess of 3%, a σ phase is formed, causing embrittlement of the material. Therefore, in order to impart good corrosion resistance and strength, addition of 3% or less, preferably 2-3%.

【００４２】Ｃは材料が溶接継ぎ手として使用される場
合は熱影響部の耐食性からできるだけ低減させることが
好ましく、利用できる素材粉末中のＣ量に依存する。し
かし非溶接部材として利用する場合には材料の強化，粒
界の強化に高めに添加するほうがよい。上限で０.１％
が好適である。これ以上では炭化物の析出が起こりやす
くなり、本来のオーステナイト鋼の特性が失われる。C is preferably reduced as much as possible from the corrosion resistance of the heat-affected zone when the material is used as a welding joint, and depends on the amount of C in the available material powder. However, when it is used as a non-welded member, it is better to add a higher amount to strengthen the material and strengthen the grain boundaries. 0.1% at upper limit
Is preferred. Above this, carbide precipitation is likely to occur, and the original properties of the austenitic steel are lost.

【００４３】Ｔｉ，Ｚｒ，Ｎｂは、炭化物及び酸化物形
成元素であり、また固溶状態ではオーバーサイズ原子で
あるためそれらの添加により照射によって導入される原
子空孔を固着して耐照射性を向上させる。０.１％ 以上
の高炭素組成では、これらの元素の添加はそれらの元素
を含む多量の炭化物を生成して材料を脆くするため、有
効でない。一般に素材粉末は０.２％ 近くの酸素を含有
しており、また含有Ｃ量も考慮してＯ，Ｃを固定化する
ためにはＴｉ，Ｚｒ，Ｎｂの添加は、単独添加では、そ
れぞれ１.０，２.０，１.０％、また複合添加では最大
１.５％までが好適である。添加元素の余剰分は固溶し
て効果を発揮する。Ti, Zr, and Nb are carbide and oxide forming elements, and are oversized atoms in a solid solution state, so that their addition fixes atomic vacancies introduced by irradiation to improve irradiation resistance. Improve. At a high carbon composition of 0.1% or more, the addition of these elements is not effective because it generates a large amount of carbide containing these elements and makes the material brittle. Generally, the raw material powder contains about 0.2% of oxygen. In addition, in order to fix O and C in consideration of the content of C, addition of Ti, Zr, and Nb is one in each case. 0.0, 2.0, and 1.0%, and up to 1.5% in a combined addition is preferable. The surplus of the added element is dissolved to exhibit an effect.

【００４４】以上のように、材料の結晶粒微を微細化し
て結晶粒界を多数導入することで、強度が増し、また、
耐食，耐応力腐食割れ性を向上させ、さらに、耐放射線
照射損傷性が向上する。As described above, the strength is increased by refining the crystal grains of the material and introducing a large number of crystal grain boundaries.
Corrosion resistance and stress corrosion cracking resistance are improved, and radiation damage resistance is also improved.

【００４５】本発明の鋼は、一般的に粒界が材料劣化の
主因となり得る環境化で使用される強度部材に適用され
得る。また、原子炉炉心だけでなく、水冷却環境や水素
が存在する環境で使用され、放射線照射損傷を受ける構
造部材に適用され得る。The steel of the present invention can be generally applied to a strength member used in an environment where grain boundaries can be a major cause of material deterioration. Further, it can be used not only in a reactor core but also in a water cooling environment or an environment where hydrogen exists, and can be applied to structural members that are damaged by radiation irradiation.

【００４６】[0046]

【発明の実施の形態】BEST MODE FOR CARRYING OUT THE INVENTION

（実施例１）本発明の結晶粒超微細化オーステナイト鋼
の作製方法の実施例を説明する。本実施例では機械的合
金化処理に図２のアトライタを使用した。この装置の構
成は、容積２５リットルのステンレス製粉砕タンク１，
タンク１の冷却水入口２，冷却水出口３，アルゴンまた
は窒素ガスの置換ガスをシールするガスシール４，重量
５kgの混合粉末５，粉砕タンク内の直径１０mmの鋼製ボ
ール６，アジテータアーム７からなる。外部駆動系から
回転がアーム軸８に伝えられ、アジテータアーム７が回
転運動する。アジテータアーム７によってボール６が撹
拌され、ボール６間同士、ボール６とタンク１の内壁間
で衝突が生じ、混合粉末５が強加工され微細結晶粒を有
する合金粉末が得られた。アーム軸８の回転速度は１７
０rpm で行った。本発明に係る各種結晶粒超微細化オー
ステナイト鋼の主要化学成分（重量％）が表１中Ｎo.１
−８に示される。(Example 1) An example of a method for producing an ultra-fine grained austenitic steel of the present invention will be described. In this embodiment, the attritor of FIG. 2 was used for the mechanical alloying process. The configuration of this device is a stainless steel grinding tank 1 having a capacity of 25 liters,
From the cooling water inlet 2 of the tank 1, the cooling water outlet 3, a gas seal for sealing a replacement gas of argon or nitrogen gas 4, a mixed powder having a weight of 5 kg 5, a steel ball 10 mm in diameter in a grinding tank 6, and an agitator arm 7. Become. The rotation is transmitted to the arm shaft 8 from the external drive system, and the agitator arm 7 rotates. The balls 6 were agitated by the agitator arm 7, and collisions occurred between the balls 6, and between the balls 6 and the inner wall of the tank 1, and the mixed powder 5 was strongly processed to obtain an alloy powder having fine crystal grains. The rotation speed of the arm shaft 8 is 17
Performed at 0 rpm. The main chemical components (% by weight) of the various ultra-fine grained austenitic steels according to the present invention are No. 1 in Table 1.
-8.

【００４７】[0047]

【表１】 [Table 1]

【００４８】Ｎo.４，６は容器内を窒素ガスで置換して
行った。代表例として本発明のＮｏ．５の鋼種について
図３，図４及び図５にミリング時間とＸ線回折法により
測定した回折ピーク，平均結晶粒径及び相変化の関係を
それぞれ示した。平均結晶粒径は１００ｎｍ以下につい
てはＸ線回折法を用い、１００ｎｍ以上については電子
顕微鏡を用いて測定した。ミリング時間が３０時間以上
で平均結晶粒径はほぼ８ｎｍで飽和してγ→α′変態が
完了しており、６０時間ミリングした該粉末を熱間等方
加圧処理（ＨＩＰ）〔条件１：８５０℃×０.５時間，
２０００kgｆ／cm〕によりバルク材とした。表２に、Ｈ
ＩＰ処理条件をまとめた。In Nos. 4 and 6, the inside of the container was replaced with nitrogen gas. As a typical example, No. 1 3, 4 and 5 show the relationship between the milling time, the diffraction peak measured by the X-ray diffraction method, the average crystal grain size and the phase change, respectively. The average crystal grain size was measured by using an X-ray diffraction method for a size of 100 nm or less, and measured by using an electron microscope for a size of 100 nm or more. The milling time is 30 hours or more, the average crystal grain size is saturated at about 8 nm, and the γ → α ′ transformation is completed. The powder milled for 60 hours is subjected to hot isostatic pressing (HIP) [condition 1: 850 ° C. × 0.5 hours,
2000 kgf / cm]. Table 2 shows that
The IP processing conditions are summarized.

【００４９】[0049]

【表２】 [Table 2]

【００５０】（実施例２）本発明の結晶粒超微細化オー
ステナイト鋼の作製方法の実施例を説明する。本実施例
では機械的合金化処理に図６の遊星型ボールミル装置を
使用した。この装置の構成は、真空引き弁９と、Ａｒガ
スまたは窒素ガスの置換弁１０及び温度計測用の***１
１を具備するステンレス製の蓋１２，容積５００ccのス
テンレス容器１３，重量３００ｇの混合粉末１４，容器
１３内の直径１０mmの鋼製ボール１５からなる。外部駆
動系から回転が回転盤１６に伝えられ、その上に十文字
に配置された４基の容器１３には遠心力が生じると共に
各容器１３自身の回転も起こり、ボール１５は容器１３
の内壁に沿って回転運動し、ボール１５間同士、ボール
１５と容器１３の内壁間で衝突が生じ、混合粉末１４が
強加工され微細結晶粒を有する合金粉末が得られた。回
転盤の回転速度は１５０rpm で行った。本発明に係る各
種結晶粒超微細化オーステナイト鋼の主要化学成分が表
１中Ｎo.１−２４に示される。Ｎo.９，１１，１７は容
器内を窒素ガスで置換して行った。微細結晶粒を有する
合金粉末を熱間等方加圧処理（ＨＩＰ）〔条件１：８５
０℃×０.５時間，２０００kgｆ／cm2〕によりバルク材
とした。(Example 2) An example of a method for producing an ultra-fine grained austenitic steel according to the present invention will be described. In this embodiment, the planetary ball mill shown in FIG. 6 was used for mechanical alloying. This device is composed of a vacuum evacuation valve 9, an Ar gas or nitrogen gas replacement valve 10, and a small hole 1 for temperature measurement.
The container 13 comprises a stainless steel lid 12, a stainless steel container 13 having a capacity of 500 cc, a mixed powder 14 weighing 300 g, and a steel ball 15 having a diameter of 10 mm in the container 13. The rotation is transmitted from the external drive system to the turntable 16, and a centrifugal force is generated in the four containers 13 arranged in a cross shape thereon, and each container 13 itself rotates.
, A collision occurred between the balls 15 and between the balls 15 and the inner wall of the container 13, and the mixed powder 14 was strongly processed to obtain an alloy powder having fine crystal grains. The rotation speed of the turntable was 150 rpm. The main chemical components of various grain ultra-fine austenitic steels according to the present invention are shown in Table 1 as No. 1-24. Nos. 9, 11, and 17 were performed by replacing the inside of the container with nitrogen gas. Hot isostatic pressing (HIP) of alloy powder having fine crystal grains [Condition 1:85
At 0 ° C. × 0.5 hours, 2000 kgf / cm 2 ], a bulk material was obtained.

【００５１】（実施例３）表１に示した組成の結晶粒超
微細化オーステナイト鋼のＨＩＰ処理したバルク材料
を、９００℃，９５０℃，１０００℃，１０５０℃の温
度でそれぞれ０.５時間真空焼鈍した。また、１０５０
℃で、０.２５，０.５，１.０，２.０,５.０，１０.０
時間真空焼鈍し、これらの試料に室温で引張試験（歪み
速度：〜10-4／ｓ）を行った。Ｃ濃度の高い鋼及びＴ
ｉ，Ｚｒ，Ｎｂを添加した鋼では、Ｃ濃度の低い鋼及び
Ｔｉ，Ｚｒ，Ｎｂを添加した鋼に比して結晶粒の成長が
遅れ、Ｃ，Ｔｉ，Ｚｒ，Ｎｂには結晶粒成長抑制効果が
あった。代表例として本発明のＮo.５の鋼種について図
７に焼鈍時間３０分の場合の焼鈍温度と平均結晶粒径、
図８に焼鈍温度１０５０℃の場合の焼鈍時間と平均結晶
粒径、図９に平均結晶粒径と耐力の関係を従来材の実用
３１６Ｌ鋼と共にそれぞれ示し、表３には平均結晶粒径
と耐力及び伸びの関係を示した。Example 3 A HIP-treated bulk material of ultra-fine grained austenitic steel having the composition shown in Table 1 was vacuumed at 900 ° C., 950 ° C., 1000 ° C., and 1050 ° C. for 0.5 hour each. Annealed. Also, 1050
0.25, 0.5, 1.0, 2.0, 5.0, 10.0 at ° C.
After vacuum annealing for hours, these samples were subjected to a tensile test (strain rate: 1010 −4 / s) at room temperature. Steel with high C concentration and T
In the steel to which i, Zr, and Nb are added, the growth of crystal grains is delayed as compared with the steel having a low C concentration and the steel to which Ti, Zr, and Nb are added, and the growth of crystal grains is suppressed in C, Ti, Zr, and Nb. There was an effect. As a typical example, FIG. 7 shows the annealing temperature and the average crystal grain size when the annealing time is 30 minutes for the steel type No. 5 of the present invention.
FIG. 8 shows the relationship between the annealing time and the average grain size at an annealing temperature of 1050 ° C., and FIG. 9 shows the relationship between the average grain size and the proof stress together with the conventional 316L steel, and Table 3 shows the average grain size and the proof stress. And the relationship between elongation.

【００５２】[0052]

【表３】 [Table 3]

【００５３】また表４に本発明のＮo.５，Ｎo.７、及び
Ｎo.１７の鋼種について、１０５０℃で、０.５ 時間真
空焼鈍した時の平均結晶粒径，耐力及び伸びをまとめ
た。Table 4 summarizes the average grain size, yield strength, and elongation of the No. 5, No. 7, and No. 17 steels of the present invention after vacuum annealing at 1050 ° C. for 0.5 hour. .

【００５４】[0054]

【表４】 [Table 4]

【００５５】平均結晶粒径は１００ｎｍ以下については
Ｘ線回折法を用い、１００ｎｍ以上については電子顕微
鏡を用いて測定した。表１に示した組成の機械的合金化
処理粉末に実施例１及び２よりも高い温度でＨＩＰ処理
〔条件２：９００℃／０.５時間，２０００kgｆ／cm2，
条件３：９５０℃／０.５時間,２０００kgｆ／cm2〕し
た。条件２では実施例１及び２よりも平均結晶粒径は大
きくなり、条件３ではサブミクロンサイズの平均結晶粒
径が得られた。代表的な例として本発明のＮo.５の鋼種
について表５にそれぞれの条件で得られた結晶粒径をま
とめた。The average crystal grain size was measured by using an X-ray diffraction method when the average crystal grain size was 100 nm or less, and by using an electron microscope when the average crystal grain size was 100 nm or more. HIP treatment was performed on the mechanically alloyed powder having the composition shown in Table 1 at a higher temperature than in Examples 1 and 2 [condition 2: 900 ° C./0.5 hours, 2000 kgf / cm 2 ,
Condition 3: 950 ° C./0.5 hour, 2000 kgf / cm 2 ]. Under condition 2, the average crystal grain size was larger than in Examples 1 and 2, and under condition 3, a submicron average crystal grain size was obtained. As a typical example, Table 5 summarizes the crystal grain sizes obtained under the respective conditions for the steel type No. 5 of the present invention.

【００５６】[0056]

【表５】 [Table 5]

【００５７】本実施例と実施例１及び２で固化したバル
ク材料に、７００℃〜１０５０℃の温度範囲で５％〜４
０％の圧下率まで熱間圧延を行い急冷し、その後室温で
引張試験（歪み速度：〜１０-4／ｓ）した。ＨＩＰ処理
による固化成形後に真空焼鈍した材料よりも耐力，伸び
が向上した。代表的な例として本発明のＮo.５の鋼種に
ついて７００℃で２０％の圧下率まで熱間圧延した試料
の応力−歪曲線を図１０に示し、表６に７００℃で熱間
圧延したときに得られた平均結晶粒径を示した。The bulk material solidified in the present example and Examples 1 and 2 was added with a temperature of 5% to 4% in a temperature range of 700 ° C. to 1050 ° C.
The steel sheet was hot-rolled to a rolling reduction of 0%, rapidly cooled, and then subjected to a tensile test (strain rate: -10 -4 / s) at room temperature. The yield strength and elongation were improved as compared with the material annealed in vacuum after solidification molding by HIP processing. As a typical example, FIG. 10 shows a stress-strain curve of a sample hot-rolled at 700 ° C. to a rolling reduction of 20% for the steel type No. 5 of the present invention. The obtained average crystal grain size is shown in FIG.

【００５８】[0058]

【表６】 [Table 6]

【００５９】（実施例４）表１に示した組成の結晶粒超
微細化オーステナイト鋼のＨＩＰ処理したバルク材料に
応力腐食割れ試験としてＣＢＢ試験を行った。図１１は
ＣＢＢ試験方法を示す斜視図である。試験片１７に隙間
をつけるためのグラファイトファイバーウール１８と共
にホルダ１９の間に挟み、ボルト穴２０にボルトを挿入
し、ホルダ１９間にアールをつけて締め付け、オートク
レーブ中で応力腐食割れ試験に供した。試験条件は２８
８℃，８５kg／cm2 の高温高圧純水（溶存酸素量８ppm
）中で５００時間浸漬した。その後試験片を取り出
し、光学顕微鏡による試験片の断面観察から割れ発生の
有無を調べた。全ての試料で割れは認められなかった。Example 4 A CBB test was performed as a stress corrosion cracking test on a HIP-treated bulk material of an ultrafine grained austenitic steel having the composition shown in Table 1. FIG. 11 is a perspective view showing the CBB test method. The test piece 17 was sandwiched between a holder 19 together with a graphite fiber wool 18 for providing a gap, a bolt was inserted into a bolt hole 20, a radius was fastened between the holders 19, and subjected to a stress corrosion cracking test in an autoclave. . Test conditions are 28
8 ℃, 85kg / cm 2 high temperature and high pressure pure water (dissolved oxygen content 8ppm
) For 500 hours. Thereafter, the test piece was taken out, and the presence or absence of cracks was examined by observing the cross section of the test piece using an optical microscope. No cracks were observed in any of the samples.

【００６０】（実施例５）実施例１で作製した本発明の
Ｎo.５の結晶粒超微細化オーステナイト鋼を800℃で熱
間鍛造し、一般産業用構造部材として直径２０mm，長さ
３００mmの棒及び幅５０mm，長さ２００，厚さ５mmの板
を製造した。また、実施例１で作製した本発明のＮo.
２，Ｎo.５及びＮo.１７の結晶粒超微細化オーステナイ
ト鋼を８００℃で熱間鍛造し、図１２に示す沸騰水型原
子炉炉心用の各種構造部材を製造した。本原子炉は蒸気
温度２８６℃，蒸気圧力７０.７atgで運転され、発電出
力として５００，８００，１１００ＭＷの発電が可能で
ある。各名称は次の通りである。中性子線パイプ５１，
炉心支持板５２，中性子計装検出管５３，制御棒５４，
炉心シュラウド５５，上部格子板５６，燃料集合体５
７，上鏡スプレイノズル５８，ベントノズル５９，圧力
容器蓋６０，フランジ６１，計測用ノズル６２，気水分
離器６３，シュラウドヘッド６４，給水入口ノズル６
５，ジェットポンプ６６，蒸気乾燥機６８，蒸気出口ノ
ズル６９，給水スパージャ７０，炉心スプレイ用ノズル
７１，下部炉心格子７２，再循環水入口ノズル７３，バ
ッフル板７４，制御棒案内管７５。(Example 5) The ultra-fine grained austenitic steel of No. 5 of the present invention prepared in Example 1 was hot forged at 800 ° C to obtain a general industrial structural member having a diameter of 20 mm and a length of 300 mm. Rods and plates 50 mm wide, 200 long and 5 mm thick were produced. Further, the No. of the present invention prepared in Example 1 was used.
Ultra-fine grained austenitic steels of No. 2, No. 5 and No. 17 were hot forged at 800 ° C. to produce various structural members for a boiling water reactor core shown in FIG. This reactor is operated at a steam temperature of 286 ° C. and a steam pressure of 70.7 atg, and can generate power of 500, 800, and 1100 MW as a power generation output. Each name is as follows. Neutron pipe 51,
Core support plate 52, neutron instrumentation detection tube 53, control rod 54,
Core shroud 55, upper grid plate 56, fuel assembly 5
7, upper mirror spray nozzle 58, vent nozzle 59, pressure vessel lid 60, flange 61, measuring nozzle 62, steam separator 63, shroud head 64, water supply inlet nozzle 6
5, jet pump 66, steam dryer 68, steam outlet nozzle 69, water supply sparger 70, core spray nozzle 71, lower core grid 72, recirculated water inlet nozzle 73, baffle plate 74, control rod guide tube 75.

【００６１】前述の上部格子板５６はリム胴２１，フラ
ンジ２２及びグリットプレート３５を有し、これらには
SUS316鋼多結晶の圧延材が用いられる。グリットプレー
ト３５は互いに交叉しているだけで互いに固定はされて
いない。また、炉心支持板５２は同じくSUS316鋼多結晶
圧延材が用いられ、一枚の圧延板により製造され、燃料
支持金具を取り付ける穴が設けられ、円周面で炉容器に
固定される。従っていずれも中性子照射を受ける中心部
では熔接部がない構造である。The above-mentioned upper lattice plate 56 has the rim cylinder 21, the flange 22, and the grit plate 35,
A rolled material of SUS316 steel polycrystal is used. The grit plates 35 cross each other but are not fixed to each other. The core support plate 52 is also made of SUS316 steel polycrystalline rolled material, is manufactured from a single rolled plate, is provided with a hole for mounting a fuel support bracket, and is fixed to the furnace vessel on the circumferential surface. Therefore, all of the structures have no welded portion in the central portion receiving neutron irradiation.

【００６２】図１３は上部格子板の一部平面図である。
図１４は図１３のVII−VII切断の断面図及び図１５は図
１６のXIII部分を拡大した断面図である。前述の本発明
の合金を図１５のボルト２３に適用したものである。本
発明のボルト２３はリム胴２１と上部フランジ２２を固
定するもので、丸棒の材料より切削加工によってネジを
製造したものである。FIG. 13 is a partial plan view of the upper lattice plate.
14 is a sectional view taken along the line VII-VII of FIG. 13, and FIG. 15 is an enlarged sectional view of a portion XIII in FIG. The above-mentioned alloy of the present invention is applied to the bolt 23 of FIG. The bolt 23 of the present invention fixes the rim body 21 and the upper flange 22, and is a screw manufactured by cutting a round bar material.

【００６３】図１６は上部格子板の部分拡大図、図１７
は図１６Ｘの部分拡大図及び図１８は図１７IXの部分拡
大図である。上部格子板５６のグリットプレート３１と
サポートプレート３２を締め付け固定するボルト及びナ
ット，グリットプレート３１とサポートプレート３２お
よびサポートプレート３２とグリットプレート３５を締
めるボルト３６及びナット３７を上述と同様に本発明の
Ｎo.２，Ｎo.５及びＮo.１７超微細結晶粒オーステナイ
ト鋼で作製した。FIG. 16 is a partially enlarged view of the upper lattice plate, and FIG.
Is a partial enlarged view of FIG. 16X, and FIG. 18 is a partial enlarged view of FIG. 17IX. The bolts and nuts for tightening and fixing the grit plate 31 and the support plate 32 of the upper lattice plate 56, the bolts 36 and the nuts 37 for tightening the grit plate 31, the support plate 32, and the support plate 32 and the grit plate 35 are the same as described above. No. 2, No. 5 and No. 17 were made of ultrafine grained austenitic steel.

【００６４】図１９は炉心支持板５２の断面図であり、
炉心支持板には図２０の燃料支持金具、図２１の周辺燃
料支持金具、図２２の図２１のXV拡大図である。アイボ
ルト４２が設けられ、これらの図２０〜図２２の物品が
前述の本発明の超微細結晶粒オーステナイト鋼によって
作製されたものである。更に、炉心支持板４１に取り付
けられる処心支持板ピン及び図２３のワッシャ４３を同
様に超微細結晶粒オーステナイト鋼で作製した。FIG. 19 is a sectional view of the core support plate 52.
FIG. 22 is a fuel support fitting of FIG. 20, a peripheral fuel support fitting of FIG. 21, and an XV enlarged view of FIG. 21 of FIG. An eyebolt 42 is provided, and these articles shown in FIGS. 20 to 22 are made of the above-described ultrafine-grained austenitic steel of the present invention. Further, the centering support plate pin attached to the core support plate 41 and the washer 43 of FIG. 23 were similarly made of ultrafine grain austenitic steel.

【００６５】さらに図２３は沸騰水型原子炉炉心各種構
造物、たとえば炉心シュラウド５５に発生した応力腐食
割れ等の不具合いを含む部分を機械的に保護するクラン
プ７７，補修用ボルト７８，補修用ナット７９からなる
補修方法を示す。図２４はテーパ無しボルト８０を使用
した場合の補修部断面図、図２５はテーパ付ボルト８１
を使用した場合の補修部の断面図で、テーパ付ボルト８
１はスリット付スリーブ８２を介して炉心シュラウド５
５，クランプ７７を固定する。ボルト，ナットは実施例
１で作製した本発明のＮo.２，Ｎo.５及びＮo.１７の超
微細結晶粒オーステナイト鋼で作製した。Further, FIG. 23 shows a clamp 77, a repair bolt 78, and a repair bolt for mechanically protecting various structures of the boiling water reactor core, for example, a portion including a defect such as stress corrosion cracking generated in the core shroud 55. The repair method including the nut 79 is shown. FIG. 24 is a sectional view of a repaired part when a taperless bolt 80 is used, and FIG.
FIG. 4 is a sectional view of a repaired part when a bolt 8 is used.
1 is a core shroud 5 through a slit sleeve 82.
5. Fix the clamp 77. The bolts and nuts were made of the ultrafine grained austenitic steels of No. 2, No. 5 and No. 17 of the present invention prepared in Example 1.

【００６６】本発明の方法で作製した部材を、沸騰水型
原子炉中で生じる条件を模擬し、更に、中性子照射量で
１×１０22ｎ／cm2(＞１ＭｅＶ）まで中性子照射した。
非照射材と照射材に室温で引張試験（歪み速度：〜１０
-4／ｓ）した。本発明による結晶粒超微細化オーステナ
イト鋼は従来実用材３１６Ｌ鋼に比して、耐力の増加及
び伸びの低下に代表される材料の照射劣化がわずかであ
った。また、本発明材の中でも、Ｔｉ，Ｚｒ，Ｎｂ添加
をした材料が良好な耐照射損傷性を示した。代表的な例
として表７に、本発明の表１中のＮo.２，Ｎo.５及びＮ
o.１７と従来実用材３１６Ｌ鋼について、照射前後の耐
力及び伸びをまとめた。The members produced by the method of the present invention were simulated under the conditions generated in a boiling water reactor, and were further irradiated with neutrons at a neutron irradiation dose of 1 × 10 22 n / cm 2 (> 1 MeV).
Tensile test for non-irradiated material and irradiated material at room temperature (strain rate: -10
−4 / s). In the ultrafine-grained austenitic steel according to the present invention, irradiation deterioration of a material typified by an increase in proof stress and a decrease in elongation was slight as compared with the conventional 316L steel. Further, among the materials of the present invention, the material to which Ti, Zr, and Nb were added exhibited good irradiation damage resistance. Table 7 shows typical examples of No. 2, No. 5 and N in Table 1 of the present invention.
The proof stress and elongation before and after irradiation were summarized for o.17 and the conventional practical material 316L steel.

【００６７】[0067]

【表７】 [Table 7]

【００６８】前述した使用箇所としてその中性子照射量
が１×１０22ｎ／cm2 である高い中性子照射を受ける部
分で、ボルト，ナットの如く高応力を受け、外部からそ
の表面を直接観察できない部材を耐照射損傷性の高い部
材によって構成することが重要である。そして、これら
の部材は周囲の構造物との材質と類似又はほぼ同一の組
成とすることが高温純水中での電位を同等にする点から
も必要である。また本発明の方法で作製した超微細結晶
粒オーステナイト鋼に含まれる多量の結晶粒界は照射欠
陥の消滅場所として働き得ることから、母相中の照射に
よる欠陥の蓄積がより抑えられ、いわゆる照射脆化，照
射下クリープ等の抑制効果も大きい。A part where the neutron irradiation amount is 1 × 10 22 n / cm 2, which is subjected to high stress such as bolts and nuts, and whose surface cannot be directly observed from outside, such as bolts and nuts It is important to form a member with high resistance to irradiation damage. It is necessary that these members have a composition similar or substantially the same as the material of the surrounding structure in order to make the potential in high-temperature pure water equivalent. In addition, since a large amount of grain boundaries contained in the ultrafine grained austenitic steel produced by the method of the present invention can serve as a place where irradiation defects disappear, the accumulation of defects due to irradiation in the parent phase is further suppressed. The effect of suppressing embrittlement and creep under irradiation is also large.

【００６９】本実施例ではボルト，ナットを製造した
が、上部格子板のグリットプレート３５，炉心支持板５
２を同じ材料の超微細結晶粒オーステナイト鋼で使用す
ることも非常に有効である。そして、大型部材を熱間静
水圧によって製造することができるので、図１３〜図２
５の各種炉内構造材全てを部材の種類に応じて組成を選
択して用いることができる。In this embodiment, bolts and nuts are manufactured. However, the grit plate 35 of the upper lattice plate and the core support plate 5
It is also very effective to use No. 2 in ultra-fine grained austenitic steel of the same material. Since large members can be manufactured by hot isostatic pressure, FIGS.
All of the various in-furnace structural materials of No. 5 can be selected and used in accordance with the type of the member.

【００７０】図２６は円形の上部格子板５６の切断面の
断面図及び図２７は円形の炉心支持板５２の切断面の断
面図である。これらの構造物は同じく表１に示すＮo.５
の合金を用い、実施例１に示す製造法による熱間圧延及
び熱処理によって得た板を用いて溶接によって製造した
ものである。FIG. 26 is a sectional view of a cut surface of the circular upper lattice plate 56, and FIG. 27 is a sectional view of a cut surface of the circular core support plate 52. These structures are also shown in Table 1
And manufactured by welding using a plate obtained by hot rolling and heat treatment by the manufacturing method shown in Example 1 using the alloy of Example 1.

【００７１】図２８は中性子計装検出管５３を示す炉心
部断面拡大図である。中性子計装検出管５３は原子炉圧
力容器下鏡に溶接接続されたハウジングに溶接によって
接続される。本実施例では同じく表１に示すＮo.５の合
金を用い、シームレスの中性子計装検出管５３が熱間に
よって製造され、実施例１に記載の最終熱処理が施され
たものである。FIG. 28 is an enlarged cross-sectional view of the core part showing the neutron instrumentation detection tube 53. The neutron instrumentation detection tube 53 is connected by welding to a housing that is welded to the reactor pressure vessel lower mirror. In this embodiment, a seamless neutron instrumentation detection tube 53 is manufactured by hot working using an alloy of No. 5 shown in Table 1 and subjected to the final heat treatment described in Embodiment 1.

【００７２】図２９は制御棒の斜視図であり、本実施例
ではシース及びＢＣチューブに表１に示すＮo.５の合金
を用いた。ＢＣチューブは熱間によって素管を作った
後、ピルガーミルによって冷間圧延と焼鈍とを繰返して
得た。またシースは冷間圧延と焼鈍を繰返し薄板とした
後、溶接によって得た。FIG. 29 is a perspective view of the control rod. In this embodiment, an alloy of No. 5 shown in Table 1 was used for the sheath and the BC tube. The BC tube was obtained by forming a raw tube by hot working, and then repeatedly performing cold rolling and annealing by a Pilger mill. The sheath was obtained by welding after cold rolling and annealing were repeated to form a thin plate.

【００７３】図３０は燃料集合体５７の部分断面図であ
る。燃料集合体５７の主な構成は燃料棒１５１，ウォー
タロッド１５２，チャンネルボックス１５４，上部タイ
プレート１５５，下部タイプレート１５６，スペーサ１
５７及びハンドル１６１からなり、結合するためのボル
ト及びナットが多数使用される。これらの構成部品には
本発明の合金を用いることができる。ハンドル，上部及
び下部タイプレートの構造材は熱間鍛造後に溶体化処理
が施され、チャンネルボックス及びスペーサの薄板は熱
間圧延後に溶体化処理し、冷間圧延と焼鈍を繰返し製造
され、燃料棒の被覆管及びウォータロッドの薄肉管はピ
ルガーミルによって製造される。FIG. 30 is a partial sectional view of the fuel assembly 57. The main structure of the fuel assembly 57 is a fuel rod 151, a water rod 152, a channel box 154, an upper tie plate 155, a lower tie plate 156, and a spacer 1.
57 and a handle 161 and a large number of bolts and nuts for connection are used. The alloy of the present invention can be used for these components. The handle, the upper and lower tie plate structural materials are subjected to solution treatment after hot forging, and the thin sheets of the channel box and spacer are subjected to solution treatment after hot rolling, and are repeatedly manufactured by cold rolling and annealing, and fuel rods are manufactured. And thin tubes of water rods are manufactured by a Pilger mill.

【００７４】図３１は燃料棒の部分断面図であり、被覆
管１６４及び端栓１６７ともに本発明に係る合金が用い
られる。FIG. 31 is a partial cross-sectional view of the fuel rod. The alloy according to the present invention is used for both the cladding tube 164 and the end plug 167.

【００７５】図３２は中性子源パイプの一部断面斜視図
で、本実施例では表１に示すＮo.５の合金を用いて製造
した。本パイプのパイプ部分は熱間にてシームレス管と
し、上部の棒の部分と下部の厚肉部分は熱間鍛造及び熱
処理とも実施例１と同じ製造工程によって得た。接合部
はいずれも電子ビーム溶接によって接合した。FIG. 32 is a perspective view, partially in section, of a neutron source pipe. In this embodiment, the neutron source pipe was manufactured using an alloy of No. 5 shown in Table 1. The pipe portion of this pipe was a hot seamless tube, and the upper rod portion and the lower thick portion were obtained by the same manufacturing process as in Example 1 for both hot forging and heat treatment. All joints were joined by electron beam welding.

【００７６】以上の構成によって得られるＢＷＲ発電プ
ラントの主な仕様は表８に示す通りである。The main specifications of the BWR power plant obtained by the above configuration are as shown in Table 8.

【００７７】[0077]

【表８】 [Table 8]

【００７８】本実施例によれば、本発明に係る合金によ
って構成した各部材はいずれも３０年無交換で使用可能
となり、更に検査によって４０年で無交換で使用できる
見通しが得られた。原子炉温度は２８８℃であり、１２
ケ月運転後で１回当り５０日以内、好ましくは４０日以
内、特に好ましくは３０日での定期点検が繰返し実施さ
れるとともに、稼働率８５％以上、より好ましくは９０
％以上、特に好ましくは９２％，熱効率３５％とする。According to the present embodiment, all the members made of the alloy according to the present invention can be used without replacement for 30 years, and further inspection has shown that they can be used without replacement in 40 years. The reactor temperature was 288 ° C and 12
Periodic inspections are performed repeatedly within 50 days, preferably within 40 days, particularly preferably within 30 days at one time after the operation for a period of months, and the operation rate is 85% or more, more preferably 90% or more.
% Or more, particularly preferably 92% and thermal efficiency of 35%.

【００７９】（実施例６）図３３は新型沸騰水型原子力
発電における原子炉の断面図である。(Embodiment 6) FIG. 33 is a sectional view of a nuclear reactor in a new type boiling water nuclear power generation.

【００８０】原子炉圧力容器は、原子力発電所の中心機
器であり、ＡＢＷＲでは、特にインターナルポンプを取
り付けるノズル部は、原子炉圧力容器内に温度および圧
力変化が生じても、インターナルポンプの回転機能へ影
響を与えば、また電動機部への熱の伝達が少なくなるよ
うな、スリーブ型の最適形状である。The reactor pressure vessel is a central component of a nuclear power plant. In the ABWR, particularly, a nozzle portion to which an internal pump is attached has a function of the internal pump even if temperature and pressure changes occur in the reactor pressure vessel. The sleeve-shaped optimal shape is such that the rotation function is affected and heat transfer to the electric motor part is reduced.

【００８１】また炉内構造物は、インターナルポンプ採
用による流動振動への影響を少なくしている。In the furnace internal structure, the influence of the internal pump on the flow vibration is reduced.

【００８２】炉心流量の計測は、インターナルポンプの
部分運転の状態を考慮して、実験による検証も含めて精
度の確保が図られている。タービンに流れる蒸気流量の
計測は、原子炉圧力容器の主蒸気ノズル部に設けたベン
チュリ構造によって行い、計測精度が十分確保される。The accuracy of the measurement of the core flow rate is ensured in consideration of the partial operation state of the internal pump, including verification by experiments. The flow rate of the steam flowing through the turbine is measured by a venturi structure provided at the main steam nozzle of the reactor pressure vessel, and the measurement accuracy is sufficiently ensured.

【００８３】ＲＰＶ（原子炉圧力容器）は、冷却材の圧
力バウンダリを構成するとともに、炉心および圧力容器
内部構造物を内蔵し保持する機能を持つ。The RPV (reactor pressure vessel) has a function of forming a pressure boundary of a coolant and having a built-in core core and internal structure of the pressure vessel.

【００８４】従来のＲＰＶでは、燃料集合体７６４体，
ジェットポンプおよび内部構造物を収納して内径約６.
４ｍ となっているが、ＡＢＷＲでは燃料集合体が８７
２体に増加したこと、インターナルポンプの炉内取り扱
いスペースを確保し内径を約７.１ｍとした。In the conventional RPV, 764 fuel assemblies,
Approximately 6.
4m, but ABWR has 87 fuel assemblies.
The internal diameter was increased to about 7.1 m by increasing the number of internal pumps to 2, and securing space for handling the internal pump inside the furnace.

【００８５】従来のＲＰＶの内高は約２２ｍであるのに
対し、ＡＢＷＲでは次に示す（ａ）〜（ｄ）の要因によ
って約２１ｍにした。The inner height of the conventional RPV is about 22 m, whereas that of the ABWR is about 21 m due to the following factors (a) to (d).

【００８６】（ａ）高効率気水分離器の採用によって、
スタンドパイプ長さを短くしたこと。 （ｂ）ＦＭＣＲＤの採用により、制御棒落下速度制限器
が不要になったこと。(A) By employing a high-efficiency steam-water separator,
The length of the stand pipe has been shortened. (B) The adoption of FMCRD eliminates the need for a control rod drop speed limiter.

【００８７】（ｃ）上ぶた・主フランジ構造変更による
上ぶた高さを低くしたこと。(C) The height of the upper lid is reduced by changing the upper lid / main flange structure.

【００８８】（ｄ）下鏡の皿型形状の高さを低くしたこ
と。(D) The height of the dish shape of the lower mirror is reduced.

【００８９】下鏡形状はインターナルポンプの採用に伴
い、インターナルポンプの圧力容器下部への据付け必要
スペースを確保すること、および冷却水の循環流路を考
慮して下鏡形状を従来の半球型から皿型にした。また、
インターナルポンプを一体鍛造とし、溶接線数の少ない
設計とした。With the adoption of the internal pump, the lower mirror shape is changed to the conventional hemispheric shape in consideration of securing the space required for installation of the internal pump below the pressure vessel and taking into account the cooling water circulation flow path. From the mold to a dish. Also,
The internal pump is integrally forged and has a design with a small number of welding lines.

【００９０】支持スカートは、インターナルポンプの取
り扱いなどに必要なスペースを確保するとともに、イン
ターナルポンプ用の熱交換器をペデスタル内に設置する
ために胴部を円錐形状とした。The supporting skirt has a conical shape for securing the space necessary for handling the internal pump and for installing the heat exchanger for the internal pump in the pedestal.

【００９１】インターナルポンプの採用に伴い、従来の
プラントの冷却材再循環出口・入口ノズルがなくなるの
で、胴部炉心領域以下に大口径ノズルのないものにし、
大きな冷却材喪失事故を仮定する必要はない。With the adoption of the internal pump, the coolant recirculation outlet / inlet nozzles of the conventional plant are eliminated, so that there is no large diameter nozzle below the trunk core region.
It is not necessary to assume a large coolant loss accident.

【００９２】従来のプラントでは、流量制限器は主蒸気
管上の隔離弁に至る立下り部分に設置されていたが、こ
れを主蒸気ノズルに設置することにより、主蒸気配管破
断事故に対する安全余裕の向上，格納容器スペースの最
適化を図った。In the conventional plant, the flow restrictor is installed at the falling part of the main steam pipe to the isolation valve, but by installing this at the main steam nozzle, the safety margin against the main steam pipe breakage accident is provided. And the space for the containment vessel has been optimized.

【００９３】炉内構造物要目の実施例５のＢＷＲとの比
較を表８に示す。Table 8 shows a comparison with the BWR of the fifth embodiment, which is an essential part of the furnace internals.

【００９４】炉内構造物は、ＲＰＶ内にあって、炉内の
支持と冷却材の流路の形成、および炉心で発生した熱
水，蒸気を気水分離する機能などの主要な役目のほか、
仮想事故下での冷却水の炉心注水路の確保など、その性
格上十分な健全性と信頼性が要求されている。[0094] The furnace internal structure is located in the RPV, and has other main functions such as support in the furnace and formation of a flow path for a coolant, and a function of separating hot water and steam generated in the core into steam and water. ,
Sufficient soundness and reliability are required due to its characteristics, such as securing a cooling water core injection channel under a virtual accident.

【００９５】表９はＡＢＷＲプラント用蒸気タービン・
発電機設備の基本仕様は、５０Ｈｚ用で比較すると、Ｂ
ＷＲプラントに比較しＡＢＷＲプラントでは、原子炉熱
出力１９.２％増に対して電気出力２３.３％増とした高
効率形プラントである。Table 9 shows a steam turbine for an ABWR plant.
The basic specifications of the generator equipment are as follows:
Compared to the WR plant, the ABWR plant is a high-efficiency plant in which the electric power output is increased by 23.3% with respect to the reactor thermal output by 19.2%.

【００９６】[0096]

【表９】 [Table 9]

【００９７】本実施例でも実施例５と同様に各炉内部材
の結合のためのボルト，ナットを実施例１〜４に記載の
平均結晶粒１０〜６００ｎｍを有する焼結鋼を使用する
ことができることは勿論であるが、その他実施例５に記
載の炉心構造物への適用についても前述の実施例と同様
である。In this embodiment, as in the case of the fifth embodiment, the sintered steel having an average crystal grain of 10 to 600 nm as described in the first to fourth embodiments can be used for the bolts and nuts for connecting the members in the furnace. Of course, it is possible to apply the present invention to the core structure described in the fifth embodiment in the same manner as in the above-described embodiment.

【００９８】（実施例７）図３４は加圧水型原子炉（Ｐ
ＷＲ）の炉内構造の斜視図である。Embodiment 7 FIG. 34 shows a pressurized water reactor (P
It is a perspective view of a furnace internal structure of (WR).

【００９９】原子炉関係設備には原子炉，一次冷却回路
およびその補助設備などがあり、図に示すように原子炉
容器とその中に収納される炉，炉内構造物，制御棒クラ
スタおよび駆動装置よりなる。Reactor-related equipment includes a nuclear reactor, a primary cooling circuit and its auxiliary equipment, and as shown in the figure, a reactor vessel and a furnace housed therein, a reactor internal structure, a control rod cluster, and a drive rod. Device.

【０１００】炉心は燃料集合体群が上，下部炉心板およ
びバッフル（シュラウド）で固定された部分で、全体的
にほぼ円柱形をなしている。The core is a portion where the fuel assemblies are fixed by upper and lower core plates and baffles (shrouds), and has a substantially columnar shape as a whole.

【０１０１】原子炉容器の冷却材出入口ノズルおよび低
圧注入ノズルは炉心上部よりさらに上方に取り付けら
れ、炉心は常に冷却材中にあるように考慮されている。The coolant inlet and outlet nozzles and the low-pressure injection nozzle of the reactor vessel are mounted further above the core, and the core is considered to be always in the coolant.

【０１０２】原子炉容器上部のノズルより入る一次冷却
材は炉心バルブ構造物と原子炉容器間の円環部を下方に
流れ、原子炉容器底部で上方に方向を変えて混合板を通
り、一流量分布で炉心下部に入る。燃料要素の核***に
より発生する熱を吸収して高温になった一次冷却材は原
子炉容器上部のノズルより蒸気発生器に送られる。The primary coolant entering from the nozzle at the top of the reactor vessel flows downward through the annular portion between the core valve structure and the reactor vessel, changes its direction upward at the bottom of the reactor vessel, passes through the mixing plate, and Enter the lower part of the core with flow distribution. The primary coolant, which has become high in temperature by absorbing heat generated by the fission of the fuel element, is sent to the steam generator from a nozzle at the top of the reactor vessel.

【０１０３】炉心の有する反応度は次の２方法で制御さ
れる。The reactivity of the core is controlled by the following two methods.

【０１０４】（１）制御棒クラスタによる起動，停止，
負荷変化などに伴う比較的急速な反応度変化の制御。(1) Start, stop, and
Control of relatively rapid reactivity change due to load change.

【０１０５】（２）一次冷却材中に溶解されるほう素濃
度の調整による燃料燃焼に伴う反応度減少の補償，Ｘ
ｅ，Ｓｍの変化に伴う反応度の変化，常温から運転温度
までの温度変化によって起こる反応度の変化など緩慢な
反応度変化の制御。(2) Compensation for the decrease in reactivity due to fuel combustion by adjusting the concentration of boron dissolved in the primary coolant, X
Control of slow reactivity changes, such as changes in reactivity caused by changes in e and Sm, and changes caused by temperature changes from room temperature to operating temperature.

【０１０６】炉心は出力により所定数の燃料集合体を
上，下炉心板とバッフルにより、ほぼ円柱形に形成され
ている。発電出力と燃料集合体数とは３００〜５００Ｍ
Ｗｅでは１２１個，８００ＭＷｅでは１５７〜１７７
個，１１００ＭＷｅでは１９３〜２４９個である。The core is formed in a substantially columnar shape by a predetermined number of fuel assemblies according to the output, an upper core plate, a lower core plate and a baffle. Power generation output and number of fuel assemblies are 300-500M
121 for We, 157 to 177 for 800 MWe
The number is 193 to 249 in 1100 MWe.

【０１０７】炉心重量は下部炉心支持板，炉心バレル，
上部炉心支持板などにより原子炉容器のフランジに支持
されている。また、炉心部の横振動は炉心バレル下端側
面にある数個のキーとそれに対応する位置にある原子炉
容器側キー溝により抑制される。The core weight was calculated using the lower core support plate, core barrel,
It is supported on the flange of the reactor vessel by an upper core support plate and the like. Further, the lateral vibration of the core portion is suppressed by several keys on the lower side surface of the core barrel and the reactor vessel-side key grooves at corresponding positions.

【０１０８】炉心は大体同数の同心円状の燃料集合体を
有する３領域に分けられ、初装荷燃料の場合は濃縮度を
変え、外周部の方に濃縮度の高い燃料集合体を装荷す
る。燃料交換の場合は中心領域の燃料を取り出し、その
外側の二つの領域の燃料を中心方向に移動し、外周に新
燃料を装填する３領域、外→内式３サイクル方式である
が、他、炉心中央部の高燃焼度に達した燃料を取り出し
その位置に外周部の燃料を系し、外周部に新燃料を装荷
する。いわゆる３領域チェッカーボード式３サイクル方
式もある。The reactor core is divided into three regions having approximately the same number of concentric fuel assemblies. In the case of the initially loaded fuel, the enrichment is changed, and a fuel assembly with a high enrichment is loaded on the outer peripheral portion. In the case of refueling, the fuel in the central area is taken out, the fuel in the two areas outside the central area is moved toward the center, and the outer periphery is charged with new fuel. The fuel that has reached the high burnup in the center of the core is taken out, the fuel in the outer periphery is used at that position, and new fuel is loaded in the outer periphery. There is also a so-called three-region checkerboard type three-cycle system.

【０１０９】これらの方式により、炉心の出力分布が平
坦化されて出力密度を高くすることができ、また燃料の
平均燃焼度が高くなり、燃料費を低下させることができ
る。ＰＷＲでは燃料取替期間は燃料により異なるが１年
以上である。According to these methods, the power distribution of the reactor core is flattened and the power density can be increased, and the average burnup of fuel can be increased to reduce the fuel cost. In PWRs, the refueling period is one year or more, depending on the fuel.

【０１１０】なお、燃焼度は次第に上がり、平衡炉心平
均約３３０００ＭＷＤ／ＭＴ（最大燃焼度５００００Ｍ
ＷＤ／ＭＴ）のものがある。The burn-up gradually increased, and the equilibrium core average was about 33,000 MWD / MT (maximum burn-up 50,000 M
WD / MT).

【０１１１】本実施例でも実施例６と同様に炉内構造材
として実施例１〜５に記載の平均結晶粒径１０〜６００
ｎｍの微細結晶粒を有する焼結鋼を用いることができ
る。炉心構造材の部品として、上部炉心支持板，炉心バ
レル，上部炉心板，燃料集合体では実施例５と同様、下
部炉心支持板，下部炉心板，バッフル支持板，炉心バッ
フル，制御棒クラスタ，支持パット，制御棒クラスタ案
内管，制御棒クラスタ駆動軸の他、これを結合するボル
ト，ナット類が特に有効である。Also in this embodiment, as in Embodiment 6, the average crystal grain size of 10 to 600
A sintered steel having fine crystal grains of nm can be used. As the components of the core structural material, the lower core support plate, the lower core plate, the baffle support plate, the core baffle, the control rod cluster, and the support for the upper core support plate, the core barrel, the upper core plate, and the fuel assembly as in the fifth embodiment. In addition to the pad, the control rod cluster guide tube, the control rod cluster drive shaft, and the bolts and nuts connecting them are particularly effective.

【０１１２】本実施例によれば実施例５と同様の運転年
数，稼働率，運転期間，定検期間及び熱効率が得られ
る。According to this embodiment, the same operating years, operation rate, operation period, regular inspection period, and thermal efficiency as those of the fifth embodiment can be obtained.

【０１１３】（実施例８）図３５は、本発明鋼を用いた
トーラス型核融合装置の概要を縦断面図にて示したもの
である。図で、ペース１３１上にプラズマ１３３の加熱
及び制御を行うポロイダル磁場コイル１３４とダイバー
コイル１３５、及びプラズマ１３３を閉じ込めるトロイ
ダル磁場コイル１３６の内側に中空ドーナツ型の真空容
器１３７内に、例えばヘリウムのような冷却剤を供給し
て熱交換するブランケット１３８の内側に、燃料として
重水素若しくは三重水素を入れてプラズマ１３３を生成
するとともに、真空容器１３７の下部１３７ａに遮蔽筒
体１３９に嵌装し、この遮蔽筒体１３９の内側にダイバ
ータコイル１３５に接続され、冷却管ヘッダ１４０に支
持された各ダイバータ１４１にプラズマ１３３より引出
されたプラズマの一部１３３ａ（Ｈｅ等の不純物）を当
て、さらに遮蔽筒体１３９の開口部１３９ａに排気管４
２を介して排気ポンプ１４３を設け、排気管１４２の上
位の真空容器１３７に中性粒子入射装置１４４を設置し
た。(Embodiment 8) FIG. 35 is a longitudinal sectional view showing an outline of a torus-type fusion apparatus using the steel of the present invention. In the figure, a poloidal magnetic field coil 134 and a diver coil 135 for heating and controlling the plasma 133 on a pace 131, and a toroidal magnetic field coil 136 for confining the plasma 133 inside a hollow donut-shaped vacuum vessel 137, such as helium. Deuterium or tritium is added as fuel to the inside of the blanket 138 for supplying heat and exchanging heat with a suitable coolant to generate plasma 133, and is fitted to the shielding cylinder 139 in the lower portion 137 a of the vacuum vessel 137. A part 133a (impurity such as He) of the plasma extracted from the plasma 133 is applied to each diverter 141 supported by the cooling pipe header 140 and connected to the diverter coil 135 inside the shielding cylinder 139. 139, the exhaust pipe 4
An exhaust pump 143 is provided via the exhaust pipe 142, and a neutral particle injector 144 is installed in a vacuum vessel 137 above the exhaust pipe 142.

【０１１４】核融合装置は水冷構造を有する真空容器１
３７内に重水素等を入れておき、他方、ポロイダル磁場
コイル１３４，ダイバータコイル１３５及びトロイダル
磁場コイル１３６に電流を供給し、真空容器１３７内の
重水素等をプラズマ１３３に置換すると共に、真空容器
１３７内に中性粒子入射装置１４４で中性粒子を照明し
てプラズマ１３３を二次加熱し、このプラズマ１３３に
生じた熱エネルギをブランケット３８内に流れる冷却剤
と熱交換し、この熱交換した冷却剤を装置外に取り出し
て、これにより、例えばタービンを駆動し得るものであ
る。また一方、真空容器１３７内のプラズマ１３３のス
パッタリングにより生じる不純物は、プラズマ発生効率
を低減させるばかりでなく、真空容器１３７表面の高熱
による損傷の原因となるので、この損傷の原因となる不
純物を除去するためにダイバータ１４１が設けられてお
り、ダイバータ１４１に不純物を当てて除去するもので
ある。ブランケット１３８の内側には第一壁１４６が設
けられ、水冷却される金属ベース１４７にセラミックス
タイル１４８がメタル接合されたものとなっている。The nuclear fusion device is a vacuum vessel 1 having a water-cooled structure.
Deuterium and the like are put in the 37, and current is supplied to the poloidal magnetic field coil 134, the diverter coil 135 and the toroidal magnetic field coil 136 to replace deuterium and the like in the vacuum vessel 137 with the plasma 133, Neutral particles are illuminated in 137 by a neutral particle injector 144 to secondary heat the plasma 133, and the heat energy generated in the plasma 133 exchanges heat with the coolant flowing in the blanket 38, and this heat exchange is performed. The coolant can be taken out of the device, for example, to drive a turbine. On the other hand, impurities generated by the sputtering of the plasma 133 in the vacuum vessel 137 not only reduce the plasma generation efficiency but also cause damage to the surface of the vacuum vessel 137 due to high heat. A diverter 141 is provided for removing the diverter 141 by applying impurities to the diverter 141. A first wall 146 is provided inside the blanket 138, and a ceramic style 148 is metal-bonded to a water-cooled metal base 147.

【０１１５】図３６はダイバータ１４１の概要を示すも
のである。図で、ダイバータ１４１はプラズマから大き
な熱負荷と、ダイバータ１４１に発生するうず電流が大
きな電磁力となって作用する。ダイバータ１４１は、長
尺の板が複数トーラス方向に並び、冷却管ヘッダ１４０
とサブヘッダ１４０ａ及びダイバータ１４１の下面に取
り付けた支持架台１４５により支持されている。また、
ダイバータ１４１は複数枚を１ブロックとし、トーラス
方向に複数個のブロックにより構成されている。各ブロ
ックは水冷却される金属ベース１４７にセラミックスタ
イル１４８が結合した構造を有する。セラミックスタイ
ル１４８は０.２cal／cm・sec・℃ 以上の高熱伝導性を
有するものが好ましい。特にＳｉＣにＢｅ又はＢｅ化合
物を0.2〜２重量％以上含む焼結体、ＡｌＮ又はこれに
前述のＢｅ化合物と同様に含む焼結体を用いるのが好ま
しい。FIG. 36 shows an outline of the diverter 141. In the figure, the diverter 141 acts as a large heat load from the plasma and an eddy current generated in the diverter 141 as a large electromagnetic force. The diverter 141 includes a plurality of long plates arranged in a torus direction, and a cooling pipe header 140.
And a supporting frame 145 attached to the lower surface of the sub-header 140a and the diverter 141. Also,
The diverter 141 includes a plurality of diverters as one block, and includes a plurality of blocks in the torus direction. Each block has a structure in which a ceramic style 148 is joined to a metal base 147 to be water-cooled. The ceramic style 148 preferably has a high thermal conductivity of 0.2 cal / cm · sec · ° C or higher. Particularly, it is preferable to use a sintered body containing 0.2 to 2% by weight or more of Be or a Be compound in SiC, AlN or a sintered body containing AlN or the same as the above-described Be compound.

【０１１６】本実施例で、ダイバータ１４１，真空容器
１３７及び第一壁１４６はいずれも多量の中性子、およ
びプラズマから漏洩する種々の粒子線の照射を受け、ま
た冷却のために水と接する構造になっており、高温水と
接触することになる。これらの構造物の金属ベースに表
１のＮo.５に関わる鋼で製作することにより、中性子照
射下での粒界水素割れ感受性を低減することができ、耐
照射脆化性の向上が図れる。In this embodiment, the diverter 141, the vacuum vessel 137, and the first wall 146 all receive irradiation of a large amount of neutrons and various particle beams leaking from the plasma, and have a structure in contact with water for cooling. And comes into contact with high-temperature water. By manufacturing the metal base of these structures from steel related to No. 5 in Table 1, the sensitivity to grain boundary hydrogen cracking under neutron irradiation can be reduced, and the irradiation embrittlement resistance can be improved.

【０１１７】これらの構造はいずれも実施例１に示す熱
間圧延した後、冷間圧換と焼鈍を繰返した後、同様に１
０５０℃，３０分の溶体化処理を行い、全オーステナイ
ト相からなる。[0117] In any of these structures, after the hot rolling shown in Example 1 and the cold pressing and annealing were repeated, the structure was similarly reduced to 1 mm.
A solution treatment at 050 ° C. for 30 minutes is performed, and the entire austenite phase is formed.

【０１１８】[0118]

【発明の効果】本発明によれば、一般的に粒界が材料劣
化の主因となり得る環境化で使用される強度部材に適用
され、耐食性，強度に優れるため、製品の安全性，信頼
性の向上に顕著な効果が得られる。また、原子炉炉心だ
けでなく、水冷却環境や水素が存在する環境で使用さ
れ、放射線照射損傷を受ける核融合炉用構造部材に適用
され、耐照射損傷性に優れるため、製品の安全性，信頼
性の向上に顕著な効果が得られる。According to the present invention, the grain boundary is generally applied to a strength member used in an environment in which the material may be a major cause of material deterioration, and since it has excellent corrosion resistance and strength, the safety and reliability of the product can be improved. A remarkable effect is obtained for improvement. It is used not only in the reactor core, but also in water-cooled or hydrogen-existing environments, and is applied to structural members for fusion reactors that are subject to radiation irradiation damage. A remarkable effect can be obtained for improving the reliability.

【図面の簡単な説明】[Brief description of the drawings]

【図１】本発明の結晶粒超微細化オーステナイト鋼の平
均結晶粒径と耐力及び伸びの関係を示す特性図。FIG. 1 is a characteristic diagram showing the relationship between the average grain size, proof stress and elongation of the ultrafine grained austenitic steel of the present invention.

【図２】本発明に係る結晶粒超微細化オーステナイト鋼
を製造するのに用いた装置の斜視図。FIG. 2 is a perspective view of an apparatus used to manufacture the ultrafine grained austenitic steel according to the present invention.

【図３】本発明の結晶粒超微細化オーステナイト鋼を製
造するのに用いた機械的合金化粉末のミリング時間とＸ
線回折強度の関係を示す特性図。FIG. 3 shows the milling time and X of the mechanically alloyed powder used to produce the grain refined austenitic steel of the present invention.
FIG. 4 is a characteristic diagram showing a relationship between line diffraction intensities.

【図４】本発明の結晶粒超微細化オーステナイト鋼を製
造するのに用いた機械的合金化粉末のミリング時間と平
均結晶粒径の関係を示す特性図。FIG. 4 is a characteristic diagram showing the relationship between the milling time and the average crystal grain size of the mechanically alloyed powder used for producing the ultrafine grained austenitic steel of the present invention.

【図５】本発明の結晶粒超微細化オーステナイト鋼を製
造するのに用いた機械的合金化粉末のミリング時間とＸ
線回折強度から求めた相変化の関係を示す特性図。FIG. 5 shows the milling time and X of the mechanically alloyed powder used to produce the grain refined austenitic steel of the present invention.
FIG. 4 is a characteristic diagram showing a relationship between phase changes obtained from X-ray diffraction intensity.

【図６】本発明に係る結晶粒超微細化オーステナイト鋼
を製造するのに用いた装置の説明図。FIG. 6 is an explanatory view of an apparatus used for producing an ultra-fine grained austenitic steel according to the present invention.

【図７】本発明のＮo.５オーステナイト鋼の熱処理温度
と平均結晶粒径の関係を示す特性図。FIG. 7 is a characteristic diagram showing the relationship between the heat treatment temperature and the average crystal grain size of the No. 5 austenitic steel of the present invention.

【図８】本発明のＮo.５オーステナイト鋼の熱処理時間
と平均結晶粒径の関係を示す特性図。FIG. 8 is a characteristic diagram showing the relationship between the heat treatment time and the average grain size of the No. 5 austenitic steel of the present invention.

【図９】本発明のＮo.５オーステナイト鋼と従来材実用
３１６Ｌ鋼の平均結晶粒径と耐力の関係を示す特性図。FIG. 9 is a characteristic diagram showing the relationship between the average grain size and the proof stress of the No. 5 austenitic steel of the present invention and the conventional material 316L steel.

【図１０】本発明のＮo.５オーステナイト鋼の真空焼鈍
材と圧延急冷材の応力−歪曲線を示す特性図。FIG. 10 is a characteristic diagram showing stress-strain curves of a vacuum-annealed material and a rolled and quenched material of No. 5 austenitic steel of the present invention.

【図１１】応力腐食割れ試験方法を示す斜視図。FIG. 11 is a perspective view showing a stress corrosion cracking test method.

【図１２】本発明の結晶粒超微細化オーステナイト鋼を
用いた原子炉炉心を示す斜視図。FIG. 12 is a perspective view showing a reactor core using the ultrafine grained austenitic steel of the present invention.

【図１３】上部格子板の部分平面図。FIG. 13 is a partial plan view of an upper lattice plate.

【図１４】図１５のVII部分の断面図。FIG. 14 is a cross-sectional view taken along the line VII of FIG.

【図１５】VIII部分の拡大図。FIG. 15 is an enlarged view of a portion VIII.

【図１６】上部格子板部分の拡大図。FIG. 16 is an enlarged view of an upper lattice plate portion.

【図１７】図１８のＸ部の拡大図。FIG. 17 is an enlarged view of a portion X in FIG. 18;

【図１８】XI部の拡大図。FIG. 18 is an enlarged view of a part XI.

【図１９】炉心支持板の断面図。FIG. 19 is a sectional view of a core support plate.

【図２０】燃料支持金具の斜視図。FIG. 20 is a perspective view of a fuel support.

【図２１】周辺燃料支持金具の断面図。FIG. 21 is a sectional view of a peripheral fuel support fitting.

【図２２】図２１のXV部の拡大図。FIG. 22 is an enlarged view of an XV part in FIG. 21;

【図２３】不具合い部の補修方法を示す説明図。FIG. 23 is an explanatory view showing a method of repairing a defective portion.

【図２４】テーパ無しボルトを使用した補修部の断面
図。FIG. 24 is a cross-sectional view of a repaired portion using a taperless bolt.

【図２５】テーパ付ボルトを使用した補修部の断面図。FIG. 25 is a cross-sectional view of a repair part using a tapered bolt.

【図２６】上部格子板の正面図。FIG. 26 is a front view of an upper lattice plate.

【図２７】炉心支持板の正面図。FIG. 27 is a front view of a core support plate.

【図２８】中性子計装検出管の断面図。FIG. 28 is a cross-sectional view of a neutron instrumentation detection tube.

【図２９】制御棒の部分の斜視図。FIG. 29 is a perspective view of a control rod part.

【図３０】燃料集合体の断面図。FIG. 30 is a sectional view of a fuel assembly.

【図３１】燃料棒の部分断面図。FIG. 31 is a partial sectional view of a fuel rod.

【図３２】中性子源ホルダの断面図。FIG. 32 is a sectional view of a neutron source holder.

【図３３】ＡＢＷＲ原子炉の断面図。FIG. 33 is a sectional view of an ABWR reactor.

【図３４】ＰＷＲの炉心構造を示す断面図。FIG. 34 is a sectional view showing a core structure of a PWR.

【図３５】核融合炉の断面図。FIG. 35 is a sectional view of a fusion reactor.

【図３６】ダイバータの斜視図。FIG. 36 is a perspective view of a diverter.

【符号の説明】[Explanation of symbols]

１…粉砕タンク、２…冷却水入口、３…冷却水出口、７
…アジテータアーム。1 ... grinding tank, 2 ... cooling water inlet, 3 ... cooling water outlet, 7
... Agitator arm.

───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 ＦＩ Ｇ２１Ｂ 1/00 Ｇ２１Ｂ 1/00 Ｄ Ｇ２１Ｃ 3/10 Ｇ２１Ｃ 3/10 Ｂ 3/30 5/00 Ｃ 3/34 3/30 Ｖ 5/00 3/34 Ｙ (72)発明者 加藤 隆彦 茨城県日立市幸町三丁目１番１号 株式会 社日立製作所日立工場内 (72)発明者 近藤 保夫 茨城県日立市大みか町七丁目１番１号 株 式会社日立製作所日立研究所内 (72)発明者 稲垣 正寿 茨城県日立市大みか町七丁目１番１号 株 式会社日立製作所日立研究所内──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 6 Identification code FI G21B 1/00 G21B 1/00 D G21C 3/10 G21C 3/10 B 3/30 5/00 C 3/34 3/30 V 5/00 3/34 Y (72) Inventor Takahiko Kato 3-1-1, Komachi, Hitachi, Hitachi, Ibaraki Prefecture Inside the Hitachi Works, Hitachi, Ltd. (72) Yasuo Kondo 7-1, Omikacho, Hitachi, Ibaraki No. 1 Inside Hitachi, Ltd. Hitachi Laboratory (72) Inventor Masatoshi Inagaki 7-1-1, Omika-cho, Hitachi City, Ibaraki Prefecture Inside Hitachi, Ltd. Hitachi Laboratory

Claims (20)

【特許請求の範囲】[Claims] 【請求項１】重量で、Ｃ０.１％以下，Ｓｉ１％以下，
Ｎ０.４％以下，Ｍｎ２％を越え１５％以下の範囲で
（Ｍｎ＋Ｎｉ）９〜２５％及びＣｒ１４〜２０％を含有
し、平均結晶粒径が１μｍ以下であり、９０体積％以上
のオーステナイト相を有することを特徴とする高耐食性
高強度Ｃｒ−Ｍｎ系オーステナイト焼結鋼。(1) C 0.1% or less, Si 1% or less by weight,
It contains 9-25% of (Mn + Ni) and 14-20% of Cr in the range of N 0.4% or less, Mn more than 2% and 15% or less, has an average crystal grain size of 1 μm or less, and has an austenite phase of 90% by volume or more. High corrosion resistance and high strength Cr-Mn austenitic sintered steel characterized by having. 【請求項２】重量で、Ｃ０.１％以下，Ｓｉ１％以下，
Ｎ０.４％以下，Ｍｎ２％を越え１５％以下の範囲で
（Ｍｎ＋Ｎｉ）９〜２５％，Ｃｒ１４〜２０％及びＭｏ
３％以下を含有し、平均結晶粒径が１μｍ以下であり、
９０体積％以上のオーステナイト相を有することを特徴
とする高耐食性高強度Ｃｒ−Ｍｎ系オーステナイト焼結
鋼。2. The composition according to claim 1, wherein C is 0.1% or less, Si is 1% or less,
(Mn + Ni) 9 to 25%, Cr 14 to 20% and Mo in the range of N 0.4% or less, Mn 2% to 15% or less.
3% or less, the average crystal grain size is 1 μm or less,
A high-corrosion-resistant, high-strength Cr-Mn-based austenitic sintered steel having an austenite phase of 90% by volume or more. 【請求項３】重量で、Ｃ０.１％以下，Ｓｉ１％以下，
Ｎ０.４％以下，Ｍｎ２％を越え１５％以下の範囲で
（Ｍｎ＋Ｎｉ）９〜２５％，Ｃｒ１４〜２０％及びＴｉ
１.０％以下，Ｚｒ２.０％以下，Ｎｂ１.０％以下の１
種又は複数の元素を２.０％ 以下を含有し、平均結晶粒
径が１μｍ以下であり、９０体積％以上のオーステナイ
ト相を有することを特徴とする高耐食性高強度Ｃｒ−Ｍ
ｎ系オーステナイト焼結鋼。3. The composition according to claim 1, wherein C is 0.1% or less, Si is 1% or less,
N: 0.4% or less, (Mn + Ni) 9 to 25%, Cr 14 to 20% and Ti in the range of more than 2% to 15% or less.
1.0% or less, Zr 2.0% or less, Nb 1.0% or less
High corrosion resistance and high strength Cr-M containing 2.0% or less of a seed or a plurality of elements, having an average crystal grain size of 1 µm or less, and having an austenite phase of 90% by volume or more.
n-based austenitic sintered steel. 【請求項４】重量で、Ｃ０.１％以下，Ｓｉ１％以下，
Ｎ０.４％以下，Ｍｎ２％を越え１５％以下の範囲で(Ｍ
ｎ＋Ｎｉ)９〜２５％，Ｃｒ１４〜２０％，Ｍｏ３％以
下及びＴｉ１.０％以下，Ｚｒ２.０％以下，Ｎｂ１.０
％ 以下の１種又は複数の元素を２.０％ 以下を含有
し、平均結晶粒径が１μｍ以下であり、９０体積％以上
のオーステナイト相を有することを特徴とする高耐食性
高強度Ｃｒ−Ｍｎ系オーステナイト焼結鋼。4. The method according to claim 1, wherein C is 0.1% or less, Si is 1% or less,
In the range of N 0.4% or less and Mn 2% or more and 15% or less (M
n + Ni) 9 to 25%, Cr 14 to 20%, Mo 3% or less, Ti 1.0% or less, Zr 2.0% or less, Nb 1.0
% Of one or more elements of 2.0% or less, an average crystal grain size of 1 μm or less, and an austenite phase of 90% by volume or more. Austenitic sintered steel. 【請求項５】重量で、Ｃ０.１％以下，Ｓｉ１％以下，
Ｎ０.４％以下，Ｍｎ２％を越え１５％以下の範囲で
（Ｍｎ＋Ｎｉ）９〜２５％、及びＣｒ１４〜２０％含有
する鋼粉又はこれにＭｏ３％以下，Ｔｉ１.０％以下，
Ｚｒ２.０％以下，Ｎｂ１.０％ 以下の１種又はＴｉ，
Ｚｒ，Ｎｂの複数の元素を２.０％ 以下を含有する鋼粉
に結晶粒径２０ｎｍ以下でかつ加工誘起マルテンサイト
変態相を有する加工粉末を形成する工程と、前記加工粉
末を１０００℃以下の温度で熱間静水圧焼結又は熱間押
し出し加工を施す工程とを有することを特徴とする高耐
食性高強度Ｃｒ−Ｍｎ系オーステナイト焼結鋼。5. The method according to claim 1, wherein C is 0.1% or less, Si is 1% or less,
Steel powder containing (Mn + Ni) 9 to 25% and Cr 14 to 20% in the range of N 0.4% or less, Mn 2% to 15% or less, or Mo 3% or less, Ti 1.0% or less,
One kind of Zr 2.0% or less, Nb 1.0% or less or Ti,
Forming a working powder having a crystal grain size of 20 nm or less and a work-induced martensitic transformation phase in a steel powder containing 2.0% or less of a plurality of elements of Zr and Nb; A step of performing hot isostatic sintering or hot extrusion at a temperature. A high-corrosion-resistant, high-strength Cr-Mn-based austenitic sintered steel, characterized by comprising: 【請求項６】重量で、Ｃ０.１％以下，Ｓｉ１％以下，
Ｐ０.０４５％以下，Ｓ０.０３％ 以下，Ｎ０.４％以
下，Ｍｎ２％を越え１５％以下の範囲で(Ｍｎ＋Ｎｉ）
９〜２５％及びＣｒ１４〜２０％を含有するオーステナ
イト鋼において、加工誘起マルテンサイト相を含む機械
的加工粉末を用いて７００℃〜１０５０℃の温度で固形
化熱処理、あるいは固形化熱処理とそれに続く固形化物
の加工熱処理を実施し、室温の体積率で９０％以上がオ
ーステナイト相であり、平均結晶粒径が１０ｎｍ〜１０
００ｎｍであることを特徴とする高耐食性高強度Ｃｒ−
Ｍｎ系オーステナイト焼結鋼。6. The composition according to claim 1, wherein C is 0.1% or less, Si is 1% or less,
(Mn + Ni) in the range of P 0.045% or less, S 0.03% or less, N 0.4% or less, Mn more than 2% and 15% or less.
In an austenitic steel containing 9-25% and 14-20% Cr, a solidification heat treatment or a solidification heat treatment followed by a solidification heat treatment at a temperature of 700 ° C. to 1050 ° C. using a mechanically processed powder containing a work induced martensite phase. And 90% or more by volume ratio at room temperature is an austenite phase, and the average crystal grain size is 10 nm to 10 nm.
High corrosion resistance and high strength Cr-
Mn-based austenitic sintered steel. 【請求項７】重量で、Ｃ０.１％以下，Ｓｉ１％以下，
Ｐ０.０４５％以下，Ｓ０.０３％以下，Ｎ０.４％以
下，Ｍｎ２％を越え１５％以下の範囲で(Ｍｎ＋Ｎｉ）
９〜２５％，Ｃｒ１４〜２０％及びＭｏ２〜３％を含有
するオーステナイト鋼において、加工誘起マルテンサイ
ト相を含む機械的加工粉末を用いて、７００℃〜１０５
０℃の温度で固形化熱処理、あるいは固形化熱処理とそ
れに続く固形化物の加工熱処理を実施し、室温の体積率
で９０％以上がオーステナイト相であり、平均結晶粒径
が１０ｎｍ〜１０００ｎｍであることを特徴とする高耐
食性高強度Ｃｒ−Ｍｎ系オーステナイト焼結鋼。7. By weight, C 0.1% or less, Si 1% or less,
(Mn + Ni) in the range of P 0.045% or less, S 0.03% or less, N 0.4% or less, Mn more than 2% and 15% or less.
In an austenitic steel containing 9 to 25%, 14 to 20% of Cr and 2 to 3% of Mo, a mechanically processed powder containing a work-induced martensite phase is used.
A solidification heat treatment at a temperature of 0 ° C. or a solidification heat treatment followed by a processing heat treatment of the solidified material, and at least 90% by volume of the room temperature is an austenite phase and the average crystal grain size is 10 nm to 1000 nm. High corrosion resistance and high strength Cr-Mn austenitic sintered steel characterized by the following characteristics. 【請求項８】重量で、Ｃ０.１％以下，Ｓｉ１％以下，
Ｐ０.０４５％以下，Ｓ０.０３％ 以下，Ｎ０.４％以
下，Ｍｎ２％を越え１５％以下の範囲で(Ｍｎ＋Ｎｉ）
９〜２５％，Ｃｒ１４〜２０％、及びＴｉ１.０％以
下，Ｚｒ２.０％ 以下，Ｎｂ１.０％以下のうち１種あ
るいは複数の元素を２.０％以下 を含むオーステナイト
鋼において、加工誘起マルテンサイト相を含む機械的加
工粉末を用いて、７００℃〜１０５０℃の温度で固形化
熱処理、あるいは固形化熱処理とそれに続く該固形化物
の加工熱処理を実施し、室温での体積率で９０％以上が
オーステナイト相であり、平均結晶粒径が１０ｎｍ〜１
０００ｎｍであることを特徴とする高耐食性高強度Ｃｒ
−Ｍｎ系オーステナイト焼結鋼。8. The method according to claim 1, wherein C is less than 0.1%, Si is less than 1%,
(Mn + Ni) in the range of P 0.045% or less, S 0.03% or less, N 0.4% or less, Mn more than 2% and 15% or less.
In the austenitic steel containing 9% to 25%, Cr 14% to 20%, and 1.0% or less of Ti, 2.0% or less of Zr, and 1.0% or less of Nb, 2.0% or less of one or more elements is induced by work. Using a mechanically processed powder containing a martensite phase, a heat treatment for solidification at a temperature of 700 ° C. to 1050 ° C. or a heat treatment for solidification followed by a heat treatment for the solidification is performed, and the volume ratio at room temperature is 90%. The above is the austenite phase, and the average crystal grain size is 10 nm to 1
000 nm, high corrosion resistance and high strength Cr
-Mn-based austenitic sintered steel. 【請求項９】重量で、Ｃ０.１％以下，Ｓｉ１％以下，
Ｐ０.０４５％以下，Ｓ０.０３％ 以下，Ｎ０.４％以
下，Ｍｎ２％を越え１５％以下の範囲で（Ｍｎ＋Ｎｉ）
９〜２５％，Ｃｒ１４〜２０％，Ｍｏ２.０〜３.０％、
及びＴｉ１.０％ 以下，Ｚｒ２.０％以下，Ｎｂ１.０％
以下のうち１種あるいは複数の元素を２.０％以下 を含
むオーステナイト鋼において、加工誘起マルテンサイト
相を含む機械的加工粉末を用いて７００℃〜１０５０℃
の温度で固形化熱処理、あるいは固形化熱処理とそれに
続く固形化物の加工熱処理を実施し、室温の体積率で９
０％以上がオーステナイト相であり、平均結晶粒径が１
０ｎｍ〜１０００ｎｍであることを特徴とする高耐食性
高強度Ｃｒ−Ｍｎ系オーステナイト焼結鋼。9. By weight, C 0.1% or less, Si 1% or less,
(Mn + Ni) in the range of P 0.045% or less, S 0.03% or less, N 0.4% or less, Mn more than 2% and 15% or less.
9-25%, Cr 14-20%, Mo 2.0-3.0%,
And Ti 1.0% or less, Zr 2.0% or less, Nb 1.0%
In austenitic steel containing 2.0% or less of one or more of the following elements, 700 ° C to 1050 ° C using mechanically processed powder containing a work-induced martensite phase.
The solidification heat treatment or the solidification heat treatment followed by the solidification material processing heat treatment is performed at a temperature of
0% or more is an austenite phase and the average grain size is 1
A highly corrosion-resistant, high-strength Cr-Mn-based austenitic sintered steel having a thickness of 0 nm to 1000 nm. 【請求項１０】重量で、Ｃ０.１％以下，Ｓｉ１％以
下，Ｎ０.４％以下，Ｍｎ２％を越え１５％以下の範囲
で（Ｍｎ＋Ｎｉ）９〜２５％及びＣｒ１４〜２０％を含
有する鋼粉又はこれにＭｏ３％以下，Ｔｉ１.０％以
下，Ｚｒ２.０％以下，Ｎｂ１.０％ 以下の少なくとも
１種でＴｉ，Ｚｒ，Ｎｂの複数の元素を合計で２.０％
以下を含有する鋼粉をアトマイズ粉末あるいは総体とし
て前記組成を満たす混合粉末を１００℃以下で３０〜１
００時間アトライタあるいはボールミルを用いて機械的
にグラインディングまたは合金化処理し、結晶粒径が１
５ｎｍ以下の加工誘起マルテンサイト変態相を有する加
工粉末を形成する工程と、前記加工粉末を熱間静水圧焼
結または熱間押し出し法にて７００〜１０５０℃の温度
範囲で固形化熱処理あるいは固形化熱処理とそれに続く
最終加工熱処理をすることにより室温の体積率で９０％
以上がオーステナイト相となり、１０ｎｍ〜１０００ｎ
ｍの範囲で平均結晶粒径を調整することを特徴とする高
耐食性高強度Ｃｒ−Ｍｎ系オーステナイト焼結鋼の製造
方法。10. A steel containing, by weight, 9-25% of (Mn + Ni) and 14-20% of Cr in a range of not more than 0.1% of C, not more than 1% of Si, not more than 0.4% of N, not less than 2% of Mn and not more than 15%. Powder or at least one of Mo 3% or less, Ti 1.0% or less, Zr 2.0% or less, Nb 1.0% or less, and a plurality of elements of Ti, Zr, and Nb in a total of 2.0%
A steel powder containing the following is atomized powder or a mixed powder satisfying the above-mentioned composition as a whole at a temperature of 100 ° C. or less and 30 to 1
Mechanical grinding or alloying treatment using an attritor or a ball mill for 00 hours.
Forming a working powder having a work-induced martensitic transformation phase of 5 nm or less, and heat-treating or solidifying the working powder in a temperature range of 700 to 1050 ° C. by hot isostatic sintering or hot extrusion. 90% by volume ratio at room temperature by heat treatment followed by final processing heat treatment
The above becomes an austenite phase and 10 nm to 1000 n
A method for producing a high-corrosion-resistant, high-strength Cr-Mn-based austenitic sintered steel, wherein the average crystal grain size is adjusted in the range of m. 【請求項１１】重量で、Ｃ０.１％以下，Ｓｉ１％以
下，Ｎ０.４％以下，Ｍｎ２％を越え１５％以下の範囲
で（Ｍｎ＋Ｎｉ）９〜２５％及びＣｒ１４〜２０％を含
有するＣｒ−Ｍｎ系オーステナイト焼結鋼又はこれにＭ
ｏ３％以下，Ｔｉ１.０％ 以下，Ｚｒ２.０％以下，Ｎ
ｂ１.０％以下の少なくとも１種でＴｉ，Ｚｒ，Ｎｂの
複数の元素を合計で２.０％ 以下を含有するＣｒ−Ｍｎ
系オーステナイト焼結鋼よりなることを特徴とする原子
炉内部材。11. Cr containing from 9 to 25% of (Mn + Ni) and from 14 to 20% of Cr in a range of not more than 0.1% of C, not more than 1% of Si, not more than 0.4% of N, not less than 2% of Mn and not more than 15% by weight. -Mn based austenitic sintered steel or M
o 3% or less, Ti 1.0% or less, Zr 2.0% or less, N
b: Cr-Mn containing at least one element of 1.0% or less and a plurality of elements of Ti, Zr, and Nb in a total amount of 2.0% or less.
A reactor internal member comprising austenitic sintered steel. 【請求項１２】重量で、Ｃ０.１％以下，Ｓｉ１％以
下，Ｎ０.４％以下，Ｍｎ２％を越え１５％以下の範囲
で（Ｍｎ＋Ｎｉ）９〜２５％及びＣｒ１４〜２０％を含
有するＣｒ−Ｍｎ系オーステナイト焼結鋼又はこれにＭ
ｏ３％以下，Ｔｉ１.０％ 以下，Ｚｒ２.０％以下，Ｎ
ｂ１.０％以下の少なくとも１種でＴｉ，Ｚｒ，Ｎｂの
複数の元素を合計で２.０％ 以下を含有するＣｒ−Ｍｎ
系オーステナイト焼結鋼よりなることを特徴とする締結
部材。12. A Cr containing 9-25% of (Mn + Ni) and 14-20% of Cr in a range of not more than 0.1% of C, not more than 1% of Si, not more than 0.4% of N, not less than 2% of Mn and not more than 15% by weight. -Mn based austenitic sintered steel or M
o 3% or less, Ti 1.0% or less, Zr 2.0% or less, N
b: Cr-Mn containing at least one element of 1.0% or less and a plurality of elements of Ti, Zr, and Nb in a total amount of 2.0% or less.
A fastening member comprising austenitic sintered steel. 【請求項１３】水と接触し、中性子照射を受けるＣｒ−
Ｍｎ系オーステナイト鋼からなる構造部材において、平
均結晶粒径が１μｍ以下であることを特徴とする高耐食
性高強度構造部材。13. A Cr— contacted with water and subjected to neutron irradiation.
A high-corrosion-resistant high-strength structural member comprising a Mn-based austenitic steel having an average crystal grain size of 1 μm or less. 【請求項１４】原子炉圧力容器内に中性子源パイプ，炉
心支持板，中性子計装管，制御棒挿入パイプ，シュラウ
ド，上部格子板，燃料集合体用被覆管及びチャンネルボ
ックスの構造部品を備えた原子炉において、前記構造部
品の少なくとも一つが、１μｍ以下の平均結晶粒径を有
するＣｒ−Ｍｎ系オーステナイト鋼よりなることを特徴
とする原子炉。14. A reactor pressure vessel having structural components such as a neutron source pipe, a core support plate, a neutron instrumentation tube, a control rod insertion pipe, a shroud, an upper grid plate, a fuel assembly cladding tube, and a channel box. A nuclear reactor, wherein at least one of the structural components is made of a Cr-Mn austenitic steel having an average grain size of 1 m or less. 【請求項１５】中性子源パイプ，炉心支持板，中性子計
装管，制御棒挿入パイプ，シュラウド，上部格子板，燃
料集合体用被覆管及びチャンネルボックスの構造部品を
備えた原子炉において、前記構造部品の少なくとも一つ
が、重量で、Ｃ０.１％ 以下，Ｓｉ１％以下，Ｎ０.４
％ 以下，Ｍｎ２％を越え１５％以下の範囲で（Ｍｎ＋
Ｎｉ）９〜２５％及びＣｒ１４〜２０％を含み、又はこ
れにＭｏ３％以下，Ｔｉ１.０％以下，Ｚｒ２.０％以
下，Ｎｂ１.０％ 以下の少なくとも１種でＴｉ，Ｚｒ，
Ｎｂの複数の元素を合計で２.０％ 以下を含み、１μｍ
以下の平均結晶粒径を有するＣｒ−Ｍｎ系オーステナイ
ト鋼よりなることを特徴とする原子炉。15. A nuclear reactor comprising a neutron source pipe, a core support plate, a neutron instrumentation tube, a control rod insertion pipe, a shroud, an upper grid plate, a fuel assembly cladding tube and a channel box. At least one of the parts is C0.1% or less, Si1% or less, N0.4 by weight.
%, Mn + 2% to 15% or less (Mn +
Ni) 9 to 25% and Cr 14 to 20%, or at least one of Mo 3% or less, Ti 1.0% or less, Zr 2.0% or less, Nb 1.0% or less Ti, Zr,
1 μm containing a total of 2.0% or less of a plurality of elements of Nb
A nuclear reactor comprising a Cr-Mn austenitic steel having the following average crystal grain size. 【請求項１６】請求項１４において、前記原子炉の熱出
力が３２００ＭＷ以上，原子炉圧力７.０ＭＰａ 以上，
原子炉水温度２８８℃以上，前記電気出力が１１００Ｍ
Ｗ以上であり、前記原子炉圧力容器内に設けられた中性
子源パイプ，炉心支持板，中性子計装管，制御棒挿入パ
イプ，シュラウド及び上部格子板の各構成部品の少なく
とも一つを３０年以上無交換で使用でき、稼働率を８５
％以上とした原子力発電プラント。16. The reactor according to claim 14, wherein the heat output of the reactor is 3200 MW or more, the reactor pressure is 7.0 MPa or more,
Reactor water temperature 288 ° C or higher, electric output 1100M
W or more, and at least one of the components of the neutron source pipe, core support plate, neutron instrumentation tube, control rod insertion pipe, shroud, and upper grid plate provided in the reactor pressure vessel for at least 30 years Can be used without replacement, operating rate is 85
% Of nuclear power plants. 【請求項１７】請求項１４において、前記原子炉の熱出
力が４３００ＭＷ以上，原子炉圧力が７.０ＭＰａ 以
上，原子炉水温度が２８８℃以上，前記電気出力が１５
００ＭＷ以上，稼働率８５％以上及び１２ケ月運転後の
定検期間を１回当り５０日以内とした原子力発電プラン
ト。17. The reactor according to claim 14, wherein the thermal output of the reactor is 4300 MW or more, the reactor pressure is 7.0 MPa or more, the reactor water temperature is 288 ° C. or more, and the electric output is 15
A nuclear power plant with 00MW or more, an operation rate of 85% or more, and a regular inspection period of less than 50 days per operation after 12 months operation. 【請求項１８】原子炉圧力容器内に中性子源パイプ，炉
心支持板，中性子計装管，制御棒挿入パイプ，シュラウ
ド，上部格子板，燃料集合体用被覆管及びチャンネルボ
ックスの構造部品を備えてなる原子炉用構成部品におい
て、前記構造部品の少なくとも一つが全オーステナイト
組織を有し、平均結晶粒径が１μｍ以下であるＣｒ−Ｍ
ｎ系オーステナイト鋼よりなることを特徴とする原子炉
用構成部品。18. A reactor pressure vessel having structural components such as a neutron source pipe, a core support plate, a neutron instrumentation tube, a control rod insertion pipe, a shroud, an upper lattice plate, a fuel assembly cladding tube, and a channel box. A structural component for a nuclear reactor, wherein at least one of the structural components has a total austenite structure and has an average crystal grain size of 1 μm or less.
A component for a nuclear reactor, comprising n-type austenitic steel. 【請求項１９】水冷構造を有する真空容器内にプラズマ
側にセラミックスタイルが設けられ水冷構造を有するダ
イバータ、およびプラズマ側にセラミックスタイルが設
けられ水冷構造を有する第一壁の構成部品を備えた核融
合炉において、前記構成部品の少なくとも一つが平均結
晶粒径が１μｍ以下であるＣｒ−Ｍｎ系オーステナイト
鋼よりなることを特徴とする核融合炉。19. A diverter having a water-cooled structure provided with a ceramic style on the plasma side in a vacuum vessel having a water-cooled structure, and a core having a first wall having a water-cooled structure provided with a ceramic style on the plasma side. In a fusion reactor, at least one of the constituent parts is made of a Cr-Mn austenitic steel having an average crystal grain size of 1 µm or less. 【請求項２０】水冷構造を有する真空容器，セラミック
スタイルが設けられ水冷構造を有するダイバータ、およ
びプラズマ側にセラミックスタイルが設けられ水冷構造
を有する第一壁を備えた核融合炉用構成部品において、
前記構成部品の少なくとも一つが、平均結晶粒径が１μ
ｍ以下であるＣｒ−Ｍｎ系オーステナイト鋼よりなるこ
とを特徴とする核融合炉用構成部品。20. A component for a fusion reactor comprising a vacuum vessel having a water cooling structure, a diverter provided with a ceramic style and having a water cooling structure, and a first wall provided with a ceramic style on the plasma side and having a water cooling structure,
At least one of the components has an average crystal grain size of 1 μm.
m. A component for a nuclear fusion reactor, comprising a Cr-Mn austenitic steel having a diameter of not more than m.
JP8241586A 1996-09-12 1996-09-12 Chromium-manganese austenitic sintered steel with high corrosion resistance and high strength, its production, and its use Pending JPH1088289A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
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Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
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Publication Number Publication Date
JPH1088289A true JPH1088289A (en) 1998-04-07

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JP2014181371A (en) * 2013-03-19 2014-09-29 Toyota Central R&D Labs Inc Highly corrosion resistant metal part and method for producing the same
JP2016113673A (en) * 2014-12-16 2016-06-23 セイコーエプソン株式会社 Metal powder for powder metallurgy, compound, granulated powder, and sintered body
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EP1234894A1 (en) * 2001-02-27 2002-08-28 Hitachi, Ltd. Corrosion resistant, high strength alloy and a method for manufacturing the same
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WO2004110695A1 (en) * 2003-06-10 2004-12-23 Sumitomo Metal Industries, Ltd. Austenitic steel weld joint
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CN102732806A (en) * 2012-06-26 2012-10-17 江苏兴海特钢有限公司 Intergranular corrosion resistant austenitic system stainless steel
JP2014181371A (en) * 2013-03-19 2014-09-29 Toyota Central R&D Labs Inc Highly corrosion resistant metal part and method for producing the same
JP2016113673A (en) * 2014-12-16 2016-06-23 セイコーエプソン株式会社 Metal powder for powder metallurgy, compound, granulated powder, and sintered body
JP2016125103A (en) * 2015-01-06 2016-07-11 セイコーエプソン株式会社 Metal powder for powder metallurgy, compound, granulated powder and sintered body

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