JPH03267350A - Irradiation resisting austenitic stainless steel - Google Patents
Irradiation resisting austenitic stainless steelInfo
- Publication number
- JPH03267350A JPH03267350A JP6423290A JP6423290A JPH03267350A JP H03267350 A JPH03267350 A JP H03267350A JP 6423290 A JP6423290 A JP 6423290A JP 6423290 A JP6423290 A JP 6423290A JP H03267350 A JPH03267350 A JP H03267350A
- Authority
- JP
- Japan
- Prior art keywords
- irradiation
- stainless steel
- austenitic stainless
- steel
- concentration
- 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
Links
- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 12
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 15
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 14
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 13
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 4
- 229910052710 silicon Inorganic materials 0.000 claims abstract 3
- 229910000831 Steel Inorganic materials 0.000 abstract description 19
- 239000010959 steel Substances 0.000 abstract description 19
- 230000007797 corrosion Effects 0.000 abstract description 9
- 238000005260 corrosion Methods 0.000 abstract description 9
- 229910052799 carbon Inorganic materials 0.000 abstract description 5
- 238000005336 cracking Methods 0.000 abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 3
- 239000000203 mixture Substances 0.000 abstract description 2
- 230000006866 deterioration Effects 0.000 abstract 2
- 230000007423 decrease Effects 0.000 description 14
- 239000000463 material Substances 0.000 description 11
- 239000000654 additive Substances 0.000 description 6
- 230000000996 additive effect Effects 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 230000007547 defect Effects 0.000 description 4
- 238000007792 addition Methods 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000011148 porous material Substances 0.000 description 2
- 230000005855 radiation Effects 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 230000001133 acceleration Effects 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 230000005012 migration Effects 0.000 description 1
- 238000013508 migration Methods 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、新規なオーステナイト系ステンレス鋼に係り
、特に原子炉炉心部材として中性子照射を受ける炉心部
の機器部品類の、機械的性質を低下させることなく、照
射下での粒界Ｃｒ濃度低下を防止するのに好適なオース
テナイトステンレス鋼に関する。[Detailed Description of the Invention] [Field of Industrial Application] The present invention relates to a new austenitic stainless steel, particularly for use in reducing the mechanical properties of equipment parts in the reactor core that are subjected to neutron irradiation as core members of nuclear reactors. The present invention relates to an austenitic stainless steel suitable for preventing a decrease in grain boundary Cr concentration under irradiation without causing any irradiation.
従来、軽水炉炉心の機器部品には主として、５ＵＳ３０
４が使用されている。原子炉の運転期間中、炉心部の機
器部品は中性子照射を受けるので機器部品材料は耐照射
性に優れたものが望まれている。Conventionally, 5US30 was mainly used for light water reactor core equipment parts.
4 is used. During the operation of a nuclear reactor, equipment components in the reactor core are exposed to neutron irradiation, so materials for equipment parts are desired to have excellent irradiation resistance.
材料の耐照射性で、特に、重要な性質は照射脆化と照射
下の応力腐食割れである。照射脆化については、例えば
、特許１３２３６１５号に見られる様に、材料に微量の
添加元素を含有させることにより改善されることが指摘
されている。また照射下の応力腐食割れ性については同
様に微量の■族及び■族元素を添加することにより改善
されることが特開昭６２−９３０７５号公報に記載され
ている。Particularly important properties in the radiation resistance of materials are radiation embrittlement and stress corrosion cracking under irradiation. It has been pointed out that irradiation embrittlement can be improved by incorporating a trace amount of an additive element into the material, as seen in, for example, Japanese Patent No. 1,323,615. Furthermore, it is described in JP-A-62-93075 that the stress corrosion cracking resistance under irradiation can be similarly improved by adding trace amounts of group (1) and group (2) elements.
しかしながら、上記発明の従来技術においては、原子炉
中で高い線量の中性子照射を被むることにより結晶粒界
でのＣｒの濃度が減少し、オーステナイトステンレス鋼
の耐照射脆化性及び照射下での耐応力腐食割れ性が悪化
することを認識していない。However, in the prior art of the above invention, the concentration of Cr at grain boundaries decreases due to exposure to high doses of neutron irradiation in a nuclear reactor, and the irradiation embrittlement resistance of austenitic stainless steel and its resistance to irradiation decrease. They were not aware that stress corrosion cracking resistance would deteriorate.
本発明は、照射下での粒界Ｃｒ濃度低下を防止するに耐
照射性オーステナイトステンレス鋼を提供することを目
的とする。An object of the present invention is to provide an irradiation-resistant austenitic stainless steel that prevents a decrease in grain boundary Cr concentration under irradiation.
本発明は、重量で、Ｃ０．ＯＯ１〜０．０３％。 The present invention has a C0. OO1-0.03%.
Ｓｉ１％以下、Ｍｎ２％以下、Ｃｒ１５−１８％。Si 1% or less, Mn 2% or less, Cr 15-18%.
Ｎｉ８〜１５％、Ｍｏ０〜３％を有するオーステナイト
ステンレス鋼にＴｉ、Ｚｒ、Ｈｆの一種または二種以上
を、
で含有し、さらに添加元素Ｔｉ、Ｚｒ、Ｈｆの、照射下
における粒界Ｃｒ濃度低下を防止する効果を損わないた
めに、Ｎの含有量を０．００１〜０．１にしたものであ
る。One or more of Ti, Zr, and Hf are contained in an austenitic stainless steel having 8 to 15% Ni and 0 to 3% Mo, and the grain boundary Cr concentration of the additional elements Ti, Zr, and Hf is reduced under irradiation. In order not to impair the effect of preventing this, the N content is set to 0.001 to 0.1.
オーステナイトステンレス鋼の照射下で誘起される粒界
でのＣｒ濃度の低下は、照射により材料中に導入される
照射点欠陥すなわち空孔と格子間原子の粒界への移動に
よるものである。つまりＣｒは、空孔と相互作用するこ
とにより空孔の流れと逆向きに移動する交換機構により
粒界から離れていく。本発明は、上記粒界Ｃｒ濃度減少
を防止する方法として、Ｃｒの移動の駆動力となる点欠
陥の量を減少させることを思いついた。さらに照射によ
って生成される点欠陥の量を減少させる方法として、空
孔と強く相互作用する元素の添加により空孔をその元素
にトラップして格子間原子との相互消滅を促進させる方
法を考案し、種々の元素の添加と有効な添加量の検討を
行った。その結果、Ｔｉ、Ｚｒ、Ｈｆの一種または二種
以上を前述のように含有させるものである。The decrease in Cr concentration at grain boundaries induced under irradiation of austenitic stainless steel is due to the migration of irradiation point defects, ie, vacancies, and interstitial atoms introduced into the material by irradiation to the grain boundaries. In other words, Cr moves away from grain boundaries by an exchange mechanism in which it interacts with pores and moves in the opposite direction to the flow of pores. The present invention has come up with the idea of reducing the amount of point defects that act as a driving force for Cr movement, as a method for preventing the above-mentioned decrease in grain boundary Cr concentration. Furthermore, as a method to reduce the amount of point defects generated by irradiation, we devised a method of adding an element that strongly interacts with vacancies to trap vacancies in that element and promote mutual annihilation with interstitial atoms. We investigated the addition of various elements and their effective amounts. As a result, one or more of Ti, Zr, and Hf are contained as described above.
これらの添加により、照射による粒界でのＣｒ濃度の減
少を防止できることを、中性子照射の模擬試験として超
高圧電子顕微鏡を用いた電子照射試験により発見し、本
発明をするに至った。これら添加元素の働きは、上記の
様にこれらの添加元素が照射により生成した点欠陥すな
わち空孔を強くトラップすることにより格子間原子との
相互消滅を促進させ、空孔の量が著しく引き下げられる
ため粒界からのＣｒの移動を抑制するものと考えられ、
その結果、照射下で誘起される粒界でのＣｒ濃度低下の
防止を達成できたと考えられる。It was discovered through an electron irradiation test using an ultra-high-voltage electron microscope as a neutron irradiation simulation test that the addition of these materials can prevent a decrease in the Cr concentration at grain boundaries due to irradiation, leading to the present invention. As mentioned above, these additive elements strongly trap point defects, or vacancies, generated by irradiation, thereby promoting mutual annihilation with interstitial atoms, and the amount of vacancies is significantly reduced. Therefore, it is thought to suppress the movement of Cr from the grain boundaries,
As a result, it is considered that the reduction in Cr concentration at grain boundaries induced by irradiation could be prevented.
また上記添加元素の効果は、ＣまたはＮが多量に存在す
ると、ＣまたはＮが粒界でＣｒの化合物を照射中に生成
し、粒界でＣｒ濃度の減少が誘起させるため、Ｃまたは
Ｎを各々０．０３重量％または０．１ 重量％より引き
下げないと、有効な働きをしない。但し、鋼の製造性及
びコストの点から、ＣまたはＮの下限値は０．００１
重量％以上が好ましい。また上記Ｔｉ、Ｚｒ、Ｈｆの添
加量は最低値以下では上記効果がなくさらに最高値以上
では、溶接性や加工性が悪化する。In addition, the effect of the above additive elements is that when a large amount of C or N exists, C or N forms at the grain boundaries during irradiation with Cr compounds, which induces a decrease in the Cr concentration at the grain boundaries. It will not work effectively unless it is reduced below 0.03% by weight or 0.1% by weight, respectively. However, from the viewpoint of steel manufacturability and cost, the lower limit of C or N is 0.001.
It is preferably at least % by weight. Furthermore, if the amounts of Ti, Zr, and Hf added are below the minimum value, the above effects will not be obtained, and if the amounts are above the maximum value, weldability and workability will deteriorate.
また、他の成分元素は耐照射性９強度、耐食性を考慮し
て、下記の範囲内とすることが好ましい。In addition, other component elements are preferably within the following ranges in consideration of irradiation resistance 9 strength and corrosion resistance.
（１）Ｓｉ：１％以下
Ｓｉは耐照射脆化向上のために有効であるが、１％をこ
えるとかえって高温水中での応力腐食割れ性を害するの
で好ましくない。また、鋼の溶解の際、脱酸を完全する
ためには、１％以下添加してもよい。(1) Si: 1% or less Si is effective for improving resistance to irradiation embrittlement, but if it exceeds 1%, it is not preferable because it actually impairs stress corrosion cracking in high-temperature water. Furthermore, in order to complete deoxidation during melting of steel, it may be added in an amount of 1% or less.
（２） Ｍｎ ： ２％以下
強度や加工性向上に有効であるが、２％を越えると逆に
脆化をもたらすため、２％以下とする。(2) Mn: 2% or less is effective in improving strength and workability, but exceeding 2% causes embrittlement, so it should be kept at 2% or less.
（３）Ｎｉ：８〜１５％以下
Ｎｉは耐食性、照射下でのオーステナイト相安定性及び
耐照射性から８〜１５％が望ましい。(3) Ni: 8 to 15% or less Ni is desirably 8 to 15% in terms of corrosion resistance, austenite phase stability under irradiation, and irradiation resistance.
（４）Ｃｒ： １５−２０％以下
Ｃｒは１５％以下では強度及び耐食性が低下し、また、
２０％以上では耐照射性が低下するので特に１５〜１８
％の範囲が望ましい。(4) Cr: 15-20% or less If Cr is 15% or less, strength and corrosion resistance decrease, and
If it exceeds 20%, the irradiation resistance will decrease, so especially if it is 15 to 18%.
A range of % is desirable.
（５）Ｍｏ：０〜３％以下
ＭＯは、添加しなくても上記機器部品材料として使用で
きるが、さらに耐食性の向上に配慮する場合に有効な添
加元素である。しかし、３％を越えて添加するとδ相の
析出を促進し材料の脆化を引きおこすので好ましくない
。(5) Mo: 0 to 3% or less MO can be used as the above-mentioned equipment component material without being added, but it is an effective additive element when consideration is given to improving corrosion resistance. However, adding more than 3% is not preferable because it promotes precipitation of the δ phase and causes embrittlement of the material.
実施例１
第１表に１本発明のオーステナイトステンレス鋼＆２，
３．４の化学組成（重量％）を比較鋼１゜５．６．７と
共に示す。Ｎα１はいわゆる５ＵＳ３１６Ｌ鋼である。Example 1 Table 1 shows 1 austenitic stainless steel of the present invention &2,
The chemical composition (wt%) of 3.4 is shown together with comparative steel 1°5.6.7. Nα1 is so-called 5US316L steel.
残部はＦｅである。Ｎα２，３゜４は各々本発明の添加
元素Ｔｉ、Ｚｒ、Ｈｆを本発明の添加量の範囲で含有し
たものである。また＆５，６．７は化較鋼として各々Ｖ
、Ｎｂ、Ｔａを原子％で本発明鋼（Ｎα１ないし３）と
同程度含有した鋼である。これらの鋼を溶製、造塊後、
熱間圧延、冷間圧延し、最終的に１０ｏＯ〜１１５０℃
で３０分間溶体化処理を施して照射用試料とした。試料
は中性子照射を模擬した超高圧電子顕微鏡を用いた電子
照射で試験した。照射条件は電子の加速電圧ＩＭｅＶ、
５００℃、１０ｄｐａ （１ｄｐａは中性子照射量の約
ｌＸｌ０”ｎ／ａＪに相当する）である。第１図は照射
後結晶粒界近傍のＣｒ濃度変化をＥＤＸ （エネルギ分
散型Ｘ線分析装置）で分析した結果を示す。比較材Ｎα
１，５゜６．７では粒界で著しいＣｒ濃度の低下が観察
されるが、本発明鋼Ｎα２，３．４では粒界でのＣｒ濃
度低下は防止されている。The remainder is Fe. Nα2, 3°4 each contains the additive elements Ti, Zr, and Hf according to the present invention within the range of the additive amount according to the present invention. In addition, &5 and 6.7 are respectively V as comparative steels.
, Nb, and Ta in atomic % to the same extent as the steels of the present invention (Nα1 to 3). After melting these steels and forming ingots,
Hot rolled, cold rolled, finally 10oO~1150℃
The sample was subjected to solution treatment for 30 minutes to prepare a sample for irradiation. The samples were tested by electron irradiation using an ultra-high voltage electron microscope that simulates neutron irradiation. The irradiation conditions are electron acceleration voltage IMeV,
500°C, 10 dpa (1 dpa corresponds to approximately lXl0"n/aJ of neutron irradiation). Figure 1 shows the change in Cr concentration near grain boundaries after irradiation using EDX (energy dispersive X-ray analyzer). The analysis results are shown below. Comparative material Nα
At 1.5°6.7, a significant decrease in Cr concentration is observed at the grain boundaries, but in the steel of the present invention Nα2, 3.4, the decrease in Cr concentration at the grain boundaries is prevented.
さらにＴｉとＺｒを各々０．２，０．２重量％＆１に添
加した鋼、ＺｒとＨｆを各々０．２．０．３重量％Ｎα
１に添加した鋼、ＴｉとＨｆを各々０．２゜０．４ 重
量％Ｎａ １に添加した鋼、Ｔｉ、Ｚｒ。Furthermore, steel with Ti and Zr added at 0.2 and 0.2 wt% &1, and Nα with Zr and Hf added at 0.2 and 0.3 wt% each
Steel with added Ti and Hf at 0.2° and 0.4% by weight Na 1, Ti and Zr respectively.
Ｈｆを各々０．１２，０．２１，０．３０ 添加した鋼
を作製し、上記と同様の照射試験したが、粒界でのＣｒ
濃度の減少は防止されていた。これらの鋼は本発明のオ
ーステナイト鋼である。Steels with 0.12, 0.21, and 0.30 Hf added were prepared and subjected to the same irradiation test as above, but Cr at the grain boundaries
A decrease in concentration was prevented. These steels are the austenitic steels of the present invention.
実施例２
第２図は、ＢＷＲ型原子炉炉心部の概略断面図であり、
図中、１は中性子源パイプ、２は上部格子板、３は中性
子計装管、４は制御棒を示す。これらの部品を実施例１
で示した本発明のＮα５，６゜７並びにＴｉとＺｒ、Ｚ
ｒとＨｆ、ＴｉとＨｆ及びＴｉとＺｒとＨｆを複合添加
した鋼で作製したが従来製造方法で容易に製造できた。Example 2 FIG. 2 is a schematic cross-sectional view of the core of a BWR type nuclear reactor.
In the figure, 1 is a neutron source pipe, 2 is an upper grid plate, 3 is a neutron instrumentation tube, and 4 is a control rod. These parts are shown in Example 1.
Nα5,6°7 of the present invention shown in , and Ti, Zr, Z
The steels were manufactured using composite additions of r and Hf, Ti and Hf, and Ti, Zr, and Hf, and could easily be manufactured using conventional manufacturing methods.
また図中１〜４で示す機器部品の他にこれらの機器部品
間に介在する細いパーツ等も本発明の上記材料で容易に
作製できた。In addition to the device parts 1 to 4 in the figure, thin parts interposed between these device parts could also be easily manufactured using the above-mentioned materials of the present invention.
本発明によれば、原子炉炉心及び核融合炉炉壁で中性子
照射を受ける機器部品材料の照射下で起こる粒界Ｃｒ濃
度の減少を防止することができる。According to the present invention, it is possible to prevent a decrease in grain boundary Cr concentration that occurs under irradiation of equipment component materials that are irradiated with neutrons in a nuclear reactor core and a fusion reactor wall.
その結果、これら炉の安全性、信頼性の向上に効果があ
り、ひいては、該機器部品材料の長寿命化による炉運転
の経済性向上に効果がある。As a result, it is effective in improving the safety and reliability of these furnaces, and in turn, it is effective in improving the economic efficiency of furnace operation by extending the life of the equipment component materials.
第１図は、本発明の鋼の照射による粒界近傍のＣｒ濃度
変化を比較鋼と共にＣｒ濃度の関係を示す線図、第２図
は、本発明鋼で作製したＢＷＲ炉内構造物の断面図であ
る。
１・・・中性子源パイプ、２・・・上部格子板、３・・
・中性子計装管、４・・・制御棒。
７．７．０ト 弁封 ４゛川勝男隔ニノ□
！ｆ−１図Figure 1 is a diagram showing the relationship between the change in Cr concentration near grain boundaries due to irradiation of the steel of the present invention and the comparative steel, and Figure 2 is a cross-section of a BWR reactor internal structure fabricated using the steel of the present invention. It is a diagram. 1... Neutron source pipe, 2... Upper grid plate, 3...
・Neutron instrumentation tube, 4...control rod.
7.7.0 Benfu 4゛Katsuo Kawa Nino□! f-1 diagram
Claims (1)
、Ｍｎ２％以下、Ｃｒ１５〜１８％、Ｎｉ８〜１５％、
ＭｏＯ〜３％と、Ｔｉ０．４％を越え０．５％未満、Ｚ
ｒ０．２％を越え０．９％未満及びＨｆ０．２％を越え
１．７％未満の少なくとも１種とを含み、Ｔｉ、Ｚｒ及
びＨｆが下記の式の範囲内であることを特徴とする耐照
射性オーステナイトステンレス鋼。 ０．２＜Ｔｉ＋（Ｚｒ／１．９）＋（Ｈｆ／３．７）＜
０．５２、特許請求の範囲第１項において、重量比で０
．００１〜０．１％のＮを含有することを特徴とする耐
照射性オーステナイトステンレス鋼。[Claims] 1. By weight: C 0.001 to 0.03%, Si 1% or less, Mn 2% or less, Cr 15 to 18%, Ni 8 to 15%,
MoO ~ 3%, Ti over 0.4% and less than 0.5%, Z
It is characterized by containing at least one of r more than 0.2% and less than 0.9% and Hf more than 0.2% and less than 1.7%, and Ti, Zr and Hf are within the range of the following formula. Irradiation resistant austenitic stainless steel. 0.2<Ti+(Zr/1.9)+(Hf/3.7)<
0.52, in claim 1, the weight ratio is 0.
．． An irradiation-resistant austenitic stainless steel characterized by containing 0.001 to 0.1% of N.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6423290A JPH03267350A (en) | 1990-03-16 | 1990-03-16 | Irradiation resisting austenitic stainless steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6423290A JPH03267350A (en) | 1990-03-16 | 1990-03-16 | Irradiation resisting austenitic stainless steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH03267350A true JPH03267350A (en) | 1991-11-28 |
Family
ID=13252172
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6423290A Pending JPH03267350A (en) | 1990-03-16 | 1990-03-16 | Irradiation resisting austenitic stainless steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH03267350A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1715071A1 (en) * | 2004-01-13 | 2006-10-25 | Mitsubishi Heavy Industries, Ltd. | Austenitic stainless steel, method for producing same and structure using same |
-
1990
- 1990-03-16 JP JP6423290A patent/JPH03267350A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1715071A1 (en) * | 2004-01-13 | 2006-10-25 | Mitsubishi Heavy Industries, Ltd. | Austenitic stainless steel, method for producing same and structure using same |
| EP1715071A4 (en) * | 2004-01-13 | 2007-08-29 | Mitsubishi Heavy Ind Ltd | Austenitic stainless steel, method for producing same and structure using same |
| US8172959B2 (en) | 2004-01-13 | 2012-05-08 | Mitsubishi Heavy Industries, Ltd. | Austenitic stainless steel, manufacturing method for the same, and structure using the same |
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