JPS6289846A - Ferritic or martensitic stainless steel excellent in neutron irradiation embrittlement-resisting property - Google Patents
Ferritic or martensitic stainless steel excellent in neutron irradiation embrittlement-resisting propertyInfo
- Publication number
- JPS6289846A JPS6289846A JP60227658A JP22765885A JPS6289846A JP S6289846 A JPS6289846 A JP S6289846A JP 60227658 A JP60227658 A JP 60227658A JP 22765885 A JP22765885 A JP 22765885A JP S6289846 A JPS6289846 A JP S6289846A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- neutron irradiation
- ferritic
- martensitic stainless
- less
- 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
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 19
- 229910001105 martensitic stainless steel Inorganic materials 0.000 title claims description 13
- 230000000155 isotopic effect Effects 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 229910000831 Steel Inorganic materials 0.000 abstract description 18
- 239000010959 steel Substances 0.000 abstract description 18
- 229910052796 boron Inorganic materials 0.000 abstract description 4
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
- 239000010935 stainless steel Substances 0.000 abstract description 4
- 229910052748 manganese Inorganic materials 0.000 abstract description 3
- 239000002994 raw material Substances 0.000 abstract description 2
- 230000009466 transformation Effects 0.000 abstract description 2
- 230000000694 effects Effects 0.000 description 11
- 239000000463 material Substances 0.000 description 8
- 229910052758 niobium Inorganic materials 0.000 description 8
- 238000010438 heat treatment Methods 0.000 description 7
- 229910052719 titanium Inorganic materials 0.000 description 7
- 238000007670 refining Methods 0.000 description 5
- 229910000734 martensite Inorganic materials 0.000 description 4
- 150000004767 nitrides Chemical class 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000009377 nuclear transmutation Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 238000009877 rendering Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000001784 detoxification Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 230000004992 fission Effects 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 230000002459 sustained effect Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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
- Y02E30/30—Nuclear fission reactors
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、中性子照射を受ける原子炉用構造材料、例え
ば高速増殖炉や軽水炉あるいは核融合炉などの原子炉容
器材料やその周辺材料として使用される耐中性子照射脆
化特性に優れたフェライト系またはマルテンサイト系ス
テンレス鋼に関するものである。Detailed Description of the Invention (Field of Industrial Application) The present invention is applicable to structural materials for nuclear reactors subjected to neutron irradiation, such as reactor vessel materials and peripheral materials for fast breeder reactors, light water reactors, nuclear fusion reactors, etc. The invention relates to ferritic or martensitic stainless steels that have excellent neutron irradiation embrittlement resistance.
（従来の技術）
原子炉用構造材料としては、高温強度と耐食性に優れた
オーステナイト系ステンレス鋼が一般的である。(Prior Art) Austenitic stainless steel, which has excellent high-temperature strength and corrosion resistance, is commonly used as a structural material for nuclear reactors.
最近では、安価で熱膨張係数が小さいフェライト系ステ
ンレス鋼、マルテンサイト系ステンレス鋼も注目を浴び
るに至ってい葛が、これらの材料に共通する問題として
、中性子照射による高温引張り延性の低下やクリープ脆
化が生じることが指摘されている。すなわち、これらの
鋼中には不可避的に混入するか高温特性、強度、加工性
改善のために積極的に添力ｑされたＢが含有されており
、このＢ（粒界に偏在しやすい傾向がある）に起因して
上記の延性低下やクリープ脆化を招くことが判った。Recently, ferritic stainless steel and martensitic stainless steel, which are inexpensive and have a small coefficient of thermal expansion, have attracted attention. It has been pointed out that this phenomenon occurs. In other words, these steels contain B that is either unavoidably mixed in or actively added to improve high-temperature properties, strength, and workability. It was found that this causes the above-mentioned decrease in ductility and creep embrittlement.
すなわち、一般に天然のＢは、同位体の質量数が１０と
１１の２種の同位元素ｒｌ’ＢＪ 、 ｒ”ＢＪによっ
て構成され、その自然存在比はＩＯＢが約２０％、目Ｂ
が約８０％程度である。これらの同位元素のうち、特に
ｔｏＢは熱中性子吸収が太き（、そのため熱中性子照射
を受ける原子炉容器に、Ｂを含有するフェライト系また
はマルテンサイト系ステンレス鋼を用いた場合、比較的
軽度の熱中性子照射でも、１０Ｂ（ｎ 、 ｚ）’Ｌｉ
核反応が生じて、ＩＯＢが崩壊し、その結果Ｈｅガスを
発生させ、そのＨｅが粒界の結合力を弱め、材料の高温
強度や延性の低下を惹起するという問題があった。That is, in general, natural B is composed of two types of isotopes rl'BJ and r''BJ with isotopic mass numbers of 10 and 11, and the natural abundance ratio is about 20% for IOB and 20% for order B.
is about 80%. Among these isotopes, toB has a particularly strong thermal neutron absorption (therefore, if B-containing ferritic or martensitic stainless steel is used in the reactor vessel that receives thermal neutron irradiation, a relatively mild Even with thermal neutron irradiation, 10B(n, z)'Li
A nuclear reaction occurs, the IOB collapses, and as a result, He gas is generated, which causes a problem in that the He weakens the bonding force of the grain boundaries and causes a decrease in the high-temperature strength and ductility of the material.
またＢは積極的に添加しない場合においても通常の製鋼
過程を経て得られたフェライト・マルテンサイト系ステ
ンレス鋼では、少なくとも数ｐｐｍ程度を含有しており
、その程度の微量のＢを含有する場合でも、熱中性子照
射を受ければ前記同様にＩＯＢ （ｎ−α）’Ｌｉ核反
応に起因した中性子照射脆化が生じるおそれがある。Furthermore, even when B is not actively added, ferritic/martensitic stainless steel obtained through the normal steelmaking process contains at least several ppm, and even when B is contained in such a small amount, If it is subjected to thermal neutron irradiation, there is a risk that neutron irradiation embrittlement will occur due to the IOB (n-α)'Li nuclear reaction, as described above.
（発明が解決しようとする問題点）
上述したところから明らかなように、耐中性子照射脆化
を防止するためには、鋼中に存在するＩＯＢを低減する
ことが効果的である。しかしながら、ステンレス鋼にお
いては、Ｂを故意に添加しない場合でも不可避的に２〜
５ ｐｐｍ程度のＢを含有している。(Problems to be Solved by the Invention) As is clear from the above, in order to prevent neutron irradiation embrittlement, it is effective to reduce IOB present in steel. However, in stainless steel, even if B is not intentionally added, 2~
Contains about 5 ppm of B.
この点に関連して本発明者らは、先に特願昭６０−１３
５０７０号と５して提案したように、自然存在比より高
いＪＩＢの量比（”Ｂ／ＣＯＢ＋”Ｂ））を存するＢ含
有原料を用いた脱Ｂ精錬により、ＩＩＩＢを低減するこ
とのできる技術の開発に成功した。In connection with this point, the present inventors previously filed a patent application filed in 1986-13.
As proposed in No. 5070 and No. 5, technology that can reduce IIIB through B-free refining using B-containing raw materials that have a JIB quantitative ratio ("B/COB +" B) higher than the natural abundance ratio. was successfully developed.
しかしながら、実際にはＩＯＢを著しく低減はできても
完全に除くことは困難であるし、ましてコスト的にも不
利はまねかれない。However, in reality, even if IOB can be significantly reduced, it is difficult to completely eliminate it, and even more so, it is not disadvantageous in terms of cost.
要するに本発明の目的は、天然に存在するＢのうち中性
子照射による核変換のためＨｅを生じる１（ＩＢの悪影
響を無くし、中性子照射環境下でも中性子照射脆化を生
じることなく、高温引張延性やクリープ特性にも優れた
フェライト系またはマルテンサイト系ステンレス鋼を提
案することにある。In short, the purpose of the present invention is to eliminate the negative effects of 1 (IB), which generates He due to nuclear transmutation by neutron irradiation among naturally occurring B, and to improve high-temperature tensile ductility without causing neutron embrittlement even in a neutron irradiation environment. Our objective is to propose a ferritic or martensitic stainless steel that also has excellent creep properties.
（問題点を解決するための手段）
上述した問題点解決のために本発明では、Ｂの存在は完
全に無くすことができないということを前程とした上で
その存在を無害化することを自損した。そのためにまず
１°Ｂが少なり１１Ｂの多いボロンを使うことにより粒
界Ｂを低減させること、および場合によってはＴｉまた
はＮｂの少なくとも一種以上をＮとともに添加し、その
際に生じるＴｉ＋Ｎｂの微細な炭・窒化物と一緒にＢを
粒内１粒界に均一かつ微細に析出分散させ、粒界に存在
するＩｏＢを低減させて無害化するようにしたのである
。(Means for Solving the Problems) In order to solve the above-mentioned problems, the present invention assumes that the existence of B cannot be completely eliminated, and that it is necessary to make its existence harmless at its own detriment. did. To achieve this, first, the grain boundary B is reduced by using boron with less 1°B and more 11B, and in some cases, at least one type of Ti or Nb is added together with N, resulting in fine particles of Ti+Nb. B is uniformly and finely precipitated and dispersed at one grain boundary within the grain together with carbon/nitride, thereby reducing IoB existing at the grain boundary and rendering it harmless.
すなわち、本発明は上述の要請に応えられるものとして
、Ｃ： ０．１ ｗｔ％以下、Ｓｉ：１ｗｔ％以下Ｍｎ
：２ｗｔ％以下、Ｃｒ ： １１〜１９ｗｔ％、Ｎｉ：
３ｗｔ％以下、を含有し、同位体の質量数が１１のＢと
同質量数が１０のＢとの比が９以上のＢを０．０００１
〜０．０１ｗｔ％必須成分として含有するもの、
または上記の成分組成に加えて、Ｎ≦０．０５ｗｔ％と
０．Ｏ１〜０．５ ｗｔ％のＴｉもしくは０．０１〜１
．Ｏｗｔ％のＮｂのいずれか１種または２種とを任意成
分として含有し、残部がＦｅおよび不可避的不純物より
なる耐中性子照射脆化特性に優れたフェライト系または
マルテンサイト系ステンレス鋼の開発を実現させたもの
である。That is, the present invention satisfies the above-mentioned requirements, and provides C: 0.1 wt% or less, Si: 1 wt% or less, Mn
: 2wt% or less, Cr: 11-19wt%, Ni:
3wt% or less, and the ratio of B with an isotope mass number of 11 to B with an isotope mass number of 10 is 0.0001
〜0.01 wt% as an essential component, or in addition to the above component composition, N≦0.05 wt% and 0.01 wt%. O1-0.5 wt% Ti or 0.01-1
．． Realized the development of ferritic or martensitic stainless steel with excellent neutron irradiation embrittlement resistance, containing Owt% of any one or two types of Nb as an optional component, and the remainder consisting of Fe and unavoidable impurities. This is what I did.
要するに本発明鋼によれば、粒界１０Ｂを低減させて無
害化することにより、中性子照射により生じる粒界上の
Ｈｅもそれだけ減少するから従来問題となっていた中性
子照射脆化を回避することが可能となる。さらに＋０１
３無害化に加えて、中性子による核変換のおそれのない
ｚＢを積極的に添加することにあわせ、Ｔｉ、 Ｎｂを
Ｎとともに添加することで微細な炭・窒化物を生成させ
ることにより、粒界強化が実現され、クリープ延性、ク
リープ強度の増加、高温強度、高温引張り延性の向上が
達成されるのである。In short, according to the steel of the present invention, by reducing the grain boundaries 10B and rendering them harmless, He on the grain boundaries generated by neutron irradiation is also reduced accordingly, making it possible to avoid neutron irradiation embrittlement, which has been a problem in the past. It becomes possible. Plus +01
3. In addition to detoxification, in addition to actively adding zB, which has no risk of nuclear transmutation by neutrons, Ti and Nb are added together with N to generate fine carbon and nitrides, thereby improving grain boundaries. Strengthening is achieved and increases in creep ductility, creep strength, high temperature strength, and high temperature tensile ductility are achieved.
（作 用）
高温環境下で使用される材料としては、高温引張り延性
や高温強度あるいはクリープ強度やクリープ延性を向上
させるためＢを添加して粒界強化を行うことが望ましい
。その際、中性子照射環境下で使用されてもＨｅガスの
生じないＩＩＢのみを添加できればより望ましいが現実
のフェライト系またはマルテンサイト系ステンレス鋼に
は少なくとも数ｐｐｍ程度の１１１Ｂが含まれる。(Function) For materials used in high-temperature environments, it is desirable to add B to strengthen grain boundaries in order to improve high-temperature tensile ductility, high-temperature strength, creep strength, and creep ductility. At that time, it would be more desirable to add only IIB, which does not generate He gas even when used in a neutron irradiation environment, but actual ferritic or martensitic stainless steel contains at least several ppm of 111B.
そこで、該ステンレス鋼中のＢの挙動について、特にＩ
ＩＢ／ＩＯＢの比を変えた場合の粒界１ＯＢの濃度変化
に着目して研究をすすめた結果、第１図に示すように、
該ＩＩｓ／ＩＱＢが９以上の場合には粒界１ＯＢ濃度が
著しく低減することを見い出した。しかも、ＴｉやＮｂ
の一種以上を含むフェライトマルテンサイト系ステンレ
ス鋼の場合その傾向がより顕著になることも判った。な
お、図の相対的粒界”Ｂ濃度はフィノショントラックエ
ノチング法により求めたものである。Therefore, regarding the behavior of B in the stainless steel, especially I
As a result of conducting research focusing on the concentration change of grain boundary 1OB when changing the IB/IOB ratio, as shown in Figure 1,
It has been found that when the IIs/IQB is 9 or more, the grain boundary 1OB concentration is significantly reduced. Moreover, Ti and Nb
It was also found that this tendency becomes more pronounced in the case of ferritic martensitic stainless steel containing one or more of the following. Note that the relative grain boundary "B" concentration in the figure was determined by the finition track enoching method.
次に本発明鋼についての成分組成限定理由について詳し
く述べる。Next, the reasons for limiting the composition of the steel of the present invention will be described in detail.
Ｂ ： ０．０００１〜０．０１％についてＢは、粒界
強化作用を有し、高温引張り延性やクリープ延性を改善
する作用がある。この効果を発揮するためには、０．０
００１％以上の添加が必要であり、０．０１％以上でも
その効果は期待できるがコスト高を招くので上限を０．
０１％とした。B: 0.0001 to 0.01% B has a grain boundary strengthening effect and has an effect of improving high temperature tensile ductility and creep ductility. To achieve this effect, 0.0
It is necessary to add more than 0.001%, and although the effect can be expected even if it is more than 0.01%, it increases the cost, so the upper limit is set to 0.01% or more.
It was set as 01%.
また、上記ＢについてはＪＩＢ／ＩＯＢの比が９以上を
示すことが必要であることについて既に述べたが、フェ
ライト系又はマルテンサイト系ステンレス鋼、場合によ
ってはＴｉ、Ｎｂ、Ｎの少なくとも１種以上を含有する
フェライト系またはマルテンサイト系ステンレス鋼の場
合、上記の比が９以上で粒界の１０Ｂの相対的な濃度が
著しく低減するからであり、中性子照射脆化のおそれが
なく、高温強度。Regarding B above, it has already been mentioned that it is necessary to have a JIB/IOB ratio of 9 or more. This is because, in the case of ferritic or martensitic stainless steel containing 10B, when the above ratio is 9 or more, the relative concentration of 10B in the grain boundaries is significantly reduced, there is no fear of neutron irradiation embrittlement, and the high-temperature strength is improved.
張り延性およびクリープ特性を改善するのに有効である
。Effective in improving tensile ductility and creep properties.
Ｃ：０．１％以下について
Ｃは、フェライト系またはマルテンサイト系ステンレス
鋼において、引張り強さなどの機械的性質の改善にきわ
めて有効に作用する元素であり、用途にあわせた強度に
なるようにその添加量を調節する。しかし多量の添加は
機械的性質の強化は果されるものの、延性や靭性などの
低下をまねくので、その上限を０．１％とする。C: 0.1% or less C is an element that is extremely effective in improving mechanical properties such as tensile strength in ferritic or martensitic stainless steels, and it can be used to improve the strength of ferritic or martensitic stainless steels. Adjust the amount added. However, if added in large amounts, although mechanical properties may be strengthened, it may lead to a decrease in ductility, toughness, etc., so the upper limit is set at 0.1%.
５ｉｌ１％以下について
Ｓｉは、通常脱酸剤として添加されるが、１％を超える
添加は鋼の熱間加工性を低下させ、製造性を害するので
１％以下にする。Si is usually added as a deoxidizing agent, but addition of more than 1% lowers the hot workability of the steel and impairs manufacturability, so it should be kept at 1% or less.
門ｎ：２％以下について
Ｍｎは、脱酸作用や鋼の熱間加工性を向上させる効果が
あるが、多量の添加は鋼の脆化をもたらす傾向があるの
でその上限を２％とする。Mn: 2% or less Mn has the effect of deoxidizing and improving the hot workability of steel, but addition of a large amount tends to cause embrittlement of steel, so the upper limit is set at 2%.
Ｃｒ：１１〜１９％について
Ｃｒは、１１％未満ではステンレス鋼としての耐食性が
発揮できず、また多量の添加は伸びおよび衝撃値の低下
をまねくので、１１〜１９％とする。Cr: 11 to 19% If Cr is less than 11%, the corrosion resistance of stainless steel cannot be exhibited, and addition of a large amount leads to a decrease in elongation and impact value, so Cr is set to 11 to 19%.
Ｎｉ：３％以下について
Ｎｉは、靭性の向上に効果がある元素であるが、３％を
超えて添加しても効果の持続は認められるとしても高価
な元素であり、コストアップとなるので、上限を３％と
する。Ni: 3% or less Ni is an element that is effective in improving toughness, but even if the effect is sustained even if added in excess of 3%, it is an expensive element and increases costs. The upper limit is set at 3%.
Ｎ ： ０．０５％以下について
Ｎは、それ自身単独でまたは後述のＴｉ、 Ｎｂとの複
合添加により、ＢＮとして析出するか、ＴｉＮ、ＮｂＮ
を核とするＢの窒化物を形成し、Ｂを粒内・外に均一分
散させるのに効果がある。ただその効果を導くにも極く
少量でよく、上限はＢＮが粗大化しない０．０５％が望
ましいので、添加量を０．０５％以下とした。N: For 0.05% or less, N may be precipitated as BN by itself or in combination with Ti and Nb as described below, or may be precipitated as BN or as TiN, NbN.
This is effective in forming a B nitride with B as a nucleus and uniformly dispersing B inside and outside the grain. However, a very small amount is required to achieve this effect, and the upper limit is preferably 0.05% at which BN does not become coarse, so the amount added is set to 0.05% or less.
Ｔｉ ： ０．０１〜０．５％、Ｎｂ ： ０．０１〜
１．０％についてＴｉ、 Ｎｂは、炭化物や窒化物を形
成して微細に分散、析出するが、これがＢの析出核とな
ってＢを粒内、外に均一に微細分散させるのに有効に作
用する。こうした作用は、Ｔｉの場合０．０１％、Ｎｂ
Ｏ場合０．０１％以上の添加は必要である。一方、Ｔｉ
：（１１，５％、Ｎｂ：１％を超える添加は製造性の低
下を招くので、上述のように０．０１−０．５％、０．
Ｏ１〜１．０％に限定する。なお、これらは少なくとも
１種を添加すれば足りる。Ti: 0.01~0.5%, Nb: 0.01~
At 1.0%, Ti and Nb form carbides and nitrides that are finely dispersed and precipitated, but these serve as B precipitation nuclei and are effective in uniformly and finely dispersing B inside and outside the grains. act. These effects are 0.01% for Ti and 0.01% for Nb.
In the case of O, it is necessary to add 0.01% or more. On the other hand, Ti
:(11.5%, Nb: Addition of more than 1% leads to a decrease in productivity, so as mentioned above, 0.01-0.5%, 0.
O is limited to 1-1.0%. Note that it is sufficient to add at least one of these.
本発明鋼の製造、とくに精錬に当っては、脱Ｂ精錬前も
しくは該精錬後のいずれかにＴｉ、 Ｎｂの１種または
２種および＋１３７１０３−≧−９であるＢを添加する
。その後の加熱、圧延、熱処理は常法に従う既知工程を
そのまま利用する。ただし、Ｂを粒内に均一に分散させ
る熱処理として好ましくは、８００〜１０００℃で１分
以上保持することが望ましい。In the production of the steel of the present invention, particularly during refining, one or both of Ti and Nb and B satisfying +137103-≧-9 are added either before or after the B-refining refining. For subsequent heating, rolling, and heat treatment, known processes according to conventional methods are used as they are. However, as a heat treatment for uniformly dispersing B within the grains, it is preferable to hold the temperature at 800 to 1000°C for 1 minute or more.
この熱処理により相変態と再結晶が生じる。すなわち、
フェライトまたはマルテンサイト相よりオーステナイト
相が生じるとともに再結晶が生じ、熱処理前の旧誼界が
新しい粒界におきかわる。このことによりＢが新しい粒
界に対して均一に分散するのである
（実施例）
小型実験炉により、表−１に示す鋼を真空溶製した。本
発明については、その後１１Ｂ／１０１３≧９のフェロ
ボロン合金を投入して脱Ｂ精錬を行って成分調整と鋼塊
鋳造した。その後１２５０”Ｃで加熱後熱間圧延を行い
、２５ｍｍ厚の仮を製造した。この板を焼なまし熱処理
すべく ８００’Ｃ−３０分加熱して急冷した。This heat treatment causes phase transformation and recrystallization. That is,
The austenite phase is generated from the ferrite or martensite phase, recrystallization occurs, and old grain boundaries before heat treatment are replaced by new grain boundaries. This allows B to be uniformly dispersed in new grain boundaries (Example) Steels shown in Table 1 were vacuum melted in a small experimental furnace. In the present invention, a ferroboron alloy of 11B/1013≧9 was then added to perform B-removal refining, component adjustment, and steel ingot casting. Thereafter, hot rolling was carried out after heating at 1250'C to produce a 25 mm thick blank.This plate was heated at 800'C for 30 minutes and rapidly cooled for annealing heat treatment.
かかる熱処理材に対して粒界１ＯＢの存在（有無）クリ
ープ破断強度、同破断伸びを本発明鋼、比較鋼について
求めた。なお、粒界Ｂの存在はフィッショントラックエ
ッチングおよびオージェ分析法によって求めた。その結
果を第２表に示す。この表から判るように、本発明鋼は
Ｂが鋼中に均一に分散しているため、粒界に存在するＩ
ＯＢは検出できない程度に減少しているが、比較例では
粒界に存在するＩＯＢは検出可能な程度に多い。さらに
クリープ破断強度、破断伸びも、本発明鋼は比較鋼に比
べて優れている。For such heat-treated materials, the presence (presence or absence) of grain boundaries 1OB, creep rupture strength, and creep rupture elongation were determined for the inventive steel and comparative steel. The presence of grain boundaries B was determined by fission track etching and Auger analysis. The results are shown in Table 2. As can be seen from this table, in the steel of the present invention, since B is uniformly dispersed in the steel, I
Although the number of OBs has decreased to an undetectable level, in the comparative example, the number of IOBs present at grain boundaries is large enough to be detected. Furthermore, the creep rupture strength and elongation at break of the steel of the present invention are also superior to comparative steels.
表 ２
（発明の効果）
以上説明したように本発明によれば、中性子照射環境下
で使用しても中性子照射脆化を起すことがなく、高温引
張り強度、延性ならびにクリープ特性に優れた原子炉用
構造材料として好適なフェライト系またはマルテンサイ
ト系ステンレス鋼を得ることができる。Table 2 (Effects of the Invention) As explained above, the present invention provides a nuclear reactor that does not cause neutron embrittlement even when used in a neutron irradiation environment and has excellent high-temperature tensile strength, ductility, and creep properties. Ferritic or martensitic stainless steel suitable as a structural material can be obtained.
第１図は、フェライト系またはマルテンサイト系ステン
レス鋼における粒界１０Ｂ濃度に及ぼす１１Ｂ／１０３
比の影響を示すグラフである。Figure 1 shows the effect of 11B/103 on the grain boundary 10B concentration in ferritic or martensitic stainless steel.
It is a graph showing the influence of ratio.
Claims (1)
２ｗｔ％以下、Ｃｒ：１１〜１９ｗｔ％Ｎｉ：３ｗｔ％
以下、 を含有し、さらに同位体の質量数が１１のＢと同質量数
が１０のＢとの比が９以上のＢを０．０００１〜０．０
１ｗｔ％を含有し、残部がＦｅと不可避的不純物とから
なる耐中性子照射脆化特性に優れたフェライト系または
マルテンサイト系ステンレス鋼。 ２、Ｃ：０．１ｗｔ％以下、Ｓｉ：１ｗｔ％以下Ｍｎ：
２ｗｔ％以下、Ｃｒ：１１〜１９ｗｔ％Ｎｉ：３ｗｔ％
以下、 を含有し、同位体の質量数が１１のＢと同質量数が１０
のＢとの比が９以上のＢを０．０００１〜０．０１ｗｔ
％必須成分として含有し、 Ｔｉ：０．０１〜０．５ｗｔ％、もしくは Ｎｂ：０．０１〜１．０ｗｔ％ のいずれか１種または２種、および０．０５ｗｔ％以下
のＮとを任意成分として含有し、残部がＦｅおよび不可
避的不純物よりなる耐中性子照射脆化特性に優れたフェ
ライト系またはマルテンサイト系ステンレス鋼。[Claims] 1. C: 0.1 wt% or less, Si: 1 wt% or less Mn:
2wt% or less, Cr: 11-19wt% Ni: 3wt%
Hereinafter, 0.0001 to 0.0 B containing the following and further having a ratio of B with an isotopic mass number of 11 to B with an isotopic mass number of 10 of 9 or more is used.
A ferritic or martensitic stainless steel with excellent neutron irradiation embrittlement resistance, containing 1 wt% and the remainder consisting of Fe and unavoidable impurities. 2. C: 0.1 wt% or less, Si: 1 wt% or less Mn:
2wt% or less, Cr: 11-19wt% Ni: 3wt%
Hereinafter, the isotopic mass number is 11 and the isotopic mass number is 10.
0.0001 to 0.01wt of B with a ratio of 9 or more to B
% as an essential component, and one or two of Ti: 0.01 to 0.5 wt% or Nb: 0.01 to 1.0 wt%, and 0.05 wt% or less of N as optional components. A ferritic or martensitic stainless steel with excellent neutron irradiation embrittlement resistance, with the balance being Fe and unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60227658A JPS6289846A (en) | 1985-10-15 | 1985-10-15 | Ferritic or martensitic stainless steel excellent in neutron irradiation embrittlement-resisting property |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60227658A JPS6289846A (en) | 1985-10-15 | 1985-10-15 | Ferritic or martensitic stainless steel excellent in neutron irradiation embrittlement-resisting property |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS6289846A true JPS6289846A (en) | 1987-04-24 |
Family
ID=16864309
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60227658A Pending JPS6289846A (en) | 1985-10-15 | 1985-10-15 | Ferritic or martensitic stainless steel excellent in neutron irradiation embrittlement-resisting property |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6289846A (en) |
-
1985
- 1985-10-15 JP JP60227658A patent/JPS6289846A/en active Pending
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US9238857B2 (en) | Precipitation-strengthened Ni-based heat-resistant alloy and method for producing the same | |
| CN103160745B (en) | A kind of Large-tonnage high-Ta low-activation martensitic steel for nuclear fusion reactor and manufacture method thereof | |
| KR101140651B1 (en) | High-Cr ferritic/martensitic steels having an improved creep resistance and preparation method thereof | |
| CN1890758B (en) | Fuel elements for fast neutron reactors (variants) and cladding for the preparation of said elements | |
| US4818485A (en) | Radiation resistant austenitic stainless steel alloys | |
| JPS6013061B2 (en) | High strength ferrite alloy | |
| KR100896988B1 (en) | High chromium ferrite / martensitic steel with improved neutron irradiation stability containing concentrated boron-11 for 4th generation nuclear fission and fusion reactor core parts | |
| US9598750B2 (en) | High Cr ferritic/martensitic steels having an improved creep resistance for in-core component materials in nuclear reactor, and preparation method thereof | |
| EP0174418B1 (en) | Austenitic alloys based on iron-manganese and iron-manganese-chromium | |
| JP2831051B2 (en) | Austenitic stainless steel welding wire | |
| US4622067A (en) | Low activation ferritic alloys | |
| USH326H (en) | Mn-Fe base and Mn-Cr-Fe base austenitic alloys | |
| JPS6289846A (en) | Ferritic or martensitic stainless steel excellent in neutron irradiation embrittlement-resisting property | |
| RU2135623C1 (en) | Low-activated radioresistant steel | |
| JPH0425342B2 (en) | ||
| JPH0248613B2 (en) | ||
| CN119980083B (en) | Non-magnetic stainless steel plate material suitable for ultralow temperature and high strength and toughness at-269 ℃ and manufacturing method thereof | |
| US4361443A (en) | Solid solution strengthened iron-base austenitic alloy | |
| JPS6289845A (en) | Austenitic stainless steel excellent in neutron irradiation embrittlement-resisting property | |
| KR102445585B1 (en) | Low-emission austenitic stainless steel containing tantalum and manufacturing method thereof | |
| JP3481418B2 (en) | Thick steel plate with excellent toughness of weld heat affected zone | |
| CA3105268C (en) | Radiation-resistant austenite steel for in-vessel baffle | |
| US20210269905A1 (en) | Radiation-Resistant Austenitic Steel for an Internal Baffle for Pressurized Water Reactors | |
| CN115125453A (en) | FeCrW-based iron-horse alloy and preparation method and application thereof | |
| JPS6289812A (en) | Manufacture of high chromium steel for nuclear reactor |