JPH02225648A - High strength oxide dispersion strengthened ferritic steel - Google Patents
High strength oxide dispersion strengthened ferritic steelInfo
- Publication number
- JPH02225648A JPH02225648A JP4380989A JP4380989A JPH02225648A JP H02225648 A JPH02225648 A JP H02225648A JP 4380989 A JP4380989 A JP 4380989A JP 4380989 A JP4380989 A JP 4380989A JP H02225648 A JPH02225648 A JP H02225648A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- oxide dispersion
- dispersion strengthened
- strength
- powder
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 50
- 239000010959 steel Substances 0.000 title claims abstract description 50
- 229910001175 oxide dispersion-strengthened alloy Inorganic materials 0.000 title claims abstract description 23
- 239000012535 impurity Substances 0.000 claims abstract description 10
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 229910052721 tungsten Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 2
- 239000000843 powder Substances 0.000 abstract description 13
- 239000000203 mixture Substances 0.000 abstract description 8
- 230000007704 transition Effects 0.000 abstract description 7
- 229910045601 alloy Inorganic materials 0.000 abstract description 5
- 239000000956 alloy Substances 0.000 abstract description 5
- 229910052804 chromium Inorganic materials 0.000 abstract description 4
- 239000002994 raw material Substances 0.000 abstract description 4
- 239000002775 capsule Substances 0.000 abstract description 3
- 229910000734 martensite Inorganic materials 0.000 abstract description 3
- 238000005242 forging Methods 0.000 abstract description 2
- 238000005551 mechanical alloying Methods 0.000 abstract description 2
- 238000004663 powder metallurgy Methods 0.000 abstract description 2
- 238000005496 tempering Methods 0.000 abstract description 2
- 230000009466 transformation Effects 0.000 abstract description 2
- 230000007547 defect Effects 0.000 abstract 1
- 238000000034 method Methods 0.000 abstract 1
- 238000007789 sealing Methods 0.000 abstract 1
- 239000000126 substance Substances 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 11
- 229910000859 α-Fe Inorganic materials 0.000 description 9
- 239000011162 core material Substances 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 238000009864 tensile test Methods 0.000 description 4
- 241000473391 Archosargus rhomboidalis Species 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 238000010622 cold drawing Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 239000006185 dispersion Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000005253 cladding Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000003628 erosive effect Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000009689 gas atomisation Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- DKSXWSAKLYQPQE-UHFFFAOYSA-K neodymium(3+);triiodide Chemical compound I[Nd](I)I DKSXWSAKLYQPQE-UHFFFAOYSA-K 0.000 description 1
- 239000003758 nuclear fuel Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 230000008961 swelling Effects 0.000 description 1
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
この発明は、高温強度の高いフェライト系の酸化物分散
強化型鋼であって、特に原子炉の炉心材料として好適な
澗に関するものである。DETAILED DESCRIPTION OF THE INVENTION (Industrial Application Field) The present invention relates to a ferrite-based oxide dispersion strengthened steel with high high temperature strength, and in particular to oak, which is suitable as a core material for a nuclear reactor.
（従来の技術）
フェライト系の鋼は、オーステナイト系の鋼に比較して
中性子照射を受けた場合の耐スエリング性に優れている
ため、原子炉、特に高速増殖炉の炉心材料として注目さ
れている。しかしながら、一般にフェライト鋼は、オー
ステナイト鋼に比べて高温強度が低い、この高温強度を
高めたフェライト鋼として、例えば、特開昭６０−８２
９６号公報に開示されているような酸化物分散強化型フ
エライトがある。(Conventional technology) Ferritic steel is attracting attention as a core material for nuclear reactors, especially fast breeder reactors, because it has superior swelling resistance when exposed to neutron irradiation compared to austenitic steel. . However, ferritic steel generally has lower high-temperature strength than austenitic steel.
There is an oxide dispersion strengthened ferrite as disclosed in Japanese Patent No. 96.
上記の酸化物分散強化型フェライト鋼は、オーステナイ
ト調を凌ぐ高温強度をもつが、次のような難点がある。The above-mentioned oxide dispersion strengthened ferritic steel has high-temperature strength superior to austenitic steel, but has the following drawbacks.
即ち、この種の鋼は、高温引張において６５０°Ｃ付近
に延性のピークを持ち、それ以上の温度では逆に延性が
低下する。これは、酸化物分散強化型合金では、粒内強
度が極めて高いために低延性の破壊が粒界で起きるから
であると考えられる。上記のような校内破壊−粒界破壊
のモードは、歪速度依存性をもち、歪速度が大きい場合
には粒界破壊から粒内破壊に移る遷移温度は高温側にあ
るが、クリープのように歪速度が極めて小さい場合には
低温側に移行する。この遷移温度が、原子炉の炉心材料
などの使用温度（およそ６５０″Ｃ）付近にあるため、
この温度域でのクリープｉ度が安定しないということに
なる。That is, this type of steel has a ductility peak around 650° C. under high-temperature tension, and the ductility decreases at temperatures higher than that. This is thought to be because in oxide dispersion strengthened alloys, fractures with low ductility occur at grain boundaries due to extremely high intragranular strength. The intergranular fracture-grain boundary fracture mode described above is strain rate dependent, and when the strain rate is large, the transition temperature from intergranular fracture to intragranular fracture is on the high temperature side, but as with creep, When the strain rate is extremely small, the temperature shifts to the low temperature side. Since this transition temperature is near the operating temperature of nuclear reactor core materials (approximately 650"C),
This means that the creep i degree is not stable in this temperature range.
更に、酸化物分散強化型フェライト鋼は、室温延性が低
いという難点もある。そのため、原子炉の燃料被覆管等
で寸法精度を出すために必須の冷間抽伸が難しい。Furthermore, oxide dispersion strengthened ferritic steel also has the disadvantage of low room temperature ductility. Therefore, cold drawing, which is essential for achieving dimensional accuracy in nuclear reactor fuel cladding tubes, etc., is difficult.
（発明が解決しようとする課Ｂ）
酸化物分散強化型フェライト鋼の粒内−粒界破壊遷移温
度は、その使用目的温度の６５０°Ｃ付近にある。この
ことは、使用温度でのクリープ強度が不安定であること
を意味し、例えば、原子炉の炉心材料として用いるとき
に、設計基準の策定に困難を来す、さらに、酸化物分散
強化型フェライト鋼の室温延性の低さは、前記のように
冷間抽伸の困難を招き製品製造上の問題を生じている。(Problem B to be Solved by the Invention) The transgranular-intergranular fracture transition temperature of oxide dispersion strengthened ferritic steel is around 650°C, which is the intended use temperature. This means that the creep strength of ferrite is unstable at the operating temperature, making it difficult to formulate design standards when used as a core material for nuclear reactors. As mentioned above, the low room temperature ductility of steel makes cold drawing difficult and causes problems in product manufacturing.
本発明は、元来高温強度の高い酸化物分散強化型フェラ
イト鋼について、その高温強度をさらに高めるとともに
、使用目的温度域でのクリープ強度の安定化と、室温延
性を向」二させることを課題とするものである。The present invention aims to further increase the high-temperature strength of oxide dispersion-strengthened ferritic steel, which originally has high high-temperature strength, as well as to stabilize creep strength in the intended use temperature range and improve room-temperature ductility. That is.
（課題を解決するための手段）
本発明者らは、上記の課題を解決する手段として、酸化
物分散強化型フェライト鯛の粒界の強化が最も有効であ
ると考えた。そこで、本来の高い高温強度を維持しつつ
、粒界強度を高める成分系を追求し、下記の組成をもつ
フェライ）ＩＩが最も目的に適うことをｆｌｌｌＷした
。(Means for Solving the Problems) The present inventors believed that strengthening the grain boundaries of oxide dispersion-strengthened ferrite sea bream is the most effective means for solving the above problems. Therefore, we sought a component system that would increase the grain boundary strength while maintaining the original high temperature strength, and found that Ferrai) II having the following composition was most suitable for the purpose.
本発明の要旨は、
Φ Ｍ１％で、１２゜５％から２５％までのＣｒと、０
．２％から２％までのＴｉと、０．０５％から２％まで
のＹ！０．と、０．００３％から０．０２％までのＢと
を含有し、残部がＦｅおよび不純物からなる高強度酸化
物分散強化型フェライト鋼、にあり、また、
■ 上記■の成分に加えて、それぞれ２％から４％まで
のＮｏとＷの少なくとも一方を含む高強度酸化物分散強
化型フェライト鋼、
■ 上記■の成分に加えて、２％までのＮｉを含有する
高強度酸化物分散強化型フェライト爛、■ 上記■の成
分に加えて、それぞれ２％から４％までのＦＩｏとＷの
少なくとも一方と、２％までのＮｉを含有する高強度酸
化物分散強化型フェライト鋼、にある。The gist of the present invention is that Φ M1%, Cr from 12°5% to 25%, and 0
．． Ti from 2% to 2% and Y from 0.05% to 2%! 0. and 0.003% to 0.02% of B, with the balance consisting of Fe and impurities, and ■ In addition to the ingredients in ■ above, High-strength oxide dispersion-strengthened ferritic steel containing at least one of 2% to 4% of No and W, ■ High-strength oxide dispersion-strengthened steel containing up to 2% of Ni in addition to the components of ■ above. Ferrite erosion, (1) A high-strength oxide dispersion-strengthened ferritic steel containing, in addition to the components (2) above, at least one of FIo and W, each from 2% to 4%, and up to 2% Ni.
上記本発明鋼の不純物としては、約０．２％以下のＣ１
約１．０％以下のｓｉ、約１．０％以下のＦｇｎなどが
ある。なお、本明細書において、成分含有量についての
％は全て重量％を意味する。The impurities in the steel of the present invention include about 0.2% or less of C1.
Examples include si of about 1.0% or less and Fgn of about 1.0% or less. In addition, in this specification, all % regarding component content means weight %.
（作用）
以下、本発明鋼の構成成分の含有量の限定理由をその作
用効果とともに説明する。(Function) Hereinafter, the reason for limiting the content of the constituent components of the steel of the present invention will be explained together with its function and effect.
ｃｒは、鋼の組織をフェライトにし、耐食性、耐酸化性
を与える必須の成分である。耐食性確保のために１２．
５％以上が必要である。しかし、２５％を趙えると延性
が劣化するため、上限は２５％までとする。Cr is an essential component that makes the steel structure ferrite and provides corrosion resistance and oxidation resistance. 12. To ensure corrosion resistance.
5% or more is required. However, the upper limit is set to 25% because the ductility deteriorates if the tensile strength exceeds 25%.
Ｔｉは、Ｔ８０．との相互作用によって複酸化物を生成
し、またＹ、０．を微細化する元素で、分散強化による
高強度化に有効である。しかし、その含有量が０．２％
未満では長時間側でのクリープ強度向上の効果が乏しい
ため０．２％以上含有させる必要がある。一方、τｌの
含有量が２％を趙えると延性が低下する。Ti is T80. A double oxide is produced by interaction with Y, 0. It is an element that makes steel fine, and is effective in increasing strength through dispersion strengthening. However, its content is 0.2%
If it is less than 0.2%, the effect of improving creep strength over a long period of time is poor, so it is necessary to contain it in an amount of 0.2% or more. On the other hand, when the content of τl exceeds 2%, the ductility decreases.
ＹｔＯｓは、分散強化の作用を担う重要な成分である。YtOs is an important component responsible for dispersion strengthening.
即ち、基地中に均一に分散して高温強度を高める。 ０
．０５％未満ではクリープ強度が不安定であるからその
含有量は０．０５％以上とするのがよい。That is, it is uniformly dispersed in the matrix and increases high-temperature strength. 0
．． If the content is less than 0.05%, the creep strength is unstable, so the content is preferably 0.05% or more.
一方、２％を趨える含有量になると、強度向上の効果は
飽和し、延性を低下させる好ましくない作用が現れる。On the other hand, when the content exceeds 2%, the effect of improving strength is saturated and an undesirable effect of reducing ductility appears.
Ｂは、本発明鋼を特徴づけるものの一つで、鋼の粒界強
化の作用をもつ、即ち、Ｂは粒界に偏析して、粒界の強
度を高め、酸化物分散強化型鋼の特徴である粒界−粒内
破壊遷移温度を上昇させる。B is one of the characteristics of the steel of the present invention, and has the effect of strengthening the grain boundaries of the steel. In other words, B segregates at the grain boundaries, increases the strength of the grain boundaries, and is a characteristic of oxide dispersion strengthened steel. Increase a certain grain boundary-transgranular fracture transition temperature.
このような作用は、０．００３％未満では不十分である
。しかし、０．０２％を超えて含有させても、それ以」
−の効果はない。Such an effect is insufficient at less than 0.003%. However, even if the content exceeds 0.02%,
− has no effect.
ｌｉｏとＷは、鋼の基地に固溶して粒内強度を向上させ
るだけでなく、粒界強度の向上にも役立つ。Lio and W not only improve the intragranular strength by forming a solid solution in the steel matrix, but also help improve the grain boundary strength.
このような効果を期待する場合、それぞれ２％以上、４
％までの範囲で、一方または両方を含有させることがで
きる。それぞれ４％を趙えると金属間化合物の析出が多
くなり靭性が劣化する弊害がある。If such an effect is expected, 2% or more and 4%, respectively.
% of one or both. If each content is 4%, the precipitation of intermetallic compounds increases, which has the disadvantage of deteriorating toughness.
Ｎｉは、オーステナイト相を安定化させる成分であり、
その添加によって広義のフェライトｌｌ（フェライト士
マルテンサイトの２相綱）の製造を容易にする。しかし
、Ｎｉは、中性子照射で誘導放射能を帯びるので、原子
炉の炉心材料としては、その含有量は２％以下に止める
のがよい。Ni is a component that stabilizes the austenite phase,
Its addition facilitates the production of ferrite II in a broad sense (a two-phase class of ferrite and martensite). However, since Ni takes on induced radioactivity when irradiated with neutrons, its content should be kept at 2% or less when used as a core material for a nuclear reactor.
綱に通常含有されているＣは、Ｎｉと同様の作用をもつ
が、０．２％以下に抑えるのがよい、ＳｌおよびＭｎも
中性子照射で誘導放射能を帯びるので、少ない方がよい
、許容上限値はそれぞれ１．０％である。C, which is normally contained in steel, has the same effect as Ni, but it is best to keep it below 0.2%. Sl and Mn also take on induced radioactivity when irradiated with neutrons, so the less the better, the more acceptable. The upper limit values are each 1.0%.
本発明の分散強化型フェライト綱は、粉末冶金法で製造
される。その概略を説明すれば下記のとおりである。The dispersion-strengthened ferritic steel of the present invention is manufactured by powder metallurgy. The outline is as follows.
原料としては、Ｙ＊Ｏｓを除くベース組成の合金粉末（
例えばガスアトマイズ粉末）にＹ、０．粉末を混合する
か、または、Ｆｅ、 Ｃｒ、 Ｔｉなどの純金属粉末と
Ｙ！島粉末を前記の組成になるように配合して混合し、
機械的合金化（Ｍｅｃｈａｎｉｃａｌ Ａｌｌｏｙｉｎ
ｇ）を行わせたものを用いる。この合金化には、通常の
ボールミルも使用できるが、高エネルギーのアトライタ
ーを用いるのが望ましい、こうして得た原料粉末をカプ
セルに入れ、脱気封入し、熱間押出し、＋１１Ｐ鍛造な
どで成形する。成形温度は１１００〜９００°Ｃが望ま
しい。As a raw material, alloy powder with a base composition excluding Y*Os (
For example, gas atomized powder) with Y, 0. Mix powders or mix Y! with pure metal powders such as Fe, Cr, Ti, etc. Blend and mix the island powder to the above composition,
Mechanical Alloyin
g) is used. Although a normal ball mill can be used for this alloying, it is preferable to use a high-energy attritor.The raw material powder obtained in this way is put into a capsule, degassed and sealed, and then formed by hot extrusion, +11P forging, etc. . The molding temperature is preferably 1100 to 900°C.
熱処理は、フェライト単相鋼では１１００−１０００℃
での溶体化、マルテンサイト相を含む鯛の場合は１１０
０〜１０００°Ｃでの溶体化と＾ｃ、変態点以下での焼
戻しを行う。Heat treatment is 1100-1000℃ for ferritic single phase steel.
110 for sea bream containing martensitic phase.
Solution treatment at 0 to 1000°C and tempering at a temperature below the transformation point are performed.
（実施例）
下記の工程で第１表に示す２６種類の合金の試験片を作
成し、高温引張試験とクリープ試験を実施した。(Example) Test pieces of 26 types of alloys shown in Table 1 were prepared using the following steps, and a high temperature tensile test and a creep test were conducted.
■ 平均粒２ｚ＋ｓｏμ■のアルゴンガスアトマイズ法
によって製造した母合金粉末に、Ｙ２Ｏ，の粉末（平均
粒径０．０２μｍ）を添加してアトライターで機械的合
金化を行った。アトライターの回転数は２９０ｒｐｍと
し、処理時間は４８時間とした。(2) Y2O powder (average particle size: 0.02 μm) was added to a master alloy powder produced by argon gas atomization with an average particle size of 2z+soμ■, and mechanical alloying was performed using an attritor. The rotation speed of the attritor was 290 rpm, and the treatment time was 48 hours.
■ 得られた合金粉末を軟鋼製カプセル（６７１−径）
に充填して脱気したのち、１１００℃に加熱して押出し
加工によって３０−―φの丸棒とした。■ Put the obtained alloy powder into a mild steel capsule (671-diameter)
After filling and deaerating it, it was heated to 1100°C and extruded into a 30-φ round bar.
■ 上記の丸棒を１１００℃で熱間圧延して７謹磐厚の
板とし、＋１００°Ｃで溶体化処理を行った。(2) The above round bar was hot-rolled at 1100°C to form a 7-inch thick plate, which was then solution-treated at +100°C.
■ 溶体化後の板から、２■−厚Ｘ ６ｍｄｉｉＸ３（
１ｗｍＧＬの板状引張試験片を採取し、室温、６００
’Ｃ１６５０°Ｃ１７００°Ｃおよび８００℃での引張
試験と、６５０℃でのクリープ破断試験を行った。■ From the plate after solution treatment, 2■ - thickness x 6mdii x 3 (
A plate-shaped tensile test piece of 1wmGL was taken and heated at room temperature at 600°C.
Tensile tests at 1650°C, 1700°C and 800°C and creep rupture tests at 650°C were conducted.
第１表中に、室温での延性、高温引張試験による延性ピ
ーク温度、および６５０ ’ＣＸ １０’時間のクリー
プ破断強度を併記する。In Table 1, the ductility at room temperature, the ductility peak temperature by high temperature tensile test, and the creep rupture strength at 650'CX 10' hours are also listed.
第１表に見られるとおり、Ｂを０．００３％以上含有す
る本発明の鋼では、すべての延性ピーク温度が７００℃
以上にある。Ｂを添加していない比較鋼（８１１１７１
のそれが６５０°Ｃであることと対照してみれば、Ｂの
添加によって遷移温度が５０゛Ｃ以上高くなっているこ
とが明らかである。As seen in Table 1, in the steel of the present invention containing 0.003% or more of B, all ductility peak temperatures are 700°C.
That's all for now. Comparative steel without B addition (811171
When contrasted with that of 650°C, it is clear that the addition of B increases the transition temperature by more than 50°C.
第１図は、上記のクリープ破Ｉｆ試験の結果から、１３
Ｃｒ−１Ｔｉ ０．２９ＹｘＯｘ系の鋼のＢの含有量
と、６５０’ＣＸｌ０’時間のクリープ破断強度との関
係を図にしたものである１図示のとおり、Ｂの含有量が
０．００３％以上でクリープ破断強度が著しく大きくな
っている。この結果から、Ｂの含有量を０．００３％以
上とするのが望ましいことが明らかである。Figure 1 shows that 13
Figure 1 shows the relationship between the B content of Cr-1Ti 0.29YxOx steel and the creep rupture strength at 650'CX10' hours.As shown in the figure, the B content is 0.003% or more. The creep rupture strength is significantly increased. From this result, it is clear that it is desirable that the B content be 0.003% or more.
第１表の石２と阻１９、Ｎｌ１８と麹２４は、それぞれ
ＡＰの添加の影響をみたものである。いずれの場合もＡ
ｔを含有しないものの方がクリープ強度が高くなってい
る。この結果から、＾ｌの添加をしない方が望ましいと
いえる。Table 1 shows the effects of AP addition on Ishi 2, Ike 19, Nl 18, and Koji 24. In either case A
The material not containing t has higher creep strength. From this result, it can be said that it is preferable not to add ^l.
第２図は、第１表の本発明鋼と比較鋼の室温での延性と
、６５０℃×１０３時間のクリープ破断強度との関係を
まとめたものである０図示のとおり、本発明鋼はクリー
プ強度が高いだけでなく、優れた室ｎａｇ性も備えてい
る。これに対し、比較鋼はクリープ強度が全般に低く、
Ｎｉ１２２．２５のようにクリープ強度が比較的高いも
のは室温延性が著しく劣る。なお、本発明鋼のＮｄＩ３
．１５、】６は、ｙｊｏ、を高めにしてＭｏ、 Ｗを添
加したもので、掻めて高いクリープ強度が得られている
。Figure 2 summarizes the relationship between the ductility at room temperature and the creep rupture strength at 650°C x 103 hours for the inventive steel and comparative steel in Table 1. It not only has high strength but also has excellent indoor nag properties. On the other hand, the creep strength of comparative steels is generally low;
Materials with relatively high creep strength, such as Ni122.25, have significantly poor room temperature ductility. In addition, NdI3 of the steel of the present invention
．． 15,]6 has a high yjo and has Mo and W added thereto, and has a significantly high creep strength.
（以下、余白）
（発明の効果）
本発明は、従来の酸化物分散強化型鋼に特有の粒内−粒
界破壊遷移温度の低い欠点を解消し、併せて高温強度も
向上させたフェライト系の酸化物分散強化型鋼を提供す
るものである。この鯛は、フェライト調本来の優れた耐
久エリングを生かし、特に原子炉の炉心材料に用いて極
めて有用なものである。(Hereinafter, blank spaces) (Effects of the invention) The present invention solves the drawback of low transgranular-intergranular fracture transition temperature characteristic of conventional oxide dispersion strengthened steels, and also improves high-temperature strength. The present invention provides an oxide dispersion strengthened steel. This sea bream takes advantage of the excellent durability inherent to ferrite, making it extremely useful especially for use as a core material for nuclear reactors.
第１図は、１３Ｃｒ ｌ Ｔｉ ０．２９ＹｚＯｓ
系の鋼のＢの含有量と、６５０℃ＸｌＯ’Ｑ間のクリー
プ破断強度との関係を示すものである。
第２図は、本発明鋼と比較鋼の室温での延性と、６５０
℃×１０３時間のクリープ破断強度との関係を示すもの
である。Figure 1 shows 13Cr l Ti 0.29YzOs
It shows the relationship between the B content of the system steel and the creep rupture strength at 650°C XlO'Q. Figure 2 shows the ductility at room temperature of the inventive steel and comparative steel, and the 650
It shows the relationship between creep rupture strength at ℃×103 hours.
Claims (4)
０．２％から２％までのＴｉと、０．０５％から２％ま
でのＹ＿２Ｏ＿３と、０．００３％から０．０２％まで
のＢとを含有し、残部がＦｅおよび不純物からなる高強
度酸化物分散強化型フェライト鋼。(1) Cr from 12.5% to 25% by weight;
High strength containing 0.2% to 2% Ti, 0.05% to 2% Y_2O_3, 0.003% to 0.02% B, with the balance consisting of Fe and impurities. Oxide dispersion strengthened ferritic steel.
０．２％から２％までのＴｉと、０．０５％から２％ま
でのＹ＿２Ｏ＿３と、０．００３％から０．０２％まで
のＢと、更にそれぞれ２％から４％までのＭｏとＷの少
なくとも一方を含有し、残部がＦｅおよび不純物からな
る高強度酸化物分散強化型フェライト鋼。(2) Cr from 12.5% to 25% by weight;
Ti from 0.2% to 2%, Y_2O_3 from 0.05% to 2%, B from 0.003% to 0.02%, and Mo and W from 2% to 4% each. A high-strength oxide dispersion-strengthened ferritic steel containing at least one of the following, with the remainder consisting of Fe and impurities.
０．２％から２％までのＴｉと、０．０５％から２％ま
でのＹ＿２Ｏ＿３と、０．００３％から０．０２％まで
のＢと、２％以下のＮｉを含有し、残部がＦｅおよび不
純物からなる高強度酸化物分散強化型フェライト鋼。(3) Cr from 12.5% to 25% by weight;
Contains 0.2% to 2% Ti, 0.05% to 2% Y_2O_3, 0.003% to 0.02% B, 2% or less Ni, and the balance is Fe. High-strength oxide dispersion-strengthened ferritic steel consisting of impurities and impurities.
０．２％から２％までのＴｉと、０．０５％から２％ま
でのＹ＿２Ｏ＿３と、０．００３％から０．０２％まで
のＢと、２％以下のＮｉと、更にそれぞれ２％から４％
までのＭｏとＷの少なくとも一方を含有し、残部がＦｅ
および不純物からなる高強度酸化物分散強化型フェライ
ト鋼。(4) Cr from 12.5% to 25% by weight;
Ti from 0.2% to 2%, Y_2O_3 from 0.05% to 2%, B from 0.003% to 0.02%, Ni below 2%, and further from 2% each. 4%
contains at least one of Mo and W, with the remainder being Fe.
High-strength oxide dispersion-strengthened ferritic steel consisting of impurities and impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4380989A JPH02225648A (en) | 1989-02-23 | 1989-02-23 | High strength oxide dispersion strengthened ferritic steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP4380989A JPH02225648A (en) | 1989-02-23 | 1989-02-23 | High strength oxide dispersion strengthened ferritic steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02225648A true JPH02225648A (en) | 1990-09-07 |
Family
ID=12674072
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP4380989A Pending JPH02225648A (en) | 1989-02-23 | 1989-02-23 | High strength oxide dispersion strengthened ferritic steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02225648A (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0551701A (en) * | 1991-08-27 | 1993-03-02 | Nippon Steel Corp | Oxide disperion strengthened ferritic heat resisting steel plate |
| FR2777020A1 (en) * | 1998-04-07 | 1999-10-08 | Commissariat Energie Atomique | PROCESS FOR THE MANUFACTURE OF A FERRITIC - MARTENSITIC ALLOY REINFORCED BY OXIDE DISPERSION |
| US20150252458A1 (en) * | 2014-03-05 | 2015-09-10 | Korea Atomic Energy Research Institute | Ferritic/martensitic oxide dispersion strengthened steel with enhanced creep resistance and method of manufacturing the same |
| CN106834883A (en) * | 2017-02-20 | 2017-06-13 | 天津大学 | A kind of method of residual ferrite and martensite lath structure in control 9Cr ODS steel |
| CN106834882A (en) * | 2017-02-20 | 2017-06-13 | 天津大学 | The method of residual ferrite distribution in austenite phase transformation area isothermal holding control 9Cr ODS steel |
| CN107058852A (en) * | 2017-02-20 | 2017-08-18 | 天津大学 | A kind of method for refining residual ferrite in oxide dispersion intensifying martensite steel |
| CN110343935A (en) * | 2019-07-11 | 2019-10-18 | 中国科学院金属研究所 | Oxide dispersion strengthening ferrite steel is prepared using surface oxidation+explosive compaction |
| CN111979469A (en) * | 2020-07-31 | 2020-11-24 | 青岛理工大学 | Preparation method of oxide dispersion strengthened steel based on powder forging |
-
1989
- 1989-02-23 JP JP4380989A patent/JPH02225648A/en active Pending
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0551701A (en) * | 1991-08-27 | 1993-03-02 | Nippon Steel Corp | Oxide disperion strengthened ferritic heat resisting steel plate |
| FR2777020A1 (en) * | 1998-04-07 | 1999-10-08 | Commissariat Energie Atomique | PROCESS FOR THE MANUFACTURE OF A FERRITIC - MARTENSITIC ALLOY REINFORCED BY OXIDE DISPERSION |
| EP0949346A1 (en) * | 1998-04-07 | 1999-10-13 | Commissariat A L'energie Atomique | Process of producing a dispersion strengthened ferritic-martensitic alloy |
| US6485584B1 (en) | 1998-04-07 | 2002-11-26 | Commissariat A L'energie Atomique | Method of manufacturing a ferritic-martensitic, oxide dispersion strengthened alloy |
| US20150252458A1 (en) * | 2014-03-05 | 2015-09-10 | Korea Atomic Energy Research Institute | Ferritic/martensitic oxide dispersion strengthened steel with enhanced creep resistance and method of manufacturing the same |
| US10011893B2 (en) * | 2014-03-05 | 2018-07-03 | Korea Atomic Energy Research Institute | Ferritic/martensitic oxide dispersion strengthened steel with enhanced creep resistance and method of manufacturing the same |
| CN106834883A (en) * | 2017-02-20 | 2017-06-13 | 天津大学 | A kind of method of residual ferrite and martensite lath structure in control 9Cr ODS steel |
| CN106834882A (en) * | 2017-02-20 | 2017-06-13 | 天津大学 | The method of residual ferrite distribution in austenite phase transformation area isothermal holding control 9Cr ODS steel |
| CN107058852A (en) * | 2017-02-20 | 2017-08-18 | 天津大学 | A kind of method for refining residual ferrite in oxide dispersion intensifying martensite steel |
| CN110343935A (en) * | 2019-07-11 | 2019-10-18 | 中国科学院金属研究所 | Oxide dispersion strengthening ferrite steel is prepared using surface oxidation+explosive compaction |
| CN111979469A (en) * | 2020-07-31 | 2020-11-24 | 青岛理工大学 | Preparation method of oxide dispersion strengthened steel based on powder forging |
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