JPH08225893A - Austenitic stainless steel for shielding neutron - Google Patents
Austenitic stainless steel for shielding neutronInfo
- Publication number
- JPH08225893A JPH08225893A JP7030613A JP3061395A JPH08225893A JP H08225893 A JPH08225893 A JP H08225893A JP 7030613 A JP7030613 A JP 7030613A JP 3061395 A JP3061395 A JP 3061395A JP H08225893 A JPH08225893 A JP H08225893A
- Authority
- JP
- Japan
- Prior art keywords
- content
- stainless steel
- hot
- austenitic stainless
- corrosion resistance
- 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.)
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Classifications
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- 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
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- Heat Treatment Of Steel (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】この発明は、核燃料輸送用容器、
使用済核燃料保管用ラック等の原子力関連の中性子遮蔽
材として用いられるステンレス鋼に関する。This invention relates to a container for transporting nuclear fuel,
The present invention relates to stainless steel used as a nuclear-related neutron shielding material such as a rack for storing spent nuclear fuel.
【０００２】[0002]
【従来の技術】Ｂ（ほう素）は中性子捕獲断面積が大き
いため、Ｂを含有するオーステナイトステンレス鋼は中
性子の制御材及び遮蔽材として用いられ、例えば特公昭
57-45464号公報に開示されているようなＢを１％前後含
有したSUS304系ステンレス鋼が用いられている。また、
Ｂが(Cr,Fe)2Ｂとして析出して母材中のCr量の低下が起
こり耐食性を劣化させるため、特開昭62−222049号公報
にはCr含有量を高めたＢ含有ステンレス鋼が提案されて
いる。2. Description of the Related Art Since B (boron) has a large neutron capture cross section, austenitic stainless steel containing B is used as a neutron control material and a shielding material.
A SUS304-based stainless steel containing about 1% of B as disclosed in JP-A-57-45464 is used. Also,
Since B is precipitated as (Cr, Fe) 2 B and the amount of Cr in the base material is reduced to deteriorate the corrosion resistance, JP-A-62-222049 discloses a B-containing stainless steel having an increased Cr content. Proposed.
【０００３】しかし、中性子吸収能力を有するＢ含有量
を高くすると前述のごとくＢ化合物が析出するため耐食
性が低下すると共に熱間加工性を著しく損ない、熱間圧
延時に割れが発生するようになる。つまり、熱間圧延に
際しては圧延が進むにつれて板の温度が低下しＢ含有鋼
では耳割れの発生が起こるようになり、歩留まりの低下
や再加熱などの処理が必要となり製造コストの増加につ
ながる。このため、例えば特開昭61−201726号公報には
鉄筒にてＢ含有オーステナイトステンレス鋼を覆った上
で熱間圧延を行う方法が提案されているが、鉄筒で密着
包囲した後圧延や鍛造で圧着させた後熱間圧延を行うた
め多大な工数を要し実用的でない。However, if the B content having a neutron absorbing capacity is increased, the B compound is precipitated as described above, so that the corrosion resistance is lowered and the hot workability is significantly impaired, and cracks are generated during hot rolling. In other words, during hot rolling, the temperature of the plate decreases as the rolling progresses, and ear cracking occurs in the B-containing steel, resulting in a reduction in yield and the need for treatment such as reheating, which leads to an increase in manufacturing cost. For this reason, for example, Japanese Patent Laid-Open No. 61-201726 proposes a method of hot rolling after covering the B-containing austenitic stainless steel with an iron cylinder. Since it is hot-rolled after being pressed by forging, it requires a large number of steps and is not practical.
【０００４】また、Ｂ添加による熱間加工性劣化を回避
するため、Ｂ以外の中性子吸収元素を添加することも提
案されており、例えば特開平5-255812号公報には、Ｂ含
有量を低減しその代わりGdを添加するオーステナイトス
テンレス鋼が、特開平6-192792号公報には、熱間加工性
を向上させるためMgを添加したＢ含有オーステナイトス
テンレス鋼が提案されている。In order to avoid the deterioration of hot workability due to the addition of B, it has been proposed to add a neutron absorbing element other than B. For example, in Japanese Patent Laid-Open No. 5-255812, the B content is reduced. However, Japanese Patent Laid-Open No. 6-192792 proposes a B-containing austenitic stainless steel to which Mg is added to improve hot workability.
【０００５】さらに、近年、保管用ラックの小型化のた
め、素材であるステンレス鋼のさらなる薄肉化が要望さ
れており、より中性子吸収能力の高い鋼材の開発と共
に、大圧下の熱間圧延でも耳割れが発生しない、より熱
間加工性に優れた鋼材の開発が要望されている。Further, in recent years, in order to reduce the size of storage racks, there has been a demand for further thinning of the raw material stainless steel. With the development of steel materials having a higher neutron absorption capacity, even during hot rolling under large pressure, There is a demand for the development of a steel material that is free from cracks and has better hot workability.
【０００６】また、使用済核燃料の水中での保管用ラッ
ク材では水中での耐食性も要求されることから、従来よ
り高耐食性を有するオーステナイトステンレス鋼が必要
となってきている。Further, since a rack material for storing spent nuclear fuel in water is also required to have corrosion resistance in water, austenitic stainless steel having higher corrosion resistance than before has been required.
【０００７】[0007]
【発明が解決しようとする課題】本発明の目的は、中性
子吸収能力が高く、かつ熱間圧延性と耐食性に優れる中
性子遮蔽用オーステナイトステンレス鋼を提供すること
にある。SUMMARY OF THE INVENTION An object of the present invention is to provide a neutron shielding austenitic stainless steel which has a high neutron absorption capacity and is excellent in hot rolling property and corrosion resistance.
【０００８】[0008]
【課題を解決するための手段】Ｂ含有オーステナイトス
テンレス鋼における、Ｂ化合物形成による熱間延性の低
下および耐食性を改善するため、元素の影響を検討した
結果、下記の知見を得、本発明を完成させた。Means for Solving the Problems In order to improve the reduction of hot ductility and the corrosion resistance of B-containing austenitic stainless steel due to the formation of B compounds, the effects of the elements were examined, and the following findings were obtained to complete the present invention. Let
【０００９】一般に、希土類元素は加工性を向上させ
ると言われているが、その中でも中性子吸収元素である
GdにＹを複合添加することにより、それぞれを単独で添
加した場合の熱間延性向上効果を合わせたよりも大幅に
熱間延性が向上する。It is generally said that rare earth elements improve workability, but among them, they are neutron absorbing elements.
By adding Y to Gd in combination, the hot ductility is significantly improved as compared with the effect of improving the hot ductility in the case where each of them is added alone.
【００１０】さらに、Gd、Ｙに加えて希土類元素のTbと
Dyも添加することで、より熱間延性が向上する。Furthermore, in addition to Gd and Y, the rare earth element Tb and
The hot ductility is further improved by adding Dy.
【００１１】Gdは中性子吸収能力を高めるのみでな
く、不働態皮膜を安定化して耐食性を向上させる。さら
に、Ｃ量の低減およびMoの添加により優れた耐食性を得
ることができる。Gd not only enhances the neutron absorption capacity, but also stabilizes the passive film and improves the corrosion resistance. Further, excellent corrosion resistance can be obtained by reducing the amount of C and adding Mo.
【００１２】ここに本発明は、重量％で、Ｃ：0.03％以
下、Ni： 7〜22％、Cr：18〜26％、Mo： 0〜 3.0％、
Ｂ： 0.5〜 2.0％、Gd：0.05〜 1.2％、Ｙ： 0.005〜
0.3％を含有する中性子遮蔽用オーステナイトステンレ
ス鋼である。In the present invention, C: 0.03% or less, Ni: 7-22%, Cr: 18-26%, Mo: 0-3.0% by weight.
B: 0.5-2.0%, Gd: 0.05-1.2%, Y: 0.005-
Austenitic stainless steel for neutron shielding containing 0.3%.
【００１３】上記の鋼に、さらにTbとDyの１種または２
種を合計で 0.005〜 0.1重量％含有させてもよい。In addition to the above steels, one or two of Tb and Dy
The seed may be contained in a total amount of 0.005 to 0.1% by weight.
【００１４】[0014]
【作用】以下に、本発明のオーステナイトステンレス鋼
の化学組成の限定について述べる。なお、以下の「％」
は、「重量％」を意味する。The function of the chemical composition of the austenitic stainless steel of the present invention will be described below. The following "%"
Means "% by weight".
【００１５】Ｃ：0.03％以下 Ｃは溶接時の熱影響によりCr23C6を析出させ、粒界での
耐食性劣化を招くので、その含有量を0.03％以下とす
る。C: 0.03% or less Since C precipitates Cr 23 C 6 due to the heat effect during welding and causes deterioration of corrosion resistance at grain boundaries, its content is 0.03% or less.
【００１６】Ni： 7〜22％ Niはオーステナイト組織の安定化のために必要な元素で
あり 7％以上の含有が必要である。一方、Ni含有量が22
％を超えてもその効果は飽和し、コストアップを招くの
みである。したがって、Ni含有量を 7〜22％とする。Ni: 7 to 22% Ni is an element necessary for stabilizing the austenite structure, and it is necessary to contain 7% or more. On the other hand, the Ni content is 22
Even if it exceeds%, the effect is saturated and only the cost is increased. Therefore, the Ni content is 7 to 22%.
【００１７】Cr：Cr：18〜26％ Crは耐食性を向上させるために必要な元素である。Cr含
有量が18％未満では耐食性が確保できない。また、含有
量が高いほど耐食性は向上するが、26％を超えるとNi含
有量も高くする必要がありコストアップになると共に、
Cr量増加により熱間加工性が劣化する。したがって、Cr
含有量を18〜26％とする。Cr: Cr: 18-26% Cr is an element necessary for improving the corrosion resistance. If the Cr content is less than 18%, corrosion resistance cannot be secured. Also, the higher the content, the higher the corrosion resistance, but if it exceeds 26%, the Ni content also needs to be high, which increases costs and
The hot workability deteriorates as the Cr content increases. Therefore Cr
The content is 18 to 26%.
【００１８】Mo： 0〜 3.0％ Moは耐食性、特に耐隙間腐食性向上に有効な元素であ
り、使用環境に応じて必要により含有させる。含有させ
る場合は、その含有量は 0.1〜 3.0％とする。 0.1％未
満では表面の不働態皮膜が強化されないため耐孔食性の
十分な向上が望めない。一方、 3.0％を超えて含有して
も耐孔食性の向上効果が飽和するだけでなく、熱間加工
性を著しく劣化させる。Mo: 0 to 3.0% Mo is an element effective in improving corrosion resistance, especially crevice corrosion resistance, and is contained if necessary depending on the use environment. When it is contained, its content is 0.1 to 3.0%. If it is less than 0.1%, the passive film on the surface is not strengthened, so that it is not possible to expect a sufficient improvement in pitting corrosion resistance. On the other hand, if the content exceeds 3.0%, not only the effect of improving the pitting corrosion resistance is saturated, but also the hot workability is significantly deteriorated.
【００１９】Ｂ： 0.5〜 2.0％ Ｂは中性子吸収のために必要な元素であり、 0.5％以上
含有させる必要がある。一方、 2.0％を超えると熱間圧
延性が著しく低下する。したがって、Ｂ含有量は 0.5〜
2.0％とする。B: 0.5 to 2.0% B is an element necessary for neutron absorption and must be contained in an amount of 0.5% or more. On the other hand, if it exceeds 2.0%, the hot rolling property is significantly deteriorated. Therefore, the B content is 0.5 to
2.0%
【００２０】Gd：0.05〜 1.2％ Gdは中性子吸収を高めると共に、不働態皮膜を安定化し
耐食性を向上させる。Gd: 0.05 to 1.2% Gd enhances neutron absorption and stabilizes the passive film to improve corrosion resistance.
【００２１】さらに、Ｂ化合物に固溶しＢ化合物自体の
延性を向上させるため、合金の熱間加工性を向上させ
る。Gd含有量が0.05％未満では、中性子吸収効果や耐食
性改善効果が小さく、さらに熱間延性向上効果も小さ
い。一方、 1.2％を超えるとGd−(Fe,Cr,Ni)の低融点共
晶化合物が生成し鍛造ができなくなる。したがって、Gd
含有量は0.05〜 1.2％とする。なお、耐食性確保とＹと
の複合添加による熱間加工性向上には 0.1％以上含有さ
せるのが望ましい。Further, since it forms a solid solution with the B compound to improve the ductility of the B compound itself, the hot workability of the alloy is improved. When the Gd content is less than 0.05%, the neutron absorption effect and the corrosion resistance improving effect are small, and the hot ductility improving effect is small. On the other hand, if it exceeds 1.2%, a low melting point eutectic compound of Gd- (Fe, Cr, Ni) is formed and forging cannot be performed. Therefore, Gd
The content should be 0.05 to 1.2%. In order to secure corrosion resistance and improve hot workability by adding Y together, it is desirable to contain 0.1% or more.
【００２２】Ｙ： 0.005〜 0.3％ Ｙは熱間加工性向上に対して必須の元素である。また、
Ｙ単独で含有する場合には熱間加工性向上効果は小さい
が、Gdと複合添加することにより熱間加工性が著しく向
上する。ＹはGdと同様にＢ化合物に固溶しＢ化合物自体
の延性を向上させる以外に、特に合金中のＳ、Ｏなどの
固定効果が大きいためと考えられる。Y: 0.005-0.3% Y is an essential element for improving hot workability. Also,
When Y alone is contained, the effect of improving hot workability is small, but when added together with Gd, hot workability is significantly improved. It is considered that Y has a large effect of fixing S, O, etc. in the alloy, in addition to improving the ductility of the B compound itself by forming a solid solution with the B compound, similar to Gd.
【００２３】Ｙ含有量が 0.005％未満ではその効果が小
さく、 0.3％を超えた場合は効果が飽和しコストアップ
となる。したがって、Ｙ含有量を 0.005〜 0.3％とす
る。熱間加工性向上効果を顕著にするためには 0.01 ％
以上の含有が望ましい。If the Y content is less than 0.005%, the effect is small, and if it exceeds 0.3%, the effect is saturated and the cost is increased. Therefore, the Y content is set to 0.005 to 0.3%. 0.01% to make the hot workability improvement effect remarkable
The above content is desirable.
【００２４】TbとDyの１種または２種を合計で 0.005〜
0.1 ％ Tb、Dyの１種または２種を合計で 0.005％以上含有する
ことにより熱間加工性をさらに向上できるため、必要に
より含有させる。これらの元素はGdと同様に、Ｂ化合物
の延性を向上させるためと考えられる。一方、 0.1％を
超えた場合はその効果が飽和するため上限を 0.1% とす
る。One or two kinds of Tb and Dy are added in a total amount of 0.005 to
The hot workability can be further improved by containing one or two kinds of 0.1% Tb and Dy in a total amount of 0.005% or more. These elements are considered to improve the ductility of the B compound, similar to Gd. On the other hand, if it exceeds 0.1%, the effect is saturated, so the upper limit is made 0.1%.
【００２５】上記元素以外に一般にステンレス鋼製造に
関わる下記元素の制御により性能向上を達成できる。In addition to the above elements, performance improvement can be achieved by controlling the following elements that are generally involved in stainless steel production.
【００２６】Si、Mn：Si、Mnはいずれも脱酸元素として
有効である。しかし、Si含有量が 1.0％を超えた場合、
Mn含有量が 5.0％超えた場合には、溶接性や清浄度を低
下させる。したがって、含有させる場合には、Si含有量
は0.05〜 1.0％、Mn含有量は 0.5〜 5.0％とするのが望
ましい。Si, Mn: Si and Mn are all effective as deoxidizing elements. However, if the Si content exceeds 1.0%,
If the Mn content exceeds 5.0%, the weldability and cleanliness are reduced. Therefore, when it is contained, it is desirable that the Si content is 0.05 to 1.0% and the Mn content is 0.5 to 5.0%.
【００２７】Al：AlもSi、Mnと同様に脱酸元素として有
効であり、0.05％以上含有させることが望ましい。一
方、 0.5％を超えると合金の清浄度を低下させるため上
限を 0.5％に制限する。Al: Al is also effective as a deoxidizing element like Si and Mn, and it is desirable to contain 0.05% or more. On the other hand, if it exceeds 0.5%, the cleanliness of the alloy decreases, so the upper limit is limited to 0.5%.
【００２８】Mg：Mgの少量を含有することにより熱間鍛
造性が向上する。このため、必要により0.01％以上のMg
を含有させても良い。ただし、 0.1％を超えて含有させ
ても効果が飽和するので上限は 0.1％とする。Mg: The hot forgeability is improved by containing a small amount of Mg. Therefore, if necessary, 0.01% or more Mg
May be contained. However, if the content exceeds 0.1%, the effect will be saturated, so the upper limit is made 0.1%.
【００２９】[0029]
（実施例１）表１に示す化学組成を有する合金を30kg真
空溶解にて製作し、厚み40mmに鍛造後高温延性試験片を
採取した。Ｂ添加鋼の高温延性は特に1000℃以下の温度
が低い領域で問題になることから、 900℃で引張速度 1
/sで引張り試験を行い絞りを測定した。(Example 1) An alloy having the chemical composition shown in Table 1 was manufactured by 30 kg vacuum melting, and after forging to a thickness of 40 mm, a high temperature ductile test piece was sampled. Since the high temperature ductility of B-added steel becomes a problem especially in the low temperature region of 1000 ° C or less, the tensile speed at 900 ° C is 1
A tensile test was performed at / s to measure the aperture.
【００３０】また、同じ材料をさらに熱間圧延、冷間圧
延して厚さ 5mmとした後、固溶化熱処理（1100℃水冷）
を施し、 650℃×2hの鋭敏化処理を行った後、 3mm×20
mm×30mmと 3mm×12mm×30mmの隙間腐食試験片を採取し
た。これらの試験片をテフロンボルトで取り付けメタル
／メタルの隙間を形成させた後、隙間腐食試験に供し
た。隙間腐食試験は3000ppmH3BO4＋ 1000ppmCl- 水溶
液、80℃、空気飽和条件の液中に1000時間浸漬した。The same material was further hot-rolled and cold-rolled to a thickness of 5 mm, and then solution heat treated (1100 ° C. water-cooled).
And sensitizing treatment at 650 ℃ × 2h, then 3mm × 20
mm × 30 mm and 3 mm × 12 mm × 30 mm crevice corrosion test pieces were collected. These test pieces were attached with Teflon bolts to form a metal / metal gap and then subjected to a crevice corrosion test. For the crevice corrosion test, the sample was immersed in a 3000 ppm H 3 BO 4 +1000 ppm Cl − aqueous solution at 80 ° C. in an air saturated condition for 1000 hours.
【００３１】その結果も合わせて表１に示す。なお、試
験結果の絞り比とは、試験後の破断部の径の減少量を試
験前の径で除した値を百分率で示したものである。ま
た、隙間腐食試験での腐食減量は、上記大小二つの試験
片の減量を合計した値であり、単位はmgである。The results are also shown in Table 1. The drawing ratio of the test result is a value obtained by dividing the amount of decrease in the diameter of the fractured portion after the test by the diameter before the test in percentage. The corrosion weight loss in the crevice corrosion test is the sum of the weight loss of the two test pieces, large and small, in mg.
【００３２】さらに、図１は、Ｂ含有量が約 1％の合金
について、熱間延性に及ぼすGd含有量とＹ含有量の影響
を示した図である。Further, FIG. 1 is a diagram showing the effects of the Gd content and the Y content on the hot ductility of the alloy having a B content of about 1%.
【００３３】[0033]
【表１】 [Table 1]
【００３４】表１から、本発明合金の合金1 〜21では優
れた高温延性および耐食性を有している。さらに、Tb、
Dyを含有する合金12〜16や、Mgを含有させた合金19では
より優れた高温延性を有している。また、合金17、18は
Moの含有で耐食性がより向上している。From Table 1, alloys 1 to 21 of the alloy of the present invention have excellent hot ductility and corrosion resistance. In addition, Tb,
Alloys 12 to 16 containing Dy and alloy 19 containing Mg have more excellent high temperature ductility. Also, alloys 17 and 18
Corrosion resistance is further improved by the inclusion of Mo.
【００３５】一方、比較合金である、ＹやGdのいずれか
一方でも含有しないか少量しか含有しない合金a 〜f で
はMgの有無にかかわらず延性が悪い。また、Ｂ添加量が
多い合金g はGdとＹを含有していても高温延性が低下し
ている。On the other hand, the comparative alloys, alloys a to f containing no or only a small amount of either Y or Gd have poor ductility regardless of the presence or absence of Mg. Further, the alloy g containing a large amount of B has low hot ductility even when it contains Gd and Y.
【００３６】さらに、Ｃ含有量が高い合金h 、Cr含有量
が低い合金i では耐食性が劣化している。Further, alloy h having a high C content and alloy i having a low Cr content have deteriorated corrosion resistance.
【００３７】図１から、本発明範囲のGdとＹ含有量の合
金は50％以上の絞り比を有し優れた熱間延性を示してお
り、GdとＹ両方を含有することにより熱間延性に関する
相乗効果が得られていることが分かる。特に、GdとＹの
含有量がそれぞれ 0.1％以上、0.01％以上の合金4 〜9
では絞り比が60％を超えており、良好な高温延性値が得
られている。一方、合金c のようにＹ含有量が0.05％未
満であるとGdが含有されていても高温延性値は低く、ま
た、合金a や合金b の場合はＹ含有量が0.005%以上でも
Gd含有量が0.05％未満のため十分な高温延性が得られな
い。From FIG. 1, alloys having Gd and Y contents within the range of the present invention have an excellent hot ductility with a drawing ratio of 50% or more. By incorporating both Gd and Y, the hot ductility is It can be seen that a synergistic effect regarding is obtained. In particular, alloys 4-9 with Gd and Y contents of 0.1% or more and 0.01% or more, respectively.
In the drawing, the drawing ratio exceeds 60%, and a good hot ductility value is obtained. On the other hand, when the Y content is less than 0.05% as in alloy c, the high temperature ductility value is low even if Gd is contained, and in the case of alloys a and b, the Y content is 0.005% or more.
Since the Gd content is less than 0.05%, sufficient hot ductility cannot be obtained.
【００３８】（実施例２）次に、表２に示す化学組成を
有する合金を用いて実規模製造ラインでの圧延実験を行
った。溶解、分解圧延後 200mm厚さ×1200mm幅のスラブ
を1100℃に加熱後、板厚20mmまで熱間圧延し、発生した
耳割れ長さを測定した。その結果も合わせて表２に示
す。(Example 2) Next, a rolling experiment was carried out on an actual scale production line using an alloy having the chemical composition shown in Table 2. After melting and decomposing and rolling, a slab having a thickness of 200 mm and a width of 1200 mm was heated to 1100 ° C. and then hot-rolled to a plate thickness of 20 mm, and the length of the generated edge crack was measured. The results are also shown in Table 2.
【００３９】[0039]
【表２】 [Table 2]
【００４０】表２から、ＹとGdの両方を含有する本発明
合金22、23では耳割れ長さは非常に小さかった。一方、
比較合金である、Ｙを含有しない合金j ではGdを含有し
ていても大きな耳割れが発生し、さらに延性改善のため
にMgを含有させた合金k でも耳割れの発生は改善されな
かった。From Table 2, the alloys 22 and 23 of the present invention containing both Y and Gd had a very short edge crack length. on the other hand,
A comparative alloy, alloy j containing no Y, had large edge cracks even if it contained Gd, and alloy k containing Mg to improve ductility did not improve the occurrence of edge cracks.
【００４１】[0041]
【発明の効果】本発明により従来のＢ含有オーステナイ
トステンレス鋼よりも熱間加工性および耐食性が優れた
中性子遮蔽用オーステナイトステンレス鋼を提供でき
る。According to the present invention, it is possible to provide an austenitic stainless steel for neutron shielding which is superior in hot workability and corrosion resistance to the conventional B-containing austenitic stainless steel.
【図面の簡単な説明】[Brief description of drawings]
【図１】熱間延性に及ぼすGd含有量とＹ含有量の影響を
示した図である。FIG. 1 is a diagram showing the effects of Gd content and Y content on hot ductility.
Claims (2)
％、Cr：18〜26％、Mo： 0〜 3.0％、Ｂ： 0.5〜 2.0
％、Gd：0.05〜 1.2％、Ｙ： 0.005〜 0.3％を含有する
ことを特徴とする中性子遮蔽用オーステナイトステンレ
ス鋼。1. By weight%, C: 0.03% or less, Ni: 7-22
%, Cr: 18 to 26%, Mo: 0 to 3.0%, B: 0.5 to 2.0
%, Gd: 0.05 to 1.2%, Y: 0.005 to 0.3%, an austenitic stainless steel for neutron shielding.
種または２種を合計で 0.005〜 0.1重量％含有すること
を特徴とする中性子遮蔽用オーステナイトステンレス
鋼。2. The steel according to claim 1, further comprising Tb and Dy
Austenitic stainless steel for neutron shielding, characterized by containing 0.005 to 0.1% by weight of one or two kinds in total.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7030613A JP3060873B2 (en) | 1995-02-20 | 1995-02-20 | Austenitic stainless steel for neutron shielding |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7030613A JP3060873B2 (en) | 1995-02-20 | 1995-02-20 | Austenitic stainless steel for neutron shielding |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH08225893A true JPH08225893A (en) | 1996-09-03 |
| JP3060873B2 JP3060873B2 (en) | 2000-07-10 |
Family
ID=12308731
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7030613A Expired - Fee Related JP3060873B2 (en) | 1995-02-20 | 1995-02-20 | Austenitic stainless steel for neutron shielding |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3060873B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2013027253A1 (en) * | 2011-08-22 | 2013-02-28 | 日本冶金工業株式会社 | Boron-containing stainless steel having excellent hot workability and excellent surface properties |
| KR20190027668A (en) * | 2017-09-07 | 2019-03-15 | 한국생산기술연구원 | Neutron absorber and a fabrication method thereof |
| KR102556317B1 (en) * | 2022-08-12 | 2023-07-18 | 주식회사 에이티에스 | Alloy for plasma etching equipment and fasteners including same |
-
1995
- 1995-02-20 JP JP7030613A patent/JP3060873B2/en not_active Expired - Fee Related
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2013027253A1 (en) * | 2011-08-22 | 2013-02-28 | 日本冶金工業株式会社 | Boron-containing stainless steel having excellent hot workability and excellent surface properties |
| CN103748249A (en) * | 2011-08-22 | 2014-04-23 | 日本冶金工业株式会社 | Boron-containing stainless steel having excellent hot workability and excellent surface properties |
| US9303301B2 (en) | 2011-08-22 | 2016-04-05 | Nippon Yakin Kogyo Co., Ltd. | Boron-containing stainless steel having excellent hot workability and surface property |
| KR20190027668A (en) * | 2017-09-07 | 2019-03-15 | 한국생산기술연구원 | Neutron absorber and a fabrication method thereof |
| KR102556317B1 (en) * | 2022-08-12 | 2023-07-18 | 주식회사 에이티에스 | Alloy for plasma etching equipment and fasteners including same |
| WO2024034937A1 (en) * | 2022-08-12 | 2024-02-15 | 주식회사 에이티에스 | Alloy for plasma etching equipment, and fastening mechanism including same |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3060873B2 (en) | 2000-07-10 |
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