JPS63134627A - Manufacture of austenitic stainless steel having superior cryogenic characteristic after heat treatment for forming nb3sn - Google Patents
Manufacture of austenitic stainless steel having superior cryogenic characteristic after heat treatment for forming nb3snInfo
- Publication number
- JPS63134627A JPS63134627A JP27937686A JP27937686A JPS63134627A JP S63134627 A JPS63134627 A JP S63134627A JP 27937686 A JP27937686 A JP 27937686A JP 27937686 A JP27937686 A JP 27937686A JP S63134627 A JPS63134627 A JP S63134627A
- Authority
- JP
- Japan
- Prior art keywords
- heat treatment
- nb3sn
- stainless steel
- austenitic stainless
- steel
- 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.)
- Granted
Links
- 238000010438 heat treatment Methods 0.000 title claims abstract description 43
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 20
- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 18
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 22
- 239000010959 steel Substances 0.000 claims abstract description 22
- 238000005098 hot rolling Methods 0.000 claims abstract description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 3
- 230000015572 biosynthetic process Effects 0.000 claims description 10
- 238000000034 method Methods 0.000 claims description 7
- 238000005097 cold rolling Methods 0.000 claims description 4
- 229910052684 Cerium Inorganic materials 0.000 claims description 3
- 229910052791 calcium Inorganic materials 0.000 claims description 3
- 229910052726 zirconium Inorganic materials 0.000 claims description 2
- 229910000657 niobium-tin Inorganic materials 0.000 abstract description 18
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 4
- 229910052758 niobium Inorganic materials 0.000 abstract description 4
- 229910052748 manganese Inorganic materials 0.000 abstract description 3
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 3
- 229910052799 carbon Inorganic materials 0.000 abstract description 2
- 229910052759 nickel Inorganic materials 0.000 abstract description 2
- 239000000463 material Substances 0.000 description 15
- 229910001566 austenite Inorganic materials 0.000 description 11
- 230000000694 effects Effects 0.000 description 9
- 239000000243 solution Substances 0.000 description 7
- 230000006866 deterioration Effects 0.000 description 6
- 230000006641 stabilisation Effects 0.000 description 6
- 238000011105 stabilization Methods 0.000 description 6
- 230000032683 aging Effects 0.000 description 5
- 230000005291 magnetic effect Effects 0.000 description 5
- 230000000087 stabilizing effect Effects 0.000 description 5
- 238000005482 strain hardening Methods 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 150000001875 compounds Chemical class 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 230000035699 permeability Effects 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 239000013078 crystal Substances 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 239000002887 superconductor Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910001455 Ni+ Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000003302 ferromagnetic material Substances 0.000 description 1
- 238000007656 fracture toughness test Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 229910001293 incoloy Inorganic materials 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野コ
本発明はＮｂ３Ｓｎ生成熱処理後の極低温特性に優れた
オーステナイト系ステンレス鋼の製造方法に関し、さら
に詳しくは、超電導磁石の支持体に代表される極低温用
構造材料であって、使用に先立って冷間加工、Ｎｂ３Ｓ
ｎ生成熱処理が行なわれてし極低温特性に優れたオース
テナイト系ステンレス鋼の製造方法に関する。Detailed Description of the Invention [Industrial Field of Application] The present invention relates to a method for producing austenitic stainless steel having excellent cryogenic properties after heat treatment for Nb3Sn formation, and more specifically relates to a method for producing austenitic stainless steel, which is typified by supports for superconducting magnets. Structural material for cryogenic temperatures, cold worked and Nb3S prior to use.
The present invention relates to a method for producing austenitic stainless steel that has been subjected to n-forming heat treatment and has excellent cryogenic properties.
［従来技術］
一般に、超電導磁石はＮｂＴｉ線より８テスラ程度の磁
界を発生できるが、それ以上の高磁界を発生させるため
にはＮｂ３Ｓｎに代表される化合物超電導体を利用する
ことが有効であるとされている。[Prior art] Generally, superconducting magnets can generate a magnetic field of about 8 Tesla than NbTi wires, but in order to generate a higher magnetic field, it is effective to use compound superconductors such as Nb3Sn. has been done.
しかし、超電導体か化合物であるため可塑性が悪いとい
う問題があり、そのため、Ｎｂ３Ｓｎ生成前に支持材料
と共に加工を行なう導体製造工程または超電導磁石の製
造工程の最後に、Ｎｂ３Ｓｎを６００〜８００°Ｃ×５
０〜３００時間の熱処理によって生成させ、Ｎｂ３Ｓｎ
の変形を最小に抑制している。However, since it is a superconductor or a compound, it has a problem of poor plasticity. Therefore, Nb3Sn is heated at 600 to 800°C 5
Produced by heat treatment for 0 to 300 hours, Nb3Sn
deformation is suppressed to a minimum.
従って１、構造材料は、Ｎｂ３Ｓｎの生成熱処理を同時
に受けるため、時効されて延性、靭性の劣化が生じ、こ
の劣化は極低温において特に顕著になるという問題があ
る。Therefore, 1. Since the structural material is simultaneously subjected to heat treatment for Nb3Sn formation, it is aged and deteriorates in ductility and toughness, and this deterioration becomes particularly noticeable at extremely low temperatures.
このような極低温における特性の劣化に対して、Ｎｉを
多量に含有させたインコロイ合金等が使用されているが
、非常に高価であるので安価なステンレス鋼が望まれて
いる。In order to deal with such deterioration of characteristics at extremely low temperatures, Incoloy alloy containing a large amount of Ni is used, but since it is very expensive, inexpensive stainless steel is desired.
しかして、最近になってＮｉ５Ｃｒ系ステンレス鋼にＶ
を含有させて特性の改善を行なった例として特公昭６１
−０００４１６号公報により提案されているが、このＶ
を含有させた綱は時効前の冷間加工により極低温下にお
ける延性が大幅に劣化するという問題があり、この冷間
加工を考慮した特性改善が重要な技術的に解決すべき問
題である。However, recently, V
As an example of improving properties by incorporating
-000416, but this V
Steel containing steel has the problem that its ductility at extremely low temperatures is significantly degraded due to cold working before aging, and improving properties by taking this cold working into consideration is an important technical problem to be solved.
［発明が解決しようとする問題点コ
本発明は、上記に説明したような従来にお（Ｊる極低温
構造用材料としての種々の問題点に鑑みなされたもので
あり、本発明者が鋭意研究を行なった結果、Ｎｂ３Ｓｎ
等の化合物系超電導磁石の構造材料で冷間加工が行なわ
れた後、Ｎｂ３Ｓｎ生成熟処理を行っても、極低温にお
いて延性、靭性に優れた極低温特性に優れたオーステナ
イト系ステンレス鋼の製造方法を開発したのである。[Problems to be Solved by the Invention] The present invention has been made in view of the various problems that have arisen in the past as materials for cryogenic structures, as explained above, and the present inventors have endeavored to solve them. As a result of research, Nb3Sn
A method for manufacturing an austenitic stainless steel with excellent cryogenic properties that exhibits excellent ductility and toughness at cryogenic temperatures even after Nb3Sn biomaturation treatment is performed after cold working with structural materials for compound-based superconducting magnets such as was developed.
［問題点を解決するための手段］
本発明に係るＮｂ３Ｓｎ生成熱処理後の極低温特性に優
れたオーステナイト系ステンレス鋼の製造方法は、
（１） Ｃ０，０３ｗｔ％以下、Ｓ ｉ ０．１〜２．
０ｗｔ％、Ｍｎ ０．１〜２０．０ｗｔ％、Ｐ ０．０
２５ｗｔ％以下、Ｓ ０．０１５ｔｗｔ％以下、Ｎｉ
３〜１５ｗｔ％、Ｃｒ１２〜２０ｗｔ％、Ｍｏ ０．５
〜２．５ｗｔ％、Ｎｂ ０．０１〜０．１８ｗｔ％、Ｎ
０．０５〜０．２５ｗｔ％を含有し、かつ、
Ｎｉ＋０．５Ｍｎ＋３０Ｃ＋３ＯＮ
＞２／３（Ｃｒ＋Ｍｏ＋ Ｓ １−８）を満足し、残部
Ｆｅおよび不可避不純物からなる鋼塊または鋼片を熱間
圧延或いは熱間圧延、冷間圧延を行い、次いで、１００
０〜１１５０℃の温度において溶体化処理を行った後、
さらに、８２０〜９００℃の温度に加熱することを特徴
とするＮｂ３Ｓｎ生成熱処理後の極低温特性に優れたオ
ーステナイト系ステンレス鋼の製造方法を第１の発明と
し、
（２） Ｃ０．０３ｗｔ％以下、Ｓ ｉ ０．１〜２．
０ｗｔ％、Ｍｎ ０．１〜２０．０ｗｔ％、Ｐ ０．０
２５ｗｔ％、Ｓ ０．０１５ｗｔ％以下、Ｎｉ３〜Ｌ５
ｗｔ％、Ｃｒ１２〜２０ｗｔ％、Ｍｏ ０．５〜２．５
ｗｔ％、Ｎｂ ０．０１〜０．１８ｗｔ％、Ｎ ０．０
５〜０．２５ｗｔ％を含有し、さらに、
Ｃａ、Ｃｅ、Ｚｒのうちから進んだ１種または２種以上
０．００１〜０．１００ｗｔ％を含有し、かつ、
Ｎｉ＋０．５Ｍｎ＋３００＋３ＯＮ
＞２／３（Ｏｒ＋Ｍｏ＋Ｓ １−８）
を満足し、残部Ｆｅおよび不可避不純物からなる鋼塊ま
たは鋼片を熱間圧延或いは熱間圧延、冷間圧延を行い、
次いで、１０００〜１１５０℃の温度において溶体化処
理を行った後、さらに、８２０〜９００℃の温度に加熱
することを特徴とするＮｂ３Ｓｎ生成熱処理後の極低温
特性に優れたオーステナイト系ステンレス鋼の製造方法
を第２の発明とする２つの発明よりなるものである。[Means for solving the problems] The method for producing austenitic stainless steel with excellent cryogenic properties after Nb3Sn generation heat treatment according to the present invention is as follows: (1) C0.03 wt% or less, Si 0.1 to 2 ．．
0wt%, Mn 0.1-20.0wt%, P 0.0
25wt% or less, S 0.015twt% or less, Ni
3-15wt%, Cr12-20wt%, Mo 0.5
~2.5wt%, Nb 0.01~0.18wt%, N
A steel ingot or billet containing 0.05 to 0.25 wt% and satisfying Ni+0.5Mn+30C+3ON>2/3 (Cr+Mo+S 1-8), with the remainder being Fe and unavoidable impurities is hot rolled or heated. Inter-rolling and cold rolling are performed, and then 100
After solution treatment at a temperature of 0 to 1150°C,
Further, the first invention provides a method for producing austenitic stainless steel having excellent cryogenic properties after Nb3Sn formation heat treatment, which is characterized by heating to a temperature of 820 to 900°C, (2) C0.03 wt% or less, S i 0.1-2.
0wt%, Mn 0.1-20.0wt%, P 0.0
25wt%, S 0.015wt% or less, Ni3~L5
wt%, Cr12-20wt%, Mo 0.5-2.5
wt%, Nb 0.01-0.18wt%, N 0.0
5 to 0.25 wt%, further contains 0.001 to 0.100 wt% of one or more of Ca, Ce, and Zr, and Ni+0.5Mn+300+3ON>2/3( Or+Mo+S 1-8) A steel ingot or billet consisting of the balance Fe and unavoidable impurities is hot-rolled, hot-rolled, and cold-rolled,
Next, after performing solution treatment at a temperature of 1000 to 1150°C, the production of an austenitic stainless steel with excellent cryogenic properties after Nb3Sn formation heat treatment is characterized in that it is further heated to a temperature of 820 to 900°C. This invention consists of two inventions, with the second invention being a method.
本発明に係るＮｂａＳｎ生成熱処理後の極低温特性に優
れたオーステナイト系ステンレス鋼の製造方法について
以下詳細に説明する。The method for manufacturing an austenitic stainless steel having excellent cryogenic properties after NbaSn generation heat treatment according to the present invention will be described in detail below.
先ず、本発明に係るＮｂ３Ｓｎ生成熱処理後の極低温特
性に優れたオーステナイト系ステンレス鋼の製造方法（
以下本発明に係る鋼の製造方法ということかある。）に
おいて使用するオーステナイト系ステンレス鋼の含有成
分および成分割合について説明する。First, the method for producing austenitic stainless steel with excellent cryogenic properties after NbSn generation heat treatment according to the present invention (
The following may be referred to as the method for manufacturing steel according to the present invention. The components and component ratios of the austenitic stainless steel used in ) will be explained.
Ｃはオーステナイトの安定化と耐力向上に必要な元素で
あるが、含有量が０．０３ｗｔ％を越えるような多量の
含有であるとＮｂ３Ｓｎ生成熱処理中にに炭化物を析出
して延性、靭性を劣化させるようになる。よって、Ｃ含
有量は（１，０３ｗｔ％以下とする。C is an element necessary for stabilizing austenite and improving its yield strength, but if the content exceeds 0.03 wt%, carbides will precipitate during the heat treatment to form Nb3Sn, resulting in deterioration of ductility and toughness. You will be able to do it. Therefore, the C content is 1.03 wt% or less.
Ｓｉは脱酸のためと高温における耐酸化性を改善する元
素であり、含有量が０．１ｗｔ％未満ではこのような効
果は少なく、また、２．０ｗｔ％を越えて多量に含有さ
れると靭性を劣化させる。よって、Ｓｉ含有量は０，１
〜２．０ｗｔ％とする。Si is an element for deoxidation and improving oxidation resistance at high temperatures, and if the content is less than 0.1 wt%, this effect will be small, and if it is contained in a large amount exceeding 2.0 wt%, Degrades toughness. Therefore, the Si content is 0.1
~2.0wt%.
Ｍｎはオーステナイトの安定化、Ｎの固溶限の上昇に有
効であるが、含有量がＱ、１ｗｔ％未満ではこのような
効果は少なく、また、２０．０ｗｔ％を越えて含有され
るとＣｒとの共存で時効中に脆いσ相が析出し、靭性を
劣化させる。よって、Ｍｎ含宵量は０．１〜２０．０ｗ
ｔ％とする。Mn is effective in stabilizing austenite and increasing the solid solubility limit of N, but if the content is less than 1 wt%, this effect is small, and if it is contained in more than 20.0 wt%, Cr In the coexistence with steel, a brittle σ phase precipitates during aging and deteriorates toughness. Therefore, the Mn content is 0.1 to 20.0w
It is assumed to be t%.
ＰはＮｂ３Ｓｎ生成熱処理によりオーステナイト粒界に
移動、偏析し、粒界脆化を促進するため極力低（抑える
必要があるが、経済性を考慮してＰ含有量は０．０２５
ｗｔ％とする。P moves to the austenite grain boundaries and segregates during the Nb3Sn formation heat treatment, promoting grain boundary embrittlement, so it must be kept as low as possible (it must be suppressed, but considering economic efficiency, the P content is set to 0.025.
Let it be wt%.
Ｓは鋼の熱間加工性、延性、靭性を劣化させる有害な元
素であり、Ｐと同様極力低く抑える必要があるが、経済
性を琴慮してＳ含有量は０．０１５ｗｔ％とする。S is a harmful element that deteriorates the hot workability, ductility, and toughness of steel, and like P, it is necessary to keep it as low as possible, but in consideration of economic efficiency, the S content is set to 0.015 wt%.
Ｎｉはオーステナイト安定化と延性、靭性の向上に有効
な元素で、特に、Ｎｌ１３Ｓｎ生成熱処理後または冷間
加工＋Ｎｂ＊Ｓｎ生成熱処理後における延性、靭性の劣
化に対して有効であり、オーステナイト組成を確保する
ために３ｗｔ％以上は含有させることが必要で、また、
上記した効果は１５ｗｔ％を越えて含有させると飽和し
、かつ、コスト上昇を招く。よって、Ｎｉ含有ｍは３〜
１５ｗｔ％とする。Ni is an element that is effective in stabilizing austenite and improving ductility and toughness. It is especially effective against deterioration of ductility and toughness after heat treatment to generate Nl13Sn or after heat treatment to generate cold working + Nb*Sn, ensuring the austenite composition. In order to achieve this, it is necessary to contain 3 wt% or more, and
The above-mentioned effects become saturated when the content exceeds 15 wt%, and the cost increases. Therefore, Ni content m is 3~
It is set to 15 wt%.
Ｃｒは耐蝕性の面から含有量はｔ２ｗｔ％以上とする必
要かあり、しかし、２０ｗｔ％を越えて多量に含有させ
るとオーステナイトを不安定にし、かつ、Ｍｎとの共存
で時効中に脆いσ相の析出を起して靭性を劣化させる。From the viewpoint of corrosion resistance, the content of Cr needs to be t2wt% or more. However, if it is contained in a large amount exceeding 20wt%, it will destabilize austenite and cause brittle σ phase during aging due to coexistence with Mn. This causes precipitation of and deteriorates toughness.
よって、Ｏｒ含有量は１２〜２０ｗｔ％とする。Therefore, the Or content is set to 12 to 20 wt%.
ＭＯは耐力を向上させるのに必要であり、かつ、Ｎｂが
含有されている場合Ｎｈ、Ｓｎ生成熱処理中における原
子拡散を抑制し、耐時効性の向上に有効であり、含有量
が０．５ｗｔ％未満ではこのような効果は少なく、また
、２．５ｗｔ％を越える多量の含有はコスト上昇につな
がる。よって、ＭＯＣ含有量０．５〜２．５ｗｔ％とす
る。MO is necessary to improve yield strength, and when Nb is contained, it suppresses atomic diffusion during Nh and Sn generation heat treatment and is effective in improving aging resistance, and when the content is 0.5 wt. If the content is less than 2.5 wt%, such an effect will be small, and if the content exceeds 2.5 wt%, the cost will increase. Therefore, the MOC content is set to 0.5 to 2.5 wt%.
Ｎｂは炭素、窒素を固定して有害なＣｒ炭窒化物が粒界
に析出するのを抑制するので耐時効性を高め、特に、冷
間加工材の粒界割れを防止する特性を有し、かつ、ＭＯ
との共存含有によりこのような効果が顕著となり、含有
量がｌ］、０１ｗｔ５未満では上記した効果は少なく、
また、０．１８ｗｔ％を越えて多量に含有させると強化
元素の窒素を消費して強度低下および靭性劣化を生じさ
せる。よって、Ｎｂ含有爪は０．０１〜０．１８ｗｔ％
とする。Nb fixes carbon and nitrogen and suppresses the precipitation of harmful Cr carbonitrides at grain boundaries, thereby increasing aging resistance and, in particular, has the property of preventing intergranular cracking in cold-worked materials. And MO
Such effects become noticeable when coexisting with
Furthermore, if the content exceeds 0.18 wt%, nitrogen, which is a reinforcing element, will be consumed, resulting in a decrease in strength and toughness. Therefore, the Nb-containing nail is 0.01 to 0.18 wt%
shall be.
Ｎはオーステナイトを安定化し、かつ、耐力向上に有効
な元素であり、含有量が０．０５ｗｔ％未満ではこのよ
うな効果は少なく、また、０．２５ｗｊ％を越えて多量
に含有させると靭性の劣化と溶接欠陥の発生を招く。よ
って、Ｎ含有量は０．０５〜０．２５ｗｔ％とする。N is an element that is effective in stabilizing austenite and improving its yield strength. If the content is less than 0.05wt%, this effect is small, and if it is contained in a large amount exceeding 0.25wj%, it may deteriorate the toughness. This leads to deterioration and welding defects. Therefore, the N content is set to 0.05 to 0.25 wt%.
Ｃａ、Ｃｅ５Ｚｒは鋼を清浄化し、介在物を微細化、球
状化し、靭性を向上させる元素であり、含有量がＱ、０
０１ｗｔ％未満ではこのような効果は少なく、また、０
．ｌｗｔ％を越えて多量に含有させるとかえって清浄化
を悪くする。よって、Ｃａ、 Ｃｅ。Ca, Ce5Zr are elements that clean steel, make inclusions finer and spheroidal, and improve toughness.
If it is less than 0.01 wt%, this effect is small, and if it is less than 0.
．． If it is contained in a large amount exceeding 1wt%, cleaning will become worse. Therefore, Ca, Ce.
Ｚｒの含有量は０．００１〜０．１ｗｔ％とする。The content of Zr is 0.001 to 0.1 wt%.
Ｎｉ＋０．５Ｍｎ＋３００＋３ＯＮ
＞２／３（Ｃｒ＋Ｍｏ＋ Ｓ １−８）は、極低温で延
性、靭性の高い安定したオーステナイト組織を得るため
に必要であり、これを満足しない成分系の材料において
は、冷間加工後或いはＮｂ３Ｓｎ生成熱処理後オーステ
ナイト中にマルテンサイトが生成し、極低温での延性、
靭性を大きく損なうことになる。Ni + 0.5Mn + 300 + 3ON > 2/3 (Cr + Mo + S 1-8) is necessary to obtain a stable austenitic structure with high ductility and toughness at extremely low temperatures, and materials with component systems that do not satisfy this need to be cold worked. After or Nb3Sn generation heat treatment, martensite is generated in austenite, which increases ductility at extremely low temperatures.
Toughness will be greatly impaired.
本発明に係る鋼の製造方法によれば、上記した化学成分
を有する鋼塊または鋼片を熱間圧延或いは熱間圧延、冷
間圧延を行い、次いで、１０００〜１１５０℃しの温度
において溶体化処理を行った後、さらに、８２０〜９０
０℃の温度に加熱することにより、Ｎｂ３Ｓｎ生成熱処
理後の極低温特性に優れたオーステナイト系ステンレス
鋼が製造される。According to the method for manufacturing steel according to the present invention, a steel ingot or slab having the above-mentioned chemical components is hot rolled, hot rolled, or cold rolled, and then solution-treated at a temperature of 1000 to 1150°C. After processing, further 820 to 90
By heating to a temperature of 0° C., an austenitic stainless steel with excellent cryogenic properties after Nb3Sn generation heat treatment is produced.
熱間圧延または熱間圧延、冷間圧延を行った後に、ｌ０
００〜１１５０℃の温度で溶体化処理を行うのであるが
、この温度が１０００°Ｃ未満であると析出物の固溶が
充分でなく、オーステナイト結晶粒が細かくなるため、
延性、靭性が劣化し、また、１１５０°Ｃを越える温度
で溶体化処理を行うとオーステナイト結晶粒が粗大化が
著しく耐力の低下が大きくなる。After hot rolling or hot rolling, cold rolling, l0
Solution treatment is performed at a temperature of 00 to 1150°C, but if this temperature is less than 1000°C, the solid solution of the precipitates will not be sufficient and the austenite crystal grains will become fine.
Ductility and toughness deteriorate, and when solution treatment is performed at a temperature exceeding 1150°C, austenite crystal grains become coarse and the yield strength decreases significantly.
さらに、このような溶体化処理後に８２０〜９００℃に
再加熱安定化熱処理するが、この姿定化熱処理は、その
後の加工において行なわれる溶接或いはＮｂａＳｎ生成
熱処理時にＣｒ炭窒堪物の結晶粒界析出を抑制し、延性
、靭性の劣化を小さくするのに有効である。Furthermore, after such solution treatment, a stabilization heat treatment is performed at 820 to 900°C, but this shape stabilization heat treatment is performed during welding or NbaSn formation heat treatment performed in subsequent processing to remove the grain boundaries of the Cr-carbonitride material. It is effective in suppressing precipitation and reducing deterioration in ductility and toughness.
真空溶解により鋼（第１表のＮｏ、１）を溶製し、鍛造
後、板厚３０市に熱間圧延した。さらに、１１００℃の
温度で溶体化処理を行った鋼板を供試板とし、安定化熱
処理温度と一２６９°Ｃの温度における破壊靭性Ｋｌｃ
値との関係を調査した。その結果第１図に示す。この供
試鋼板はいずれも安定化熱処理後、７００℃×１００時
間のＮｂ３Ｓｎ生成熱処理が施されている。Steel (No. 1 in Table 1) was produced by vacuum melting, forged, and then hot rolled to a plate thickness of 30 mm. Furthermore, a steel plate solution-treated at a temperature of 1100°C was used as a test plate, and the fracture toughness Klc at the stabilization heat treatment temperature and at a temperature of -269°C was determined.
We investigated the relationship with the value. The results are shown in Figure 1. All of these test steel plates were subjected to Nb3Sn generation heat treatment at 700° C. for 100 hours after stabilization heat treatment.
この第１図からも明らかなように、８２０〜９００℃の
温度範囲で熱処理を行った鋼は、ト１ｂ３Ｓ＋ｒ生成熱
処理後においても高い破壊靭性を示している。As is clear from FIG. 1, the steel heat-treated in the temperature range of 820 to 900° C. exhibits high fracture toughness even after the heat treatment to form T1b3S+r.
これは、８２０〜９００℃の温度に加熱することにより
、球状のＮｂ炭窒化物が生成、安定化し、その後のＮｂ
３Ｓｎ生成熱処理（７００℃×１００時間）による延性
、靭性を阻害するＣｒ炭窒化物の粒界析出を抑制するた
めと考えられる。This is because spherical Nb carbonitrides are generated and stabilized by heating to a temperature of 820 to 900°C, and the subsequent Nb
It is thought that this is to suppress grain boundary precipitation of Cr carbonitrides that inhibit ductility and toughness due to the 3Sn generation heat treatment (700° C. x 100 hours).
［実 施 例］
本発明に係るＮｂａＳｎ生成熱処理後の極低温特性に侵
れ１こオーステナイト系ステンレス鋼の製造方法の実施
例を説明する。[Example] An example of the method of manufacturing a single austenitic stainless steel having poor cryogenic properties after NbaSn generation heat treatment according to the present invention will be described.
実施例
第１表（１）に示す５種類の含有成分および含有割合の
鋼を真空溶解により溶製し、鍛造後、板厚３０ｍｍの閏
仮に熱間圧延した。EXAMPLE Steel having the five types of components and content ratios shown in Table 1 (1) was produced by vacuum melting, forged, and then hot rolled into a 30 mm thick plate.
この鋼板を使用し、所定の熱処理、熱間加工を行い、さ
らに、７００℃×１００時間のＮｂ５ＳＩ＋生成熱処理
を行った後、引張り、破壊靭性試験片を採取し、−２６
９℃の温度での試験に供した。Using this steel plate, predetermined heat treatment and hot working were performed, and after further Nb5SI+ formation heat treatment was performed at 700°C for 100 hours, tensile and fracture toughness test pieces were taken.
It was subjected to a test at a temperature of 9°C.
また、板厚３０ｍｄｔ４板の一部を使用し、熱間圧延、
冷間圧延を行い、板厚１．５〜２ 、０ ｍｍの冷間圧
延鋼板を製造し、３０ｍｍ材と同様の処理を行った後、
引張り試験片を採取し、−２６９℃の温度で試験を実施
した。In addition, using a part of 4 plates with a thickness of 30 mdt, hot rolling,
After performing cold rolling to produce a cold rolled steel plate with a plate thickness of 1.5 to 2.0 mm, and performing the same treatment as the 30 mm material,
Tensile test specimens were taken and tested at a temperature of -269°C.
なお、透磁率は低透磁率針により測定した。Note that the magnetic permeability was measured using a low magnetic permeability needle.
第１表（１）のＮ０１１〜８は本発明に係る銅の製造方
法に使用する鋼と同一の鋼を用いて、製造条件（第１表
（２））を変化させたしのである。Nos. 011 to 8 in Table 1 (1) were obtained by using the same steel as the steel used in the copper manufacturing method according to the present invention, but by changing the manufacturing conditions (Table 1 (2)).
Ｎ０１１．３．５．７材は本発明に係る鋼の製造方法を
用いて試作したものであり、Ｎｏ、２．４．６．８と比
較して、延性、靭性の著しい向上が認められる。Material No. 11.3.5.7 was prototyped using the steel manufacturing method according to the present invention, and compared to No. 2.4.6.8, significant improvements in ductility and toughness were observed.
Ｎ０８９、ＩＯ材は同−鋼であるが、安定化熱処理が実
施されていないＮｏ、 １０材は、ＮＯ３９材と比較し
て延性、靭性が劣っている。Ｎｏ、ｌＩ。The No. 89 and IO materials are the same steels, but the No. 10 materials, which have not been subjected to stabilization heat treatment, are inferior in ductility and toughness compared to the No. 39 materials. No, lI.
Ｉ２材についても同様のことがいえる。The same can be said about I2 material.
マタ、Ｎｏ、 １３、ｌ ４ ＨハＳ ＵＳ ３０４
ｔ、ａテあり、Ｍｏ、Ｎｂが含有されていないため、安
定化熱処理の有無に拘わらず、延性、靭性が低い。Mata, No. 13, l 4 H HaS US 304
Since it has t and ate and does not contain Mo or Nb, its ductility and toughness are low regardless of the presence or absence of stabilizing heat treatment.
Ｎｏ、 ｌ ５．１６材は個々の成分範囲は満足してい
るが、Ｎｉ＋０．５Ｍｎ＋３００＋３ＯＮ＞２／３（Ｃ
ｒ＋Ｍｏ＋５ｉ−８）を満足しないため、オーステナイ
ト中に強磁性体であるマルテンサイトが生成し、透磁率
が高くなっている。このマルテンサイト生成のため延性
、靭性が極めて低い。No. l 5.16 material satisfies the individual component ranges, but Ni+0.5Mn+300+3ON>2/3(C
r+Mo+5i-8), martensite, which is a ferromagnetic material, is generated in austenite, resulting in high magnetic permeability. Due to this martensite formation, ductility and toughness are extremely low.
［発明の効果］
以上説明したように、本発明に係るＮｂ３Ｓｎ生成熱処
理後の極低温特性に優れたオーステナイト系ステンレス
鋼の製造方法は上記の構成であるから、冷間加工および
Ｎｂ３Ｓｎ生成熱処理を行っても極低温特性に優れ、超
電導磁石の支持体に代表される極低温用構造材として好
適なオーステナイト系ステンレス鋼を製造することがで
きるという効果を有する。[Effects of the Invention] As explained above, since the method for producing austenitic stainless steel having excellent cryogenic properties after Nb3Sn generation heat treatment according to the present invention has the above configuration, cold working and Nb3Sn generation heat treatment are performed. It has the effect of producing an austenitic stainless steel that has excellent cryogenic properties and is suitable for cryogenic structural materials such as supports for superconducting magnets.
第１図は一２９６℃での破壊靭性・Ｋｌｃと安定化処理
温度との関係を示す図である。
矛１図FIG. 1 is a diagram showing the relationship between fracture toughness/Klc and stabilization treatment temperature at -296°C. Spear 1
Claims (2)
％、Ｍｎ０．１〜２０．０ｗｔ％、Ｐ０．０２５ｗｔ％
以下、Ｓ０．０１５ｗｔ％以下、Ｎｉ３〜１５ｗｔ％、
Ｃｒ１２〜２０ｗｔ％、Ｍｏ０．５〜２．５ｗｔ％、Ｎ
ｂ０．０１〜０．１８ｗｔ％、Ｎ０．０５〜０．２５ｗ
ｔ％を含有し、かつ、 Ｎｉ＋０．５Ｍｎ＋３０Ｃ＋３０Ｎ ＞２／３（Ｃｒ＋Ｍｏ＋Ｓｉ−８） を満足し、残部Ｆｅおよび不可避不純物からなる鋼塊ま
たは鋼片を熱間圧延或いは熱間圧延、冷間圧延を行い、
次いで、１０００〜１１５０℃の温度において溶体化処
理を行った後、さらに、８２０〜９００℃の温度に加熱
することを特徴とするＮｂ＿３Ｓｎ生成熱処理後の極低
温特性に優れたオーステナイト系ステンレス鋼の製造方
法。(1) C0.03wt% or less, Si0.1-2.0wt
%, Mn0.1-20.0wt%, P0.025wt%
Below, S0.015wt% or less, Ni3 to 15wt%,
Cr12-20wt%, Mo0.5-2.5wt%, N
b0.01~0.18wt%, N0.05~0.25w
t% and satisfies Ni + 0.5Mn + 30C + 30N > 2/3 (Cr + Mo + Si - 8), and the remainder consists of Fe and unavoidable impurities, hot rolling, hot rolling, cold rolling. ,
Production of austenitic stainless steel with excellent cryogenic properties after Nb_3Sn formation heat treatment, which is characterized by performing solution treatment at a temperature of 1000 to 1150°C and then heating to a temperature of 820 to 900°C. Method.
％、Ｍｎ０．１〜２０．０ｗｔ％、Ｐ０．０２５ｗｔ％
、Ｓ０．０１５ｗｔ％以下、Ｎｉ３〜１５ｗｔ％、Ｃｒ
１２〜２０ｗｔ％、Ｍｏ０．５〜２．５ｗｔ％、Ｎｂ０
．０１〜０．１８ｗｔ％、Ｎ０．０５〜０．２５ｗｔ％
を含有し、さらに、 Ｃａ、Ｃｅ、Ｚｒのうちから選んだ１種または２種以上
０．００１〜０．１００ｗｔ％ を含有し、かつ、 Ｎｉ＋０．５Ｍｎ＋３０Ｃ＋３０Ｎ ＞２／３（Ｃｒ＋Ｍｏ＋Ｓｉ−８） を満足し、残部Ｆｅおよび不可避不純物からなる鋼塊ま
たは鋼片を熱間圧延或いは熱間圧延、冷間圧延を行い、
次いで、１０００〜１１５０℃の温度において溶体化処
理を行った後、さらに、８２０〜９００℃の温度に加熱
することを特徴とするＮｂ＿３Ｓｎ生成熱処理後の極低
温特性に優れたオーステナイト系ステンレス鋼の製造方
法。(2) C0.03wt% or less, Si0.1-2.0wt
%, Mn0.1-20.0wt%, P0.025wt%
, S0.015wt% or less, Ni3-15wt%, Cr
12-20wt%, Mo0.5-2.5wt%, Nb0
．． 01-0.18wt%, N0.05-0.25wt%
and further contains 0.001 to 0.100 wt% of one or more selected from Ca, Ce, and Zr, and satisfies Ni+0.5Mn+30C+30N>2/3(Cr+Mo+Si-8) Then, the steel ingot or billet consisting of the remaining Fe and unavoidable impurities is hot-rolled, hot-rolled, and cold-rolled,
Production of austenitic stainless steel with excellent cryogenic properties after Nb_3Sn formation heat treatment, which is characterized by performing solution treatment at a temperature of 1000 to 1150°C and then heating to a temperature of 820 to 900°C. Method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP27937686A JPH0629459B2 (en) | 1986-11-22 | 1986-11-22 | Nb (3) Method for producing austenitic stainless steel having excellent cryogenic properties after Sn formation heat treatment |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP27937686A JPH0629459B2 (en) | 1986-11-22 | 1986-11-22 | Nb (3) Method for producing austenitic stainless steel having excellent cryogenic properties after Sn formation heat treatment |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63134627A true JPS63134627A (en) | 1988-06-07 |
| JPH0629459B2 JPH0629459B2 (en) | 1994-04-20 |
Family
ID=17610281
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP27937686A Expired - Lifetime JPH0629459B2 (en) | 1986-11-22 | 1986-11-22 | Nb (3) Method for producing austenitic stainless steel having excellent cryogenic properties after Sn formation heat treatment |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0629459B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5429688A (en) * | 1992-02-27 | 1995-07-04 | Barbosa; Celso A. | Work hardened stainless steel for springs |
| WO1999032682A1 (en) * | 1997-12-23 | 1999-07-01 | Allegheny Ludlum Corporation | Austenitic stainless steel including columbium |
| EP3133179A4 (en) * | 2014-04-17 | 2018-03-21 | Nippon Steel & Sumitomo Metal Corporation | Austenitic stainless steel and method for producing same |
-
1986
- 1986-11-22 JP JP27937686A patent/JPH0629459B2/en not_active Expired - Lifetime
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5429688A (en) * | 1992-02-27 | 1995-07-04 | Barbosa; Celso A. | Work hardened stainless steel for springs |
| WO1999032682A1 (en) * | 1997-12-23 | 1999-07-01 | Allegheny Ludlum Corporation | Austenitic stainless steel including columbium |
| EP3133179A4 (en) * | 2014-04-17 | 2018-03-21 | Nippon Steel & Sumitomo Metal Corporation | Austenitic stainless steel and method for producing same |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0629459B2 (en) | 1994-04-20 |
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