JPH02156047A - High-hardness nonmagnetic stainless steel and its production - Google Patents
High-hardness nonmagnetic stainless steel and its productionInfo
- Publication number
- JPH02156047A JPH02156047A JP30966788A JP30966788A JPH02156047A JP H02156047 A JPH02156047 A JP H02156047A JP 30966788 A JP30966788 A JP 30966788A JP 30966788 A JP30966788 A JP 30966788A JP H02156047 A JPH02156047 A JP H02156047A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- less
- hardness
- creq
- ppm
- 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
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 25
- 239000010935 stainless steel Substances 0.000 title claims abstract description 21
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 9
- 238000005482 strain hardening Methods 0.000 claims abstract description 16
- 238000001816 cooling Methods 0.000 claims abstract description 14
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 12
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 11
- 230000032683 aging Effects 0.000 claims abstract description 10
- 239000000203 mixture Substances 0.000 claims abstract description 10
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 7
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 7
- 229910052760 oxygen Inorganic materials 0.000 claims abstract 4
- 239000000463 material Substances 0.000 claims description 11
- 239000012535 impurity Substances 0.000 claims description 6
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 abstract description 17
- 229910001566 austenite Inorganic materials 0.000 abstract description 15
- 238000000034 method Methods 0.000 abstract description 6
- 229910000859 α-Fe Inorganic materials 0.000 abstract description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 abstract 1
- 238000010438 heat treatment Methods 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 11
- 238000000137 annealing Methods 0.000 description 8
- 229910000831 Steel Inorganic materials 0.000 description 5
- 230000005389 magnetism Effects 0.000 description 5
- 239000010959 steel Substances 0.000 description 5
- 230000035699 permeability Effects 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000000087 stabilizing effect Effects 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 238000003483 aging Methods 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000004891 communication Methods 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 229920006395 saturated elastomer Polymers 0.000 description 2
- 229910018487 Ni—Cr Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000000593 degrading effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000012266 salt solution Substances 0.000 description 1
- 238000003860 storage Methods 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
- 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)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、通信機器、音響製品、コンピューター関連機
器および精密電子機器等の磁気を利用する機器等各種産
業機械の部品等に好適な、ビッカース硬さ４５０以上か
つ透磁率ｉ、ｏｏｓ以下の高硬度非磁性ステンレス鋼お
よびその製造方法に関するものである。Detailed Description of the Invention [Industrial Field of Application] The present invention provides a Vickers material suitable for parts of various industrial machines such as communication equipment, audio products, computer-related equipment, and precision electronic equipment that utilize magnetism. The present invention relates to a high hardness nonmagnetic stainless steel having a hardness of 450 or more and a magnetic permeability of i, oos or less, and a method for manufacturing the same.
上述のような高硬度でかつ非磁性であることが要求され
る部品としては、画像音声記憶装置（以下ＶＴＲと呼ぶ
）に用いられるシリンダー軸、キャプスタイン軸及びＶ
ＴＲカセットテープ内に使用されるガイドローラー、ガ
イドビン、板ばねや線ばね等の各種ばねがある。また、
通信機器、音響製品、コンピューター関連機器、精密電
子機器等に用いられる各種ばねやプーリー、チェーン。The above-mentioned parts that are required to be highly hard and non-magnetic include cylinder shafts, Capstein shafts, and VTRs used in video and audio storage devices (hereinafter referred to as VTRs).
There are various types of springs used in TR cassette tapes, such as guide rollers, guide bins, leaf springs, and wire springs. Also,
Various springs, pulleys, and chains used in communication equipment, audio products, computer-related equipment, precision electronic equipment, etc.
シャフト、ローブ等も高硬度でかつ非磁性であることが
要求される。さらに、低温装置等に非磁性かつ高硬度が
要求される部品もある。これらの部品は、耐錆性も要求
されており、この点からオーステナイト系ステンレス鋼
が材料として使用される場合が多い。−船釣には、常温
で安定なオーステナイト組織を有する５ＵＳ３０５．５
ＵＳ３１６等のステンレス鋼が従来多く使用されている
。The shaft, lobes, etc. are also required to be highly hard and non-magnetic. Furthermore, there are parts that are required to be non-magnetic and highly hard, such as in low-temperature equipment. These parts are also required to have rust resistance, and from this point of view austenitic stainless steel is often used as the material. -For boat fishing, 5US305.5 has an austenite structure that is stable at room temperature.
Stainless steel such as US316 has been commonly used.
しかし、上述のオーステナイト系ステンレス鋼を高硬度
化するためには冷間加工を施す必要があり、冷間加工を
施すと加工誘起マルテンサイトの生成により非磁性を確
保できなくなる。However, in order to increase the hardness of the austenitic stainless steel mentioned above, it is necessary to perform cold working, and when cold working is performed, nonmagnetic properties cannot be ensured due to the formation of work-induced martensite.
ステンレス鋼を高硬度化するには、Ｃ，Ｎを多量に添加
し固溶硬化を利用する方法があるが、この方法では結晶
粒界等に炭窒化物が生成し耐錆性を劣化させる。冷間加
工による加工硬化の利用は、オーステナイト組織を充分
安定にしなければ加工誘起マルテンサイトが生成し透磁
率を上げる場合があり、オーステナイトを安定化するに
は多量の合金元素を添加する必要があり熱間加工性を劣
化させる。また、Ｍ等を添加し析出硬化を利用する方法
もあるが、高合金化し熱間加工性が劣化する。In order to increase the hardness of stainless steel, there is a method of adding large amounts of C and N to utilize solid solution hardening, but this method produces carbonitrides at grain boundaries and the like, which deteriorates rust resistance. When using work hardening through cold working, if the austenite structure is not sufficiently stabilized, deformation-induced martensite may be generated and increase the magnetic permeability, and it is necessary to add a large amount of alloying elements to stabilize the austenite. Deteriorates hot workability. There is also a method of adding M or the like to utilize precipitation hardening, but this results in high alloying and deteriorates hot workability.
Ｎｔの一部をＭｎで置き換え、ＣおよびＮ含有量を高め
て高硬度化したオーステナイト系ステンレス鋼（特開昭
６０−１９７８５３号公報、特開昭６１−３７９５３号
公報等）が知られているが、熱間加工性、耐錆性および
高硬度非磁性を全て考慮した検討はなされていない。Austenitic stainless steels (JP-A-60-197853, JP-A-61-37953, etc.) are known in which a part of Nt is replaced with Mn and the C and N contents are increased to increase hardness. However, no studies have been conducted that take into account hot workability, rust resistance, and high hardness and nonmagnetic properties.
本発明は、従来のかかる熱間加工性および耐錆性の問題
を解決して、工業的にトラブルなく製造し得るビッカー
ス硬度４５０以上かつ透磁率１．００５以下の高硬度非
磁性ステンレス鋼およびその製造方法を提供することを
目的とする。The present invention solves the conventional hot workability and rust resistance problems and provides a high hardness non-magnetic stainless steel with a Vickers hardness of 450 or more and a magnetic permeability of 1.005 or less, which can be industrially manufactured without trouble. The purpose is to provide a manufacturing method.
（課題を解決するための手段および作用）本発明者らは
、この目的のためにＭｎ−Ｎｉ−Ｃｒ系のオーステナイ
ト系ステンレス鋼の組成を種々検討し、これを達成した
。(Means and effects for solving the problem) The present inventors have studied various compositions of Mn-Ni-Cr-based austenitic stainless steel for this purpose, and have achieved this goal.
本発明の要旨は、つぎのとおりである。The gist of the present invention is as follows.
（１） 重量％にて、Ｃ： ０．１０〜０．３０％、
Ｓｉ：０．１〜２％、Ｍｎ：１５〜２５％、Ｓ≦０．０
０６％、 Ｎｉ５４％、 Ｃｒ： １５〜２２％、Ｍｏ
：０．１０〜３％。(1) In weight%, C: 0.10 to 0.30%,
Si: 0.1-2%, Mn: 15-25%, S≦0.0
06%, Ni54%, Cr: 15-22%, Mo
:0.10~3%.
０≦０．０１％、Ｎ：０．３〜０．６％、 Ｃａ ：
０．０００１〜０．０１％、残部Ｆｅおよび不可避的不
純物からなり、かつ下記の式で示されるＮｉｅｑが１８
以上、Ｃｒｅｑが２３以下、ＰＶがＯ以下の範囲の組成
からなる高硬度非磁性ステンレス鋼。0≦0.01%, N: 0.3-0.6%, Ca:
0.0001 to 0.01%, balance Fe and unavoidable impurities, and Nieq expressed by the following formula is 18
As described above, the high hardness non-magnetic stainless steel has a composition in which Creq is 23 or less and PV is O or less.
Ｎｉｅｑ−ＮｉＸ＋３０Ｃχ÷３ＯＮ％＋０．５Ｍｎχ
・・・・・・・・・・・・（１）Ｃｒｓｑ＝Ｃｒ！＋１
．５Ｓｉ％＋Ｍｏχ・・・・・・・・・・・・・・・・
・・・・・（２）ＰＶ＝Ｓ（ｐｐｍ）＋Ｏ（ｐｐｍ）−
０，８Ｃａ（ｐｐｍ）−３０”（３）（２）重量％にて
、Ｃ： ０．１０〜０．３０％、Ｓｉ：０．１〜２％、
Ｍｎ： １５〜２５％、Ｓ≦０．００６％＋ Ｎｔ≦
４％、 Ｃｒ： １５〜２２％、 Ｍｏ： ０．１０〜
３％。Nieq-NiX+30Cχ÷3ON%+0.5Mnχ
・・・・・・・・・・・・(1)Crsq=Cr! +1
．． 5Si%+Moχ・・・・・・・・・・・・・・・
...(2) PV = S (ppm) + O (ppm) -
0.8Ca (ppm) - 30'' (3) (2) At weight%, C: 0.10 to 0.30%, Si: 0.1 to 2%,
Mn: 15-25%, S≦0.006%+Nt≦
4%, Cr: 15-22%, Mo: 0.10-
3%.
０≦０．０１％、Ｎ：０．３〜０．６％、 Ｃａ ：
０．０００１〜０．０１％、残部Ｐｅおよび不可避的不
純物からなり、かつ下記の式で示されるＮｔｅｑが１８
以上、Ｃｒｅｑが２３以下、Ｐｖが０以下の範囲の組成
からなるステンレス鋼の熱間加工材、もしくは冷間加工
材を、１０００℃以上かつ１２００℃以下の温度で焼鈍
し、５℃／ｓｅｃ、以上の冷却速度で冷却し、ついで冷
間加工することを特徴とする高硬度非磁性ステンレス鋼
の製造方法。0≦0.01%, N: 0.3-0.6%, Ca:
0.0001 to 0.01%, the balance is Pe and unavoidable impurities, and Nteq represented by the following formula is 18
As described above, hot-worked stainless steel material or cold-worked material having a composition in the range of Creq 23 or less and Pv 0 or less is annealed at a temperature of 1000°C or higher and 1200°C or lower, and then annealed at 5°C/sec. A method for producing high-hardness non-magnetic stainless steel, characterized by cooling at a cooling rate above and then cold working.
１Ｊｔｅｑ＝Ｎｉ％＋３０Ｃ％＋３０Ｎ％＋０．５Ｍｎ
χ−−−−・・・−・−（１）Ｃｒｅｑ＝Ｃｒ％＋１．
５ＳｉＸ＋Ｍｏχ ・・・・・・・・・・・・・・・・
・・・・・（２）ＰＶ＝Ｓ（ｐｐｍ）＋０（ｐｐｍ）−
０，８Ｃａ（ｐｐｍ）−３０＝（３）（３）重量％にて
、ＣＦ ０．１．０〜０．３０％、Ｓｔ：０．１〜２％
、 Ｍｎ： １５〜２５％、Ｓ≦０．００６％、 Ｎｉ
５４％、 Ｃｒ： １５〜２２％、Ｍｏ：０．１０〜３
％。1Jteq=Ni%+30C%+30N%+0.5Mn
χ−−−−・−・−(1) Creq=Cr%+1.
5SiX+Moχ・・・・・・・・・・・・・・・
...(2) PV = S (ppm) + 0 (ppm) -
0.8Ca (ppm) - 30 = (3) (3) At weight%, CF 0.1.0-0.30%, St: 0.1-2%
, Mn: 15-25%, S≦0.006%, Ni
54%, Cr: 15-22%, Mo: 0.10-3
%.
０≦０．０１％、Ｎ：０．３〜０．６％、 Ｃａ ：
０．０００１〜０．０１％、残部Ｆｅおよび不可避的不
純物からなり、かつ下記の式で示されるＮｉｅｑが１８
以上、Ｃｒａｑが２３以下、ＰｖがＯ以下の範囲の組成
からなるステンレス鋼の熱間加工材、もしくは冷間加工
材を、１０００℃以上かつ１２００℃以下の温度で焼鈍
し、５℃／ｓｅｃ、以上の冷却速度で冷却し、ついで冷
間加工し、さらに３００℃以上かつ７００℃以下の温度
で時効処理を施すことを特徴とする高硬度非磁性ステン
レス鋼の製造方法。0≦0.01%, N: 0.3-0.6%, Ca:
0.0001 to 0.01%, balance Fe and unavoidable impurities, and Nieq expressed by the following formula is 18
As described above, a hot-worked or cold-worked stainless steel material having a composition in which Craq is 23 or less and Pv is O or less is annealed at a temperature of 1000°C or more and 1200°C or less, and then annealed at 5°C/sec. A method for producing high-hardness non-magnetic stainless steel, which comprises cooling at a cooling rate above, followed by cold working, and further aging treatment at a temperature of 300°C or higher and 700°C or lower.
Ｎｉｅｑ＝Ｎｉ％＋３０Ｃ％＋３ＯＮχ十０．５Ｍｒ＋
２ − ・＝ −・＝ （１）Ｃｒｅｑ−Ｃｒ＄＋１．
５Ｓｉｘ十Ｍｏｚ・・・・・・・・・・・・・・・・・
・・・・（２）ＰＶ＝Ｓ（ｐｐｍ）十〇（ｐｐｍ）−０
，８Ｃａ（ｐｐｍ）−３０・・・・・・・本発明の対象
材は、熱間加工を行った材料あるいはさらに冷間加工を
行った材料で形状は板（ストリップおよびシート）、線
、管等いずれでもよい。Nieq=Ni%+30C%+3ONχ10.5Mr+
2 − ・= −・= (1) Creq−Cr$+1.
5Six 10Moz・・・・・・・・・・・・・・・・・・
...(2) PV = S (ppm) 10 (ppm) - 0
, 8Ca (ppm) -30...The materials targeted by the present invention are materials that have been hot worked or materials that have been further cold worked, and their shapes include plates (strips and sheets), wires, and tubes. etc. Any one is fine.
以下、本発明の構成要件の限定理由について説明する。The reasons for limiting the constituent elements of the present invention will be explained below.
本発明鋼の成分限定理由はつぎのとおりである。The reason for limiting the composition of the steel of the present invention is as follows.
Ｃは、オーステナイト安定化元素であると同時に高硬度
化に寄与する元素である。これらの効果は、０．１０％
未満では充分でなく、また０、３０％を越えるとオース
テナイト粒界に炭化物が析出し、耐錆性を劣化させる。C is an element that stabilizes austenite and at the same time contributes to increasing hardness. These effects are 0.10%
If it is less than 0.30%, it is not sufficient, and if it exceeds 0.30%, carbides will precipitate at the austenite grain boundaries, degrading the rust resistance.
従って、Ｃを０．１０〜０．３０％とした。Therefore, C was set at 0.10 to 0.30%.
Ｓｔは、加工硬化性および時効硬化性の向上を目的とし
て添加する元素であるが、０．１％未満では充分でなく
、また、２％を越えるとフェライトとオーステナイトの
２相となり非磁性を確保できない。従って、Ｓｉを０．
１〜２％とした。St is an element added for the purpose of improving work hardenability and age hardenability, but if it is less than 0.1%, it is not sufficient, and if it exceeds 2%, it becomes two phases of ferrite and austenite, ensuring non-magnetism. Can not. Therefore, Si is 0.
It was set at 1 to 2%.
Ｍｎは、安価にオーステナイト組織を安定化させる作用
があり、鋼の非磁性を確保するために必要な元素である
。また、窒素の固溶量を増大させる作用がある。この効
果は１５％未満では充分でなく、また２５％を越えると
その効果が飽和する。Mn has the effect of stabilizing the austenite structure at a low cost, and is an element necessary to ensure the nonmagnetism of steel. It also has the effect of increasing the amount of solid solution of nitrogen. This effect is not sufficient if it is less than 15%, and the effect is saturated if it exceeds 25%.
従って、Ｍｎを１５〜２５％とした。Therefore, Mn was set at 15 to 25%.
Ｓは、０．００６％を越えると熱間加工性を阻害する。When S exceeds 0.006%, hot workability is inhibited.
従ってＳを０．００６％以下とした。Therefore, S was set to 0.006% or less.
Ｎｉは、有力なオーステナイト安定化元素であり、非磁
性を確保するためには必要な元素であるが、４％を越え
ると加工硬化を低下させる。従って、Ｎｉを４％以下と
した。Ni is a powerful austenite stabilizing element and is a necessary element to ensure nonmagnetism, but if it exceeds 4%, work hardening decreases. Therefore, the Ni content was set to 4% or less.
Ｃｒは、耐錆性の点から１５％未満では充分でなく、ま
た２２％を越えるとフェライトとオーステナイトの２相
となり非磁性を確保できない。従って、Ｃｒを１５〜２
２％とした。If Cr is less than 15%, it is not sufficient from the viewpoint of rust resistance, and if it exceeds 22%, it becomes two phases of ferrite and austenite, making it impossible to ensure nonmagnetism. Therefore, Cr is 15 to 2
It was set at 2%.
Ｍｏは、炭窒化物の析出の抑制を図り耐錆性を向上させ
、さらに時効硬化性を向上させる元素であるが、その効
果は０．１０％未満では充分でなく、３％を越えるとフ
ェライトとオーステナイトの２相となり非磁性を確保で
きない。従って、Ｍｏを０．１０〜３％とした。Mo is an element that suppresses the precipitation of carbonitrides, improves rust resistance, and further improves age hardenability, but its effect is insufficient if it is less than 0.10%, and if it exceeds 3%, it will cause ferrite. Since it has two phases, ie, austenite and austenite, non-magnetism cannot be ensured. Therefore, Mo was set at 0.10 to 3%.
０は、０．０１％を越えると熱間加工性を阻害する。従
って、０を０．０１％以下とした。0 inhibits hot workability when it exceeds 0.01%. Therefore, 0 was set to 0.01% or less.
Ｎは、Ｃと同様オーステナイト安定化元素であると同時
に固溶硬化に寄与する元素である。この効果は、０．３
％未満では充分でなく、０．６％を越えると鋼塊中にブ
ローホールが発生し熱間加工性を低下させる。従って、
Ｎを０．３〜０．６％とした。Like C, N is an austenite stabilizing element and at the same time an element that contributes to solid solution hardening. This effect is 0.3
If it is less than 0.6%, it is not sufficient, and if it exceeds 0.6%, blowholes will occur in the steel ingot, reducing hot workability. Therefore,
N was set at 0.3 to 0.6%.
Ｃａは熱間加工性を向上させる元素であり、その効果は
０．０００１％未満では充分でなく、また０、０１％を
越えて添加してもその効果が飽和すると共にコスト上昇
を招き好ましくない。従って、Ｃａを０．０００１〜０
．０１％とした。Ca is an element that improves hot workability, and its effect is not sufficient if it is less than 0.0001%, and if it is added in excess of 0.01%, the effect is saturated and the cost increases, which is not preferable. . Therefore, Ca is 0.0001~0
．． It was set as 01%.
Ｎｉ＠ｑはオーステナイト安定度を示す指標であり、１
８未満では焼鈍後もしくは冷間加工後の非磁性を確保で
きない。従って、Ｎｉ＠ｑを１８以上とした。Ni@q is an index showing austenite stability, and is 1
If it is less than 8, non-magnetism after annealing or cold working cannot be ensured. Therefore, Ni@q was set to 18 or more.
Ｃｒｅｑはフェライト安定度を示す指標であり、２３を
越えるとフェライトとオーステナイトの２相となり非磁
性を確保できない。従って、Ｃｒｅｑを２３以下とした
。Creq is an index indicating ferrite stability, and if it exceeds 23, two phases of ferrite and austenite occur, and nonmagnetism cannot be ensured. Therefore, Creq was set to 23 or less.
ｐｖは熱間加工性を示す指標であり、０を越えると熱間
加工時に割れる等の問題が生じる。従って、ｐｖを０以
下とした。pv is an index showing hot workability, and if it exceeds 0, problems such as cracking will occur during hot working. Therefore, pv was set to 0 or less.
請求項（２）の製造条件の限定理由はつぎのとおりであ
る。The reasons for limiting the manufacturing conditions in claim (2) are as follows.
焼鈍温度は１０００℃未満では充分再結晶せず、また炭
窒化物の固溶が充分でなく高硬度が得られず、さらに、
炭窒化物の生成により耐錆性を低下させるおそれがある
。また、１２００℃を越えると結晶粒が粗大化し、硬度
の低下を招くおそれがある。従って、焼鈍温度を１００
０℃以上かつ１２００℃以下とした。If the annealing temperature is less than 1000°C, sufficient recrystallization will not occur, and solid solution of carbonitrides will not be sufficient, making it impossible to obtain high hardness.
The formation of carbonitrides may reduce rust resistance. Furthermore, if the temperature exceeds 1200°C, the crystal grains may become coarse, which may lead to a decrease in hardness. Therefore, the annealing temperature is set to 100
The temperature was 0°C or higher and 1200°C or lower.
さらに、本発明に係わる如き高Ｃ，Ｎステンレス鋼は、
冷却速度が遅いと炭窒化物を生成し耐錆性を劣化させる
おそれがある０本発明においては、上記成分の材料を上
記条件で焼鈍した後の冷却速度が５℃／ｓｅｃ、未満で
あると、良好な耐錆性が得られない場合がある。従って
、本発明鋼の焼鈍後の冷却速度を５°（／ｓｅｃ、以上
とした。Furthermore, the high C, N stainless steel according to the present invention is
If the cooling rate is slow, carbonitrides may be generated and rust resistance may deteriorate.In the present invention, if the cooling rate after annealing the material with the above components under the above conditions is less than 5°C/sec. , good rust resistance may not be obtained. Therefore, the cooling rate after annealing of the steel of the present invention was set to 5° (/sec) or more.
冷間加工は高硬度を得るために行い、加工度を３０％以
上とするのが好ましい。Cold working is performed to obtain high hardness, and the degree of working is preferably 30% or more.
請求項（３）は、冷間加工後、さらに時効処理を施して
より高硬度とする方法に係わる。請求項（３）における
時効処理条件の限定理由はつぎのとおりである。Claim (3) relates to a method of further performing an aging treatment after cold working to obtain higher hardness. The reasons for limiting the aging treatment conditions in claim (3) are as follows.
Ｍｏを添加することにより時効硬化特性が向上するが、
時効処理温度が３００℃未満では充分な時効硬化特性が
得られず、７００℃を越えると過時効を招き硬度が低下
する。従って、時効処理温度を３００℃以上かつ７００
’Ｃ以下とした。Although the age hardening properties are improved by adding Mo,
If the aging treatment temperature is less than 300°C, sufficient age-hardening characteristics cannot be obtained, and if it exceeds 700°C, over-aging will occur and the hardness will decrease. Therefore, the aging treatment temperature should be set to 300°C or higher and 700°C.
'C or below.
第１表に示す成分のステンレス鋼を熱間加工したときの
熱間加工性を第２表に示す。Ｏは熱間加工時に割れが認
められなかったもの、×は割れが認められたものである
。本発明鋼のＡ−Ｆ鋼は、いずれも熱間加工性が優れて
いる。Table 2 shows the hot workability of stainless steels having the components shown in Table 1. O indicates that no cracks were observed during hot working, and × indicates that cracks were observed. All of the A-F steels of the present invention have excellent hot workability.
つぎに、第１表のステンレス鋼を熱間加工し、さらに冷
間加工した後、各種条件で焼鈍し冷却し冷間加工した状
態での硬度および耐錆性と、さらに時効処理した状態で
の硬度および耐錆性を第２表に示す、耐錆性のＯは１５
％および５％食塩水に１００時間浸漬して発錆しなかっ
たもの、Δは１５％では発錆したが５％では発錆しなか
ったもの、×は１５％でも５％でも発錆したものである
。Next, we will examine the hardness and rust resistance of the stainless steels listed in Table 1 after hot working, cold working, annealing and cooling under various conditions, and cold working, and the hardness and rust resistance of the stainless steels after further aging treatment. The hardness and rust resistance are shown in Table 2, and the rust resistance O is 15
% and 5% salt solution for 100 hours without rusting, Δ indicates rusting at 15% but not 5%, × indicates rusting at both 15% and 5%. It is.
第２表中の、Ｎα１〜Ｎα１０が本発明例、ｋｌｌ〜Ｎ
α１４が比較例である。阻７およびＮＣＬ８は請求項（
１）のみに対応し成分は本発明条件を満足しているが、
ＮＯ，７は焼鈍温度が、阻８は焼鈍後の冷却速度が請求
項（２）および（３）の条件をはずれるので、耐錆性が
や〜劣るが、用途によっては充分使用に耐え得る。また
Ｎα１〜Ｎα６およびＮα１〜Ｎα１０において、時効
処理を行った請求項（３）に対応するものは、冷間加工
状態の請求項（２）に対応するものよりも硬度が向上し
ている。しかし、両者共にＨｖ４５０以上の高硬度と、
１．００５以下の透磁率が得られている。In Table 2, Nα1 to Nα10 are examples of the present invention, kll to N
α14 is a comparative example. 7 and NCL8 are claimed in claim (
Although it only corresponds to 1) and the components satisfy the conditions of the present invention,
Since the annealing temperature for No. 7 and the cooling rate after annealing for No. 8 are outside the conditions of claims (2) and (3), the rust resistance is somewhat inferior, but it can be used satisfactorily depending on the application. Moreover, among Nα1 to Nα6 and Nα1 to Nα10, those corresponding to claim (3) subjected to aging treatment have improved hardness than those corresponding to claim (2) in a cold worked state. However, both have high hardness of Hv450 or more,
A magnetic permeability of 1.005 or less has been obtained.
本発明により、耐錆性に優れた高硬度非磁性ステンレス
網が、熱間加工性の問題なく製造でき、磁気を利用する
電子機器の部品、特にＶＴＲあるいはＶＴＲカセットテ
ープの各穂軸に使用して、機器の磁気特性を乱すことな
く、耐誘性、耐摩耗性に効果を発揮する。According to the present invention, a high-hardness non-magnetic stainless steel mesh with excellent rust resistance can be manufactured without problems in hot workability, and can be used for parts of electronic devices that use magnetism, especially for each cob of a VTR or VTR cassette tape. This provides effective induction and abrasion resistance without disturbing the magnetic properties of the device.
Claims (3)
０．１〜２％、Ｍｎ：１５〜２５％、Ｓ≦０．００６％
、Ｎｉ≦４％、Ｃｒ：１５〜２２％、Ｍｏ：０．１０〜
３％、Ｏ≦０．０１％、Ｎ：０．３〜０．６％、Ｃａ：
０．０００１〜０．０１％、残部Ｆｅおよび不可避的不
純物からなり、かつ下記の式で示されるＮｉｅｑが１８
以上、Ｃｒｅｑが２３以下、ＰＶが０以下の範囲の組成
からなる高硬度非磁性ステンレス鋼。 Ｎｉｅｑ＝Ｎｉ％＋３０Ｃ％＋３０Ｎ％＋０．５Ｍｎ％
・・・・・・・・・・・・（１） Ｃｒｅｑ＝Ｃｒ％＋１．５Ｓｉ％＋Ｍｏ％・・・・・・
・・・・・・・・・・・・（２） ＰＶ＝Ｓ（ｐｐｍ）＋Ｏ（ｐｐｍ）−０．８Ｃａ（ｐｐ
ｍ）−３０・・・・・・・（３）(1) In weight%, C: 0.10-0.30%, Si:
0.1-2%, Mn: 15-25%, S≦0.006%
, Ni≦4%, Cr: 15-22%, Mo: 0.10-
3%, O≦0.01%, N: 0.3-0.6%, Ca:
0.0001 to 0.01%, balance Fe and unavoidable impurities, and Nieq expressed by the following formula is 18
As described above, the high hardness nonmagnetic stainless steel has a composition in which Creq is 23 or less and PV is 0 or less. Nieq=Ni%+30C%+30N%+0.5Mn%
・・・・・・・・・・・・(1) Creq=Cr%+1.5Si%+Mo%・・・・・・
・・・・・・・・・・・・(2) PV=S(ppm)+O(ppm)−0.8Ca(pp
m)-30・・・・・・(3)
０．１〜２％、Ｍｎ：１５〜２５％、Ｓ≦０．００６％
、Ｎｉ≦４％、Ｃｒ：１５〜２２％、Ｍｏ：０．１０〜
３％、Ｏ≦０．０１％、Ｎ：０．３〜０．６％、Ｃａ：
０．０００１〜０．０１％、残部Ｆｅおよび不可避的不
純物からなり、かつ下記の式で示されるＮｉｅｑが１８
以上、Ｃｒｅｑが２３以下、ＰＶが０以下の範囲の組成
からなるステンレス鋼の熱間加工材、もしくは冷間加工
材を、１０００℃以上かつ１２００℃以下の温度で焼鈍
し、５℃／ｓｅｃ．以上の冷却速度で冷却し、ついで冷
間加工することを特徴とする高硬度非磁性ステンレス鋼
の製造方法。 Ｎｉｅｑ＝Ｎｉ％＋３０Ｃ％＋３０Ｎ％＋０．５Ｍｎ％
・・・・・・・・・・・・（１） Ｃｒｅｑ＝Ｃｒ％＋１．５Ｓｉ％＋Ｍｏ％・・・・・・
・・・・・・・・・・・・（２） ＰＶ＝Ｓ（ｐｐｍ）＋Ｏ（ｐｐｍ）−０．８Ｃａ（ｐｐ
ｍ）−３０・・・・・・・（３）(2) In weight%, C: 0.10-0.30%, Si:
0.1-2%, Mn: 15-25%, S≦0.006%
, Ni≦4%, Cr: 15-22%, Mo: 0.10-
3%, O≦0.01%, N: 0.3-0.6%, Ca:
0.0001 to 0.01%, balance Fe and unavoidable impurities, and Nieq expressed by the following formula is 18
As described above, a hot-worked or cold-worked stainless steel material having a composition in the range of Creq of 23 or less and PV of 0 or less is annealed at a temperature of 1000°C or higher and 1200°C or lower, and then annealed at 5°C/sec. A method for producing high-hardness non-magnetic stainless steel, characterized by cooling at a cooling rate above and then cold working. Nieq=Ni%+30C%+30N%+0.5Mn%
・・・・・・・・・・・・(1) Creq=Cr%+1.5Si%+Mo%・・・・・・
・・・・・・・・・・・・(2) PV=S(ppm)+O(ppm)−0.8Ca(pp
m)-30・・・・・・(3)
０．１〜２％、Ｍｎ：１５〜２５％、Ｓ≦０．００６％
、Ｎｉ≦４％、Ｃｒ：１５〜２２％、Ｍｏ：０．１０〜
３％、Ｏ≦０．０１％、Ｎ：０．３〜０．６％、Ｃａ：
０．０００１〜０．０１％、残部Ｆｅおよび不可避的不
純物からなり、かつ下記の式で示されるＮｉｅｑが１８
以上、Ｃｒｅｑが２３以下、ＰＶが０以下の範囲の組成
からなるステンレス鋼の熱間加工材、もしくは冷間加工
材を、１０００℃以上かつ１２００℃以下の温度で焼鈍
し、５℃／ｓｅｃ．以上の冷却速度で冷却し、ついで冷
間加工し、さらに３００℃以上かつ７００℃以下の温度
で時効処理を施すことを特徴とする高硬度非磁性ステン
レス鋼の製造方法。 Ｎｉｅｑ＝Ｎｉ％＋３０Ｃ％＋３０Ｎ％＋０．５Ｍｎ％
・・・・・・・・・・・・（１） Ｃｒｅｑ＝Ｃｒ％＋１．５Ｓｉ％＋Ｍｏ％・・・・・・
・・・・・・・・・・・（２） ＰＶ＝Ｓ（ｐｐｍ）＋Ｏ（ｐｐｍ）−０．８Ｃａ（ｐｐ
ｍ）−３０・・・・・・・（３）(3) In weight%, C: 0.10-0.30%, Si:
0.1-2%, Mn: 15-25%, S≦0.006%
, Ni≦4%, Cr: 15-22%, Mo: 0.10-
3%, O≦0.01%, N: 0.3-0.6%, Ca:
0.0001 to 0.01%, balance Fe and unavoidable impurities, and Nieq expressed by the following formula is 18
As described above, a hot-worked or cold-worked stainless steel material having a composition in the range of Creq of 23 or less and PV of 0 or less is annealed at a temperature of 1000°C or higher and 1200°C or lower, and then annealed at 5°C/sec. A method for producing high-hardness non-magnetic stainless steel, which comprises cooling at a cooling rate above, followed by cold working, and further aging treatment at a temperature of 300°C or higher and 700°C or lower. Nieq=Ni%+30C%+30N%+0.5Mn%
・・・・・・・・・・・・(1) Creq=Cr%+1.5Si%+Mo%・・・・・・
・・・・・・・・・・・・(2) PV=S(ppm)+O(ppm)−0.8Ca(pp
m)-30・・・・・・(3)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63309667A JPH0759723B2 (en) | 1988-12-07 | 1988-12-07 | High hardness non-magnetic stainless steel manufacturing method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63309667A JPH0759723B2 (en) | 1988-12-07 | 1988-12-07 | High hardness non-magnetic stainless steel manufacturing method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02156047A true JPH02156047A (en) | 1990-06-15 |
| JPH0759723B2 JPH0759723B2 (en) | 1995-06-28 |
Family
ID=17995817
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63309667A Expired - Lifetime JPH0759723B2 (en) | 1988-12-07 | 1988-12-07 | High hardness non-magnetic stainless steel manufacturing method |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0759723B2 (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008512563A (en) * | 2004-09-07 | 2008-04-24 | エネルギーテクニック エッセン ゲーエムベーハー | Ultra high strength austenitic stainless steel |
| JP2011006776A (en) * | 2009-04-27 | 2011-01-13 | Daido Steel Co Ltd | High corrosion-resistant, high-strength and non-magnetic stainless steel, high corrosion-resistant, high-strength and non-magnetic stainless steel product and method for producing the same |
| CN103849715A (en) * | 2014-03-18 | 2014-06-11 | 河北师范大学 | Thermal treatment method for reducing magnesium of austenitic stainless steel castings |
| DE202014005288U1 (en) | 2013-06-27 | 2014-07-11 | Nivarox-Far S.A. | Watch spring made of austenitic stainless steel |
| EP2924514A1 (en) | 2014-03-24 | 2015-09-30 | Nivarox-FAR S.A. | Clockwork spring made of austenitic stainless steel |
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| JPS60238453A (en) * | 1984-05-14 | 1985-11-27 | Toshiba Corp | Nonmagnetic metallic belt for drive and its manufacture |
| JPS61238943A (en) * | 1985-04-15 | 1986-10-24 | Kobe Steel Ltd | High-strength non-magnetic steel excelling in rust resistance |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008512563A (en) * | 2004-09-07 | 2008-04-24 | エネルギーテクニック エッセン ゲーエムベーハー | Ultra high strength austenitic stainless steel |
| JP4798461B2 (en) * | 2004-09-07 | 2011-10-19 | エネルギーテクニック エッセン ゲーエムベーハー | Ultra high strength austenitic stainless steel |
| JP2011006776A (en) * | 2009-04-27 | 2011-01-13 | Daido Steel Co Ltd | High corrosion-resistant, high-strength and non-magnetic stainless steel, high corrosion-resistant, high-strength and non-magnetic stainless steel product and method for producing the same |
| DE202014005288U1 (en) | 2013-06-27 | 2014-07-11 | Nivarox-Far S.A. | Watch spring made of austenitic stainless steel |
| WO2014206582A2 (en) | 2013-06-27 | 2014-12-31 | Nivarox-Far S.A. | Timepiece spring made of austenitic stainless steel |
| US10048649B2 (en) | 2013-06-27 | 2018-08-14 | Nivarox-Far S.A. | Timepiece spring made of austenitic stainless steel |
| CN103849715A (en) * | 2014-03-18 | 2014-06-11 | 河北师范大学 | Thermal treatment method for reducing magnesium of austenitic stainless steel castings |
| EP2924514A1 (en) | 2014-03-24 | 2015-09-30 | Nivarox-FAR S.A. | Clockwork spring made of austenitic stainless steel |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0759723B2 (en) | 1995-06-28 |
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