JPH0678566B2 - Method for producing stainless steel foil with excellent fatigue properties - Google Patents
Method for producing stainless steel foil with excellent fatigue propertiesInfo
- Publication number
- JPH0678566B2 JPH0678566B2 JP13939588A JP13939588A JPH0678566B2 JP H0678566 B2 JPH0678566 B2 JP H0678566B2 JP 13939588 A JP13939588 A JP 13939588A JP 13939588 A JP13939588 A JP 13939588A JP H0678566 B2 JPH0678566 B2 JP H0678566B2
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- less
- fatigue properties
- steel foil
- inclusions
- 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.)
- Expired - Lifetime
Links
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)
- Metal Rolling (AREA)
- Heat Treatment Of Steel (AREA)
Description
【発明の詳細な説明】 本発明は、通信機器、音響製品、コンピューター関連機
器および精密電子部品等の機器等各種産業機器の部品等
に好適な、疲労特性に優れたステンレス鋼箔の製造方法
に関するものである。The present invention relates to a method for producing a stainless steel foil having excellent fatigue properties, which is suitable for parts of various industrial equipment such as communication equipment, audio products, computer-related equipment and equipment such as precision electronic parts. It is a thing.
〔従来の技術〕 上述の部品としては、フロッピーディスクドライブ用の
スチールベルト、ジンバルバネ、キーボード用スイッチ
バネ等の各種スイッチバネ等がある。これらは、いずれ
も高疲労特性が必要であるが、板厚が100μｍ以下のた
め大型介在物が存在すると疲労特性を劣化させる虞れが
ある。[Prior Art] As the above-mentioned parts, there are various switch springs such as a steel belt for a floppy disk drive, a gimbal spring, and a switch spring for a keyboard. All of these require high fatigue properties, but since the plate thickness is 100 μm or less, the presence of large inclusions may deteriorate the fatigue properties.
ステンレス鋼の介在物を微細化させ疲労特性を向上させ
る方法として、製品中のAlとＯ量を規定する方法が特開
昭60−33895号公報にて知られているが、冷間加工にる
影響は考慮されていない。As a method of refining the inclusions of stainless steel to improve the fatigue characteristics, a method of defining the amounts of Al and O in the product is known in JP-A-60-33895, but cold working is used. Impact is not considered.
本発明は、従来のかかる課題を改善するために成分とス
テンレス鋼の冷間加工率に着目し、疲労特性に優れたス
テンレス鋼箔を提供することを目的とする。An object of the present invention is to provide a stainless steel foil having excellent fatigue properties, focusing on the components and the cold workability of the stainless steel in order to improve such conventional problems.
〔課題を解決するための手段および作用〕 本発明は、重量％にて、C;0.02〜0.2％、Si;0.1〜２
％、Mn;0.1〜２％、Ｓ≦0.006％、Ni;6.0〜10.5％、Cr;
16〜20％、Al≦0.01％、Ｏ≦0.01％、Mg≦0.001％、Ca;
0.0001〜0.005％、N;0.01〜0.2％、残部Feからなるステ
ンレス鋼を冷間圧延と焼鈍を繰り返して冷間圧延の総圧
延率98％以上で最終板厚100μｍ以下とし、介在物の大
きさを７μｍ以下とする疲労特性に優れたステンレス鋼
箔の製造方法である。[Means and Actions for Solving the Problems] In the present invention, C: 0.02 to 0.2% and Si: 0.1 to 2 in% by weight.
%, Mn; 0.1 to 2%, S ≦ 0.006%, Ni; 6.0 to 10.5%, Cr;
16-20%, Al ≦ 0.01%, O ≦ 0.01%, Mg ≦ 0.001%, Ca;
Stainless steel consisting of 0.0001 to 0.005%, N; 0.01 to 0.2%, and balance Fe is repeatedly cold-rolled and annealed to achieve a final rolling thickness of 98% or more and a final plate thickness of 100 μm or less. Is 7 μm or less and is a method for producing a stainless steel foil having excellent fatigue properties.
本発明の対象材は、熱間圧延を行いさらに冷間加工を行
った板厚100μｍ以下の箔である。The target material of the present invention is a foil having a sheet thickness of 100 μm or less which is hot-rolled and cold-worked.
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 features of the present invention will be described below.
Ｃは、高強度化に寄与する元素であるが、その効果は0.
02％未満ではバネ特性として十分でなく、0.2％を越え
ると炭化物が析出し耐銹性を劣化させる虞がある。従っ
て、Ｃは0.02〜0.2％とした。C is an element that contributes to strengthening, but its effect is 0.
If it is less than 02%, the spring properties are not sufficient, and if it exceeds 0.2%, carbides may precipitate to deteriorate the rust resistance. Therefore, C is set to 0.02 to 0.2%.
Siは、バネ特性を得るための加工硬化性を高める元素で
あるが、その効果は0.1％未満では十分でなく、２％を
越えるとオーステナイト・フェライトの２相となり熱間
加工性を劣化させる。従って、Siを0.1〜２％とした。Si is an element that enhances work hardenability for obtaining spring characteristics, but its effect is not sufficient if it is less than 0.1%, and if it exceeds 2%, it becomes two phases of austenite and ferrite and deteriorates hot workability. Therefore, Si is set to 0.1 to 2%.
Mnは、熱間加工性を向上させる元素であるがその効果は
0.1％未満では十分でなく、２％を越えると、その効果
が飽和する。従って、Mnを0.1〜２％とした。Mn is an element that improves hot workability, but its effect is
If it is less than 0.1%, it is not enough, and if it exceeds 2%, its effect is saturated. Therefore, Mn is set to 0.1 to 2%.
Ｓは、0.006％を越えると熱間加工性を阻害させる。従
って、Ｓを0.006％以下とした。If S exceeds 0.006%, hot workability is impaired. Therefore, S is set to 0.006% or less.
Niは、オーステナイト安定化元素であり、本発明におい
ては加工硬化によりバネ特性を得るために準安定オース
テナイト組織にする必要がある。そのため、Niを6.0〜1
0.5％とした。Ni is an austenite stabilizing element, and in the present invention, it is necessary to form a metastable austenite structure in order to obtain spring characteristics by work hardening. Therefore, Ni is 6.0-1
It was set to 0.5%.
Crは、耐銹性を向上させる元素であるが、その効果は、
16％未満では十分でない。20％を越えると、オーステナ
イト・フェライトの２相となり熱間加工性を劣化させ、
さらに加工硬化し難くなる。従って、Crを16〜20％とし
た。Cr is an element that improves rust resistance, but its effect is
Less than 16% is not enough. If it exceeds 20%, it becomes two phases of austenite and ferrite, which deteriorates hot workability,
Furthermore, it becomes difficult to work and harden. Therefore, Cr is set to 16 to 20%.
Alは、0.01％を越えると粗大なAl２Ｏ３系介在物を形成
し、疲労特性を劣化させる。従って、Alを0.01％以下と
した。If Al exceeds 0.01%, coarse Al 2 O 3 -based inclusions are formed, which deteriorates fatigue characteristics. Therefore, Al is set to 0.01% or less.
Ｏは、0.01％を越えると熱間加工性を阻害するばかりで
なく、Alと結合して粗大なAl２Ｏ３系介在物を形成し、
疲労特性を劣化させる。従って、Ｏを0.01％以下とし
た。When O exceeds 0.01%, it not only hinders hot workability, but also binds with Al to form coarse Al 2 O 3 -based inclusions,
Deteriorates fatigue characteristics. Therefore, O is set to 0.01% or less.
Mgは、0.001％を越えると熱間加工性を阻害するばかり
でなく、介在物を形成し疲労特性を劣化させる。従っ
て、Mgを0.001％以下とした。When Mg exceeds 0.001%, it not only hinders hot workability, but also forms inclusions and deteriorates fatigue properties. Therefore, Mg is set to 0.001% or less.
Caは、微細分散したCa介在物を生成し、それを核として
分散したAl２Ｏ３系介在物を生成させる効果がある。そ
の効果は0.0001％未満では十分でなく、0.005％を越え
ると飽和する。従って、Caを0.0001〜0.005％とした。Ca has an effect of forming finely dispersed Ca inclusions and Al 2 O 3 -based inclusions dispersed with the inclusions as nuclei. The effect is not sufficient if it is less than 0.0001%, and is saturated if it exceeds 0.005%. Therefore, Ca is set to 0.0001 to 0.005%.
Ｎは、高強度化に寄与する元素であるが、その効果は0.
01％未満ではバネ特性として充分でなく、0.2％を越え
ると鋳片にプローホールを発生させる虞がある。従っ
て、Ｎを0.01〜0.2％とした。N is an element that contributes to strengthening, but its effect is 0.
If it is less than 01%, the spring characteristics are not sufficient, and if it exceeds 0.2%, slabs may be vulcanized. Therefore, N is set to 0.01 to 0.2%.
このような組成のステンレス鋼の熱延板を冷間圧延と焼
鈍を繰り返して板厚100μｍ以下の箔にする。A hot rolled sheet of stainless steel having such a composition is repeatedly subjected to cold rolling and annealing to form a foil having a sheet thickness of 100 μm or less.
熱延板から最終板厚までの総圧延率は、98％以上とす
る。成分を前述のように限定して介在物を微細化して
も、冷間圧延率98％未満では大きな介在物に起因してバ
ネの疲労特性が劣化する。従って、熱延板から最終板厚
までの総圧延率を98％以上とした。The total rolling rate from the hot rolled sheet to the final sheet thickness shall be 98% or more. Even if the inclusions are refined by limiting the components as described above, if the cold rolling ratio is less than 98%, the fatigue properties of the spring deteriorate due to the large inclusions. Therefore, the total rolling rate from the hot rolled sheet to the final sheet thickness is set to 98% or more.
介在物の大きさは７μｍを越えると板厚100μｍ以下の
箔の疲労特性を低下させる。従って、最終製品での介在
物の大きさは７μｍ以下とした。If the size of inclusions exceeds 7 μm, the fatigue properties of foils with a plate thickness of 100 μm or less are deteriorated. Therefore, the size of inclusions in the final product is set to 7 μm or less.
かすして、上記のような成分および冷間圧延条件によ
り、ステンレス鋼箔を製造すれば疲労特性に著しく優れ
たステンレス鋼箔が得られる。If the stainless steel foil is manufactured according to the above components and the cold rolling conditions, it is possible to obtain a stainless steel foil having excellent fatigue properties.
第１表に示すようなステンレス鋼を電気炉で溶製しAOD
炉で精錬し、連続鋳造によってスラブとした後、熱間圧
延を施した。次いで、熱延板の焼鈍・酸洗を行った後、
中間冷間圧延および中間焼鈍を行い、最終冷間圧延率を
40％以上与え、板厚100μｍ以下の箔を製造した。AOD produced by melting stainless steel as shown in Table 1 in an electric furnace
After refining in a furnace and making a slab by continuous casting, hot rolling was performed. Next, after annealing and pickling the hot rolled sheet,
Perform intermediate cold rolling and annealing to determine the final cold rolling ratio.
A foil having a plate thickness of 100 μm or less was manufactured by applying 40% or more.
本発明方法および比較法による製造条件と、熱延板およ
び最終製品の板厚、最終製品での最大介在物の大きさ、
最終製品の引張強さおよび疲労限を第２表に示す。介在
物の大きさは視野25mm2内の介在物の最大大きさを示
す。引張強さは圧延方向と平行な方向より採取し、JIS
Ｚ 2241に従い測定した。疲労試験は、プーリー曲げ
疲労試験機を用いて、10７回での疲労限を求めた。Manufacturing conditions according to the method of the present invention and the comparative method, the thickness of the hot-rolled sheet and the final product, the size of the maximum inclusions in the final product,
The tensile strength and fatigue limit of the final product are shown in Table 2. The size of the inclusions indicates the maximum size of the inclusions within the field of view of 25 mm 2 . Tensile strength is measured in the direction parallel to the rolling direction, and JIS
It was measured according to Z 2241. In the fatigue test, a pulley bending fatigue tester was used to determine the fatigue limit at 10 7 times.
第２表より本発明法は比較法に比べ高疲労特性であり、
ばね用素材として非常に優れていることがわかる。From Table 2, the method of the present invention has higher fatigue characteristics than the comparative method,
It can be seen that it is extremely excellent as a spring material.
〔発明の効果〕 以上のことから明らかな如く、本発明法によりステンレ
ス鋼箔を製造すれば、高疲労特性が得られ、電子機器等
の寿命が飛躍的に向上する。 [Effects of the Invention] As is clear from the above, when the stainless steel foil is manufactured by the method of the present invention, high fatigue characteristics are obtained, and the life of electronic devices and the like is dramatically improved.
Claims (1)
％、Mn;0.1〜２％、Ｓ≦0.006％、Ni;6.0〜10.5％、Cr;
16〜20％、Al≦0.01％、Ｏ≦0.01％、Mg≦0.001％、Ca;
0.0001〜0.005％、N;0.01〜0.2％、残部Feからなるステ
ンレス鋼を冷間圧延と焼鈍を繰り返して冷間圧延の総圧
延率98％以上で最終板厚100μｍ以下とし、介在物の大
きさを７μｍ以下とする疲労特性に優れたステンレス鋼
箔の製造方法。1. C: 0.02 to 0.2%, Si: 0.1 to 2 in% by weight
%, Mn; 0.1 to 2%, S ≦ 0.006%, Ni; 6.0 to 10.5%, Cr;
16-20%, Al ≦ 0.01%, O ≦ 0.01%, Mg ≦ 0.001%, Ca;
Stainless steel consisting of 0.0001 to 0.005%, N; 0.01 to 0.2%, balance Fe is repeatedly cold-rolled and annealed to achieve a final rolling thickness of 98% or more and a final plate thickness of 100 μm or less. Of 7 μm or less and a method for producing a stainless steel foil having excellent fatigue properties.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13939588A JPH0678566B2 (en) | 1988-06-08 | 1988-06-08 | Method for producing stainless steel foil with excellent fatigue properties |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13939588A JPH0678566B2 (en) | 1988-06-08 | 1988-06-08 | Method for producing stainless steel foil with excellent fatigue properties |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH01309919A JPH01309919A (en) | 1989-12-14 |
| JPH0678566B2 true JPH0678566B2 (en) | 1994-10-05 |
Family
ID=15244289
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP13939588A Expired - Lifetime JPH0678566B2 (en) | 1988-06-08 | 1988-06-08 | Method for producing stainless steel foil with excellent fatigue properties |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0678566B2 (en) |
Families Citing this family (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2978038B2 (en) * | 1993-08-16 | 1999-11-15 | 新日本製鐵株式会社 | Oxide inclusion ultrafine dispersion steel |
| JP3544488B2 (en) * | 1999-03-23 | 2004-07-21 | 新日本製鐵株式会社 | Stainless steel foil |
| US7396421B2 (en) * | 2003-08-07 | 2008-07-08 | Sumitomo Metal Industries, Ltd. | Duplex stainless steel and manufacturing method thereof |
| JP6162670B2 (en) * | 2014-10-03 | 2017-07-12 | 株式会社東京測器研究所 | Strain gauge alloys and strain gauges |
| JP7116647B2 (en) * | 2018-09-13 | 2022-08-10 | 日鉄ステンレス株式会社 | austenitic stainless steel foil |
| KR20220125344A (en) * | 2020-02-27 | 2022-09-14 | 닛테츠 스테인레스 가부시키가이샤 | Stainless steel for metal foil, stainless steel foil and manufacturing method thereof |
| WO2022014307A1 (en) * | 2020-07-17 | 2022-01-20 | 日立金属株式会社 | Stainless steel foil, spring for switch, substrate for flexible display, and manufacturing method of stainless steel foil |
| US20230407427A1 (en) | 2020-10-13 | 2023-12-21 | Nippon Steel Chemical & Material Co., Ltd. | Austenitic stainless steel foil |
| KR20230132832A (en) | 2021-03-31 | 2023-09-18 | 닛테츠 케미컬 앤드 머티리얼 가부시키가이샤 | Flexible stainless steel foil and flexible light-emitting device |
-
1988
- 1988-06-08 JP JP13939588A patent/JPH0678566B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH01309919A (en) | 1989-12-14 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP6306711B2 (en) | Martensitic steel with delayed fracture resistance and manufacturing method | |
| JP6103165B1 (en) | Hot press-formed parts | |
| KR102504491B1 (en) | Steel and enamel products | |
| KR102130233B1 (en) | Thin steel plate and plated steel sheet, and hot rolled steel sheet manufacturing method, cold rolled full hard steel sheet manufacturing method, heat treatment plate manufacturing method, thin steel sheet manufacturing method and plated steel sheet manufacturing method | |
| KR20150121061A (en) | Austenitic stainless-steel sheet and process for producing high-elastic-limit nonmagnetic steel material therefrom | |
| JP2019014933A (en) | Steel sheet and method of producing the same | |
| KR102471303B1 (en) | Martensitic stainless steel sheet, manufacturing method thereof, and spring member | |
| JP2001323342A (en) | Austenitic stainless steel excellent in fine blanking property | |
| JPH0678566B2 (en) | Method for producing stainless steel foil with excellent fatigue properties | |
| JP5849676B2 (en) | High-strength steel sheet for civil engineering and manufacturing method thereof | |
| JP6798907B2 (en) | Low magnetic austenitic stainless steel and cold-rolled steel sheet | |
| US5314549A (en) | High strength and high toughness stainless steel sheet and method for producing thereof | |
| JP2023500839A (en) | Austenitic stainless steel with improved yield ratio and method for producing the same | |
| EP0033600A2 (en) | Process for producing a steel with dual-phase structure | |
| JP2010189719A (en) | Age-hardening type stainless steel sheet for spring | |
| JP2001271143A (en) | Ferritic stainless steel excellent in ridging resistance and its production method | |
| JP2017145487A (en) | Ferrite austenite stainless steel sheet excellent in moldability and manufacturing method therefor | |
| JP6111109B2 (en) | Low Ni austenitic stainless steel sheet with excellent age hardening characteristics and method for producing the same | |
| JPH0261540B2 (en) | ||
| JP4331731B2 (en) | Austenitic stainless steel and springs made of that steel | |
| JP4606337B2 (en) | Austenitic stainless steel for coins and coins manufactured with the steel | |
| JP3582257B2 (en) | Manufacturing method of thin steel sheet with high impact energy absorption capacity | |
| JP2007302972A (en) | High-strength nonmagnetic stainless steel sheet superior in age hardening characteristics, and manufacturing method therefor | |
| JPH06235049A (en) | High strength nonmagnetic stainless steel and its production | |
| JP7215938B2 (en) | High-strength non-magnetic stainless steel sheet and mobile electronic equipment using the same |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| S111 | Request for change of ownership or part of ownership |
Free format text: JAPANESE INTERMEDIATE CODE: R313111 |
|
| R360 | Written notification for declining of transfer of rights |
Free format text: JAPANESE INTERMEDIATE CODE: R360 |
|
| R371 | Transfer withdrawn |
Free format text: JAPANESE INTERMEDIATE CODE: R371 |
|
| S111 | Request for change of ownership or part of ownership |
Free format text: JAPANESE INTERMEDIATE CODE: R313111 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| FPAY | Renewal fee payment (prs date is renewal date of database) |
Year of fee payment: 13 Free format text: PAYMENT UNTIL: 20071005 |
|
| FPAY | Renewal fee payment (prs date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20081005 Year of fee payment: 14 |
|
| EXPY | Cancellation because of completion of term | ||
| FPAY | Renewal fee payment (prs date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20081005 Year of fee payment: 14 |