JPH09194935A - Production of cold rolled steel sheet for gasket material, excellent in spring characteristic, and gasket material - Google Patents
Production of cold rolled steel sheet for gasket material, excellent in spring characteristic, and gasket materialInfo
- Publication number
- JPH09194935A JPH09194935A JP1822896A JP1822896A JPH09194935A JP H09194935 A JPH09194935 A JP H09194935A JP 1822896 A JP1822896 A JP 1822896A JP 1822896 A JP1822896 A JP 1822896A JP H09194935 A JPH09194935 A JP H09194935A
- Authority
- JP
- Japan
- Prior art keywords
- rolling
- cold
- steel sheet
- gasket material
- hot
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Landscapes
- Gasket Seals (AREA)
- Metal Rolling (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
Description
【発明の属する技術分野】本発明は、内燃機関におい
て、シリンダを始めとする各開口部のシール材として使
用される、ばね性に優れたガスケット材用冷延鋼板の製
造法およびその方法により製造されたガスケット材に関
する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for manufacturing a cold-rolled steel sheet for gasket material, which is used as a sealing material for each opening such as a cylinder in an internal combustion engine and has an excellent spring property, and a method therefor. Related gasket material.
【０００２】[0002]
【従来の技術】自動車のエンジン回りには、シリンダー
ヘッドガスケットをはじめとして多くのガスケットが使
用されている。このガスケット用材料として、従来はア
スベストが使用されてきたが、環境問題およびエンジン
の高性能化等に対処するため非アスベスト材料が模索さ
れている。上記アスベスト代替材料として、アラミド繊
維や黒鉛を用い、軟鋼板との複合加工としたものが使用
されている。また、従来のガスケット構造と全く異なる
ものとして、ステンレス鋼にゴム塗料を塗装したものも
使用されている。2. Description of the Related Art Many gaskets including cylinder head gaskets are used around automobile engines. Asbestos has been conventionally used as a material for this gasket, but non-asbestos materials are being sought in order to deal with environmental problems and higher engine performance. As the asbestos substitute material, aramid fiber or graphite is used, which is subjected to a composite processing with a mild steel plate. Further, as a completely different structure from the conventional gasket structure, a stainless steel coated with rubber paint is also used.
【０００３】[0003]
【発明が解決しようとする課題】しかし、上記アラミド
繊維や黒鉛を用いたものや、ステンレス鋼にゴム塗料を
塗装したものは、他の材料との複合加工となるためコス
トアップとなるという問題がある。図４はガスケット材
の使用態様を示す模式断面図である。この図に示すよう
に、ガスケット材４１は、シール性を向上させるため、
ビード部４２が形成されている。このため、ガスケット
材としての要求は、ビード加工時の加工性とばね性であ
る。この加工性とばね性とは金属学上相反する性質であ
る。即ち一般に加工性を向上させるには鋼材を軟化する
のがよく、一方ばね性を向上させるためには、鋼材を硬
化させるのがよい。従って、本発明においては、かかる
加工性とばね性との調和をとりながら、すぐれたガスシ
ール性を有するガスケット材用冷延鋼板の製造法を提供
することを目的とする。さらに本発明の他の目的は、シ
リンダ用開口部のシール性能に必要なばね性が特に良好
であり、冷却水用開口、潤滑油用開口、およびボルト孔
等の各種開口部についてもよく適応した、ばね性の良好
なシール性能が得られるガスケット材を提供することを
目的とする。However, there is a problem in that the aramid fiber or graphite or the stainless steel coated with a rubber coating causes a cost increase because it is a composite processing with other materials. is there. FIG. 4 is a schematic cross-sectional view showing how the gasket material is used. As shown in this figure, the gasket material 41 improves the sealing property.
A bead portion 42 is formed. For this reason, the requirements for the gasket material are workability and springiness during bead processing. This workability and springiness are metallurgically opposite properties. That is, in general, it is preferable to soften the steel material to improve the workability, and to harden the steel material to improve the spring property. Therefore, it is an object of the present invention to provide a method for producing a cold-rolled steel sheet for a gasket material, which has excellent gas sealing properties while maintaining such workability and spring properties in harmony. Still another object of the present invention is that the spring property required for the sealing performance of the cylinder opening is particularly good, and well adapted to various openings such as cooling water openings, lubricating oil openings, and bolt holes. It is an object of the present invention to provide a gasket material that can achieve a good spring performance and sealing performance.
【０００４】[0004]
【課題を解決するための手段】上記目的を達成するため
本発明のガスケット材用冷延鋼板の製造法は、重量％
で、Ｃ：0.10〜0.35％，Ｓｉ≦2.0％，Ｍｎ：0.5〜2.0
％，Ｐ≦0.06％，Ｓ≦0.06％，酸可溶Ａｌ：0.02〜0.1
％，Ｎ：0.0010〜0.0150％，残部Ｆｅおよび不可避的な
不純物より成る連続鋳造鋳片を、熱間圧延，酸洗，冷間
圧延を施した後、連続焼鈍において鋼板を再結晶温度以
上に加熱し、１秒から６０秒間均熱，焼鈍し、その後30
〜70％の圧下率で２次冷延を施すことを特徴とし、上記
２次冷延後、更に表面にＺｎまたはＮｉめっきを施すこ
とが望ましい。In order to achieve the above object, the method for producing a cold-rolled steel sheet for gasket material of the present invention is
And C: 0.10 to 0.35%, Si ≦ 2.0%, Mn: 0.5 to 2.0
%, P ≦ 0.06%, S ≦ 0.06%, acid-soluble Al: 0.02 to 0.1
%, N: 0.0010 to 0.0150%, the continuous cast slab consisting of the balance Fe and unavoidable impurities is hot-rolled, pickled, and cold-rolled, and then heated to a temperature above the recrystallization temperature during continuous annealing. Then soak and anneal for 1 to 60 seconds, then 30
It is characterized in that the secondary cold rolling is performed at a reduction rate of 70%, and it is desirable that the surface is further plated with Zn or Ni after the secondary cold rolling.
【０００５】さらに、本発明のガスケット材用冷延鋼板
の製造法は、重量％で、Ｃ：0.10〜0.35％，Ｓｉ≦2.0
％，Ｍｎ：0.5〜2.0％，Ｐ≦0.06％，Ｓ≦0.06％，酸可
溶Ａｌ：0.02〜0.1％，Ｎ：0.0010〜0.0150％，残部Ｆ
ｅおよび不可避的な不純物より成る連続鋳造鋳片を、熱
間圧延，酸洗，冷間圧延を施した後、連続焼鈍において
鋼板を750〜900℃の間のフェライト−オーステナイトの
二相領域に加熱し、１秒から６０秒間均熱し、その後10
00〜2000℃／秒の冷却速度で、前記二相領域から200℃
以下の温度まで冷却することを特徴とし、上記200℃以
下の温度まで冷却した後、ＺｎまたはＮｉめっきを施す
ことが望ましい。Further, according to the method of manufacturing the cold rolled steel sheet for gasket material of the present invention, the weight% is C: 0.10 to 0.35%, Si ≦ 2.0.
%, Mn: 0.5 to 2.0%, P ≦ 0.06%, S ≦ 0.06%, acid-soluble Al: 0.02 to 0.1%, N: 0.0010 to 0.0150%, balance F
Continuously cast slab consisting of e and unavoidable impurities is hot-rolled, pickled, and cold-rolled, and then the steel plate is heated to a two-phase region of ferrite-austenite between 750 and 900 ° C in continuous annealing. And soak for 1 to 60 seconds, then 10
200 ℃ from the two-phase region at a cooling rate of 00-2000 ℃ / sec
It is characterized by cooling to the following temperature, and it is desirable to perform Zn or Ni plating after cooling to the temperature of 200 ° C. or lower.
【０００６】本発明のガスケット材は、重量％で、Ｃ：
0.10〜0.35％，Ｓｉ≦2.0％，Ｍｎ：0.5〜2.0％，Ｐ≦
0.06％，Ｓ≦0.06％，酸可溶Ａｌ：0.02〜0.1％，Ｎ：
0.0010〜0.0150％，残部Ｆｅおよび不可避的な不純物よ
り成る連続鋳造鋳片を、熱間圧延，酸洗，冷間圧延を施
した後、連続焼鈍において鋼板を再結晶温度以上に加熱
し、１秒から６０秒間均熱，焼鈍し、その後30〜70％の
圧下率で２次冷延を施してなることを特徴とし、上記２
次冷延後、更に表面にＺｎまたはＮｉめっきを施すこと
が望ましい。The gasket material of the present invention has a C:
0.10 to 0.35%, Si ≦ 2.0%, Mn: 0.5 to 2.0%, P ≦
0.06%, S ≦ 0.06%, acid-soluble Al: 0.02-0.1%, N:
Continuously cast slabs consisting of 0.0010 to 0.0150%, balance Fe and unavoidable impurities were hot-rolled, pickled and cold-rolled, and then heated in a continuous annealing to a temperature above the recrystallization temperature for 1 second. To 60 seconds for soaking and annealing, and then secondary cold rolling at a reduction rate of 30 to 70%.
After the next cold rolling, it is desirable to further apply Zn or Ni plating to the surface.
【０００７】また、本発明のガスケット材は、重量％
で、Ｃ：0.10〜0.35％，Ｓｉ≦2.0％，Ｍｎ：0.5〜2.0
％，Ｐ≦0.06％，Ｓ≦0.06％，酸可溶Ａｌ：0.02〜0.1
％，Ｎ：0.0010〜0.0150％，残部Ｆｅおよび不可避的な
不純物より成る連続鋳造鋳片を、熱間圧延，酸洗，冷間
圧延を施した後、連続焼鈍において鋼板を750〜900℃の
間のフェライト−オーステナイトの二相領域に加熱し、
１秒から６０秒間均熱し、その後1000〜2000℃／秒の冷
却速度で、前記二相領域から200℃以下の温度まで冷却
してなることを特徴とし、上記200℃以下の温度まで冷
却した後、ＺｎまたはＮｉめっきを施すことが望まし
い。Further, the gasket material of the present invention has a weight%
And C: 0.10 to 0.35%, Si ≦ 2.0%, Mn: 0.5 to 2.0
%, P ≦ 0.06%, S ≦ 0.06%, acid-soluble Al: 0.02 to 0.1
%, N: 0.0010 to 0.0150%, the continuous cast slab consisting of the balance Fe and unavoidable impurities was hot-rolled, pickled, and cold-rolled, and then continuously annealed to a steel plate at a temperature of 750 to 900 ° C. Of the ferrite-austenite two-phase region,
It is characterized in that it is soaked for 1 second to 60 seconds and then cooled from the two-phase region to a temperature of 200 ° C. or lower at a cooling rate of 1000 to 2000 ° C./second, after cooling to the temperature of 200 ° C. or lower. , Zn or Ni plating is desirable.
【０００８】[0008]
【発明の実施の形態】以下、本発明を詳細に説明する。BEST MODE FOR CARRYING OUT THE INVENTION The present invention will be described in detail below.
【０００９】原板の鋼成分 本発明の原板の鋼成分は、重量％で、Ｃ：0.10〜0.35
％，Ｓｉ≦2.0％，Ｍｎ：0.5〜2.0％，Ｐ≦0.06％，Ｓ
≦0.06％，酸可溶Ａｌ：0.02〜0.1％，Ｎ：0.0010〜0.0
150％，残部Ｆｅおよび不可避的な不純物より成る。Steel Composition of Original Plate The steel composition of the original plate of the present invention is C: 0.10 to 0.35 in weight%.
%, Si ≦ 2.0%, Mn: 0.5 to 2.0%, P ≦ 0.06%, S
≤0.06%, acid-soluble Al: 0.02-0.1%, N: 0.0010-0.0
150%, balance Fe and unavoidable impurities.
【００１０】Ｃは原板に高い調質度を与えるために重要
な成分である。少なくともＣは0.10％に達しないと本発
明目的において必要な原板の耐力を保証出来ない。従っ
てＣ成分下限値を0.10％とした。一方でＣ成分が0.35％
を超えると炭化物析出量が増大し原板の加工性の低下を
もたらすと同時に、冷間圧延の負荷の増大、形状の劣
化、連続焼鈍工程での通板性阻害等、生産性低下の原因
となる。そのため本発明ではＣ成分の上限値を0.35％と
する。C is an important component for giving the original plate a high degree of tempering. If at least C does not reach 0.10%, the yield strength of the original plate required for the purpose of the present invention cannot be guaranteed. Therefore, the lower limit of the C component is set to 0.10%. On the other hand, C component is 0.35%
If it exceeds 1.0, the precipitation amount of carbides will increase and the workability of the original plate will decrease, and at the same time, it will cause a decrease in productivity such as an increase in the load of cold rolling, deterioration of the shape, and obstruction of the stripability in the continuous annealing process. . Therefore, in the present invention, the upper limit value of the C component is set to 0.35%.
【００１１】Ｍｎは不純物であるＳによる熱延中の赤熱
脆性を防止するために必要な成分である。本発明では原
板の耐力保証の見地からＭｎ成分は0.5％以上とし、一
方2.0％を超えるとスラブ圧延中に割れを生ずるので、
上限値を2.0％とする。Mn is a component necessary for preventing red hot embrittlement during hot rolling due to S as an impurity. In the present invention, from the viewpoint of guaranteeing the yield strength of the original plate, the Mn content is 0.5% or more, while if it exceeds 2.0%, cracking occurs during slab rolling.
The upper limit is 2.0%.
【００１２】Ｐは結晶粒微細化成分であり、また原板の
強度を高めることから一定の割合で添加されるが、一方
で耐食性を阻害する。本発明用途としては、Ｐが0.06％
を超えると耐食性、特に耐孔明性が著しく低下するため
上限値を0.06％とする。[0012] P is a crystal grain refining component and is added in a fixed ratio because it enhances the strength of the original plate, but it impairs corrosion resistance. For use in the present invention, P is 0.06%
If it exceeds 1.0%, the corrosion resistance, especially the hole-proofing property will be remarkably reduced, so the upper limit is made 0.06%.
【００１３】Ｓは熱延中において赤熱脆性を生じる不純
物成分であり、極力少ないことが望ましいが、鉄鋼石等
からの混入を完全に防止することができず、工程中の脱
硫も困難なことからある程度の残留もやむをえない。少
量の残留Ｓによる赤熱脆性はＭｎにより軽減できるた
め、Ｓ成分の上限値は0.06％とする。[0013] S is an impurity component which causes red hot brittleness during hot rolling, and it is desirable that it is as small as possible. However, since it is not possible to completely prevent mixing from iron and steel or the like, desulfurization during the process is difficult. A certain amount of residue is unavoidable. Since the red hot brittleness due to a small amount of residual S can be reduced by Mn, the upper limit of the S component is 0.06%.
【００１４】Ａｌは製鋼に際し脱酸剤として鋼浴中に添
加されるが、添加量が少ないと安定した脱酸効果が得ら
れないため、0.02％以上必要である。またＡｌは固溶Ｎ
と反応してＡｌＮとして析出し結晶粒の細粒化に寄与す
る。一方で0.10％を超える添加はＮの固定が著しくな
り、Ｎの固溶強化が低減するので、最大量は0.10％とす
る。Al is added to the steel bath as a deoxidizing agent during steel making, but if the addition amount is small, a stable deoxidizing effect cannot be obtained, so 0.02% or more is necessary. Al is a solid solution N
Reacts with and precipitates as AlN to contribute to the refinement of crystal grains. On the other hand, when the content exceeds 0.10%, the fixation of N becomes remarkable and the solid solution strengthening of N is reduced, so the maximum amount is made 0.10%.
【００１５】ＮはＣ，Ｍｎと同様に原板に高い調質度を
与える。耐力強化のために必要な成分であるが、0.001
％より少なくすることは製鋼上の困難を生じ、また一方
0.0150％を超える添加は製鋼時に添加するフェロ窒化物
の歩留の低下が著しく、安定性に欠けると同時に、プレ
ス成形時の異方性を著しく劣化させる。さらに連続鋳造
片の表面に割れが生じ、鋳造欠陥となるため本発明では
Ｎ成分範囲を0.001〜0.0150％とする。Like C and Mn, N gives the original plate a high degree of refining. It is a component necessary for strengthening the yield strength, but 0.001
% Lowers steelmaking difficulties, while
If the addition exceeds 0.0150%, the yield of the ferronitride added at the time of steelmaking is remarkably lowered, and the stability is poor, and at the same time, the anisotropy at the time of press forming is remarkably deteriorated. Further, since cracks occur on the surface of the continuous cast piece and cause casting defects, the N component range is 0.001 to 0.0150% in the present invention.
【００１６】Ｓｉは本発明の主要な特徴であるばね性を
得るのに有効な元素であり、その目的を達成するために
は多い程良いが、2.0％を超えると冷間圧延の負荷の増
大、形状の劣化を招くため上限値を2.0％とする。Si is an element effective for obtaining the spring property which is the main feature of the present invention. The more it is, the better it is to achieve the purpose, but if it exceeds 2.0%, the load of cold rolling increases. , The upper limit is set to 2.0% because it causes deterioration of the shape.
【００１７】熱間圧延 熱間圧延工程における鋼片加熱温度は本発明において特
定するものではないが、Ｎの積極的分解固溶および熱間
仕上圧延温度の安定的確保の見地から１１００℃以上と
するのが望ましい。熱間圧延仕上温度をＡｒ3 点以下に
すると、熱間鋼帯の結晶組織が混粒化するとともに粗大
化し、製品冷延鋼板において肌荒れが生じかつ耐力が低
下するので熱間圧延仕上温度はＡｒ3 点以上とするのが
望ましい。Hot rolling The steel billet heating temperature in the hot rolling step is not specified in the present invention, but it is 1100 ° C. or higher from the viewpoint of positively decomposing solid solution of N and ensuring stable hot finishing rolling temperature. It is desirable to do. If the hot-rolling finishing temperature is less than Ar3, the crystal structure of the hot-rolled steel strip will be mixed and coarsen, and the product cold-rolled steel sheet will be roughened and the yield strength will decrease. It is desirable to set it as above.
【００１８】巻き取り温度は４５０℃〜６５０℃とす
る。熱延時のコイルの幅方向および長手方向の品質安定
性を考慮して４５０℃を下限とする。また巻取温度が６
５０℃を超えると、熱延時および連続焼鈍時で結晶粒径
が大きくなり、ガスケットビード加工時の不良原因とな
るため、巻取温度は６５０℃以下とするのが望ましい。The coiling temperature is 450 ° C. to 650 ° C. The lower limit is 450 ° C in consideration of the quality stability in the width direction and the longitudinal direction of the coil during hot rolling. The winding temperature is 6
If it exceeds 50 ° C., the crystal grain size becomes large during hot rolling and continuous annealing, which causes defects during gasket bead processing. Therefore, the winding temperature is preferably 650 ° C. or less.
【００１９】連続焼鈍 焼鈍温度が高くなるほど引張強さは増加するが、本発明
の目的のガスケット材を得るためには最低７５０℃以上
で焼鈍する必要がある。また焼鈍温度の上限は９００℃
である。この範囲を外れると各々フェライト分率、オー
ステナイト分率が高くなり過ぎ、本発明の目的とする高
強度鋼板が得られない。Continuous Annealing The tensile strength increases as the annealing temperature increases, but it is necessary to anneal at least 750 ° C. or higher in order to obtain the gasket material of the present invention. The upper limit of annealing temperature is 900 ° C.
It is. If the ratio is out of this range, the ferrite fraction and the austenite fraction become too high, and the high-strength steel sheet aimed at by the present invention cannot be obtained.
【００２０】均熱時間は１〜６０秒とする。１秒以上あ
れば焼入れ効果が得られるが、６０秒を超えて均熱する
と、セメンタイトの固溶が多くなり、焼入れ時に目的と
する微細なコロニー状のマルテンサイトが分散した組織
が得られないばかりか経済上好ましくない。The soaking time is 1 to 60 seconds. The hardening effect can be obtained if it is 1 second or more, but if it is soaked for more than 60 seconds, the solid solution of cementite will increase, and the desired structure in which fine colony martensite is dispersed cannot be obtained. It is not economically preferable.
【００２１】図３に冷却速度と引張強さとの関係を示
す。この図から、焼鈍における均熱後の冷却速度と引張
強さとの関係は、冷却速度が速いほど引張強さは上昇す
る。本発明のガスケット材（約１２００Ｎ／ｍｍ2 以上
の強度を有するガスケット材）を得るためには１０００
〜２０００℃／秒の範囲が適性な冷却速度である。１０
００℃未満では本発明の目的とする高強度を有する鋼板
が得られない。一方２０００℃を超える冷却速度は工業
上不経済となるからである。FIG. 3 shows the relationship between the cooling rate and the tensile strength. From this figure, regarding the relationship between the cooling rate after soaking in annealing and the tensile strength, the higher the cooling rate, the higher the tensile strength. To obtain the gasket material of the present invention (gasket material having a strength of about 1200 N / mm 2 or more), 1000
The range of ˜2000 ° C./sec is a suitable cooling rate. 10
If the temperature is lower than 00 ° C, a steel sheet having high strength, which is the object of the present invention, cannot be obtained. On the other hand, a cooling rate exceeding 2000 ° C. is industrially uneconomical.
【００２２】冷却開始温度は７５０℃以下とする。冷却
開始温度は焼入れ効果に強く影響し、７５０℃より下で
はオーステナイト分率が低くなり、目標とする強度がえ
られない。冷却終点温度が２００℃を超えては鋼板が軟
質化し、本発明の目的とする高強度鋼板が得られない。
従って二相域からの冷却は２００℃以下にまですること
とした。The cooling start temperature is 750 ° C. or lower. The cooling start temperature has a strong influence on the quenching effect, and the austenite fraction becomes lower below 750 ° C, and the target strength cannot be obtained. If the cooling end temperature exceeds 200 ° C, the steel sheet becomes soft and the high-strength steel sheet targeted by the present invention cannot be obtained.
Therefore, the cooling from the two-phase region was decided to be 200 ° C. or less.
【００２３】その後、30〜70％の圧下率で２次冷延を施
す。30％未満の圧下率ではガスケットとしての必要な強
度が得られず、70％を超えると硬度が上昇し過ぎてビー
ド加工性の点で問題が生ずる。After that, secondary cold rolling is performed at a reduction rate of 30 to 70%. If the rolling reduction is less than 30%, the required strength as a gasket cannot be obtained, and if it exceeds 70%, the hardness is excessively increased and a problem occurs in bead workability.
【００２４】つぎに、本発明に用いられる鋼板として
は、シ−ト状およびコイル状の鋼板、鋼箔およびそれら
の鋼板に表面処理を施したものがあげられる。特に、下
層が金属クロム、上層がクロム水和酸化物の２層構造を
もつ電解クロム酸処理鋼板あるいは極薄錫めっき鋼板、
ニッケルめっき鋼板、亜鉛めっき鋼板およびこれらのめ
っき鋼板にクロム水和酸化物あるいは上層がクロム水和
酸化物、下層が金属クロム層からなる２層構造をもつ表
面処理をほどこしたものが耐食性の点で優れている。Next, examples of the steel sheet used in the present invention include sheet-shaped and coil-shaped steel sheets, steel foil, and those obtained by subjecting these steel sheets to surface treatment. In particular, electrolytic chromic acid-treated steel sheet or ultra-thin tin-plated steel sheet having a two-layer structure of metal chromium in the lower layer and chromium hydrated oxide in the upper layer,
In terms of corrosion resistance, nickel-plated steel sheets, zinc-plated steel sheets, and those plated steel sheets that have been subjected to a surface treatment with a two-layer structure of hydrated chromium oxide or hydrated chromium oxide as the upper layer and metallic chromium layer as the lower layer Are better.
【００２５】[0025]
【実施例】本発明製品を比較例との関係において表１を
もって説明する。表１において本発明品であるＮｏ１〜
５は、高強度でかつ高いばね性を示している（表中評価
の欄に○印を記載）。一方比較例Ｎｏ６〜１０は本発明
条件のいずれかを満足しておらず、いずれも加工性ある
いはばね性において劣っている（表中評価の欄のいずれ
かの項目に×印を記載）。EXAMPLES The products of the present invention will be described with reference to Table 1 in relation to the comparative examples. No. 1 of the present invention in Table 1
No. 5 has high strength and high springiness (marked with ○ in the evaluation column in the table). On the other hand, Comparative Examples Nos. 6 to 10 do not satisfy any of the conditions of the present invention, and all are inferior in workability or spring property (marked with X in any item in the evaluation column in the table).
【００２６】[0026]
【表１】 [Table 1]
【００２７】加工性およびばね性の評価 本発明のガスケットについての加工性およびばね性の評
価は下記のようにして行った。まず、図１に示すような
断面形状に鋼板をプレス加工（フランジ付きビード溝加
工）し、幅w，高さtのビード部を形成する。このビード
加工時にビード部に割れが発生するものは、加工性不合
格として評価×とした。Evaluation of Workability and Spring Property The workability and spring property of the gasket of the present invention were evaluated as follows. First, a steel plate is pressed into a cross-sectional shape as shown in FIG. 1 (bead groove processing with a flange) to form a bead portion having a width w and a height t. Those having cracks in the bead portion during the bead processing were evaluated as x, because the workability was unacceptable.
【００２８】図２は、ばね性を評価するための試験法で
ある圧縮試験の工程を示す。図２の（ａ）は、加工ビー
ド部の圧縮前の状態を示し、同図（ｂ）は、圧縮荷重を
負荷した状態を示し、同図（ｃ）は、圧縮荷重を除荷し
た状態を示す。図２に示すように、圧縮試験機にてビー
ド部に上方から圧縮荷重を負荷した。荷重除荷後、圧縮
量（Ｔ）に対し復元量（Ｔ１）が４０％を超えたもの
を、ばね性が合格とした。即ち表１に示すばね性の値
は、（復元量Ｔ１／圧縮量Ｔ）×１００の値である。FIG. 2 shows the steps of a compression test, which is a test method for evaluating springiness. 2A shows a state before compression of the processed bead portion, FIG. 2B shows a state in which a compressive load is applied, and FIG. 2C shows a state in which the compressive load is removed. Show. As shown in FIG. 2, a compression load was applied to the bead portion from above with a compression tester. After the load was unloaded, the amount of restoration (T1) with respect to the amount of compression (T) exceeded 40%, and the spring property was regarded as acceptable. That is, the springiness value shown in Table 1 is a value of (restore amount T1 / compression amount T) × 100.
【００２９】[0029]
【発明の効果】本発明のガスケット材は、加工性とばね
性との調和がとれ、すぐれたガスシール性を有する。さ
らに表面処理を施したガスケット材は、高温状態にさら
されてもすぐれた耐食性を示し、長期間安定したガスシ
ール性を示す。また、本発明のガスケット材は、シリン
ダ用開口部のシール性能に必要なばね特性が特に良好で
あり、冷却水用開口、潤滑油用開口、およびボルト孔等
の各種開口部についても好適に用いることができる。EFFECTS OF THE INVENTION The gasket material of the present invention has excellent workability and spring property, and has excellent gas sealing property. Furthermore, the surface-treated gasket material exhibits excellent corrosion resistance even when exposed to high temperature conditions, and exhibits stable gas sealing properties for a long period of time. Further, the gasket material of the present invention has particularly good spring characteristics required for sealing performance of the cylinder opening, and is suitably used for various openings such as cooling water openings, lubricating oil openings, and bolt holes. be able to.
【図１】ガスケットについての加工性の評価法の概略図
を示す。FIG. 1 shows a schematic diagram of an evaluation method of workability of a gasket.
【図２】ばね性を評価するための試験法の概略図を示
す。FIG. 2 shows a schematic diagram of a test method for evaluating springiness.
【図３】冷却速度と引張強さとの関係を示す。FIG. 3 shows the relationship between cooling rate and tensile strength.
【図４】ガスケット材の使用態様を示す模式断面図であ
る。FIG. 4 is a schematic cross-sectional view showing how the gasket material is used.
Ｔ 圧縮量 Ｔ１ 復元量 ４１ ガスケット材 ４２ ビード部 T compression amount T1 restoration amount 41 gasket material 42 bead part
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｃ２２Ｃ 38/06 Ｃ２２Ｃ 38/06 Ｆ１６Ｊ 15/08 Ｆ１６Ｊ 15/08 Ｆ ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 6 Identification code Internal reference number FI Technical display location C22C 38/06 C22C 38/06 F16J 15/08 F16J 15/08 F
Claims (8)
0％，Ｍｎ：0.5〜2.0％，Ｐ≦0.06％，Ｓ≦0.06％，酸
可溶Ａｌ：0.02〜0.1％，Ｎ：0.0010〜0.0150％，残部
Ｆｅおよび不可避的な不純物より成る連続鋳造鋳片を、
熱間圧延，酸洗，冷間圧延を施した後、連続焼鈍におい
て鋼板を再結晶温度以上に加熱し、１秒から６０秒間均
熱，焼鈍し、その後30〜70％の圧下率で２次冷延を施す
ことを特徴とする、ばね性に優れたガスケット材用冷延
鋼板の製造法。1. C: 0.10 to 0.35% by weight, Si ≦ 2.
0%, Mn: 0.5-2.0%, P ≦ 0.06%, S ≦ 0.06%, acid-soluble Al: 0.02-0.1%, N: 0.0010-0.0150%, continuous cast slab consisting of balance Fe and unavoidable impurities To
After hot rolling, pickling, and cold rolling, the steel sheet is heated to the recrystallization temperature or higher in continuous annealing, soaked and annealed for 1 to 60 seconds, and then secondary with a reduction rate of 30 to 70%. A method for producing a cold-rolled steel sheet for gasket material, which is excellent in spring property, characterized by being cold-rolled.
0％，Ｍｎ：0.5〜2.0％，Ｐ≦0.06％，Ｓ≦0.06％，酸
可溶Ａｌ：0.02〜0.1％，Ｎ：0.0010〜0.0150％，残部
Ｆｅおよび不可避的な不純物より成る連続鋳造鋳片を、
熱間圧延，酸洗，冷間圧延を施した後、連続焼鈍におい
て鋼板を再結晶温度以上に加熱し、１秒から６０秒間均
熱，焼鈍し、その後30〜70％の圧下率で２次冷延を施
し、更に表面にＺｎまたはＮｉめっきを施すことを特徴
とする、ばね性に優れたガスケット材用冷延鋼板の製造
法。2. C: 0.10 to 0.35% by weight, Si ≦ 2.
0%, Mn: 0.5-2.0%, P ≦ 0.06%, S ≦ 0.06%, acid-soluble Al: 0.02-0.1%, N: 0.0010-0.0150%, continuous cast slab consisting of balance Fe and unavoidable impurities To
After hot rolling, pickling, and cold rolling, the steel sheet is heated to the recrystallization temperature or higher in continuous annealing, soaked and annealed for 1 to 60 seconds, and then secondary with a reduction rate of 30 to 70%. A method for producing a cold-rolled steel sheet having excellent spring properties for a gasket material, which comprises performing cold-rolling and further plating the surface with Zn or Ni.
0％，Ｍｎ：0.5〜2.0％，Ｐ≦0.06％，Ｓ≦0.06％，酸
可溶Ａｌ：0.02〜0.1％，Ｎ：0.0010〜0.0150％，残部
Ｆｅおよび不可避的な不純物より成る連続鋳造鋳片を、
熱間圧延，酸洗，冷間圧延を施した後、連続焼鈍におい
て鋼板を750〜900℃の間のフェライト−オーステナイト
の二相領域に加熱し、１秒から６０秒間均熱し、その後
1000〜2000℃／秒の冷却速度で、前記二相領域から200
℃以下の温度まで冷却することを特徴とする、ばね性に
優れたガスケット材用冷延鋼板の製造法。3. C: 0.10 to 0.35% by weight, Si ≦ 2.
0%, Mn: 0.5-2.0%, P ≦ 0.06%, S ≦ 0.06%, acid-soluble Al: 0.02-0.1%, N: 0.0010-0.0150%, continuous cast slab consisting of balance Fe and unavoidable impurities To
After hot-rolling, pickling and cold-rolling, the steel sheet was heated in continuous annealing to the ferrite-austenite two-phase region between 750 and 900 ° C., soaked for 1 to 60 seconds, and then
200 from the two-phase region at a cooling rate of 1000 to 2000 ° C / sec.
A method for producing a cold-rolled steel sheet for gasket material, which is excellent in spring property, characterized by cooling to a temperature of ℃ or less.
0％，Ｍｎ：0.5〜2.0％，Ｐ≦0.06％，Ｓ≦0.06％，酸
可溶Ａｌ：0.02〜0.1％，Ｎ：0.0010〜0.0150％，残部
Ｆｅおよび不可避的な不純物より成る連続鋳造鋳片を、
熱間圧延，酸洗，冷間圧延を施した後、連続焼鈍におい
て鋼板を750〜900℃の間のフェライト−オーステナイト
の二相領域に加熱し、１秒から６０秒間均熱し、その後
1000〜2000℃／秒の冷却速度で、前記二相領域から200
℃以下の温度まで冷却し、その後ＺｎまたはＮｉめっき
を施すことを特徴とする、ばね性に優れたガスケット材
用冷延鋼板の製造法。4. C: 0.10 to 0.35% by weight, Si ≦ 2.
0%, Mn: 0.5-2.0%, P ≦ 0.06%, S ≦ 0.06%, acid-soluble Al: 0.02-0.1%, N: 0.0010-0.0150%, continuous cast slab consisting of balance Fe and unavoidable impurities To
After hot-rolling, pickling and cold-rolling, the steel sheet was heated in continuous annealing to the ferrite-austenite two-phase region between 750 and 900 ° C., soaked for 1 to 60 seconds, and then
200 from the two-phase region at a cooling rate of 1000 to 2000 ° C / sec.
A method for producing a cold-rolled steel sheet for gasket material, which is excellent in spring property, characterized by cooling to a temperature of ℃ or less and then performing Zn or Ni plating.
0％，Ｍｎ：0.5〜2.0％，Ｐ≦0.06％，Ｓ≦0.06％，酸
可溶Ａｌ：0.02〜0.1％，Ｎ：0.0010〜0.0150％，残部
Ｆｅおよび不可避的な不純物より成る連続鋳造鋳片を、
熱間圧延，酸洗，冷間圧延を施した後、連続焼鈍におい
て鋼板を再結晶温度以上に加熱し、１秒から６０秒間均
熱，焼鈍し、その後30〜70％の圧下率で２次冷延を施し
てなる、ばね性に優れたガスケット材。5. C: 0.10 to 0.35% by weight, Si ≦ 2.
0%, Mn: 0.5-2.0%, P ≦ 0.06%, S ≦ 0.06%, acid-soluble Al: 0.02-0.1%, N: 0.0010-0.0150%, continuous cast slab consisting of balance Fe and unavoidable impurities To
After hot rolling, pickling, and cold rolling, the steel sheet is heated to the recrystallization temperature or higher in continuous annealing, soaked and annealed for 1 to 60 seconds, and then secondary with a reduction rate of 30 to 70%. Gasket material with excellent spring properties made by cold rolling.
0％，Ｍｎ：0.5〜2.0％，Ｐ≦0.06％，Ｓ≦0.06％，酸
可溶Ａｌ：0.02〜0.1％，Ｎ：0.0010〜0.0150％，残部
Ｆｅおよび不可避的な不純物より成る連続鋳造鋳片を、
熱間圧延，酸洗，冷間圧延を施した後、連続焼鈍におい
て鋼板を再結晶温度以上に加熱し、１秒から６０秒間均
熱，焼鈍し、その後30〜70％の圧下率で２次冷延を施
し、更に表面にＺｎまたはＮｉめっきを施してなる、ば
ね性に優れたガスケット材。6. By weight%, C: 0.10 to 0.35%, Si ≦ 2.
0%, Mn: 0.5-2.0%, P ≦ 0.06%, S ≦ 0.06%, acid-soluble Al: 0.02-0.1%, N: 0.0010-0.0150%, continuous cast slab consisting of balance Fe and unavoidable impurities To
After hot rolling, pickling, and cold rolling, the steel sheet is heated to the recrystallization temperature or higher in continuous annealing, soaked and annealed for 1 to 60 seconds, and then secondary with a reduction rate of 30 to 70%. Gasket material with excellent spring properties, which is obtained by cold rolling and then Zn or Ni plating on the surface.
0％，Ｍｎ：0.5〜2.0％，Ｐ≦0.06％，Ｓ≦0.06％，酸
可溶Ａｌ：0.02〜0.1％，Ｎ：0.0010〜0.0150％，残部
Ｆｅおよび不可避的な不純物より成る連続鋳造鋳片を、
熱間圧延，酸洗，冷間圧延を施した後、連続焼鈍におい
て鋼板を750〜900℃の間のフェライト−オーステナイト
の二相領域に加熱し、１秒から６０秒間均熱し、その後
1000〜2000℃／秒の冷却速度で、前記二相領域から200
℃以下の温度まで冷却してなる、ばね性に優れたガスケ
ット材。7. By weight%, C: 0.10 to 0.35%, Si ≦ 2.
0%, Mn: 0.5-2.0%, P ≦ 0.06%, S ≦ 0.06%, acid-soluble Al: 0.02-0.1%, N: 0.0010-0.0150%, continuous cast slab consisting of balance Fe and unavoidable impurities To
After hot-rolling, pickling and cold-rolling, the steel sheet was heated in continuous annealing to the ferrite-austenite two-phase region between 750 and 900 ° C., soaked for 1 to 60 seconds, and then
200 from the two-phase region at a cooling rate of 1000 to 2000 ° C / sec.
Gasket material with excellent spring properties, which is cooled to a temperature below ℃.
0％，Ｍｎ：0.5〜2.0％，Ｐ≦0.06％，Ｓ≦0.06％，酸
可溶Ａｌ：0.02〜0.1％，Ｎ：0.0010〜0.0150％，残部
Ｆｅおよび不可避的な不純物より成る連続鋳造鋳片を、
熱間圧延，酸洗，冷間圧延を施した後、連続焼鈍におい
て鋼板を750〜900℃の間のフェライト−オーステナイト
の二相領域に加熱し、１秒から６０秒間均熱し、その後
1000〜2000℃／秒の冷却速度で、前記二相領域から200
℃以下の温度まで冷却し、その後ＺｎまたはＮｉめっき
を施してなる、ばね性に優れたガスケット材。 【０００１】8. In weight%, C: 0.10 to 0.35%, Si ≦ 2.
0%, Mn: 0.5-2.0%, P ≦ 0.06%, S ≦ 0.06%, acid-soluble Al: 0.02-0.1%, N: 0.0010-0.0150%, continuous cast slab consisting of balance Fe and unavoidable impurities To
After hot-rolling, pickling and cold-rolling, the steel sheet was heated in continuous annealing to the ferrite-austenite two-phase region between 750 and 900 ° C., soaked for 1 to 60 seconds, and then
200 from the two-phase region at a cooling rate of 1000 to 2000 ° C / sec.
A gasket material excellent in spring property, which is obtained by cooling to a temperature of ℃ or less and then plating with Zn or Ni. [0001]
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1822896A JPH09194935A (en) | 1996-01-10 | 1996-01-10 | Production of cold rolled steel sheet for gasket material, excellent in spring characteristic, and gasket material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1822896A JPH09194935A (en) | 1996-01-10 | 1996-01-10 | Production of cold rolled steel sheet for gasket material, excellent in spring characteristic, and gasket material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH09194935A true JPH09194935A (en) | 1997-07-29 |
Family
ID=11965812
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1822896A Pending JPH09194935A (en) | 1996-01-10 | 1996-01-10 | Production of cold rolled steel sheet for gasket material, excellent in spring characteristic, and gasket material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH09194935A (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003503646A (en) * | 1999-06-30 | 2003-01-28 | フェデラル−モーグル コーポレイション | Metal gasket and manufacturing method |
| WO2004050931A1 (en) * | 2002-11-29 | 2004-06-17 | Toyo Kohan Co., Ltd. | Cold rolled steel sheet for gasket material, method for production thereof and gasket material produced by the method |
| JP2004183001A (en) * | 2002-11-29 | 2004-07-02 | Toyo Kohan Co Ltd | Material for gasket, production method therefor, and gasket |
| EP1458896A1 (en) * | 2001-12-27 | 2004-09-22 | Posco | High strength cold rolled steel sheet with superior formability and weldability, and manufacturing method therefor |
| WO2005007916A1 (en) * | 2003-07-18 | 2005-01-27 | Toyo Kohan Co., Ltd. | Cold rolled steel sheet for gasket material, method for production thereof and gasket material |
| JP2005240126A (en) * | 2004-02-27 | 2005-09-08 | Toyo Kohan Co Ltd | High-strength and extremely-thin cold-rolled steel sheet, manufacturing method therefor, material for gasket using it and gasket material using the same |
| WO2006045622A1 (en) * | 2004-10-26 | 2006-05-04 | Hille & Müller GMBH | Process for the manufacture of a containment device and a containment device manufactured thereby |
| WO2011004554A1 (en) | 2009-07-08 | 2011-01-13 | 東洋鋼鈑株式会社 | Process for production of cold-rolled steel sheet having excellent press moldability, and cold-rolled steel sheet |
| US20140144553A1 (en) * | 2010-08-23 | 2014-05-29 | Kengo Hata | Cold-rolled steel sheet and process for production thereof |
| CN109317926A (en) * | 2018-09-29 | 2019-02-12 | 江苏永昊高强度螺栓有限公司 | A kind of processing technology of corrosion-resistant bolt |
-
1996
- 1996-01-10 JP JP1822896A patent/JPH09194935A/en active Pending
Cited By (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003503646A (en) * | 1999-06-30 | 2003-01-28 | フェデラル−モーグル コーポレイション | Metal gasket and manufacturing method |
| EP1458896A1 (en) * | 2001-12-27 | 2004-09-22 | Posco | High strength cold rolled steel sheet with superior formability and weldability, and manufacturing method therefor |
| EP1566460A4 (en) * | 2002-11-29 | 2006-05-10 | Toyo Kohan Co Ltd | Cold rolled steel sheet for gasket material, method for production thereof and gasket material produced by the method |
| JP2004183001A (en) * | 2002-11-29 | 2004-07-02 | Toyo Kohan Co Ltd | Material for gasket, production method therefor, and gasket |
| EP1566460A1 (en) * | 2002-11-29 | 2005-08-24 | Toyo Kohan Co., Ltd. | Cold rolled steel sheet for gasket material, method for production thereof and gasket material produced by the method |
| WO2004050931A1 (en) * | 2002-11-29 | 2004-06-17 | Toyo Kohan Co., Ltd. | Cold rolled steel sheet for gasket material, method for production thereof and gasket material produced by the method |
| WO2005007916A1 (en) * | 2003-07-18 | 2005-01-27 | Toyo Kohan Co., Ltd. | Cold rolled steel sheet for gasket material, method for production thereof and gasket material |
| JP2005240126A (en) * | 2004-02-27 | 2005-09-08 | Toyo Kohan Co Ltd | High-strength and extremely-thin cold-rolled steel sheet, manufacturing method therefor, material for gasket using it and gasket material using the same |
| WO2005083140A1 (en) * | 2004-02-27 | 2005-09-09 | Toyo Kohan Co., Ltd. | Extremely thin cold rolled steel sheet having high strength, method for production thereof, material for gasket using the sheet and gasket member using the material |
| WO2006045622A1 (en) * | 2004-10-26 | 2006-05-04 | Hille & Müller GMBH | Process for the manufacture of a containment device and a containment device manufactured thereby |
| JP2008518102A (en) * | 2004-10-26 | 2008-05-29 | ヒル・アンド・ミユラー・ゲゼルシヤフト・ミツト・ベシユレンクテル・ハフツング | Method of manufacturing containment device and containment device manufactured thereby |
| WO2011004554A1 (en) | 2009-07-08 | 2011-01-13 | 東洋鋼鈑株式会社 | Process for production of cold-rolled steel sheet having excellent press moldability, and cold-rolled steel sheet |
| US20140144553A1 (en) * | 2010-08-23 | 2014-05-29 | Kengo Hata | Cold-rolled steel sheet and process for production thereof |
| US9435013B2 (en) * | 2010-08-23 | 2016-09-06 | Nippon Steel & Sumitomo Metal Corporation | Cold-rolled steel sheet and process for production thereof |
| CN109317926A (en) * | 2018-09-29 | 2019-02-12 | 江苏永昊高强度螺栓有限公司 | A kind of processing technology of corrosion-resistant bolt |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| EP1264911A2 (en) | High-ductility steel sheet excellent in press formability and strain age hardenability, and method for manufacturing the same | |
| JP6795122B1 (en) | High-strength galvanized steel sheet and its manufacturing method | |
| JPH09194935A (en) | Production of cold rolled steel sheet for gasket material, excellent in spring characteristic, and gasket material | |
| JPS6111296B2 (en) | ||
| JPH10251794A (en) | Hot rolled steel plate for structural purpose, excellent in press formability and surface characteristic, and its production | |
| JP2003268491A (en) | High-strength steel sheet for working member, production method thereof, and production method for working member having working plane excellent in abrasion resistance | |
| JP4138465B2 (en) | Cold-rolled steel sheet for gasket material excellent in spring property, its manufacturing method, and gasket material excellent in spring property | |
| JP3596037B2 (en) | Manufacturing method of steel plate for can-making | |
| JP2003003216A (en) | Method for producing high strength galvanized steel sheet having excellent deep drawability and secondary working brittleness resistance | |
| JP2004225155A (en) | Cold rolled steel sheet for gasket material, its production method, and gasket material produced by the production method | |
| JPS5884928A (en) | Production of high-strength cold-rolled steel plate for deep drawing having excellent nonaging property, secondary workability and curing performance for baked paint | |
| JP3489295B2 (en) | Method of manufacturing cold-rolled steel strip for deep drawing by continuous annealing | |
| JP3466298B2 (en) | Manufacturing method of cold rolled steel sheet with excellent workability | |
| JP2971192B2 (en) | Manufacturing method of cold-rolled steel sheet for deep drawing | |
| WO2005083140A1 (en) | Extremely thin cold rolled steel sheet having high strength, method for production thereof, material for gasket using the sheet and gasket member using the material | |
| JP2733423B2 (en) | Plated sheet excellent in secondary workability and weldability and method for producing the same | |
| JPS6046167B2 (en) | Method for manufacturing high-strength cold-rolled steel sheets for deep scratching that are non-aging and have excellent paint-baking hardenability through continuous annealing | |
| CN113748220B (en) | Steel sheet for can and method for producing same | |
| JP3049147B2 (en) | Method for producing high-tensile cold-rolled steel sheet with excellent chemical conversion property and deep drawability | |
| JP3293001B2 (en) | Method of manufacturing high strength galvannealed hot-rolled steel sheet with excellent stretch flangeability | |
| JPH08155565A (en) | Production of light weight can excellent in bottom pressure withstanding strength | |
| JP3596036B2 (en) | Manufacturing method of steel plate for can-making | |
| JP3048739B2 (en) | Method for producing high strength alloyed hot-dip galvanized steel sheet with excellent stretch flangeability | |
| JPH03277739A (en) | High r value clad steel sheet excellent in burring resistance at the time of press forming and its manufacture | |
| JP4218598B2 (en) | High tensile alloyed hot dip galvanized steel sheet with excellent plating characteristics |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A02 | Decision of refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A02 Effective date: 20021119 |