JP2001073073A - Steel plate for thick plate disk clutch and its production - Google Patents
Steel plate for thick plate disk clutch and its productionInfo
- Publication number
- JP2001073073A JP2001073073A JP24466599A JP24466599A JP2001073073A JP 2001073073 A JP2001073073 A JP 2001073073A JP 24466599 A JP24466599 A JP 24466599A JP 24466599 A JP24466599 A JP 24466599A JP 2001073073 A JP2001073073 A JP 2001073073A
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- Prior art keywords
- plate
- steel plate
- less
- steel
- disk clutch
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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- Mechanical Operated Clutches (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、自動車のオートマ
チックトランスミッションに組み込まれるプレートディ
スククラッチに適した鋼板に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a steel plate suitable for a plate disk clutch incorporated in an automatic transmission of an automobile.
【０００２】[0002]
【従来の技術】自動車のオートマチックトランスミッシ
ョンに組み込まれるプレートディスククラッチはプレー
トの摩擦力により遊星歯車にクラッチ、ブレーキとして
働き、変速比を変える役割をはたしている。このプレー
トディスククラッチは、焼鈍されたＳ５３Ｃ等のＳＣ材
を冷延した鋼板を用い、打ち抜きし、表面に摩擦紙を貼
った、ドライブプレートと呼ばれるものと、そのままで
使用される、ドリブンプレートと呼ばれるものを交互に
配置した機構になっている。これらのプレートの接触摩
擦により、遊星歯車のブレーキ、クラッチの働きをす
る。前者は摩擦紙が存在するため、鋼板表面の耐磨耗性
を必要としなく、打ち抜き面のみの耐磨耗性を必要とす
る。後者は、鋼板表面および打ち抜き面共に耐磨耗性が
要求される。また、変速時毎に急激な応力が交番的にプ
レートに加わるため疲労特性、衝撃特性も耐磨耗性と共
に必要である。打ち抜きのまま製品として用いられるた
め、打ち抜き寸法精度も厳しい。2. Description of the Related Art A plate disk clutch incorporated in an automatic transmission of an automobile works as a clutch and a brake on a planetary gear by a frictional force of a plate, and plays a role of changing a gear ratio. The plate disk clutch is made of a cold rolled steel sheet of an annealed SC material such as S53C, and is punched and affixed to the surface with friction paper, which is called a drive plate, and used as it is, called a driven plate. It is a mechanism in which things are arranged alternately. The contact friction between these plates acts as a planetary gear brake and clutch. The former does not require the wear resistance of the steel plate surface due to the presence of friction paper, and requires the wear resistance of only the punched surface. The latter requires abrasion resistance on both the steel sheet surface and the punched surface. Further, since a sudden stress is alternately applied to the plate every time the gear is shifted, fatigue characteristics and impact characteristics are required together with wear resistance. Since it is used as a punched product, the dimensional accuracy of the punch is strict.
【０００３】従来のＳ３５Ｃの焼鈍−冷延鋼板は鋼板表
面の耐磨耗性は優れているが、打ち抜き面の耐磨耗性に
問題があり、鋼板中にある炭化物が打ち抜き時にクラッ
クとなり、疲労破壊の起点となることがあった。冷延加
工度を高く取らなければ、耐磨耗性を確保できないた
め、必然的に高冷延率となるため、現行の製鉄設備では
厚手の鋼板を製造できなく、また製品の衝撃特性も問題
がある。[0003] The conventional annealed-cold rolled steel sheet of S35C has excellent abrasion resistance on the steel sheet surface, but has a problem in abrasion resistance on a punched surface. It could be a starting point for destruction. Unless the degree of cold rolling is set high, abrasion resistance cannot be ensured, resulting in inevitably a high cold rolling rate.Thus, current steelmaking equipment cannot produce thick steel sheets, and the product has poor impact characteristics. There is.
【０００４】[0004]
【発明が解決しようとする課題】鋼の耐磨耗性の改善手
段については種々の技術が開示されているが、プレート
ディスククラッチ打ち抜き面の耐磨耗性の改善と疲労特
性、衝撃特性を同時に解決する技術の開示はない。鋼板
表面および打ち抜き面の耐磨耗性が優れ、かつ、疲労特
性、衝撃特性が優れた厚手のプレートディスククラッチ
用に適した鋼板を提供することを目的とする。Various techniques have been disclosed as means for improving the wear resistance of steel. However, the improvement of the wear resistance and the fatigue and impact characteristics of the plate disk clutch punched surface are simultaneously performed. There is no disclosure of the technology to be solved. An object of the present invention is to provide a steel plate having excellent wear resistance on the surface of a steel plate and a punched surface, and excellent in fatigue characteristics and impact characteristics and suitable for a thick plate disk clutch.
【０００５】[0005]
【課題を解決するための手段】本発明は、プレートディ
スククラッチ用鋼板について、鋼成分、製造条件等を広
範囲に検討し、得られた知見に基づき完成したものであ
る。SUMMARY OF THE INVENTION The present invention has been completed based on the findings obtained by examining a wide range of steel components, manufacturing conditions and the like for a steel plate for a plate disk clutch.
【０００６】本発明の要旨は、以下の通りである。The gist of the present invention is as follows.
【０００７】（１） 重量％で、Ｃ：０．３％以下、Ｍ
ｎ：０．６〜１．５％を含有することを特徴とするプレ
ートディスククラッチ用鋼板。(1) By weight%, C: 0.3% or less, M
n: a steel plate for a plate disk clutch, comprising 0.6 to 1.5%.
【０００８】（２） 重量％で、Ｃ：０．２５％以下、
Ｍｎ：０．９〜１．５％を含有することを特徴とするプ
レートディスククラッチ用鋼板。(2) In weight%, C: 0.25% or less,
A steel plate for a plate disk clutch, comprising Mn: 0.9 to 1.5%.
【０００９】（３） 重量％で、Ｃ：０．３％以下、Ｍ
ｎ：０．６〜１．５％、Ｓｉ：０．３５％以下、Ｐ：
０．０２％以下、Ｓ：０．０２％以下、Ａｌ：０．００
５〜０．０６％、Ｎ：０．００６％以下、Ｔｉ：０．０
１〜０．１％、Ｂ：０．００１〜０．００４％、残部Ｆ
ｅおよび不可避的不純物からなり、厚み１．８ｍｍ以上
であることを特徴とするプレートディスククラッチ用鋼
板。(3) By weight%, C: 0.3% or less, M
n: 0.6 to 1.5%, Si: 0.35% or less, P:
0.02% or less, S: 0.02% or less, Al: 0.00
5 to 0.06%, N: 0.006% or less, Ti: 0.0
1 to 0.1%, B: 0.001 to 0.004%, balance F
(e) and an unavoidable impurity, and has a thickness of 1.8 mm or more.
【００１０】（４） 重量％で、Ｃ：０．３％以下、Ｍ
ｎ：０．６〜１．５％を含有する鋼を熱延し、脱スケー
ルを行い、焼鈍を行うことなく冷延することを特徴とす
るプレートディスククラッチ用鋼板の製造方法。(4) By weight%, C: 0.3% or less, M
n: A method for producing a steel plate for a plate disk clutch, wherein a steel containing 0.6 to 1.5% is hot-rolled, descaled, and cold-rolled without annealing.
【００１１】（５） 重量％で、Ｃ：０．２５％以下、
Ｍｎ：０．９〜１．５％を含有する鋼を熱延し、脱スケ
ールを行い、焼鈍を行うことなく冷延することを特徴と
するプレートディスククラッチ用鋼板の製造方法。(5) In weight%, C: 0.25% or less,
A method for producing a steel plate for a plate disk clutch, wherein a steel containing Mn: 0.9 to 1.5% is hot-rolled, descaled, and cold-rolled without annealing.
【００１２】（６） 重量％で、Ｃ：０．３％以下、Ｍ
ｎ：０．６〜１．５％、Ｓｉ：０．３５％以下、Ｐ：
０．０２％以下、Ｓ：０．０２％以下、Ａｌ：０．００
５〜０．０６％、Ｎ：０．００６％以下、Ｔｉ：０．０
１〜０．１％、Ｂ：０．００１〜０．００４％、残部Ｆ
ｅおよび不可避的不純物からなる鋼を熱延し、脱スケー
ルを行い、焼鈍を行うことなく１．８ｍｍ以上の厚みに
冷延することを特徴とするプレートディスククラッチ用
鋼板の製造方法。(6) By weight%, C: 0.3% or less, M
n: 0.6 to 1.5%, Si: 0.35% or less, P:
0.02% or less, S: 0.02% or less, Al: 0.00
5 to 0.06%, N: 0.006% or less, Ti: 0.0
1 to 0.1%, B: 0.001 to 0.004%, balance F
e. A method for producing a steel plate for a plate disk clutch, comprising hot-rolling steel comprising unavoidable impurities, descaling, and cold-rolling to a thickness of 1.8 mm or more without annealing.
【００１３】[0013]
【発明の実施の形態】本発明の鋼板は、プレートディス
ククラッチ用鋼板に具備する特性の鋼板表面および打ち
抜き面の耐磨耗性、打ち抜き性、疲労特性、衝撃特性を
兼備し、しかも製造コストが安価で、厚手鋼板も容易に
製造可能なように成分設計したものである。ここでいう
打ち抜き性は打ち抜き寸法精度が良好で打ち抜き面のク
ラック等の欠陥がないことである。低コスト化は鋼の溶
製コストが安く、製造歩留まりが良好でしかも熱延後の
焼鈍工程を省略が可能とすることである。BEST MODE FOR CARRYING OUT THE INVENTION The steel sheet of the present invention has both the wear resistance, punching property, fatigue property and impact property of the steel sheet surface and the punched surface, which are the characteristics of a steel sheet for a plate disk clutch, and has a low manufacturing cost. The components are designed so that they are inexpensive and can easily produce thick steel plates. Here, the punching property means that the punching dimensional accuracy is good and there are no defects such as cracks on the punched surface. Lower cost means that the cost of smelting steel is low, the production yield is good, and the annealing step after hot rolling can be omitted.
【００１４】プレートディスククラッチの耐磨耗性は
基本的には鋼板の硬度に比例する。同一硬さであれば、
ＴｉＣ、セメンタイト等の硬質析出物が多いほど良好に
なる。したがって、鋼板表面の耐磨耗性は鋼板の硬さを
高くすれば良く、打ち抜き断面の耐磨耗性は打ち抜き面
の加工硬化が大きいほど優れる。The wear resistance of a plate disk clutch is basically proportional to the hardness of a steel plate. If the hardness is the same,
The more hard precipitates such as TiC and cementite, the better. Therefore, the wear resistance of the steel sheet surface may be increased by increasing the hardness of the steel sheet, and the wear resistance of the punched cross section is improved as the work hardening of the punched face increases.
【００１５】疲労特性は、基本的に鋼板の硬さで決ま
るが、打ち抜き面のクラックが入り易い場合に劣化す
る。疲労破壊は打ち抜き面から発生し、クラック等がな
い場合は、打ち抜き面の加工硬化が大きいほど優れる。
打ち抜き面の加工硬化を大きくするには、冷延圧下率が
小さいほど、Ｍｎ量が高いほど良好になる。The fatigue characteristics are basically determined by the hardness of the steel sheet, but deteriorate when the punched surface is easily cracked. The fatigue fracture occurs from the punched surface, and when there is no crack or the like, the greater the work hardening of the punched surface, the better.
In order to increase the work hardening of the punched surface, the lower the rolling reduction of the cold rolling and the higher the Mn content, the better.
【００１６】衝撃特性は同一硬さの場合、冷間圧延率
が小さいほど良好になる。In the case of the same hardness, the impact characteristics become better as the cold rolling reduction is smaller.
【００１７】打ち抜き断面のクラックは、パーライト
のような比較的大きな相の混合組織、大きな介在物が存
在する時に生じ易い。このため、現行のＳ３５Ｃは熱延
板を焼鈍し、パーライトを分解させ、フェライトとセメ
ンタイト組織にしてから、冷延により硬度の調整を行っ
ている。Cracks in the punched section are likely to occur when a relatively large phase mixed structure such as pearlite and large inclusions are present. Therefore, in the current S35C, the hardness is adjusted by cold rolling after annealing the hot-rolled sheet to decompose the pearlite to form a ferrite and cementite structure.
【００１８】打ち抜き寸法精度は鋼板の異方性が大き
いと劣る。鋼板の異方性は冷延圧下率が高いほど大きく
なる。熱延板を焼鈍することなく冷延すると、焼鈍後に
冷延したものより大きくなる。したがって、現行のＳ３
５Ｃを焼鈍することなく、冷延すると打ち抜き精度が劣
化すると同時に打ち抜き時にクラックが発生しやすく、
疲労特性が劣化する。The dimensional accuracy of punching is inferior when the anisotropy of the steel sheet is large. The anisotropy of the steel sheet increases as the rolling reduction of the cold rolling increases. If the hot-rolled sheet is cold-rolled without annealing, it will be larger than the one cold-rolled after annealing. Therefore, the current S3
If cold rolling is performed without annealing 5C, the punching accuracy will be degraded, and at the same time, cracks will easily occur at the time of punching,
Fatigue properties deteriorate.
【００１９】焼鈍を省略し、低冷延率で所定の硬さを
得、かつ、打ち抜き性、疲労特性を良好にするにはＣ量
を低め、Ｍｎ量を高くすれば良い。To omit the annealing, obtain a predetermined hardness at a low cold rolling rate, and improve the punching properties and fatigue properties, it is only necessary to lower the C content and increase the Mn content.
【００２０】以上の知見から本発明は鋼成分の内、Ｃ量
を低くし、Ｍｎ量を高くすることにより、熱延板の強度
が高くなり、低冷延率でも耐磨耗性に必要な硬さが得ら
れ、同時に焼鈍を省略しても打ち抜き性が良好な鋼板が
得られる。焼鈍を省略し、低冷延率で製造できると、衝
撃特性も良好となり打ち抜き面の加工硬化量も大きくな
るので、打ち抜き面の耐磨耗性が向上し、熱延、酸洗工
程を通板する時の板厚も必然的に薄くなり、工程能力が
障害となることなく、厚い製品の製造か可能となる。From the above findings, the present invention increases the strength of the hot-rolled sheet by lowering the amount of C and increasing the amount of Mn among the steel components. Hardness is obtained, and at the same time, a steel sheet with good punching properties can be obtained even if annealing is omitted. If annealing can be omitted and a low cold rolling rate can be manufactured, the impact characteristics will be good and the work hardening amount of the punched surface will be large, so the wear resistance of the punched surface will be improved, and the hot rolling and pickling processes In addition, the thickness of the sheet is inevitably reduced, and a thick product can be manufactured without impeding the process capability.
【００２１】以下、本発明の鋼組成について説明する。Hereinafter, the steel composition of the present invention will be described.
【００２２】Ｃ：０．３％以下 先述したように、Ｃ量が高いと熱延後の焼鈍を省略した
場合、打ち抜き性、疲労特性が劣化する。すなわち、Ｃ
量が０．３％以上になると熱延板の組織はフェライト＋
パーライトの混合組織となり、打ち抜き時に硬いパーラ
イト部とフェライトの境界部にクラックが生じ易くな
り、疲労破壊の原因となる。したがって、本発明の目的
である熱延板の焼鈍を省略する方法では、Ｃ量を０．３
％以下にする必要がある。好ましい範囲は同様の理由か
ら０．２５％以下である。Ｃ量の下限は特に限定する必
要がないが、Ｃ量があまり低くなりすぎると熱延板の強
度が低下し、耐磨耗性に必要な硬さを得るに必要な冷延
率が高くなるため、０．０５％以上とすることが好まし
い。C: 0.3% or less As described above, if the C content is high, the punching properties and fatigue properties deteriorate when annealing after hot rolling is omitted. That is, C
When the amount exceeds 0.3%, the structure of the hot rolled sheet becomes ferrite +
It becomes a mixed structure of pearlite, and cracks easily occur at the boundary between the hard pearlite portion and ferrite at the time of punching, which causes fatigue fracture. Therefore, in the method of omitting the annealing of the hot-rolled sheet, which is the object of the present invention, the C content is set to 0.3
% Or less. A preferable range is 0.25% or less for the same reason. The lower limit of the C content is not particularly limited, but if the C content is too low, the strength of the hot-rolled sheet decreases, and the cold-rolling ratio required to obtain the hardness required for abrasion resistance increases. Therefore, the content is preferably set to 0.05% or more.
【００２３】Ｍｎ：０．６〜１．５％ Ｍｎは焼鈍省略して低冷延率で耐磨耗性の確保と打ち抜
き断面の耐磨耗性のために必要な元素である。Ｍｎ量が
０．６％以下になると打ち抜き断面の耐磨耗性が不十分
な上に、表面の耐磨耗性を満足させるためには冷延率を
高く取る必要となり、本発明の目的である、厚手鋼板の
製造が困難となるばかりでなく、衝撃特性も劣化する。
したがって、０．６％以上添加する必要がある。一方、
Ｍｎ量が１．５％を超えると打ち抜き面にクラックが生
じ易くなるため、上限を１．５％に特定した。好ましい
範囲は同様の理由から０．９〜１．２％である。Mn: 0.6 to 1.5% Mn is an element necessary for securing abrasion resistance at a low cold rolling rate and omitting annealing and for abrasion resistance of a punched section. When the Mn content is 0.6% or less, the abrasion resistance of the punched cross section is insufficient, and it is necessary to increase the cold rolling ratio in order to satisfy the abrasion resistance of the surface. Certainly, not only is it difficult to manufacture a thick steel plate, but also the impact characteristics are deteriorated.
Therefore, it is necessary to add 0.6% or more. on the other hand,
If the Mn content exceeds 1.5%, cracks are likely to occur on the punched surface, so the upper limit was specified at 1.5%. A preferable range is 0.9 to 1.2% for the same reason.
【００２４】Ｓｉ：０．３５％以下 Ｓｉは脱酸剤として使用する場合、必然的に含有し、鋼
板の強化元素として有効であるが、０．３５％以上にな
るとスケール疵等の表面欠陥の原因となるため、上限を
０．３５％の範囲で添加することとしたが、０．２％以
下とすることが好ましい。Si: 0.35% or less Si is inevitably contained when used as a deoxidizing agent and is effective as a strengthening element for steel sheets. However, when it exceeds 0.35%, surface defects such as scale flaws are reduced. Because of the cause, the upper limit was added in the range of 0.35%, but it is preferably 0.2% or less.
【００２５】Ｐ：０．０２％以下 Ｐは不純物として、不可避的に混入するが、０．０２％
を超えると打ち抜き性を阻害するので０．０２％以下に
することが好ましい。P: 0.02% or less P is inevitably mixed as an impurity.
If more than 0.03%, the punching property is impaired.
【００２６】Ｓ：０．０２％以下 ＳはＭｎと結合し、介在物となり、やはり打ち抜き性を
阻害するため、０．０２％以下にすることが好ましい。S: 0.02% or less S binds to Mn to form inclusions, which also impairs the punching property. Therefore, the content of S is preferably set to 0.02% or less.
【００２７】Ａｌ：０．００５〜０．０６％溶鋼の脱酸
剤として使用される成分であり、添加量が少ないと鋼板
の打ち抜き時にクラックが生じ易くなる。一方、Ａｌ量
が多くなるとアルミ酸化物が増加し、表面欠陥が増え、
製品歩留まりを低下させるため、０．００５〜０．０６
％としたが、０．０１〜０．０６％の範囲で添加するこ
とが好ましい。Al: 0.005% to 0.06% Al is a component used as a deoxidizing agent for molten steel. If the amount of Al is small, cracks are likely to occur when punching a steel sheet. On the other hand, when the amount of Al increases, aluminum oxide increases, surface defects increase,
0.005 to 0.06 to reduce product yield
%, But is preferably added in the range of 0.01 to 0.06%.
【００２８】Ｎ：０．００６％以下 ＮはＡｌ、Ｓｉ窒化物を形成し、耐磨耗性を向上させる
が、添加量が多くなると衝撃特性を劣化させるので、上
限を０．００６％の範囲にすることが好ましい。N: 0.006% or less N forms Al and Si nitrides and improves abrasion resistance. However, if the addition amount is large, the impact characteristics are deteriorated, so the upper limit is 0.006%. Is preferable.
【００２９】Ｔｉ：０．０１〜０．１％ Ｔｉは鋼中のＮ、Ｃと結合し、窒化物、炭化物を形成
し、耐磨耗性の向上に有効な元素である。一方、添加量
が多くなると衝撃特性を劣化させることがある。したが
って、特に耐磨耗性が必要な時にＴｉを添加する場合
は、０．０１〜０．１％としたが、０．０１〜０．０６
％の範囲で添加することが好ましい。Ti: 0.01-0.1% Ti combines with N and C in steel to form nitrides and carbides, and is an element effective for improving wear resistance. On the other hand, when the addition amount is large, the impact characteristics may be deteriorated. Therefore, when Ti is added particularly when abrasion resistance is required, the content is 0.01 to 0.1%, but 0.01 to 0.06%.
% Is preferably added.
【００３０】Ｂ：０．００１〜０．００４％ Ｂは粒界に偏析し、粒界強度を高める元素であることが
良く知られている。本発明の場合、特に疲労特性を必要
とする場合は、打ち抜き面のミクロクラックを無くする
目的でＢを添加する。Ｂ量が０．００１％未満の添加で
はその効果を発揮できなく、０．００４％を超えて添加
すると粒界に（Ｆｅ、Ｂ）炭化物が生成し易くなり、逆
にミクロクラックが増加するため、０．００１〜０．０
０４％の範囲で添加することが好ましい。B: 0.001 to 0.004% It is well known that B is an element that segregates at grain boundaries and increases the strength of grain boundaries. In the case of the present invention, particularly when fatigue properties are required, B is added for the purpose of eliminating microcracks on the punched surface. When the amount of B is less than 0.001%, the effect cannot be exhibited. When the amount of B exceeds 0.004%, (Fe, B) carbide is easily generated at the grain boundary, and conversely, micro cracks increase. , 0.001-0.0
It is preferable to add in the range of 04%.
【００３１】厚み１．８ｍｍ以上 本発明は熱延板を焼鈍することなく冷延し、製品を提供
できる。この理由は、低Ｃ化、高Ｍｎ化により、パーラ
イト量を少なくできるため焼鈍を省略しても、打ち抜き
性、疲労強度に悪影響を及ぼさなく、熱延板の強度を高
くすることで、低冷延率で耐磨耗性に必要硬さが得られ
るためである。この特徴により、従来の方法に比べて同
一熱延板厚では厚い製品が得られる。したがって、従来
製造ができなかった厚手の製品が得られる。打ち抜き時
の寸法精度、歪、打ち抜き面のクラックが発生等は製品
厚みが厚いほど悪くなる。しかし、本発明はこれらの特
性が優れているため、特性上からも厚手製品が製造可能
で、１．８ｍｍ以上でこの特徴が発揮される。とりわ
け、２．４ｍｍ以上の厚みで顕著な効果を発揮する。The present invention can provide a product by cold rolling a hot-rolled sheet without annealing. The reason is that the amount of pearlite can be reduced by lowering the C and increasing the Mn, so that even if the annealing is omitted, the punching property and the fatigue strength are not adversely affected, and the strength of the hot-rolled sheet is increased, so that the low cooling is achieved. This is because the required hardness for abrasion resistance can be obtained at the elongation. Due to this feature, a thicker product can be obtained with the same hot-rolled sheet thickness as compared with the conventional method. Therefore, a thick product that could not be manufactured conventionally can be obtained. The dimensional accuracy at the time of punching, distortion, cracks on the punched surface, and the like become worse as the product thickness increases. However, since the present invention is excellent in these characteristics, a thick product can be manufactured from the viewpoint of the characteristics, and this characteristic is exhibited at 1.8 mm or more. In particular, a remarkable effect is exhibited at a thickness of 2.4 mm or more.
【００３２】[0032]
【実施例】表１の組成を持つ鋼を転炉で溶製し、連続鋳
造でスラブとし、表１に記載の条件で熱間圧延、冷間圧
延して、鋼板を製造した。これらの鋼板を図１に示すよ
うな形状のドリブンプレートを打ち抜きで作成した。こ
の時、寸法および歪を測定した。寸法精度は圧延方向と
圧延方向と９０度方向の直径差で評価した。打ち抜き歪
は打ち抜き製品を定盤に乗せ、そのときの定盤と製品と
の最大隙間で評価した。これらのプレートをオートマチ
ックトランスミッションに組み込み、耐久試験を行いプ
レートディスククラッチ用に適しているかを評価した。
耐久試験後にオートマチックトランスミッションを分解
し、ドリブンプレートにクラック等の外観欠陥が観察さ
れるか、打ち抜き面、表面に明らかに磨耗が観察される
ものを×、外観欠陥がないが、打ち抜き面、表面に磨耗
が観察されるものを△、外観欠陥も磨耗も観察されない
ものを○の評点を付け、評価した。これとは別に、磨耗
性、衝撃性、疲労特性を調査した。耐磨耗性は打ち抜き
面および板面の磨耗試験を行い、それぞれ評価した。衝
撃性は、２ｍｍＵノッチ試験片を作り、常温での衝撃値
で評価した。疲労特性は試験片中央に直系５ｍｍの打ち
抜き穴の切り欠き疲労試験を行い、疲労限で評価した。EXAMPLES Steel having the composition shown in Table 1 was melted in a converter, slab was formed by continuous casting, and hot-rolled and cold-rolled under the conditions shown in Table 1 to produce steel sheets. These steel plates were formed by punching a driven plate having a shape as shown in FIG. At this time, dimensions and strain were measured. The dimensional accuracy was evaluated based on the rolling direction and the diameter difference between the rolling direction and the 90 ° direction. The punching distortion was evaluated by placing the punched product on a surface plate and the maximum gap between the surface plate and the product at that time. These plates were assembled into an automatic transmission and subjected to a durability test to evaluate whether they were suitable for a plate disk clutch.
After the endurance test, disassemble the automatic transmission.If the driven plate shows cracks or other appearance defects, or if the punched surface and surface are clearly worn, the appearance is x. Those with abrasion were rated as △, and those with neither appearance defect nor abrasion were rated with ○. Apart from this, abrasion, impact and fatigue properties were investigated. The abrasion resistance was evaluated by performing a wear test on a punched surface and a plate surface. The impact property was evaluated by making a 2 mm U notch test piece and measuring the impact value at room temperature. The fatigue characteristics were evaluated by performing a notch fatigue test of a punched hole of 5 mm in a straight line at the center of the test piece, and evaluating the fatigue limit.
【００３３】本発明範囲の実施例のＡ、Ｂ、Ｃ、Ｄ、
Ｅ、Ｆは、耐久試験の評価が良好であるのは勿論、耐磨
耗性が優れており、とりわけ、打ち抜き面の耐磨耗性が
比較材との比較で優れていることが分かる。また、疲労
特性、衝撃特性が良好であり、優れたプレートディスク
クラッチ用鋼板に供せる。また、比較例に比べて、冷延
率が低くても、良好なプレートディスククラッチ用鋼板
が必要とする特性が発揮できるので、冷延工程より前の
製造工程能力に左右されることなく、厚手の鋼板が製造
可能である。Examples A, B, C, D, and
It is understood that E and F have excellent abrasion resistance as well as good evaluation in the durability test, and in particular, the abrasion resistance of the punched surface is excellent in comparison with the comparative material. In addition, it has good fatigue characteristics and impact characteristics, and can be used as an excellent steel plate for a plate disk clutch. In addition, compared to the comparative example, even if the cold rolling rate is low, the characteristics required for a good steel plate for a plate disk clutch can be exhibited, so that the steel sheet can be made thick without being affected by the manufacturing process capability before the cold rolling process. Can be manufactured.
【００３４】一方、Ｃが本発明範囲外のＧ、Ｈは耐久試
験と表面の耐磨耗性が良好であるが、打ち抜き時の歪、
打ち抜き精度が劣り、プレート製造時の生産性、歩留ま
り低下となる。また、本発明の実施例に比較して、打ち
抜き面の耐磨耗性、衝撃特性、疲労特性が劣る。On the other hand, C and G, which are out of the range of the present invention, have good durability test and abrasion resistance of the surface.
The punching accuracy is inferior, and the productivity and the yield during plate production decrease. Moreover, the abrasion resistance, impact characteristics, and fatigue characteristics of the punched surface are inferior to those of the examples of the present invention.
【００３５】Ｍｎ量が本発明範囲外のＪは耐久試験で磨
耗が観察される。これは耐磨耗性試験結果とも一致して
おり、耐磨耗性、疲労特性、衝撃値も低く、プレートデ
ィスククラッチ用鋼板に適さないことが分かる。In the case of J having an Mn content outside the range of the present invention, abrasion is observed in a durability test. This is consistent with the results of the wear resistance test, indicating that the wear resistance, the fatigue properties, and the impact value are low, and are not suitable for a steel plate for a plate disk clutch.
【００３６】Ｍｎ、Ｃが本発明範囲外のＩは耐磨耗性が
劣り、打ち抜き性も悪く、しかも、疲労特性、衝撃特性
も劣っている。I, whose Mn and C are out of the range of the present invention, is inferior in abrasion resistance, poor in punching properties, and inferior in fatigue properties and impact properties.
【００３７】[0037]
【表１】 [Table 1]
【００３８】[0038]
【表２】 [Table 2]
【００３９】[0039]
【発明の効果】以上の実施例で見てきたように、本発明
は優れた耐磨耗性と衝撃、疲労特性を有し、打ち抜き性
も良好なプレートディスククラッチ用鋼板である。とり
わけ、最終冷延率を小さくしても、プレートディスクク
ラッチ用鋼板に必要な特性が得られるので、厚手鋼板の
製造に適している。As can be seen from the above embodiments, the present invention is a steel plate for a plate disk clutch having excellent wear resistance, impact and fatigue characteristics, and good punching properties. In particular, even if the final cold rolling reduction is reduced, the characteristics required for a steel plate for a plate disk clutch can be obtained, so that it is suitable for the production of a thick steel plate.
【図１】ドリブンプレートの形状を示す図である。FIG. 1 is a view showing the shape of a driven plate.
１ ドリブンプレート 1 driven plate
───────────────────────────────────────────────────── フロントページの続き (72)発明者 佐柳 志郎 北九州市戸畑区飛幡町１−１ 新日本製鐵 株式会社八幡製鐵所内 Ｆターム(参考） 3J056 AA60 BA01 BC02 EA02 EA13 EA23 FA03 GA05 GA12 4K037 EA01 EA02 EA05 EA06 EA15 EA18 EA23 EA25 EA27 EA31 EB05 FG01 JA06 ────────────────────────────────────────────────── ─── Continuing on the front page (72) Inventor Shiro Sanagi 1-1 Hibata-cho, Tobata-ku, Kitakyushu Nippon Steel Corporation Yawata Works F-term (reference) 3J056 AA60 BA01 BC02 EA02 EA13 EA23 FA03 GA05 GA12 4K037 EA01 EA02 EA05 EA06 EA15 EA18 EA23 EA25 EA27 EA31 EB05 FG01 JA06
Claims (6)
０．６〜１．５％を含有することを特徴とするプレート
ディスククラッチ用鋼板。(1) C: 0.3% or less, Mn:
A steel plate for a plate disk clutch, comprising 0.6 to 1.5%.
０．９〜１．５％を含有することを特徴とするプレート
ディスククラッチ用鋼板。2. In% by weight, C: 0.25% or less, Mn:
A steel plate for a plate disk clutch, comprising 0.9 to 1.5%.
０．６〜１．５％、Ｓｉ：０．３５％以下、Ｐ：０．０
２％以下、Ｓ：０．０２％以下、Ａｌ：０．００５〜
０．０６％、Ｎ：０．００６％以下、Ｔｉ：０．０１〜
０．１％、Ｂ：０．００１〜０．００４％、残部Ｆｅお
よび不可避的不純物からなり、厚み１．８ｍｍ以上であ
ることを特徴とするプレートディスククラッチ用鋼板。3. C .: not more than 0.3% by weight, Mn:
0.6-1.5%, Si: 0.35% or less, P: 0.0
2% or less, S: 0.02% or less, Al: 0.005 to
0.06%, N: 0.006% or less, Ti: 0.01 to
0.1%, B: 0.001 to 0.004%, the balance being Fe and unavoidable impurities, and having a thickness of 1.8 mm or more, a steel plate for a plate disk clutch.
０．６〜１．５％を含有する鋼を熱延し、脱スケールを
行い、焼鈍を行うことなく冷延することを特徴とするプ
レートディスククラッチ用鋼板の製造方法。4. C .: not more than 0.3% by weight, Mn:
A method for producing a steel plate for a plate disc clutch, comprising hot rolling a steel containing 0.6 to 1.5%, descaling, and cold rolling without annealing.
０．９〜１．５％を含有する鋼を熱延し、脱スケールを
行い、焼鈍を行うことなく冷延することを特徴とするプ
レートディスククラッチ用鋼板の製造方法。5. C: 0.25% or less by weight, Mn:
A method for producing a steel plate for a plate disk clutch, wherein a steel containing 0.9 to 1.5% is hot-rolled, descaled, and cold-rolled without annealing.
０．６〜１．５％、Ｓｉ：０．３５％以下、Ｐ：０．０
２％以下、Ｓ：０．０２％以下、Ａｌ：０．００５〜
０．０６％、Ｎ：０．００６％以下、Ｔｉ：０．０１〜
０．１％、Ｂ：０．００１〜０．００４％、残部Ｆｅお
よび不可避的不純物からなる鋼を熱延し、脱スケールを
行い、焼鈍を行うことなく１．８ｍｍ以上の厚みに冷延
することを特徴とするプレートディスククラッチ用鋼板
の製造方法。6. C: 0.3% or less in weight%, Mn:
0.6-1.5%, Si: 0.35% or less, P: 0.0
2% or less, S: 0.02% or less, Al: 0.005 to
0.06%, N: 0.006% or less, Ti: 0.01 to
0.1%, B: 0.001 to 0.004%, steel consisting of the balance Fe and unavoidable impurities is hot rolled, descaled, and cold rolled to a thickness of 1.8 mm or more without annealing. A method for producing a steel plate for a plate disk clutch, characterized in that:
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24466599A JP3619400B2 (en) | 1999-08-31 | 1999-08-31 | Steel plate for thick plate disk clutch and manufacturing method thereof |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24466599A JP3619400B2 (en) | 1999-08-31 | 1999-08-31 | Steel plate for thick plate disk clutch and manufacturing method thereof |
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| Publication Number | Publication Date |
|---|---|
| JP2001073073A true JP2001073073A (en) | 2001-03-21 |
| JP3619400B2 JP3619400B2 (en) | 2005-02-09 |
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|---|---|---|---|
| JP24466599A Expired - Fee Related JP3619400B2 (en) | 1999-08-31 | 1999-08-31 | Steel plate for thick plate disk clutch and manufacturing method thereof |
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| Country | Link |
|---|---|
| JP (1) | JP3619400B2 (en) |
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