JP2011001604A - Steel plate for at separate plate - Google Patents
Steel plate for at separate plate Download PDFInfo
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- JP2011001604A JP2011001604A JP2009145836A JP2009145836A JP2011001604A JP 2011001604 A JP2011001604 A JP 2011001604A JP 2009145836 A JP2009145836 A JP 2009145836A JP 2009145836 A JP2009145836 A JP 2009145836A JP 2011001604 A JP2011001604 A JP 2011001604A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 34
- 239000010959 steel Substances 0.000 title claims abstract description 34
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 10
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 9
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 8
- 229910052796 boron Inorganic materials 0.000 claims abstract description 5
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 238000005096 rolling process Methods 0.000 claims description 2
- 238000005097 cold rolling Methods 0.000 abstract description 7
- 230000005540 biological transmission Effects 0.000 abstract description 4
- 239000000203 mixture Substances 0.000 abstract description 2
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 238000012360 testing method Methods 0.000 description 21
- 239000000463 material Substances 0.000 description 10
- 238000000034 method Methods 0.000 description 10
- 229910000734 martensite Inorganic materials 0.000 description 9
- 239000010410 layer Substances 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- 239000002783 friction material Substances 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 230000002093 peripheral effect Effects 0.000 description 3
- 239000002344 surface layer Substances 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 2
- 230000009471 action Effects 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 230000013011 mating Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 238000010998 test method Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 229910001651 emery Inorganic materials 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 230000001678 irradiating effect Effects 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000005121 nitriding Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000003908 quality control method Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
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- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
本発明は、自動車のオートマチックトランスミッションの湿式多板クラッチを構成する部材であるＡＴセパレートプレートに用いる鋼板に関する。 The present invention relates to a steel plate used for an AT separate plate which is a member constituting a wet multi-plate clutch of an automatic transmission of an automobile.
オートマチックトランスミッションの湿式多板クラッチは、摩擦材（例えば特殊な紙）を表面に貼り付けた複数の「フリクションプレート」と、その接触相手である「セパレートプレート」が交互に配置され、フリクションプレートとセパレートプレートの解放／締結を切り替える動作によって動力の伝達を制御する機構である。フリクションプレートとセパレートプレートは、いずれもリング状の鋼板部材である。湿式多板クラッチを構成するこれらのプレートは一般に「ＡＴプレート」と呼ばれる。本明細書でいう「ＡＴセパレートプレート」は、フリクションプレートの摩擦相手である上記「セパレートプレート」を意味する。 A wet type multi-plate clutch of an automatic transmission has a plurality of “friction plates” with friction materials (for example, special paper) attached to the surface, and “separate plates” that are contacted with them alternately. This is a mechanism for controlling the transmission of power by switching the release / fastening of the plate. Both the friction plate and the separate plate are ring-shaped steel plate members. These plates making up a wet multi-plate clutch are commonly referred to as “AT plates”. The “AT separate plate” in the present specification means the “separate plate” which is a friction partner of the friction plate.
ＡＴセパレートプレートは、フリクションプレートと接触するとともに、周囲のドラム（構造によっては内側のハブ）やケースに刻まれた溝と噛み合うようになっている。そのために、セパレートプレートのリング外周部（あるいは内周部）には溝と噛み合う「歯」が設けられている。歯の部分は耐摩耗性に優れることが要求される The AT separate plate is in contact with the friction plate and meshes with a peripheral drum (inner hub depending on the structure) or a groove formed in the case. For this purpose, "tooth" that engages with the groove is provided on the outer peripheral portion (or inner peripheral portion) of the ring of the separate plate. Tooth parts are required to have excellent wear resistance
特許文献１、２にはＡＴセパレートプレートに好適な比較的低コストの鋼材が開示されている。 Patent Documents 1 and 2 disclose a relatively low-cost steel material suitable for an AT separate plate.
自動車の運転中には、フリクションプレートとセパレートプレートの解放／締結状態を切り替える動作が頻繁に行われ、そのたびにセパレートプレートの表面はフリクションプレートの摩擦材と摩擦し、高温に曝される。過度な高温に曝されると、セパレートプレートの表面には「ヒートスポット」と呼ばれる変質層が局部的に形成されることがある。ヒートスポットは本来の表面に対し相対的に凸部となっており、摩擦材の摩耗を早めるなど、不具合の原因となる。 During operation of the automobile, an operation of switching between the release / fastened state of the friction plate and the separate plate is frequently performed, and the surface of the separate plate is rubbed against the friction material of the friction plate each time and is exposed to a high temperature. When exposed to an excessively high temperature, an altered layer called a “heat spot” may be locally formed on the surface of the separate plate. The heat spot is a convex portion relative to the original surface, which causes problems such as accelerated wear of the friction material.
ヒートスポットを抑制する技術として、特許文献３には低炭素鋼でフェライト→オーステナイト変態点を高温側へ移行させ、変態時の変形を軽減する手法が開示されている。特許文献４には熱伝導率の高い鋼を使用して熱拡散を促進させることにより変形を抑制する手法が開示されている。特許文献５にはオーステナイト単相鋼（ＳＵＳ）を使用することにより変態に伴う変形を回避する手法が開示されている。 As a technique for suppressing a heat spot, Patent Document 3 discloses a technique of reducing the deformation at the time of transformation by shifting the ferrite → austenite transformation point to a high temperature side in low carbon steel. Patent Document 4 discloses a technique of suppressing deformation by promoting thermal diffusion using steel having high thermal conductivity. Patent Document 5 discloses a technique for avoiding deformation associated with transformation by using austenitic single phase steel (SUS).
特許文献１、２に記載の技術は、比較的低コストで耐摩耗性および平坦性の高い部品の製造を可能にするものであり、ＡＴセパレートプレートを製造するうえで有用である。しかし、ヒートスポットの問題については特に考慮されていない。
特許文献３、４に記載の技術は、ヒートスポットの軽減を狙ったものである。しかし、歯の部分における耐摩耗性に関しては更なる向上が望まれる場合がある。
特許文献５に開示の鋼材はオーステナイト鋼であるので、コストが高い。
The techniques described in Patent Documents 1 and 2 enable the production of parts with high wear resistance and flatness at a relatively low cost, and are useful for producing an AT separate plate. However, no particular consideration is given to the heat spot problem.
The techniques described in Patent Documents 3 and 4 aim to reduce heat spots. However, further improvements may be desired with respect to wear resistance in the tooth portion.
Since the steel material disclosed in Patent Document 5 is austenitic steel, the cost is high.
本発明は、ヒートスポットの発生に対する抵抗力（耐ヒートスポット性）、および歯の部分の耐摩耗性を同時に改善することができる比較的安価なＡＴセパレートプレート用鋼板を提供しようというものである。 An object of the present invention is to provide a relatively inexpensive steel plate for an AT separate plate that can simultaneously improve resistance to heat spots (heat spot resistance) and wear resistance of a tooth portion.
上記目的は、質量％で、Ｃ：０.０５〜０.３０％、Ｓｉ：０.７％未満、Ｍｎ：１％以下、Ｐ：０.０３％以下、Ｓ：０.０３％以下、Ｃｒ：０〜０.３％、Ｍｏ：０〜０.０５％、Ｎｉ：０〜０.０５％、Ｂ：０〜０.０００３％、Ａｌ：０.００５％〜０.１％未満であり、さらにＴｉ：０.１％以下、Ｎｂ：０.３％以下、Ｖ：０.３％以下の１種以上を合計０.０６％以上含有し、残部がＦｅおよび不可避的不純物からなる組成を有し、冷間圧延により硬さが２００〜３２０ＨＶに調整されているＡＴセパレートプレート用鋼板によって達成される。 The purpose is mass%, C: 0.05 to 0.30%, Si: less than 0.7%, Mn: 1% or less, P: 0.03% or less, S: 0.03% or less, Cr : 0 to 0.3%, Mo: 0 to 0.05%, Ni: 0 to 0.05%, B: 0 to 0.0003%, Al: 0.005% to less than 0.1%, Further, it contains at least 0.06% of one or more of Ti: 0.1% or less, Nb: 0.3% or less, and V: 0.3% or less, with the balance being Fe and inevitable impurities. And achieved by a steel plate for an AT separate plate whose hardness is adjusted to 200 to 320 HV by cold rolling.
ここで、Ｃｒ、Ｍｏ、Ｎｉ、Ｂの下限０％は、鋼の品質管理における通常の分析手法において検出限界以下である場合を意味する。 Here, the lower limit of 0% for Cr, Mo, Ni and B means a case where the lower limit is below the detection limit in a normal analysis method in steel quality control.
また本発明では、特に優れた耐ヒートスポット性を有する鋼板として、上記の鋼板においてＳｉ含有量を０.７〜３.０％としたもの、あるいはさらにＡｌ含有量を０.１〜５.０％としたものが提供される。 In the present invention, as a steel plate having particularly excellent heat spot resistance, the above steel plate having a Si content of 0.7 to 3.0%, or an Al content of 0.1 to 5.0 is used. % Are provided.
本発明によれば、従来両立が困難であった「優れた耐ヒートスポット性」と「優れた耐摩耗性」を同時に実現することのできる低コストの鋼板が提供可能となる。したがって本発明は、ＡＴセパレートプレートの品質向上、ひいては湿式多板クラッチの性能向上に寄与するものである。 According to the present invention, it is possible to provide a low-cost steel sheet that can simultaneously realize “excellent heat spot resistance” and “excellent wear resistance” that have been difficult to achieve in the past. Therefore, the present invention contributes to improving the quality of the AT separate plate and thus improving the performance of the wet multi-plate clutch.
発明者らの詳細な検討によれば、ＡＴセパレートプレートにおいて問題となるヒートスポットは、マルテンサイト相を含む変質層であることが明らかとなった。セパレートプレートの表層部がフリクションプレートの摩擦材との摩擦によってオーステナイト生成領域（Ａｃ1点以上の温度域）に昇温したのち、摩擦が終了した時点で急冷されることによって、セパレートプレートの表層部が局部的にマルテンサイト相を含む変質層となり、ヒートスポットができる。ヒートスポットの部分はマルテンサイト相生成による体積増大によって、突起状となっている。 According to detailed examinations by the inventors, it has been clarified that the heat spot which is a problem in the AT separate plate is a deteriorated layer containing a martensite phase. After the surface layer of the separate plate is heated to the austenite generation region (temperature range of Ac 1 point or higher) by friction with the friction material of the friction plate, the surface layer of the separate plate is rapidly cooled when the friction is finished. Becomes a modified layer containing a martensite phase locally, and a heat spot is formed. The portion of the heat spot has a protruding shape due to an increase in volume due to martensite phase generation.
〔化学組成〕
発明者らは研究の結果、以下の成分設計を採用することが、本発明の課題を実現する上で極めて有効であることを見出した。
（１）低Ｃ化することによりマルテンサイト変態に伴う体積膨張率を低減する。
（２）焼入れ性向上元素Ｍｎ、Ｃｒ、Ｍｏ、Ｎｉ、Ｂを低減して焼入れ性を低下させ、マルテンサイトの生成を抑制する。
（３）Ｖ、Ｔｉ、Ｎｂの１種以上を積極添加して高温でのオーステナイト粒径を微細化することにより焼入れ性を低下させ、マルテンサイトの生成を抑制する。
（４）必要に応じてＳｉ、Ａｌを積極添加してＡ1、Ａ3変態点を上昇させ、マルテンサイトの生成を抑制する。
（５）Ｖ、Ｔｉ、Ｎｂの１種以上を積極添加して硬質炭化物を微細分散させ、耐摩耗性を向上させる。
[Chemical composition]
As a result of research, the inventors have found that adopting the following component design is extremely effective in realizing the object of the present invention.
(1) The volume expansion coefficient accompanying martensitic transformation is reduced by lowering C.
(2) Hardenability improving elements Mn, Cr, Mo, Ni, and B are reduced to lower the hardenability and suppress the formation of martensite.
(3) By actively adding one or more of V, Ti, and Nb to refine the austenite grain size at high temperature, the hardenability is lowered and the formation of martensite is suppressed.
(4) If necessary, Si and Al are positively added to raise the A 1 and A 3 transformation points and suppress the formation of martensite.
(5) At least one of V, Ti and Nb is positively added to finely disperse the hard carbide and improve the wear resistance.
各成分元素について簡単に説明する。以下、成分元素における「％」は特に断らない限り「質量％」を意味する。
Ｃは、耐摩耗性を担う硬質炭化物粒子を形成させるために０.０５％以上の含有量を確保する必要がある。ただし、Ｃ含有量が多くなるとマルテンサイトが生成した場合の体積膨張が増大し、ヒートスポットの突起高さが過大となりやすい。種々検討の結果、Ｃ含有量は０.３０％以下に制限される。
Each component element will be briefly described. Hereinafter, “%” in the component elements means “mass%” unless otherwise specified.
C needs to secure a content of 0.05% or more in order to form hard carbide particles responsible for wear resistance. However, when the C content increases, the volume expansion when martensite is generated increases, and the protrusion height of the heat spot tends to be excessive. As a result of various studies, the C content is limited to 0.30% or less.
Ｓｉは、通常の脱酸目的として添加する場合は０.７％未満で十分であり、０.３％以下に管理しても構わない。一方、上記（４）の目的で積極添加する場合は、０.７％以上のＳｉ含有量とすることが有効である。ただし、過剰なＳｉ含有は鋼の脆化を招くので、Ｓｉ含有量の上限は３.０％に制限される。２.０％以下の範囲で添加することがより好ましい。 When Si is added for the purpose of normal deoxidation, less than 0.7% is sufficient, and it may be controlled to 0.3% or less. On the other hand, when positively adding for the purpose of (4) above, it is effective to set the Si content to 0.7% or more. However, excessive Si content causes embrittlement of the steel, so the upper limit of Si content is limited to 3.0%. It is more preferable to add in the range of 2.0% or less.
Ｍｎは、上記（２）の理由により１.０％以下の含有量に制限される。０.６％以下とすることがより好ましい。
Ｃｒは、上記（２）の理由により０.３％以下の含有量に制限される。０.１５％以下とすることがより好ましい。０％であっても構わない。
Ｍｏは、上記（２）の理由により０.０５％以下の含有量に制限される。０％であっても構わない。
Ｂは、上記（２）の理由により０.０００３％以下の含有量に厳しく制限される。０％であっても構わない。
Mn is limited to a content of 1.0% or less for the reason (2). More preferably, it is made 0.6% or less.
Cr is limited to a content of 0.3% or less for the reason of (2) above. More preferably, the content is 0.15% or less. It may be 0%.
Mo is limited to a content of 0.05% or less for the reason of (2) above. It may be 0%.
B is strictly limited to a content of 0.0003% or less for the reason (2) above. It may be 0%.
Ｐ、Ｓは、焼入れ性の上昇、靱性の低下を招くので、それぞれ０.０３％以下に制限される。 Since P and S cause an increase in hardenability and a decrease in toughness, they are limited to 0.03% or less, respectively.
Ａｌは、脱酸のために０.００５％以上の含有量を確保するが、上記（４）の目的で積極添加する場合を除き０.１％未満の含有量で十分である。０.０４％以下の範囲に管理しても構わない。一方、上記（４）の目的で添加する場合は、０.１％以上のＡｌ含有量とすることが有効である。１.０％以上とすることがより効果的であり、２.５％以上とすることがより一層効果的である。ただし、過剰のＡｌ含有は鋼の脆化を招くので、Ａｌ含有量の上限は５.０％に制限される。 Al content of 0.005% or more is ensured for deoxidation, but a content of less than 0.1% is sufficient except when it is positively added for the purpose of (4) above. You may manage in the range of 0.04% or less. On the other hand, when it is added for the purpose of (4), it is effective to make the Al content 0.1% or more. 1.0% or more is more effective, and 2.5% or more is even more effective. However, excessive Al content causes embrittlement of the steel, so the upper limit of Al content is limited to 5.0%.
Ｔｉ、Ｎｂ、Ｖは、上記（３）、（５）の理由により、本発明では積極的に添加する。具体的には、Ｔｉ、Ｎｂ、Ｖの１種以上を添加し、その合計含有量を０.０６％以上とすることが必要であり、１.０％以上とすることがより効果的である。これらの元素の含有量が少ないと硬質炭化物の析出量が不十分となり、上記（３）、（５）の作用が十分に発揮されない。Ｔｉを添加する場合はその含有量を０.０１％以上とすることがより効果的であり、Ｎｂを添加する場合はその含有量を０.０１％以上とすることがより効果的であり、Ｖを添加する場合はその含有量を０.０５％以上とすることがより効果的である。ただし、これらの元素の含有量が過剰であると粗大な炭化物の生成を招き、靱性、疲労特性を劣化させる要因となる。種々検討の結果、Ｔｉは０.１％以下、Ｎｂは０.３％以下、Ｖは０.３％以下の含有量範囲にそれぞれ制限する必要がある。 Ti, Nb, and V are positively added in the present invention for the reasons (3) and (5) above. Specifically, it is necessary to add one or more of Ti, Nb, and V and make the total content 0.06% or more, and more effective to 1.0% or more. . If the content of these elements is small, the amount of precipitation of hard carbides becomes insufficient, and the actions (3) and (5) are not fully exhibited. When adding Ti, it is more effective to make its content 0.01% or more, and when adding Nb, it is more effective to make its content 0.01% or more, When adding V, it is more effective to make the content 0.05% or more. However, if the content of these elements is excessive, coarse carbides are generated, and the toughness and fatigue characteristics are deteriorated. As a result of various studies, it is necessary to limit the content ranges to 0.1% or less for Ti, 0.3% or less for Nb, and 0.3% or less for V.
〔硬さ〕
ＡＴセパレートプレートに適用するためには、歯の部分での耐摩耗性を確保するうえで、鋼板の硬さは２００ＨＶ以上に調整されている必要がある。ただし、硬すぎると、歯と噛み合う相手部材のスプラインの摩耗を早めるので好ましくない。種々検討の結果、３２０ＨＶ以下の範囲で硬さを調製する必要がある。なお、単に硬さを増大させるだけで十分な耐摩耗性が付与できるわけではなく、そのためには前述のようにＴｉ、Ｎｂ、Ｖの１種以上を添加して上記（５）の作用を発揮させることが重要である。
〔Hardness〕
In order to apply to the AT separate plate, the hardness of the steel sheet needs to be adjusted to 200 HV or more in order to ensure wear resistance at the tooth portion. However, if it is too hard, wear of the spline of the mating member that meshes with the tooth is accelerated, which is not preferable. As a result of various studies, it is necessary to adjust the hardness within a range of 320 HV or less. It should be noted that sufficient wear resistance cannot be imparted simply by increasing the hardness. For this purpose, at least one of Ti, Nb, and V is added as described above to exhibit the effect of (5) above. It is important to let
〔製造方法〕
本発明の対象鋼はＣ含有量が比較的低いので、軟鋼（ＳＰＣＣ）の鋼板と類似の製造工程を採用することができる。ただし、ＡＴセパレートプレートには上述の硬さ、および平坦性が要求されるので、最終的には冷間圧延仕上げにて板厚および硬さを調整する必要がある。最終的な冷間圧延率（冷間圧延工程中に中間焼鈍を入れる場合は、最後の中間焼鈍後の冷間圧延率）は概ね１０〜６０％程度の範囲で調整される。
〔Production method〕
Since the target steel of the present invention has a relatively low C content, a manufacturing process similar to that of a mild steel (SPCC) steel plate can be employed. However, since the AT separate plate is required to have the above-mentioned hardness and flatness, it is necessary to finally adjust the thickness and hardness by cold rolling finishing. The final cold rolling rate (when intermediate annealing is performed during the cold rolling step, the cold rolling rate after the final intermediate annealing) is adjusted in a range of approximately 10 to 60%.
〔金属組織〕
本発明の鋼板は、マトリクスが「フェライト＋パーライト」または「フェライト＋セメンタイト」であり、マトリクス中に硬質炭化物が微細分散している金属組織を有する。冷間圧延仕上げであるから、結晶粒は圧延方向に伸びている。
[Metal structure]
The steel sheet of the present invention has a metal structure in which the matrix is “ferrite + pearlite” or “ferrite + cementite”, and hard carbides are finely dispersed in the matrix. Because of the cold rolling finish, the crystal grains extend in the rolling direction.
表１に示す鋼を溶製し、図１に示す工程により板厚２.０ｍｍの冷延鋼板を製造し、これを供試材とした。図１中のパターン（Ａ）〜（Ｃ）の何れを採用したかについては表２中の工程欄に示してある。各供試材から試験片を採取し、下記の要領にてヒートスポット再現試験および摩耗試験を行った。 The steel shown in Table 1 was melted, and a cold-rolled steel plate having a thickness of 2.0 mm was manufactured by the process shown in FIG. 1 and used as a test material. Which of the patterns (A) to (C) in FIG. 1 is adopted is shown in the process column of Table 2. Test specimens were collected from each test material, and a heat spot reproduction test and a wear test were performed in the following manner.
〔ヒートスポット再現試験〕
発明者らは、耐ヒートスポット性を評価する手法について種々検討を行った結果、強力なレーザー光を試料表面に短時間照射することにより表層部を局部的に加熱する方法が極めて有効であることを見出した。レーザー光の出力と照射時間を適切に設定したとき、レーザー照射を停止すると鋼板の自己冷却作用により加熱部が急冷され、ヒートスポットに特徴的な変質層（マルテンサイトを含む組織変化層）を作り出すことができる。ヒートスポットの部分には突起が生じるので、その突起高さを測定することにより耐ヒートスポット性が評価できる。なお、この試験はヒートスポットが生じやすい厳しい条件で耐ヒートスポット性を評価するものであり、実際の使用においてこの試験と同程度の顕著なヒートスポットが生じるわけではない。
具体的には以下のようにして試験を行った。
[Heat spot reproduction test]
As a result of various studies on methods for evaluating heat spot resistance, the inventors have found that a method of locally heating the surface layer portion by irradiating the sample surface with a powerful laser beam for a short time is extremely effective. I found. When the laser light output and irradiation time are set appropriately, when the laser irradiation is stopped, the heated part is rapidly cooled by the self-cooling action of the steel sheet, creating a denatured layer (texture changing layer including martensite) characteristic of the heat spot. be able to. Since a protrusion is generated in the heat spot portion, the heat spot resistance can be evaluated by measuring the height of the protrusion. Note that this test evaluates the heat spot resistance under severe conditions where heat spots are likely to occur, and a remarkable heat spot similar to this test does not occur in actual use.
Specifically, the test was conducted as follows.
図２にヒートスポット再現試験方法の概要を示す。供試材から２.０ｍｍ厚×２５ｍｍ×２５ｍｍの試験片を採取し、その試験片をボルトによって鋼製ブロック（２０ｍｍ厚×６０ｍｍ×６０ｍｍ）の表面中央部に拘束した。試験片表面の中央部にレーザービームを照射した。照射条件は、ＣＯ2レーザー、実効出力１０８０Ｗ、ビーム形状６ｍｍφ、照射時間０.７５秒とした。
レーザー照射後の試験片を鋼製ブロックに固定したままの状態として、試験片表面の形状を三次元形状計測器により計測した。照射部の最高地点と非照射部測定位置の高さの差を「突起高さ」と定義し、非照射部測定位置としてｘ軸方向およびｙ軸方向の位置を採用し、それぞれの位置で測定した突起高さの平均を「平均突起高さ」とした。平均突起高さが低いほど、耐ヒートスポット性は良好であると判断される。鋼Ｎｏ.１３の現行品を対照材とし、平均突起高さで判断した耐ヒートスポット性が対照材より十分に優れていると評価されるものを○（耐ヒートスポット性；良好）、対照材と同等以下であると評価されるものを×（耐ヒートスポット性；不十分）と判定し、○評価を合格とした。結果を表２に示す。
FIG. 2 shows an outline of the heat spot reproduction test method. A 2.0 mm thick × 25 mm × 25 mm test piece was taken from the test material, and the test piece was restrained by a bolt at the center of the surface of a steel block (20 mm thick × 60 mm × 60 mm). A laser beam was applied to the center of the surface of the test piece. The irradiation conditions were a CO 2 laser, an effective output of 1080 W, a beam shape of 6 mmφ, and an irradiation time of 0.75 seconds.
The shape of the surface of the test piece was measured with a three-dimensional shape measuring instrument with the test piece after laser irradiation being fixed to the steel block. The difference in height between the highest point of the irradiated part and the non-irradiated part measurement position is defined as the “projection height”, and the x-axis direction and y-axis direction positions are adopted as the non-irradiated part measurement position, and measurement is performed at each position. The average of the heights of the protrusions was defined as “average protrusion height”. It is judged that the heat spot resistance is better as the average protrusion height is lower. When the current product of Steel No. 13 is used as a control material, the heat spot resistance judged by the average protrusion height is sufficiently superior to the control material. Those evaluated as being equivalent to or less than were judged as x (heat spot resistance; insufficient), and the evaluation was good. The results are shown in Table 2.
〔摩耗試験〕
供試材から２.０ｍｍ厚×２５ｍｍ×５０ｍｍの平坦な鋼板試料を採取し、表面を＃８００エメリー紙で研磨仕上げしたものを摩耗試験片として使用した。
大越式迅速摩耗試験機を用いて、ミッションオイルを滴下しながら以下の条件で摩耗試験を行った。回転子として、低炭素熱延鋼板の表面にガス軟窒化処理を施した、直径３０ｍｍ、厚さ３ｍｍのものを使用した。試験条件は、最終荷重６.３ｋｇｆ、摩耗速度０.６１ｍ／ｓｅｃ、摩耗距離６００ｍとした。
鋼Ｎｏ.１３の現行品を対照材とし、この試験による比摩耗量が対照材より少ないものを○（耐摩耗性；良好）、それ以外を×（耐摩耗性；不十分）と判定し、○評価を合格とした。結果を表２に示す。
[Abrasion test]
A flat steel plate sample having a thickness of 2.0 mm × 25 mm × 50 mm was taken from the test material, and the surface polished with # 800 emery paper was used as a wear test piece.
A wear test was conducted under the following conditions while dripping mission oil using an Ogoshi type rapid wear tester. A rotor having a diameter of 30 mm and a thickness of 3 mm obtained by subjecting the surface of a low carbon hot rolled steel sheet to gas soft nitriding was used. The test conditions were a final load of 6.3 kgf, a wear rate of 0.61 m / sec, and a wear distance of 600 m.
The current product of steel No. 13 was used as a control material, and the specific wear amount in this test was less than that of the control material, ○ (wear resistance: good), and the others were determined as x (wear resistance: insufficient). ○ Evaluation was accepted. The results are shown in Table 2.
表２からわかるように、本発明例のものは耐ヒートスポット性、耐摩耗性とも良好であった。
比較例Ｎｏ.３ｂは硬さを過剰に高く調整しすぎたものであり、耐摩耗性は極めて良好である反面、歯と噛み合う相手部材のスプラインの摩耗を早めることが懸念される。Ｎｏ.４ｂは硬さを低く調整しすぎたものであり、耐摩耗性に劣った。Ｎｏ.１４、１８はＣ含有量が過大であるためヒートスポットの平均突起高さが高くなった。Ｎｏ.１５〜１７は焼入れ性向上元素の含有量が過剰であるためヒートスポットの平均突起高さが高くなった。このうちＮｏ.１５はＴｉ、Ｎｂ、Ｖ無添加であるため耐摩耗性にも劣った。Ｎｏ.１９はＴｉ、Ｎｂ、Ｖの合計含有量が不足したため耐摩耗性に劣った。Ｎｏ.２０はＣ含有量が過小であるため耐摩耗性に劣った。
As can be seen from Table 2, the examples of the present invention were good in both heat spot resistance and wear resistance.
Comparative Example No. 3b is obtained by adjusting the hardness too high, and the wear resistance is very good, but there is a concern that the wear of the spline of the mating member that meshes with the tooth is accelerated. No. 4b was obtained by adjusting the hardness too low and inferior in wear resistance. In Nos. 14 and 18, since the C content was excessive, the average protrusion height of the heat spot was high. In Nos. 15 to 17, since the content of the hardenability improving element was excessive, the average protrusion height of the heat spot was increased. Among these, No. 15 was inferior in wear resistance because it contained no Ti, Nb, or V. No. 19 was inferior in wear resistance because the total content of Ti, Nb and V was insufficient. No. 20 was inferior in wear resistance because the C content was too small.
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