JP2005330587A - Method for producing gear having excellent tooth surface strength and gear having excellent tooth surface strength - Google Patents
Method for producing gear having excellent tooth surface strength and gear having excellent tooth surface strength Download PDFInfo
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Abstract
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本発明は、自動車、産業機械、農業機械等々の各種機械構造物において用いられる機械要素のうち歯車として利用される歯面強度に優れた歯車の製造方法および歯面強度に優れた歯車に関するものである。 The present invention relates to a manufacturing method of a gear excellent in tooth surface strength used as a gear and a gear excellent in tooth surface strength among mechanical elements used in various machine structures such as automobiles, industrial machines, agricultural machines and the like. is there.
この種の歯車においては、歯面での耐ピッティング性，耐摩耗性（あるいは、耐スコーリング性）に優れていることが要求されるが、このような歯面での耐ピッティング性，耐摩耗性（あるいは、耐スコーリング性）を向上させる場合には、浸炭焼入れや浸炭窒化焼入れなどの表面硬化処理を施すことによって、表面硬さを上昇させたり、硬化深さを増大させたりする方法が広く採用されている。 This type of gear is required to have excellent pitting resistance and wear resistance (or scoring resistance) on the tooth surface. To improve wear resistance (or scoring resistance), surface hardening treatment such as carburizing quenching or carbonitriding quenching is performed to increase the surface hardness or increase the curing depth. The method is widely adopted.
そして、このような表面硬化処理を施した場合に、表面からの深さとＣ量およびＮ量との関係は、例えば、図２に示すように、最表面のＣ量（０．７〜０．９重量％）は深さ方向に次第に減少するものとなっており、また、最表面のＮ量（０．１〜０．３重量％）は深さ方向に急激に減少するものとなっていた。 When such a surface hardening treatment is performed, the relationship between the depth from the surface, the C amount and the N amount is, for example, as shown in FIG. 9% by weight) gradually decreases in the depth direction, and the N amount (0.1 to 0.3% by weight) on the outermost surface decreases sharply in the depth direction. .
そこで、近年では、歯車に対する面圧負荷がさらに増大する傾向にあり、その対策として、焼入れ性の良くない異常組織を低減するために、含クロム鋼を浸炭処理し、浸炭処理後に温度を若干降下させて引続き窒化処理に移行するようにしたり、窒化処理前に再加熱処理するようにした方法（特許文献１および２）や、浸炭窒化処理により生成させた残留オーステナイトを加工硬化させて負荷能力を向上させるようにした方法（特許文献３）などが考えられた。
しかしながら、面圧負荷はさらに高まる傾向となっており、接触表面において従来以上の発熱（例えば、３００℃以上の発熱）を伴う場合もみられるようになっており、このような場合には、従来のごとき異常組織の低減や残留オーステナイトの加工硬化による活用だけでは、耐ピッティング性，耐摩耗性（あるいは、耐スコーリング性）の向上に対しては十分でないという問題点があり、このような問題点を解決することが課題としてあった。 However, the surface pressure load tends to increase further, and there is a case where the contact surface is accompanied by more heat generation than conventional (for example, heat generation of 300 ° C. or more). There is a problem that the reduction of abnormal structure and the utilization of residual austenite by work hardening are not sufficient for improving the pitting resistance and wear resistance (or scoring resistance). The problem was to solve the problem.
本発明は、このような従来の課題に着目してなされたものであって、歯面における耐ピッティング性，耐摩耗性（あるいは、耐スコーリング性）がさらに向上した歯面強度に優れた歯車の製造方法および歯面強度に優れた歯車を提供することを目的としている。 The present invention has been made by paying attention to such conventional problems, and has excellent tooth surface strength with further improved pitting resistance and wear resistance (or scoring resistance) on the tooth surface. An object of the present invention is to provide a gear manufacturing method and a gear excellent in tooth surface strength.
本発明者は、面圧負荷がさらに高まり、接触表面において従来以上の発熱（例えば、３００℃以上の発熱）を伴う場合もみられるようになってきていることにかんがみ、このような場合においても耐ピッティング性，耐摩耗性（あるいは、耐スコーリング性）をより一層十分なものとするためには、３００℃前後においても軟化のしにくい表面硬化層を形成させることが有効であることを見い出し、窒素をさらに活用した浸炭窒化に着目し、この際、焼き戻し軟化抵抗の向上に有効な窒素の深さ方向の最適分布を求めると共に、このような最適分布が得られる熱処理方法を開発して本発明に至ったものである。 In view of the fact that the surface pressure load is further increased and the contact surface has been accompanied by heat generation more than conventional (for example, heat generation of 300 ° C. or more), even in such a case, It has been found that it is effective to form a hardened surface layer that is difficult to soften even at around 300 ° C in order to further improve pitting and wear resistance (or scoring resistance). Focusing on carbonitriding that further utilizes nitrogen, we have developed an optimal distribution in the depth direction of nitrogen that is effective in improving temper softening resistance and developed a heat treatment method that can provide such an optimal distribution. The present invention has been achieved.
すなわち、本発明に係わる歯面強度に優れた歯車の製造方法は、請求項１に記載しているように、Ｃｒを０．３〜３．０重量％含有させた機械構造用はだ焼鋼を素材とし、最表面のＣ量が０．５重量％以上０．９重量％以下であり且つ最表面のＮ量が０．３重量％以上０．８重量％以下であって、Ｎ量をＣ量並みとすると共に、Ｎの侵入深さが、硬さＨｖ５５０が得られる深さである有効硬化深さの少なくとも８０％の深さにまで達している表面硬化組織を有する歯車を製造する方法であって、機械構造用はだ焼鋼からなる歯車素材に対し８００℃以上９５０℃以下の温度で浸炭処理と同時に浸窒処理を行ったのち冷却することにより、表面硬化組織が、ＣのみでなくＮをも固溶したことを特徴としている。 That is, the manufacturing method of the gear excellent in the tooth surface strength according to the present invention includes, as described in claim 1, a case-hardened steel for mechanical structure containing 0.3 to 3.0% by weight of Cr. And the amount of C on the outermost surface is not less than 0.5% by weight and not more than 0.9% by weight, and the amount of N on the outermost surface is not less than 0.3% by weight and not more than 0.8% by weight, A method of manufacturing a gear having a surface hardened structure in which the penetration depth of N reaches the depth of at least 80% of the effective hardened depth, which is the depth at which the hardness Hv550 is obtained, while maintaining the same amount of C The gear structure made of case-hardened steel for mechanical structure is cooled at a temperature of 800 ° C. or more and 950 ° C. or less at the same time as carburizing treatment and nitriding treatment. N is also a solid solution.
そして、本発明に係わる歯面強度に優れた歯車の製造方法の実施態様においては、請求項２に記載しているように、機械構造用はだ焼鋼からなる歯車素材に対し、８００℃以上９５０℃以下の温度で浸炭処理と同時に浸窒処理を行ったのち冷却し、さらに８００℃以上９３０℃以下のオーステナイト化温度にまで再加熱して再び浸窒処理を行ったのち焼入れすることを特徴としている。 And in the embodiment of the manufacturing method of the gear excellent in the tooth surface strength according to the present invention, as described in claim 2, the gear material made of case-hardened steel for mechanical structure is 800 ° C. or higher. Nitrogen treatment is performed at the same time as the carburizing process at a temperature of 950 ° C. or lower, cooled, and further reheated to an austenitizing temperature of 800 ° C. to 930 ° C. It is said.
また、本発明に係わる歯面強度に優れた歯車は、請求項３に記載しているように、Ｃｒを０．３〜３．０重量％含有させた機械構造用はだ焼鋼を素材とし、最表面のＣ量が０．５重量％以上０．９重量％以下であり且つ最表面のＮ量が０．３重量％以上０．８重量％以下であって、Ｎ量をＣ量並みとすると共に、Ｎの侵入深さが、硬さＨｖ５５０が得られる深さである有効硬化深さの少なくとも８０％の深さにまで達しており、表面硬化組織が、ＣのみでなくＮをも固溶した緻密なマルテンサイト組織を有することを特徴としている。 Further, as described in claim 3, the gear having excellent tooth surface strength according to the present invention is made of case-hardened steel for mechanical structure containing 0.3 to 3.0% by weight of Cr. The C amount on the outermost surface is 0.5 wt% or more and 0.9 wt% or less, and the N amount on the outermost surface is 0.3 wt% or more and 0.8 wt% or less, and the N amount is the same as the C amount And the penetration depth of N reaches at least 80% of the effective hardening depth, which is the depth at which the hardness Hv550 is obtained, and the surface hardening structure has not only C but also N. It is characterized by having a dense martensite structure in solid solution.
本発明に係わる歯面強度に優れた歯車の製造方法および歯面強度に優れた歯車において、その素材としては、ＳＮＣ４１５，ＳＮＣ８１５等のニッケル・クロム系，ＳＮＣＭ２２０，ＳＮＣＭ４１５，ＳＮＣＭ４２０，ＳＮＣＭ６１６，ＳＮＣＭ８１５等のニッケル・クロム・モリブデン系，ＳＣｒ４１５，ＳＣｒ４２０等のクロム系，ＳＣＭ４１５，ＳＣＭ４１８，ＳＣＭ４２０，ＳＣＭ４２１，ＳＣＭ８２２等のクロム・モリブデン系，ＳＭｎ４２０，ＳＭｎＣ４２０等のマンガンおよびマンガン・クロム系などの機械構造用合金はだ焼鋼が使用される。 In the manufacturing method of the gear excellent in tooth surface strength and the gear excellent in tooth surface strength according to the present invention, the material thereof is nickel-chromium such as SNC415, SNC815, SNCM220, SNCM415, SNCM420, SNCM616, SNCM815, etc. Alloys for mechanical structures such as nickel / chromium / molybdenum, chromium such as SCr415 and SCr420, chromium / molybdenum such as SCM415, SCM418, SCM420, SCM421, and SCM822, manganese such as SMn420 and SMnC420, and manganese / chromium alloys Hardened steel is used.
この場合、クロムを含有する機械構造用はだ焼鋼においては、Ｃｒ含有量が０．３〜３．０重量％であるものを用い、Ｃｒはこの種のはだ焼鋼において焼入れ性の向上に寄与する作用を有していることから、このような作用を得るために０．３重量％以上とすることが望ましいが、多すぎると靭性を低下させることとなるので３．０重量％以下とすることが望ましい。 In this case, in the case-hardened steel for mechanical structure containing chromium, the one having a Cr content of 0.3 to 3.0% by weight is used, and Cr improves the hardenability in this kind of case-hardened steel. In order to obtain such an action, it is desirable to be 0.3% by weight or more, but if it is too much, the toughness will be reduced, so 3.0% by weight or less Is desirable.
また、バナジウムを含有する機械構造用はだ焼鋼においては、Ｖ含有量が０．１〜０．５重量％であるものを用いることがより望ましく、Ｖはこの種のはだ焼鋼において靭性を向上させる作用を有していることから、このような作用を得るために０．１重量％以上とすることが望ましいが、多すぎても効果の向上はみられずかえって靭性を低下させることとなるので０．５重量％以下とすることが望ましい。 Further, in the case-hardening steel containing vanadium, it is more desirable to use a V content of 0.1 to 0.5% by weight, and V is toughness in this kind of case-hardening steel. In order to obtain such an action, it is desirable to make it 0.1% by weight or more, but even if it is too much, the effect is not improved and the toughness is lowered. Therefore, the content is preferably 0.5% by weight or less.
そして、このほか、Ｃ，Ｓｉ，Ｍｎ，Ｐ，Ｓ，Ｎｉ，Ｍｏ等についてもこの種のはだ焼鋼に適する範囲とすることが望ましいことはいうまでもない。 In addition to this, it goes without saying that C, Si, Mn, P, S, Ni, Mo, and the like are also preferably in a range suitable for this type of case-hardened steel.
また、その他、結晶粒微細化作用があるＡｌ，Ｔｉ，Ｚｒ，Ｎｂ，Ｎ等を含有させたり、被削性向上作用があるＰｂ，Ｓ，Ｃａ，Ｓｅ，Ｔｅ，Ｂｉ等を含有させたりしたものであってもよい。 In addition, Al, Ti, Zr, Nb, N, etc., which have a grain refinement effect, or Pb, S, Ca, Se, Te, Bi, etc., which have a machinability improving effect, are included. It may be a thing.
そして、このようなＣｒを０．３〜３．０重量％含有させた機械構造用はだ焼鋼を用いて、塑性加工や切削加工などを行うことによって歯車素材に加工したあと、この歯車素材に対し、８００℃以上９５０℃以下の温度で浸炭処理と同時に浸窒処理を行ったのち冷却することにより、表面硬化組織が、ＣのみでなくＮをも固溶した歯面強度に優れた歯車を製造する。 And after processing into gear material by performing plastic working, cutting, etc., using a case-hardened steel containing 0.3 to 3.0% by weight of Cr, this gear material On the other hand, a gear having excellent tooth surface strength in which not only C but also N is dissolved in the surface hardened structure by cooling after performing a nitriding process at the same time as a carburizing process at a temperature of 800 ° C. or more and 950 ° C. or less Manufacturing.
さらに説明すれば、歯車素材に対し、８００℃以上９５０℃以下の温度で浸炭処理と同時に浸窒処理を行ったのち冷却し、さらに８００℃以上９３０℃以下のオーステナイト化温度にまで再加熱して再び浸窒処理を行ったのち焼入れする。 More specifically, the gear blank is cooled at the temperature of 800 ° C. or more and 950 ° C. or less at the same time as the carburizing treatment and then cooled, and further reheated to an austenitizing temperature of 800 ° C. or more and 930 ° C. or less. After nitriding again, quench.
このようにして、例えば図１に示すように、最表面のＣ量が０．５重量％以上０．９重量％以下であり且つ最表面のＮ量が０．３重量％以上０．８重量％以下であって、Ｎ量をＣ量並みとすると共に、Ｎの侵入深さが、硬さＨｖ５５０が得られる深さである有効硬化深さの少なくとも８０％の深さにまで達している表面硬化組織を有する歯面強度に優れた歯車を得る。 Thus, for example, as shown in FIG. 1, the C amount on the outermost surface is 0.5 wt% or more and 0.9 wt% or less, and the N amount on the outermost surface is 0.3 wt% or more and 0.8 wt% or less. %, And the amount of penetration of N reaches the depth of at least 80% of the effective hardening depth, which is the depth at which the hardness Hv550 is obtained. A gear having a hardened structure and excellent tooth surface strength is obtained.
この場合、より好ましくは、表面硬化組織は、ＣのみでなくＮをも固溶した緻密なマルテンサイト組織からなっているものとすることがより望ましい。 In this case, more preferably, the surface hardened structure is made of a dense martensite structure in which not only C but also N is dissolved.
本発明に係わる歯面強度に優れた歯車の製造方法によれば、Ｃｒを０．３〜３．０重量％含有させた機械構造用はだ焼鋼を素材とし、最表面のＣ量が０．５重量％以上０．９重量％以下であり且つ最表面のＮ量が０．３重量％以上０．８重量％以下であって、Ｎ量をＣ量並みとすると共に、Ｎの侵入深さが、硬さＨｖ５５０が得られる深さである有効硬化深さの少なくとも８０％の深さまで達しており、表面硬化組織が、ＣのみでなくＮをも固溶した緻密なマルテンサイト組織を有する歯車を得ることができ、接触面圧が高くかつ滑り率が大きく変動するような負荷においても優れた耐ピッティング性および耐摩耗性（あるいは、耐スコーリング性）を有し、歯面強度に優れたものにできると共に、再加熱焼入れを行うことで、Ｎ量が多いにもかかわらず残留オーステナイト（γＲ）量が少なく、硬さの低下が小さい長寿命の歯車を製造することが可能であるという著大なる効果がもたらされる。さらに、本発明では、素材としてＣｒを０．３〜３．０重量％含有させた機械構造用はだ焼鋼を用いているので、焼入れ性の向上に寄与する作用が得られると共に、靭性を低下させないという更なる効果を有する。 According to the method for manufacturing a gear having excellent tooth surface strength according to the present invention, a case-hardened steel containing 0.3 to 3.0% by weight of Cr is used as a raw material, and the amount of C on the outermost surface is 0. 0.5 wt% or more and 0.9 wt% or less, and the N amount on the outermost surface is 0.3 wt% or more and 0.8 wt% or less. Has reached a depth of at least 80% of the effective hardening depth, which is the depth at which the hardness Hv550 is obtained, and the surface hardening structure has a dense martensite structure in which not only C but also N is dissolved. Gears can be obtained and have excellent pitting resistance and wear resistance (or scoring resistance) even in loads where the contact surface pressure is high and the slip rate fluctuates greatly. In addition to being able to make it superior, reheating and quenching increases the amount of N Less residual austenite ([gamma] R) amount irrespective results in Chodai Naru effect that it is possible to produce a gear reduction is small long life hardness. Furthermore, in the present invention, since the machine-structured case-hardened steel containing 0.3 to 3.0% by weight of Cr is used as a material, an effect contributing to improvement of hardenability can be obtained and toughness can be obtained. It has the further effect of not lowering.
本発明に係わる歯面強度に優れた歯車によれば、 接触面圧が高くかつ滑り率が大きく変動するような負荷においても優れた耐ピッティング性および耐摩耗性を有し、歯面強度に優れたものにでき、また、Ｃｒを０．３〜３．０重量％含有させた機械構造用はだ焼鋼を素材としているので、焼入れ性が良く且つ靭性を低下させずに製造し得ると共に、表面硬化組織が、ＣのみでなくＮをも固溶させた緻密なマルテンサイト組織であって、組織が緻密であるため、クラックの進展抵抗が大であり、長寿命であるという著大なる効果がもたらされる。 According to the gear having excellent tooth surface strength according to the present invention, it has excellent pitting resistance and wear resistance even under a load in which the contact surface pressure is high and the slip ratio greatly fluctuates. It can be made excellent, and because it is made of a case-hardened steel containing 0.3 to 3.0% by weight of Cr, it can be manufactured with good hardenability and without reducing toughness. The surface hardened structure is a dense martensite structure in which not only C but also N is dissolved, and since the structure is dense, the resistance to crack propagation is large and the life is remarkable. The effect is brought about.
（実施例１）
表１に示す鋼を素材とし、９２０℃で６０分間保持後冷却する焼ならしを行い、さらに、図４（ａ）に示すような中央太径部の直径が２６ｍｍ，中央太径部の長さが２８ｍｍ，両側細径部の直径がともに２２ｍｍ，全長が１３０ｍｍのローラーピッティング試験用試験片Ｓ１を機械加工により製作すると共に、図５に示すような直径が７０ｍｍ，厚さが１０ｍｍのピンオンディスク摩耗試験用円盤試験片Ｓ２を機械加工により製作した。
(Example 1)
The steel shown in Table 1 is used as a raw material, and normalizing is performed by holding at 920 ° C. for 60 minutes and then cooling, and the diameter of the central large diameter portion is 26 mm as shown in FIG. A roller pitting test specimen S1 having a length of 28 mm, both side diameters of 22 mm and a total length of 130 mm is manufactured by machining, and a pin having a diameter of 70 mm and a thickness of 10 mm as shown in FIG. A disk test piece S2 for on-disk wear test was manufactured by machining.
次いで、図３に示す温度−時間説明図において、温度Ｔ１＝９００℃，時間ｔ１＝２４０分，雰囲気ガスＮ１，Ｎ２＝６体積％ＮＨ３ガス，雰囲気カーボンポテンシャルＣ．Ｐ．＝１．１の条件、および、温度Ｔ２＝８４０℃，時間ｔ２＝１００分，雰囲気ガスＮ１，Ｎ２＝８体積％ＮＨ３ガス，雰囲気カーボンポテンシャルＣ．Ｐ．＝０．９５の条件による浸炭処理と浸窒処理とを同時に行ったのち、空冷（Ａ．Ｃ．）した。 Next, in the temperature-time explanatory diagram shown in FIG. 3, temperature T1 = 900 ° C., time t1 = 240 minutes, atmospheric gas N1, N2 = 6 vol% NH3 gas, atmospheric carbon potential C.I. P. = 1.1, temperature T2 = 840 ° C., time t2 = 100 minutes, atmospheric gas N1, N2 = 8 vol% NH3 gas, atmospheric carbon potential C.I. P. = Carrying treatment and nitriding treatment under the condition of 0.95 were performed at the same time, followed by air cooling (AC).
続いて、各試験片Ｓ１，Ｓ２を温度Ｔ３＝８５０℃にまで再加熱してオーステナイト化し、時間ｔ３＝１５０分，雰囲気ガスＮ３＝８体積％ＮＨ３ガスによる浸窒処理を再度行ったのち、温度１８０℃のソルト浴中に浸漬する焼入れ（Ｓ．Ｑ．）を行った。 Subsequently, each test piece S1, S2 was reheated to a temperature T3 = 850 ° C. to be austenite, and after nitriding with an atmosphere gas N3 = 8 vol% NH3 gas for a time t3 = 150 minutes, Quenching (SQ) was performed by immersion in a salt bath at 180 ° C.
そして、各試験片Ｓ１，Ｓ２の最表面のＣ量，最表面のＮ量，Ｎの侵入深さ、有効硬化深さ，有効硬化深さに対するＮの侵入深さを調べたところ、同じく表１に示す結果であった。 Then, when the amount of C on the outermost surface, the amount of N on the outermost surface, the penetration depth of N, the effective hardening depth, and the penetration depth of N with respect to the effective hardening depth of each test piece S1, S2 were examined, Table 1 It was the result shown in.
さらに、図４（ａ）に示したローラーピッティング試験用試験片Ｓ１を用いて、図４（ｂ）に示すような直径が１３０ｍｍ，厚さが１８ｍｍのローラー（ＳＣｒ４２０鋼の浸炭焼入れ品）Ｒを相手材とし、接触圧力：３．７ＧＰａ，すべり率：−４０％、潤滑油温度：８０℃の条件によるローラーピッティング試験を行って、ピッティング寿命を調べたところ、同じく表１に示す結果であった。 Further, using the roller pitting test specimen S1 shown in FIG. 4 (a), a roller (carburized and quenched product of SCr420 steel) R having a diameter of 130 mm and a thickness of 18 mm as shown in FIG. 4 (b). Was subjected to a roller pitting test under the conditions of contact pressure: 3.7 GPa, slip rate: -40%, lubricating oil temperature: 80 ° C., and the pitting life was examined. Met.
さらにまた、図５に示した円盤試験片Ｓ２を用いて、同じく図５に示すような本体部の直径が８ｍｍ，本体部先端の半径が１００ｍｍＲ，鍔部の直径が１２ｍｍのピン（ＳＫ３の熱処理品）Ｐを相手材として、接触圧力：１５０ＭＰａ，摺動速度：０．２８ｍ／ｓの条件によるピンオンディスク摩耗試験を行って摩耗深さを調べたところ、同じく表１に示す結果であった。 Furthermore, by using the disk test piece S2 shown in FIG. 5, a pin (SK3 heat treatment) having a main body diameter of 8 mm, a main body tip radius of 100 mmR, and a collar diameter of 12 mm as shown in FIG. Article) The wear depth was examined by conducting a pin-on-disk wear test under the conditions of contact pressure: 150 MPa and sliding speed: 0.28 m / s with P as the counterpart material. The results are also shown in Table 1. .
なお、表１の比較例１は浸炭処理のみを行った場合を示し、比較例２は従来の浸炭窒化焼入れを行った場合を示し、比較例３は過剰な浸窒処理を行った場合を示しており、これらの場合についても同様の評価試験を行った。 In addition, the comparative example 1 of Table 1 shows the case where only the carburizing treatment is performed, the comparative example 2 shows the case where the conventional carbonitriding quenching is performed, and the comparative example 3 shows the case where the excessive nitriding treatment is performed. In these cases, the same evaluation test was conducted.
表１に示すように、発明例１〜４ではいずれもピッティング寿命が長く、摩耗深さは小さいものとなっていた。 As shown in Table 1, in each of Invention Examples 1 to 4, the pitting life was long and the wear depth was small.
これに対して、比較例１〜３ではピッティング寿命が短く、摩耗深さは大きいものとなっていた。 In contrast, in Comparative Examples 1 to 3, the pitting life was short and the wear depth was large.
（実施例２）
表２に示す鋼を素材とし、９２０℃で６０分間保持後冷却する焼ならしを行い、さらに、図４（ａ）に示すような中央太径部の直径が２６ｍｍ，中央太径部の長さが２８ｍｍ，両側細径部の直径がともに２２ｍｍ，全長が１３０ｍｍのローラーピッティング試験用試験片Ｓ１を機械加工により製作すると共に、図５に示すような直径が７０ｍｍ，厚さが１０ｍｍのピンオンディスク摩耗試験用円盤試験片Ｓ２を機械加工により製作した。
(Example 2)
The steel shown in Table 2 is used as a raw material, and normalization is performed by cooling after holding at 920 ° C. for 60 minutes. Further, the diameter of the central large diameter portion is 26 mm as shown in FIG. A roller pitting test specimen S1 having a length of 28 mm, both side diameters of 22 mm and a total length of 130 mm is manufactured by machining, and a pin having a diameter of 70 mm and a thickness of 10 mm as shown in FIG. A disk test piece S2 for on-disk wear test was manufactured by machining.
次いで、図３に示す温度−時間説明図において、温度Ｔ１，時間ｔ１，雰囲気ガスＮ１，Ｎ２がそれぞれ表２に示す条件でかつ雰囲気カーボンポテンシャルＣ．Ｐ．が１．１の条件、および、温度Ｔ２，時間ｔ２，雰囲気ガスＮ１，Ｎ２がそれぞれ表２に示す条件でかつ雰囲気カーボンポテンシャルＣ．Ｐ．が０．９５の条件による浸炭処理と浸窒処理とを同時に行ったのち、空冷（Ａ．Ｃ．）した。 Next, in the temperature-time explanatory diagram shown in FIG. 3, the temperature T1, the time t1, the atmospheric gases N1, N2 are the conditions shown in Table 2 and the atmospheric carbon potential C.I. P. Of the atmospheric carbon potential C. and the conditions of the temperature T2, the time t2, the atmospheric gases N1, N2 shown in Table 2 and the atmospheric carbon potential C.I. P. Was subjected to carburizing treatment and nitriding treatment under the condition of 0.95 at the same time, followed by air cooling (AC).
続いて、各試験片Ｓ１，Ｓ２を再加熱してオーステナイト化し、温度Ｔ３，時間ｔ３，雰囲気ガスＮ３がそれぞれ表２に示す条件による浸窒処理を再度行ったのち、温度１８０℃のソルト浴中に浸漬する焼入れ（Ｓ．Ｑ．）を行った。 Subsequently, the test pieces S1 and S2 were reheated to austenite, and after the nitriding treatment was performed again under the conditions shown in Table 2 with the temperature T3, the time t3, and the atmosphere gas N3, respectively, in a salt bath at a temperature of 180 ° C. Quenching (SQ) was performed.
そして、各試験片Ｓ１，Ｓ２の最表面のＣ量，最表面のＮ量，Ｎの侵入深さ、有効硬化深さ，有効硬化深さに対するＮの侵入深さを調べたところ、表３に示す結果であった。 Then, when the amount of C on the outermost surface, the amount of N on the outermost surface, the penetration depth of N, the effective curing depth, and the penetration depth of N relative to the effective curing depth of each test piece S1, S2 were examined, The result was shown.
さらに、図４（ａ）に示したローラーピッティング試験用試験片Ｓ１を用いて、図４（ｂ）に示すような直径が１３０ｍｍ，厚さが１８ｍｍのローラー（ＳＣｒ４２０鋼の浸炭焼入れ品）Ｒを相手材とし、接触圧力：３．７ＧＰａ，すべり率：−４０％、潤滑油温度：８０℃の条件によるローラーピッティング試験を行って、ピッティング寿命を調べたところ、同じく表３に示す結果であった。 Further, using the roller pitting test specimen S1 shown in FIG. 4 (a), a roller (carburized and quenched product of SCr420 steel) R having a diameter of 130 mm and a thickness of 18 mm as shown in FIG. 4 (b). Was subjected to a roller pitting test under the conditions of contact pressure: 3.7 GPa, slip rate: -40%, lubricating oil temperature: 80 ° C., and the pitting life was examined. Met.
さらにまた、図５に示した円盤試験片Ｓ２を用いて、同じく図５に示すような本体部の直径が８ｍｍ，本体部先端の半径が１００ｍｍＲ，鍔部の直径が１２ｍｍのピン（ＳＫ３の熱処理品）Ｐを相手材として、接触圧力：１５０ＭＰａ，摺動速度：０．２８ｍ／ｓの条件によるピンオンディスク摩耗試験を行って摩耗深さを調べたところ、同じく表３に示す結果であった。 Furthermore, by using the disk test piece S2 shown in FIG. 5, a pin (SK3 heat treatment) having a main body diameter of 8 mm, a main body tip radius of 100 mmR, and a collar diameter of 12 mm as shown in FIG. Article) When the wear depth was examined by conducting a pin-on-disk wear test under the conditions of contact pressure: 150 MPa and sliding speed: 0.28 m / s with P as the counterpart material, the results shown in Table 3 were also obtained. .
なお、表１の比較例１１は浸炭・浸窒温度を低くかつ再浸窒温度を高くして行った場合を示し、比較例１２，１３は浸炭・浸窒温度を高くかつ再浸窒温度を低くして行った場合を示しており、これらの場合についても同様の評価試験を行ったところ、同じく表３に示す結果であった。 In addition, Comparative Example 11 in Table 1 shows a case where the carburizing / nitriding temperature is low and the renitriding temperature is high, and Comparative Examples 12 and 13 are a high carburizing / nitriding temperature and the renitriding temperature is high. The results are shown in Table 3 when the same evaluation test was performed for these cases.
表２，表３に示すように、発明例１１〜１３ではいずれもピッティング寿命が長く、摩耗深さは小さいものとなっていた。 As shown in Tables 2 and 3, in each of Invention Examples 11 to 13, the pitting life was long and the wear depth was small.
これに対して、比較例１１〜１３ではピッティング寿命が短く、摩耗深さは大きいものとなっていた。 On the other hand, in Comparative Examples 11 to 13, the pitting life was short and the wear depth was large.
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| JP2007284739A (en) * | 2006-04-14 | 2007-11-01 | Sumitomo Metal Ind Ltd | Steel component and its production method |
| JP2017171951A (en) * | 2016-03-18 | 2017-09-28 | 新日鐵住金株式会社 | Steel component and production method thereof |
| CN114473211A (en) * | 2022-03-01 | 2022-05-13 | 北京航空航天大学合肥创新研究院(北京航空航天大学合肥研究生院) | Laser composite modification method for gear surface |
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| JP2007284739A (en) * | 2006-04-14 | 2007-11-01 | Sumitomo Metal Ind Ltd | Steel component and its production method |
| JP2017171951A (en) * | 2016-03-18 | 2017-09-28 | 新日鐵住金株式会社 | Steel component and production method thereof |
| CN114473211A (en) * | 2022-03-01 | 2022-05-13 | 北京航空航天大学合肥创新研究院(北京航空航天大学合肥研究生院) | Laser composite modification method for gear surface |
| CN114473211B (en) * | 2022-03-01 | 2024-02-20 | 北京航空航天大学合肥创新研究院(北京航空航天大学合肥研究生院) | Gear surface laser composite modification method |
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