JPH0959756A - Production of high bearing resistant carburized parts - Google Patents
Production of high bearing resistant carburized partsInfo
- Publication number
- JPH0959756A JPH0959756A JP21333995A JP21333995A JPH0959756A JP H0959756 A JPH0959756 A JP H0959756A JP 21333995 A JP21333995 A JP 21333995A JP 21333995 A JP21333995 A JP 21333995A JP H0959756 A JPH0959756 A JP H0959756A
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- Prior art keywords
- carburizing
- low
- quenching
- less
- temp
- Prior art date
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Abstract
Description
【発明の詳細な説明】Detailed Description of the Invention
【０００１】[0001]
【発明の属する技術分野】本発明は、耐ピッチング性や
耐フレーキング性などを含めた耐面圧性に優れた浸炭部
品の製法に関し、例えば自動車や建設機械などを始めと
する各種産業機械に用いられる歯車やシャフト類等の部
品に対し、特に転動疲労に対する抵抗力の改善された浸
炭部品を製造する方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing carburized parts having excellent surface pressure resistance including pitting resistance and flaking resistance, and is used for various industrial machines such as automobiles and construction machines. The present invention relates to a method for manufacturing a carburized component having improved resistance to rolling fatigue, in particular, for components such as gears and shafts.
【０００２】[0002]
【従来の技術】自動車や建設機械等に使用される機械部
品の中でも、特に高い曲げ疲労特性が求められる部品に
対しては、従来より疲労特性改善のため浸炭焼入れ処理
に引き続いてショットピーニングによる表面硬化処理を
施す方法が多く採用されている。また、浸炭焼入れ時に
発生する表層部のオーステナイト粒界に沿って生成する
表面異常層は、硬さや圧縮残留応力を低下させて曲げ疲
労強度向上の障害となるため、例えば特開平１−３０６
５２１号公報等に開示にされている様に、浸炭時に表面
異常層の発生を防止し得る成分設計を行ない、且つ高速
ショットピーニング処理によって曲げ疲労強度に優れた
歯車を製造する方法が提案されている。2. Description of the Related Art Among machine parts used in automobiles and construction machines, particularly for parts requiring high bending fatigue properties, surface treatment by shot peening following carburizing and quenching treatment is conventionally performed to improve fatigue properties. Many methods of applying a curing treatment are adopted. Further, an abnormal surface layer formed along the austenite grain boundaries in the surface layer portion generated during carburizing and quenching lowers hardness and compressive residual stress and hinders the improvement of bending fatigue strength.
As disclosed in Japanese Patent No. 521, etc., a method of designing a component capable of preventing the occurrence of an abnormal surface layer during carburization and producing a gear excellent in bending fatigue strength by high speed shot peening treatment has been proposed. There is.
【０００３】こうした改善技術により、歯車類にあって
は歯元の疲労強度は著しく強化されるが、相対的に歯車
の強度が低下するため破壊の起点が歯車側に移行し、歯
車の寿命がピッチング寿命に律速される傾向が生じてく
る。With such improved technology, the fatigue strength of the tooth roots of gears is significantly strengthened, but since the strength of the gears decreases relatively, the starting point of fracture shifts to the gear side, and the life of the gears increases. The pitching life tends to be rate-controlled.
【０００４】耐ピッチング性を向上させるには、初期亀
裂発生を遅延させるための表面硬さの増大が有効であ
り、また亀裂伝播を抑制するため表面残留オーステナイ
トの増量が有効と考えられている。ところが残留オース
テナイト量が過度に多くなると、表面硬さが低下して曲
げ疲労強度を却って悪化させるので、その量の適正化が
必要となる。In order to improve the pitting resistance, it is effective to increase the surface hardness to delay the initiation of initial cracks, and it is considered to increase the amount of surface retained austenite to suppress the crack propagation. However, if the amount of retained austenite becomes excessively large, the surface hardness lowers and the bending fatigue strength deteriorates rather. Therefore, it is necessary to optimize the amount.
【０００５】こうした表面硬さと残留オーステナイト量
は、合金元素量やカーボンポテンシャル（以下、Ｃｐと
略記する）等の浸炭焼入れ処理条件に支配される因子で
あるが、現在では、使用する鋼種に応じて試行錯誤を繰
り返し、最適の浸炭焼入れ処理条件を決定しているのが
実状である。その為、必要な耐ピッチング性等が得られ
なかったり、合金元素の過剰添加や浸炭焼入れ処理条件
探索によるコストアップを招くことが多かった。The surface hardness and the amount of retained austenite are factors governed by the carburizing and quenching treatment conditions such as the amount of alloying elements and the carbon potential (hereinafter abbreviated as Cp), but at present, depending on the steel type used. The reality is that trial and error are repeated to determine the optimum carburizing and quenching treatment conditions. Therefore, the required pitting resistance or the like cannot be obtained, and the cost is often increased due to excessive addition of alloying elements or search for carburizing and quenching treatment conditions.
【０００６】[0006]
【発明が解決しようとする課題】本発明は上記の様な事
情に着目してなされたものであって、その目的は、使用
する鋼材の成分組成に応じて浸炭焼入れ処理条件をうま
く制御し、適正な表面硬さと残留オーステナイト量を確
保して優れた耐面圧性（耐ピッチング性など）を有する
浸炭部品を確実に得ることのできる方法を提供しようと
するものである。The present invention has been made in view of the above circumstances, and its purpose is to control the carburizing and quenching treatment conditions according to the composition of the steel material to be used, An object of the present invention is to provide a method capable of reliably obtaining a carburized component having excellent surface pressure resistance (pitching resistance, etc.) by ensuring an appropriate surface hardness and a retained austenite amount.
【０００７】[0007]
【課題を解決するための手段】上記課題を達成すること
のできた本発明に係る製法の構成は、Ｓｉ含有量が１％
以下（０％を含まない）、Ｃｒ含有量が３％以下（０％
を含まない）である低・中炭素低合金綱を使用し、下記
（１），（２）式が成立する焼入れ液温度（絶対温度：
Tq）、浸炭温度（絶対温度：Tc）および浸炭時のＣｐ
（％）で浸炭焼入れ処理を行なうところに特徴を有する
ものである。 650 ≦[1-(Y/100)1/3]×840+[(Y/100)1/3 ×(193×Ｂ + 19 ×Si%+8 ×Mn%+43×Mo%+28×V%+41.5)]+330 ……（１）The structure of the manufacturing method according to the present invention which has achieved the above object has a Si content of 1%.
Below (0% is not included), Cr content is below 3% (0%
The low temperature / medium carbon low alloy steel which is not included) is used, and the quenching liquid temperature (absolute temperature:
Tq), carburizing temperature (absolute temperature: Tc) and Cp during carburizing
(%) Is characterized by carrying out carburizing and quenching treatment. 650 ≤ [1- (Y / 100) 1/3 ] × 840 + [(Y / 100) 1/3 × (193 × B + 19 × Si% + 8 × Mn% + 43 × Mo% + 28 × V % + 41.5)] + 330 (1)
【０００８】[0008]
【数２】 [Equation 2]
【０００９】但しＡ=823-361×Ｂ- 11×Si%-39×Mn%-17
×Ni%-20×Cr%-5 ×Mo%-35×V%-330×N%+ 30×Al% Ｂ=Cp + Ｃ×(194.4- 0.1058×Tc)/(179.5+0.508×Tc) Ｃ=(-0.00286×Tc+1.81)×Si%+0.000479×Tc×Mn% +(-
0.000529×Tc+0.30)×Ni%+(0.000124 ×Tc+0.38)×Mo%+
(0.00255×Tc-1.30)×V%+Cr% Tqは焼入れ温度、Tcは浸炭温度（絶対温度）、Cpは浸炭
時のカーボンポテンシャル（％）を表わす。However, A = 823-361 × B-11 × Si% -39 × Mn% -17
× Ni% -20 × Cr% -5 × Mo% -35 × V% -330 × N% + 30 × Al% B = Cp + C × (194.4- 0.1058 × Tc) / (179.5 + 0.508 × Tc) C = (-0.00286 × Tc + 1.81) × Si% + 0.000479 × Tc × Mn% + (-
0.000529 x Tc + 0.30) x Ni% + (0.000124 x Tc + 0.38) x Mo% +
(0.00255 x Tc-1.30) x V% + Cr% Tq is the quenching temperature, Tc is the carburizing temperature (absolute temperature), and Cp is the carbon potential (%) during carburizing.
【００１０】尚本発明で使用する低・中炭素低合金鋼と
しては Ｃ ：０．０５〜０．５％ Ｓｉ：１％以下 Ｍｎ：０．２〜２％ Ｐ ：０．０３０％以下 Ｓ ：０．００３〜０．０７％ Ｃｒ：０．２〜３％ Ａｌ：０．０１５〜０．１％ Ｎ ：０．００５〜０．０２５％ 全酸素：０．００２％以下 の要件を満たし、残部が実質的にＦｅからなる鋼材、あ
るいは、更に他の元素として Ｎｉ：０．２〜４％ Ｍｏ：０．０８〜１％ Ｖ ：０．０３〜１％ よりなる群から選択される少なくとも１種を含有する鋼
材、あるいは更に他の元素として、Ｎｂ：０．００５〜
０．１％および／またはＴｉ：０．００５〜０．１％を
含有する鋼材、更には、他の元素として Ｐｂ：０．０９％以下 Ｃａ：０．０００５〜０．００５％ Ｚｒ：０．０１〜０．０５％ Ｔｅ：０．００５〜０．１％ Ｓｂ：０．００５〜０．１％ Ｓｅ：０．００５〜０．１％ よりなる群から選択される少なくとも１種の元素を含む
鋼材などが挙げられ、これら成分組成の要件を満足する
低・中炭素低合金鋼を素材として使用すると、耐ピッチ
ング性等の高面圧性の非常に優れた浸炭部品をより確実
に得ることができる。As the low-medium carbon low alloy steel used in the present invention, C: 0.05 to 0.5% Si: 1% or less Mn: 0.2 to 2% P: 0.030% or less S: 0.003 to 0.07% Cr: 0.2 to 3% Al: 0.015 to 0.1% N: 0.005 to 0.025% Total oxygen: 0.002% or less. Is a steel material consisting essentially of Fe, or as another element, at least one selected from the group consisting of Ni: 0.2-4% Mo: 0.08-1% V: 0.03-1% Nb: 0.005 as a steel material containing
Steel containing 0.1% and / or Ti: 0.005 to 0.1%, and further as other elements Pb: 0.09% or less Ca: 0.0005 to 0.005% Zr: 0. 01-0.05% Te: 0.005-0.1% Sb: 0.005-0.1% Se: 0.005-0.1% At least 1 element selected from the group consisting of is included. Steel, etc. can be mentioned, and if low-medium carbon low-alloy steel that satisfies the requirements of these component compositions is used as the material, it is possible to more reliably obtain carburized parts with excellent surface pressure resistance such as pitting resistance. .
【００１１】[0011]
【発明の実施の形態】本発明者らは、前述の如く従来例
では、浸炭焼入れ用鋼材の種類や成分組成などに応じて
耐面圧性の向上に最適の表面硬さや残留オーステナイト
量を試行錯誤的に求めているという事実に鑑み、鋼材の
成分組成から耐面圧性向上に最適の表面硬さや残留オー
ステナイト量を得るための浸炭焼入れ処理条件を計算に
よって求めることができれば、より簡単かつ確実に優れ
た耐面圧性の浸炭部品を得ることができると考え、多く
の鋼材を用いた浸炭焼入れ実験から、浸炭焼入れ鋼材の
成分組成や浸炭焼入れ条件と表面硬さや残留オーステナ
イト量の相関関係を明らかにすべく研究を重ねた。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS As described above, the inventors of the present invention have made trial and error in the conventional example to determine the optimum surface hardness and residual austenite amount for improving the surface pressure resistance according to the type and composition of the steel for carburizing and quenching. In light of the fact that it is required, it is easier and more reliable if the carburizing and quenching treatment conditions for obtaining the optimum surface hardness and the amount of retained austenite for improving the surface pressure resistance can be calculated from the composition of the steel material. We believe that it is possible to obtain carburized parts with excellent surface pressure resistance, and clarify the correlation between the composition and composition of carburized and quenched steels and the conditions of carburizing and quenching, surface hardness and the amount of retained austenite from carburizing and quenching experiments using many steels. I repeated my research.
【００１２】その結果、浸炭部品の表面硬さ（Ｈｖ）は
前記式（１）によってほぼ正確に再現することができ、
この値が６５０以上となる様に、換言すると前記式
（１）の関係を満足する様に浸炭焼入れ用鋼の成分組成
と浸炭焼入れ条件をうまく制御すれば、当該鋼材に最適
の表面硬さが得られること、また、浸炭部材表面の残留
オーステナイト量（Ｙ）と化学成分および浸炭焼入れ処
理条件の関係を追及したところ、浸炭部品表面の残留オ
ーステナイト量（体積％）は前記式（２）によってほぼ
正確に再現することができ、この値が２０〜５０の範囲
に納まる様に、即ち前記式（２）の関係を満たす様に鋼
材の成分組成と浸炭焼入れ条件をうまく制御すれば、当
該鋼材に最適の残留オーステナイト量が得られることを
つきとめた。As a result, the surface hardness (Hv) of the carburized component can be reproduced almost exactly by the above equation (1),
If the component composition and the carburizing and quenching conditions of the steel for carburizing and quenching are controlled so that this value becomes 650 or more, in other words, the relationship of the above-mentioned formula (1) is satisfied, the optimum surface hardness for the steel material is obtained. When the relationship between the obtained austenite amount (Y) on the surface of the carburized member and the chemical composition and the conditions for the carburizing and quenching treatment was sought, the amount of retained austenite on the surface of the carburized component (% by volume) was almost determined by the formula (2). If the composition and the carburizing and quenching conditions of the steel material can be accurately controlled so that this value falls within the range of 20 to 50, that is, the relationship of the formula (2) is satisfied, the steel material can be obtained. It was found that the optimum amount of retained austenite was obtained.
【００１３】即ち本発明では、前記式（１）によって、
得られる浸炭部品の表面硬さでＨｖ６５０以上、好まし
くは７００以上を確保すると共に、前記式（２）によっ
て、得られる浸炭部品の残留オーステナイト量を２０〜
５０体積％、より好ましくは２５〜４５体積％の範囲と
し、それらの湊合によって優れた耐面圧性を示す浸炭部
品が確実に得られる様にしたものである。That is, in the present invention, according to the equation (1),
The surface hardness of the obtained carburized component is maintained at Hv 650 or higher, preferably 700 or higher, and the residual austenite amount of the obtained carburized component is 20 to 20 according to the formula (2).
The content is set to 50% by volume, more preferably 25 to 45% by volume so that a carburized component having excellent surface pressure resistance can be reliably obtained by the entanglement thereof.
【００１４】しかして前記式（１）の関係を外れる浸炭
部材は、表面硬さがＨｖ６５０未完となって表面硬さ不
足となり、満足のいく耐ピッチング性が発揮されず、し
かも焼付きを起こしたり異常摩耗を生じ易くなる。また
浸炭焼入れ後の表層部の残留オーステナイトは、亀裂の
進展を抑制するのに有効な組織であり、上記式（２）の
値が２０未満、即ち残留オーステナイト量が２０体積％
未満のものでは満足のいく疲労強度向上効果が得られ
ず、逆に５０を超えるもの、即ち残留オーステナイト量
が５０体積％を超えるものでは、表層部が硬さ不足とな
ってやはり疲労強度特性が低下傾向を示す様になる。However, the carburized member that is out of the relationship of the above formula (1) has an unfinished surface hardness of Hv650, which results in insufficient surface hardness, and does not exhibit satisfactory pitting resistance, and in addition, seizure occurs. Abnormal wear is likely to occur. Further, the retained austenite in the surface layer portion after carburizing and quenching is a structure effective in suppressing the development of cracks, and the value of the above formula (2) is less than 20, that is, the amount of retained austenite is 20% by volume.
If it is less than 50%, a satisfactory fatigue strength improving effect cannot be obtained. On the contrary, if it exceeds 50, that is, if the amount of retained austenite exceeds 50% by volume, the surface layer portion becomes insufficient in hardness and the fatigue strength characteristic is It begins to show a downward trend.
【００１５】上記の様に本発明では、浸炭焼入れ用鋼の
成分組成に応じて浸炭焼入れ条件を、前記式（１），
（２）の関係を同時に満たす様に制御することによっ
て、浸炭部品としての表面硬さと残留オーステナイト量
を適正にコントロールし、それにより耐ピッチング性等
の耐面圧性に優れた浸炭部品を製造するところに特徴を
有するものであり、使用される浸炭焼入れ用鋼の成分組
成は特に制限されないが、好ましい鋼材の成分組成を示
すと下記の通りである。As described above, according to the present invention, the carburizing and quenching conditions are set according to the above formula (1) according to the composition of the steel for carburizing and quenching.
By controlling the surface hardness and the amount of retained austenite as a carburized part by controlling so as to satisfy the relationship of (2) at the same time, a carburized part with excellent surface pressure resistance such as pitting resistance is manufactured. The composition of the steel for carburizing and quenching used is not particularly limited, but the preferred composition of the steel material is as follows.
【００１６】Ｃ ：０．０５〜０．５％ Ｓｉ：１％以下 Ｍｎ：０．２〜２％ Ｐ ：０．０３０％以下 Ｓ ：０．００３〜０．０７％ Ｃｒ：０．２〜３％ Ａｌ：０．０１５〜０．１％ Ｎ ：０．００５〜０．０２５％ 全酸素：０．００２％以下 の要件を満たすし、残部が実質的にＦｅからなる鋼材、
あるいは上記元素に加えて、Ｎｉ：０．２〜４％、Ｍ
ｏ：０．０８〜１％およびＶ：０．０３〜１％よりなる
群から選択される少なくとも１種を含有する鋼材、ある
いは更に他の元素として、Ｎｂ：０．００５〜０．１％
および／またはＴｉ：０．００５〜０．１％を含有する
鋼材、あるいは更に、 Ｐｂ：０．０９％以下 Ｃａ：０．０００５〜０．００５％ Ｚｒ：０．０１〜０．０５％ Ｔｅ：０．００５〜０．１％ Ｓｂ：０．００５〜０．１％ Ｓｅ：０．００５〜０．１％ よりなる群から選択される少なくとも１種の元素を含む
鋼材が好ましいものとして例示される。これら浸炭焼入
れ用鋼の好ましい成分組成を選択した理由は下記の通り
である。C: 0.05 to 0.5% Si: 1% or less Mn: 0.2 to 2% P: 0.030% or less S: 0.003 to 0.07% Cr: 0.2 to 3 % Al: 0.015 to 0.1% N: 0.005 to 0.025% Total oxygen: 0.002% or less, a steel material that the balance substantially consists of Fe,
Alternatively, in addition to the above elements, Ni: 0.2 to 4%, M
o: 0.08 to 1% and V: 0.03 to 1%, a steel material containing at least one selected from the group consisting of, or as another element, Nb: 0.005 to 0.1%
And / or steel containing Ti: 0.005 to 0.1%, or further, Pb: 0.09% or less Ca: 0.0005 to 0.005% Zr: 0.01 to 0.05% Te: A steel material containing at least one element selected from the group consisting of 0.005 to 0.1% Sb: 0.005 to 0.1% Se: 0.005 to 0.1% is exemplified as a preferable material. . The reason for selecting the preferable composition of these carburizing and quenching steels is as follows.
【００１７】Ｃ：０．０５〜０．５％ Ｃは浸炭部品に所定の芯部硬さを与えると共に、有効硬
化深さを確保するのに有効な元素であり、０．０５％以
上含有するものが好ましい。しかし多過ぎると靭性や被
削性、冷間加工性などが悪くなるので、０．５％以下に
抑えるのがよい。Ｃのより好ましい含有量は０．１〜
０．３％の範囲である。 C: 0.05 to 0.5% C is an element effective for imparting a predetermined core hardness to a carburized part and ensuring an effective hardening depth, and is contained in an amount of 0.05% or more. Those are preferable. However, if it is too large, the toughness, machinability, cold workability, etc. deteriorate, so it is preferable to keep it to 0.5% or less. The more preferable content of C is 0.1 to
It is in the range of 0.3%.
【００１８】Ｓｉ：１％以下 Ｓｉは有効硬化深さを高めると共に高温強度を高めるの
に有効な元素であるが、多過ぎると粒界酸化層を生成し
て疲労特性に悪影響を及ぼすばかりでなく、浸炭を阻害
する原因になるので、１％以下、より好ましくは０．７
％以下に抑えるのがよい。 Si: 1% or less Si is an element effective in increasing the effective hardening depth and the high temperature strength, but if it is too large, not only does a grain boundary oxide layer are formed to adversely affect the fatigue characteristics. , 1% or less, more preferably 0.7 because it causes carburization.
It is better to keep it below%.
【００１９】Ｍｎ：０．２〜２％ Ｍｎは、溶製時の脱酸剤として有効に作用するほか、Ｍ
ｎＳを生成して切削加工性の向上に寄与し、更には残留
オーステナイト量を増大させる作用も有しており、それ
らの効果は０．２％程度以上含有させることによって有
効に発揮される。しかしながら多過ぎると、残留オース
テナイト量が過度に増加して曲げ疲労強度を却って低下
させるので、２％程度以下に抑えるのがよい。Ｍｎのよ
り好ましい含有量は０．３〜１．８％の範囲である。 Mn: 0.2 to 2% Mn acts effectively as a deoxidizer during melting, and M
It produces nS, contributes to the improvement of the machinability, and has the effect of increasing the amount of retained austenite, and these effects are effectively exhibited by containing about 0.2% or more. However, if the amount is too large, the amount of retained austenite excessively increases and the bending fatigue strength is rather decreased, so it is preferable to suppress it to about 2% or less. The more preferable content of Mn is in the range of 0.3 to 1.8%.
【００２０】Ｐ：０．０３０％以下 Ｐは、疲労亀裂の伝播系路となる粒界の強度を低下さ
せ、曲げ疲労強度や衝撃疲労強度を低下させる原因にな
るので、０．０３０％以下、より好ましくは０．０２０
％以下に抑えることが望まれる。 P: 0.030% or less P reduces the strength of the grain boundary that is a propagation path of fatigue cracks, and causes the bending fatigue strength and impact fatigue strength to decrease, so 0.030% or less More preferably 0.020
% Or less is desirable.
【００２１】Ｓ：０．００３〜０．０７％ Ｓは、例えばＭｎＳの様な硫化物系介在物を生成し、切
削性の向上に寄与するが、多過ぎると疲労破壊の起点と
なり、歯車の場合では歯元部の曲げ疲労強度を著しく劣
化させるので、上記範囲、より好ましくは０．０１〜
０．０３％の範囲とすることが望ましい。 S: 0.003 to 0.07% S forms sulfide inclusions such as MnS and contributes to the improvement of machinability. In this case, since the bending fatigue strength of the tooth root portion is significantly deteriorated, the above range, more preferably 0.01 to
It is desirable to set it in the range of 0.03%.
【００２２】Ｃｒ：０．２〜３％ Ｃｒは浸炭部品の芯部硬さを高めると共に有効硬化深さ
の増大に寄与する元素であり、それらの効果は０．２％
以上含有させることによって有効に発揮される。しかし
ながら、前記Ｍｎと同様に浸炭処理時に粒界酸化物を生
成して疲労特性を低下させ、また残留オーステナイト量
を過度に増大させて表面硬さを低下させるばかりでな
く、鋼材表面に酸化皮膜を形成して炭素の侵入・拡散を
抑制し浸炭を阻害することにもなるので、３％以下に抑
えるのがよい。Ｃｒのより好ましい含有量は０．５〜
２．５％の範囲である。 Cr: 0.2-3% Cr is an element that contributes to increasing the core hardness of carburized parts and increasing the effective hardening depth, and their effects are 0.2%.
It is effectively exhibited by containing the above. However, similar to the above Mn, not only does it produce grain boundary oxides during carburization to reduce fatigue properties, and excessively increase the amount of retained austenite to reduce surface hardness, but also form an oxide film on the steel surface. Since it is formed, it also suppresses the invasion / diffusion of carbon and hinders carburization. The more preferable content of Cr is 0.5 to
It is in the range of 2.5%.
【００２３】Ａｌ：０．０１５〜０．１％，Ｎ：０．０
０５〜０．０２５％ ＡｌとＮはいずれも鋼中で窒化物を形成し、表面硬化熱
処理時のオーステナイト結晶粒の成長を抑制して疲労強
度の低下を阻止する作用を発揮するが、多過ぎると前記
Ｍｎと同様に浸炭処理時に粒界酸化物を生成して疲労特
性を却って悪化させるので、それぞれ上記の範囲と定め
た。これらの利害得失を考えてＡｌのより好ましい含有
量は０．０２〜０．０５％、Ｎのより好ましい含有量は
０．００７〜０．０１５％の範囲である。 Al: 0.015 to 0.1%, N: 0.0
05 to 0.025% Al and N both form a nitride in steel and exert the effect of suppressing the growth of austenite crystal grains during the surface hardening heat treatment and preventing the fatigue strength from decreasing, but too much. Similarly to the above Mn, since grain boundary oxides are generated during the carburizing treatment and the fatigue characteristics are rather deteriorated, the respective ranges are defined as above. Considering these advantages and disadvantages, the more preferable content of Al is 0.02 to 0.05%, and the more preferable content of N is 0.007 to 0.015%.
【００２４】全酸素：０．００２％以下 Ａｌ2 Ｏ3 やＳｉＯ2 等の酸化物系介在物として疲労強
度や切削性に悪影響を及ぼすので、それらの障害を生じ
させないため０．００２％以下、より好ましくは０．０
０１５％以下に抑えることが望ましい。 Total oxygen: 0.002% or less Oxide inclusions such as Al 2 O 3 and SiO 2 adversely affect fatigue strength and machinability, so 0.002% or less in order not to cause troubles. More preferably 0.0
It is desirable to suppress it to 015% or less.
【００２５】本発明で使用される浸炭焼入れ用鋼におけ
る好ましい含有元素は上記の通りであり、残部は実施的
にＦｅからなるものが好ましいが、必要により下記の様
な元素を含む鋼材を使用することも有効である。The preferred contained elements in the steel for carburizing and quenching used in the present invention are as described above, and the balance is preferably composed of Fe practically, but if necessary, a steel material containing the following elements is used. That is also effective.
【００２６】Ｎｉ：０．２〜４％、Ｍｏ：０．０８〜１
％およびＶ：０．０３〜１％よりなる群から選択される
少なくとも１種 これらの元素はＦｅに比べて酸化物を生成しにくく、特
にＭｏは浸炭層の様な高Ｃ領域で焼入れ性を著しく高め
る作用を発揮する。従って、ＭｎやＣｒによる前述の様
な粒界酸化による焼入れ性の低下を補い、表層部を強化
するのに有効に作用する。更にこれらの元素は、高硬度
化に有効な残留オーステナイト量を確保するのに有効な
元素であり、それらの効果は夫々上記下限値以上含有さ
せることによって有効に発揮される。しかしながら含有
量が多くなり過ぎると、浸炭時に過剰量の残留オーステ
ナイトが生成し、浸炭部品の表面硬度が低下するので、
夫々上記上限値以下に抑えることが望ましい。Ni: 0.2-4%, Mo: 0.08-1
% And V: 0.03-1% selected from the group consisting of
At least one of these elements is less likely to form an oxide than Fe, and particularly Mo has the effect of significantly increasing the hardenability in a high C region such as a carburized layer. Therefore, it effectively acts to supplement the deterioration of the hardenability due to the above-described grain boundary oxidation due to Mn and Cr and strengthen the surface layer portion. Further, these elements are elements effective for securing the amount of retained austenite effective for increasing hardness, and these effects are effectively exhibited by containing each of the above lower limits or more. However, if the content is too large, an excessive amount of retained austenite is generated during carburization, and the surface hardness of the carburized parts is reduced.
It is desirable to keep the respective values below the above upper limits.
【００２７】Ｎｂ：０．００５〜０．１％および／また
はＴｉ：０．００５〜０．１％ これらの元素は、共に炭・窒化物を形成してオーステナ
イト結晶粒の微細化に寄与するが、多過ぎると炭・窒化
物の生成量が多くなり過ぎて切削性能や疲労強度に悪影
響を及ぼす様になるので注意しなければならない。 Nb: 0.005-0.1% and / or
Ti: 0.005 to 0.1% Both of these elements form carbon / nitride and contribute to the refinement of austenite crystal grains, but if too much, the amount of carbon / nitride produced becomes too large. Therefore, care must be taken as it may adversely affect cutting performance and fatigue strength.
【００２８】Ｐｂ：０．０９％以下、Ｃａ：０．０００
５〜０．００５％、Ｚｒ：０．０１〜０．０５％、Ｔ
ｅ：０．００５〜０．１％、Ｓｂ：０．００５〜０．１
％、Ｓｅ：０．００５〜０．１％よりなる群から選択さ
れる少なくとも１種 これらの元素はいずれも切削性を高める作用を有してお
り、またＣａ，Ｚｒ，Ｔｅ，Ｓｅは異方性改善効果も有
しており、それらの効果は、いずれか１種以上を下限値
以上含有させることによって有効に発揮される。しかし
Ｐｂについては、０．０９％を超えて過度に含有させる
と、摩擦熱によってＰｂが溶融して破壊の起点となりピ
ッチング寿命を低下させ、またＴｅ，Ｓｂ，Ｓｅについ
ては、夫々０．１％を超えて過度に含有させると大型の
非金属介在物を生成して破壊の起点となり、ピッチング
寿命を低下させる。ＣａはＡｌ2 Ｏ3 の周囲に軟質のＣ
ａＯを生成し耐ピッチング性に悪影響を及ぼすことなく
切削性を高める作用を発揮するが、その効果は０．００
５％で飽和する。Ｚｒは熱間圧延時にＭｎＳの変形を抑
えてＭｎＳの粒状化に寄与し、異方性の改善と切削性の
向上に有効な元素であるが、０．０５％を超えて過度に
含有させると、ＺｒＯ2 等の非金属介在物が多量に生成
して耐ピッチング性などに悪影響を及ぼす様になる。Pb: 0.09% or less, Ca: 0.000
5 to 0.005%, Zr: 0.01 to 0.05%, T
e: 0.005-0.1%, Sb: 0.005-0.1
%, Se: selected from the group consisting of 0.005 to 0.1%
At least one of these elements has the action of enhancing the machinability, and Ca, Zr, Te, and Se also have the effect of improving anisotropy. It is effectively exhibited by containing the above in the lower limit or more. However, if Pb is excessively contained in excess of 0.09%, Pb is melted by frictional heat and becomes a starting point of fracture to reduce the pitching life, and Te, Sb, and Se are each 0.1%. If the content is excessively exceeded, a large non-metallic inclusion is generated, which becomes a starting point of fracture and shortens the pitching life. Ca is a soft C around Al 2 O 3.
It produces aO and exerts the effect of enhancing the machinability without adversely affecting the pitting resistance, but its effect is 0.00
Saturate at 5%. Zr is an element that suppresses the deformation of MnS during hot rolling and contributes to the granulation of MnS, and is effective in improving anisotropy and machinability. However, when Zr exceeds 0.05%, it is contained excessively. A large amount of non-metallic inclusions such as ZrO 2 and ZrO 2 are produced to adversely affect the pitting resistance.
【００２９】本発明で使用される鋼材は、上記の様な元
素を含み残部が実質的にＦｅからなる浸炭焼入れ用鋼材
が好ましく使用されるが、本発明では、前述の如く該鋼
材の成分組成に応じて浸炭焼入れ条件を前記式（１），
（２）の関係を満たす様に制御し、浸炭部品としての表
面硬さをＨｖ６５０以上、より好ましくは７００以上と
し、且つ表層部の残留オーステナイト量が２０〜５０体
積％、より好ましくは２５〜４５体積％の範囲となる様
に制御するところにその特徴を有するものであるから、
上記した鋼材の成分組成については、含有元素の種類や
それらの含有量が上記好ましい範囲から若干外れるもの
であっても、浸炭焼入れ条件を適正に制御してやれば、
従来の浸炭部品に比べると優れた耐面圧性能を発揮し得
るものとなるので、それらも本質的には本発明の技術的
範囲に包含されるものと考えるべきである。As the steel material used in the present invention, a steel material for carburizing and quenching containing the above-mentioned elements and the balance being substantially Fe is preferably used. In the present invention, however, the component composition of the steel material is as described above. Carburizing and quenching conditions according to the above formula (1),
The surface hardness of the carburized component is controlled to Hv 650 or higher, more preferably 700 or higher, and the amount of retained austenite in the surface layer portion is 20 to 50% by volume, more preferably 25 to 45, by controlling so as to satisfy the relationship of (2). Since it has the characteristic that it is controlled to be in the range of volume%,
Regarding the component composition of the above-mentioned steel materials, even if the types of contained elements and their contents are slightly out of the preferable ranges, if the carburizing and quenching conditions are properly controlled,
Since it is possible to exhibit excellent surface pressure resistance performance as compared with the conventional carburized parts, they should be considered to be essentially included in the technical scope of the present invention.
【００３０】また本発明で採用される浸炭焼入れ条件に
ついては、要は使用する鋼材の成分組成に応じてコント
ロールすべきものであるから、当然のことながら該成分
組成に応じて変わってくるが、実用性を考慮して一般的
な条件を示すと下記の如くである。Further, the carburizing and quenching conditions adopted in the present invention should be controlled according to the composition of the steel material used, so naturally it will vary depending on the composition of the composition. The general conditions are shown below in consideration of sex.
【００３１】浸炭温度：７５０〜１２５０℃、より一般
的には８５０〜９５０℃、 浸炭時のＣｐ：０．３〜４．０、より一般的には０．７
〜１．０。尚浸炭法 としては、木炭等の固形浸炭剤を用いる固形浸炭法、
プロパン、ブタン等の炭化水素系ガスをＲｘガス等で
希釈した浸炭ガスを使用するガス浸炭法、ナトリウ
ム、カリウム等の青酸塩を含む溶融塩に浸漬する液体浸
炭法、更には滴注式浸炭法、真空浸炭法、イオン
浸炭法、プラズマ浸炭法、高周波浸炭法などを適宜
採用することができる。 浸炭焼入れ剤温度：５０〜３００℃、より一般的には５
０〜２３０℃。尚浸炭焼入れ剤としては、油やソルト等
が使用される。Carburizing temperature: 750 to 1250 ° C, more generally 850 to 950 ° C, Cp at carburizing: 0.3 to 4.0, more generally 0.7
~ 1.0. As the carburizing method, a solid carburizing method using a solid carburizing agent such as charcoal,
A gas carburizing method using a carburizing gas obtained by diluting a hydrocarbon gas such as propane and butane with Rx gas, a liquid carburizing method of immersing in a molten salt containing cyanide such as sodium and potassium, and further a drop carburizing method. A vacuum carburizing method, an ion carburizing method, a plasma carburizing method, a high frequency carburizing method or the like can be appropriately adopted. Carburizing and quenching agent temperature: 50-300 ° C, more commonly 5
0-230 ° C. As the carburizing and quenching agent, oil or salt is used.
【００３２】[0032]
【実施例】以下、実施例を挙げて本発明の構成および作
用効果をより具体的に説明するが、本発明はもとより下
記実施例によって制限を受けるものではなく、前・後記
の趣旨に適合し得る範囲で適当に変更を加えて実施する
ことも勿論可能であり、それらは何れも本発明の技術的
範囲に包含される。EXAMPLES Hereinafter, the structure and operation and effect of the present invention will be described more specifically with reference to examples. However, the present invention is not limited to the following examples, and the present invention is applicable to the above and following points. It is, of course, possible to implement the present invention with appropriate modifications within the scope of the invention, and all of them are included in the technical scope of the present invention.
【００３３】実施例１ 表１に示す成分組成の供試鋼を用いて鍛造、溶体化・焼
ならし処理を行なった後、図１，２に示す寸法形状のロ
ーラピッチング疲労試験片および小野式回転曲げ疲労試
験片に加工し、次いで表２に示す条件で浸炭焼入れ処理
を行なった後、下記の条件でローラピッチング疲労試験
および回転曲げ疲労試験を行なった。Example 1 After performing forging, solution heat treatment and normalizing treatment using sample steels having the compositional components shown in Table 1, roller pitching fatigue test pieces having the dimensions and shapes shown in FIGS. After processed into a rotary bending fatigue test piece, and then subjected to carburizing and quenching treatment under the conditions shown in Table 2, a roller pitting fatigue test and a rotary bending fatigue test were performed under the following conditions.
【００３４】尚、各供試片の成分組成と浸炭焼入れ条件
より前記式（１），（２）によって求められる計算値を
算出すると共に、各浸炭焼入れ処理後の各供試片の表面
から５μｍ深さ位置における硬さをコード法によって、
またＸ線回折装置を用いて表面から２５μｍ深さ位置に
おける残留オーステナイト量を夫々測定し、その結果を
表２に示した。結果を表３に一括して示す。The calculated values calculated by the above equations (1) and (2) were calculated from the composition of each specimen and the carburizing and quenching conditions, and 5 μm from the surface of each specimen after the carburizing and quenching treatment. By the code method, the hardness at the depth position
Further, the amount of retained austenite at a depth of 25 μm from the surface was measured using an X-ray diffractometer, and the results are shown in Table 2. The results are collectively shown in Table 3.
【００３５】［ローラピッチング疲労試験条件］ 面 圧 ：５０６７ＭＰａ すべり率 ：−４０％ 回転速度 ：１０００ｒｐｍ 潤滑油温度 ：８０℃ 疲労寿命判定基準：ピッチング発生時 試験中止回数 ：１×１０7 回 ［小野式回転曲げ疲労試験条件］ 曲げ応力 ：５００ＭＰａ 回転速度：３６００ｒｐｍ 試験中止回数：１×１０7 回[Roller Pitching Fatigue Test Conditions] Surface Pressure: 5067 MPa Slip Rate: -40% Rotational Speed: 1000 rpm Lubricating Oil Temperature: 80 ° C Fatigue Life Criteria: Number of Test Stops When Pitching Occurs: 1 x 10 7 [Ono Formula Rotating Bending Fatigue Test Conditions] Bending stress: 500 MPa Rotating speed: 3600 rpm Number of test suspensions: 1 × 10 7 times
【００３６】[0036]
【表１】 [Table 1]
【００３７】[0037]
【表２】 [Table 2]
【００３８】[0038]
【表３】 [Table 3]
【００３９】表１〜３より次の様に考察できる。Ｎｏ．
１〜９および１２は、本発明の規定要件を全て満足する
実施例であり、使用する鋼材の成分組成に対して適正な
浸炭焼入れ条件を採用しており、表面硬さと残留オース
テナイト量は、式（１），（２）からの計算値と実測値
がほぼ対応しており、夫々本発明の規定要件を満足して
いるため、ピッチング疲労試験結果および回転曲げ疲労
試験結果のいずれにおいても良好な結果が得られてい
る。The following can be considered from Tables 1 to 3. No.
Examples 1 to 9 and 12 are examples satisfying all the requirements of the present invention, and employ the appropriate carburizing and quenching conditions for the composition of the steel material to be used, and the surface hardness and the amount of retained austenite are The calculated values from (1) and (2) substantially correspond to the measured values, and each satisfy the specified requirements of the present invention. Therefore, both the pitching fatigue test result and the rotary bending fatigue test result are good. Results have been obtained.
【００４０】これに対しＮｏ．１０，１１は、用いた鋼
材のＳｉ含有量またはＣｒ含有量が多過ぎる他、該鋼材
に対して浸炭焼入れ条件も適正でなく、表面硬さと残留
オーステナイト量の計算値と実測値がいずれも本発明の
規定要件を外れる比較例、またＮｏ．１３〜１６は、鋼
材の成分組成は好ましい要件を満たしているが、浸炭焼
入れ条件が不適正であるため、表面硬さと残留オーステ
ナイト量の計算値と実測値の一方もしくは双方が本発明
の規定要件を外れる比較例であり、いずれもピッチング
疲労試験でスコーリング、ピッチングいはスポーリング
の発生が見られ、また回転曲げ疲労試験では表面あるい
は内部を起点とする疲労破壊が起こっており、本発明の
目的を達成できないことが分かる。On the other hand, No. Nos. 10 and 11 had too much Si content or Cr content in the steel materials used, and the carburizing and quenching conditions were not appropriate for the steel materials, and the calculated values and the measured values of the surface hardness and the amount of retained austenite were the same. A comparative example deviating from the requirements of the invention, and No. In Nos. 13 to 16, the composition of the steel material satisfies the preferable requirements, but since the carburizing and quenching conditions are inappropriate, one or both of the calculated value and the measured value of the surface hardness and the retained austenite amount are the prescribed requirements of the present invention. It is a comparative example out of, all of the scoring in the pitching fatigue test, the occurrence of spalling in the pitching is seen, also in the rotary bending fatigue test fatigue fracture originating from the surface or the interior has occurred, the present invention It turns out that you cannot achieve your purpose.
【００４１】[0041]
【発明の効果】本発明は以上の様に構成されており、浸
炭部品を製造するに当たり、使用する鋼材の成分組成に
応じて浸炭焼入れ条件を適正に制御することによって、
疲労特性の向上に最適の表面硬さと残留オーステナイト
量を確実に得ることができ、成分組成や浸炭条件などに
ついて試行錯誤的な模索を要することなく、耐ピッチン
グ性等を含めた高面圧性に非常に優れた浸炭部品を確実
かつ安定して製造し得ることになった。The present invention is configured as described above, and in manufacturing carburized parts, by appropriately controlling the carburizing and quenching conditions in accordance with the composition of the steel material to be used,
It is possible to reliably obtain the optimum surface hardness and retained austenite amount for the improvement of fatigue characteristics, and it is possible to obtain high surface pressure resistance including pitting resistance without the need for trial and error searching for the composition of components and carburizing conditions. It has become possible to reliably and stably manufacture excellent carburized parts.
【図１】ローラピッチング疲労試験に用いた試験片の寸
法・形状を示す図である。FIG. 1 is a diagram showing dimensions and shapes of test pieces used in a roller pitching fatigue test.
【図２】小野式回転曲げ疲労試験に用いた試験片の寸法
・形状を示す図である。FIG. 2 is a diagram showing the dimensions and shape of a test piece used for an Ono-type rotary bending fatigue test.
───────────────────────────────────────────────────── 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 38/60 Ｃ２２Ｃ 38/60 (72)発明者 森本 啓之 兵庫県神戸市西区高塚台１丁目５番５号 株式会社神戸製鋼所神戸総合技術研究所内 (72)発明者 野村 正裕 兵庫県神戸市西区高塚台１丁目５番５号 株式会社神戸製鋼所神戸総合技術研究所内─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 6 Identification number Reference number in the agency FI Technical display location C22C 38/60 C22C 38/60 (72) Inventor Hiroyuki Morimoto 1-5 Takatsukadai, Nishi-ku, Kobe-shi, Hyogo No. 5 Inside Kobe Research Institute of Kobe Steel, Ltd. (72) Inventor Masahiro Nomura 1-5-5 Takatsukadai, Nishi-ku, Kobe-shi, Hyogo Inside Kobe Research Institute of Kobe Works, Ltd.
Claims (5)
す、以下同じ）以下（０％を含まない）、Ｃｒ含有量が
３％以下（０％を含まない）である低・中炭素低合金綱
を使用し、下記（１），（２）式が成立する焼入れ液温
度（絶対温度：Tq）、浸炭温度（絶対温度：Tc）および
浸炭時のカーボンポテンシャル（％：Cp）で浸炭焼入れ
処理を行なうことを特徴とする耐高面圧浸炭部品の製
法。 650 ≦[1-(Y/100)1/3]×840+[(Y/100)1/3 ×(193×Ｂ + 19 ×Si%+8 ×Mn%+43×Mo%+28×V%+41.5)]+330 ……（１） 【数１】 但しＡ=823-361×Ｂ- 11×Si%-39×Mn%-17×Ni%-20×Cr
%-5 ×Mo%-35×V%-330×N%+ 30×Al% Ｂ=Cp + Ｃ×(194.4- 0.1058×Tc)/(179.5+0.508×Tc) Ｃ=(-0.00286×Tc+1.81)×Si%+0.000479×Tc×Mn% +(-
0.000529×Tc+0.30)×Ni%+(0.000124 ×Tc+0.38)×Mo%+
(0.00255×Tc-1.30)×V%+Cr% Tqは焼入れ温度、Tcは浸炭温度（絶対温度）、Cpは浸炭
時のカーボンポテンシャル（％）を表わす。1. Low / medium carbon low having a Si content of 1% (representing mass%, the same applies hereinafter) (not including 0%) and a Cr content of 3% or less (not including 0%). Using alloy steel, carburizing and quenching at the quenching liquid temperature (absolute temperature: Tq), carburizing temperature (absolute temperature: Tc), and carbon potential (%: Cp) during carburizing that satisfy the following formulas (1) and (2) A process for producing high surface pressure resistant carburized parts, which is characterized by performing treatment. 650 ≤ [1- (Y / 100) 1/3 ] × 840 + [(Y / 100) 1/3 × (193 × B + 19 × Si% + 8 × Mn% + 43 × Mo% + 28 × V % + 41.5)] + 330 …… (1) [Equation 1] However, A = 823-361 × B-11 × Si% -39 × Mn% -17 × Ni% -20 × Cr
% -5 x Mo% -35 x V% -330 x N% + 30 x Al% B = Cp + C x (194.4- 0.1058 x Tc) / (179.5 + 0.508 x Tc) C = (-0.00286 x Tc + 1.81) × Si% + 0.000479 × Tc × Mn% + (-
0.000529 x Tc + 0.30) x Ni% + (0.000124 x Tc + 0.38) x Mo% +
(0.00255 x Tc-1.30) x V% + Cr% Tq is the quenching temperature, Tc is the carburizing temperature (absolute temperature), and Cp is the carbon potential (%) during carburizing.
素低合金鋼を使用する請求項１に記載の製法。2. C: 0.05 to 0.5% Si: 1% or less Mn: 0.2 to 2% P: 0.030% or less S: 0.003 to 0.07% Cr: 0.2 ~ 3% Al: 0.015 to 0.1% N: 0.005 to 0.025% Total oxygen: 0.002% or less, low-medium carbon low alloy with the balance substantially Fe The method according to claim 1, wherein steel is used.
・中炭素低合金鋼を使用する請求項２に記載の製法。3. Low / medium containing at least one element selected from the group consisting of Ni: 0.2 to 4%, Mo: 0.08 to 1% V: 0.03 to 1% as another element. The method according to claim 2, wherein low carbon alloy steel is used.
〜０．１％および／またはＴｉ：０．００５〜０．１％
を含有する低・中炭素低合金鋼を使用する請求項２また
は３に記載の製法。4. As another element, Nb: 0.005
~ 0.1% and / or Ti: 0.005-0.1%
The manufacturing method according to claim 2 or 3, wherein a low / medium carbon low alloy steel containing C is used.
低・中炭素低合金鋼を使用する請求項２〜４のいずれか
に記載の製法。5. As another element, Pb: 0.09% or less Ca: 0.0005 to 0.005% Zr: 0.01 to 0.05% Te: 0.005 to 0.1% Sb: 0 0.005-0.1% Se: The low-medium carbon low alloy steel containing at least one element selected from the group consisting of 0.005-0.1% is used. The manufacturing method described.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21333995A JPH0959756A (en) | 1995-08-22 | 1995-08-22 | Production of high bearing resistant carburized parts |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21333995A JPH0959756A (en) | 1995-08-22 | 1995-08-22 | Production of high bearing resistant carburized parts |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0959756A true JPH0959756A (en) | 1997-03-04 |
Family
ID=16637522
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP21333995A Withdrawn JPH0959756A (en) | 1995-08-22 | 1995-08-22 | Production of high bearing resistant carburized parts |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0959756A (en) |
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|---|---|---|---|---|
| WO2003012156A1 (en) * | 2001-07-24 | 2003-02-13 | Ascometal | Method for making a mechanical component, and resulting mechanical component |
| WO2003104515A1 (en) * | 2002-06-11 | 2003-12-18 | 光洋サーモシステム株式会社 | Method of gas carburizing |
| WO2003104516A1 (en) * | 2002-06-11 | 2003-12-18 | 光洋サーモシステム株式会社 | Method of gas carburizing |
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| US7416614B2 (en) | 2002-06-11 | 2008-08-26 | Koyo Thermo Systems Co., Ltd. | Method of gas carburizing |
| WO2010116670A1 (en) * | 2009-03-30 | 2010-10-14 | 新日本製鐵株式会社 | Carburized steel part |
| JP2013227607A (en) * | 2012-04-25 | 2013-11-07 | Honda Motor Co Ltd | Steel for belt-type cvt pulley and the belt-type cvt pulley |
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-
1995
- 1995-08-22 JP JP21333995A patent/JPH0959756A/en not_active Withdrawn
Cited By (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2003012156A1 (en) * | 2001-07-24 | 2003-02-13 | Ascometal | Method for making a mechanical component, and resulting mechanical component |
| WO2003104515A1 (en) * | 2002-06-11 | 2003-12-18 | 光洋サーモシステム株式会社 | Method of gas carburizing |
| WO2003104516A1 (en) * | 2002-06-11 | 2003-12-18 | 光洋サーモシステム株式会社 | Method of gas carburizing |
| US7416614B2 (en) | 2002-06-11 | 2008-08-26 | Koyo Thermo Systems Co., Ltd. | Method of gas carburizing |
| US8317939B2 (en) | 2003-06-12 | 2012-11-27 | Koyo Thermo Systems Co., Ltd. | Method of gas carburizing |
| WO2004111292A1 (en) * | 2003-06-12 | 2004-12-23 | Koyo Thermo Systems Co., Ltd. | Method of gas carburizing |
| WO2005003401A1 (en) * | 2003-07-03 | 2005-01-13 | Koyo Thermo Systems Co., Ltd. | Method for gas carburizing |
| US7029540B2 (en) | 2003-07-03 | 2006-04-18 | Koyo Thermo Systems Co., Ltd. | Method of gas carburizing |
| CN1311095C (en) * | 2003-07-03 | 2007-04-18 | 光洋热***株式会社 | Gas acieration method |
| WO2010116670A1 (en) * | 2009-03-30 | 2010-10-14 | 新日本製鐵株式会社 | Carburized steel part |
| CN102317490A (en) * | 2009-03-30 | 2012-01-11 | 新日本制铁株式会社 | Carburized steel part |
| JP4677057B2 (en) * | 2009-03-30 | 2011-04-27 | 新日本製鐵株式会社 | Carburized steel parts |
| KR101280203B1 (en) * | 2009-03-30 | 2013-06-28 | 신닛테츠스미킨 카부시키카이샤 | Carburized steel part |
| US8801873B2 (en) | 2009-03-30 | 2014-08-12 | Nippon Steel & Sumitomo Metal Corporation | Carburized steel part |
| JP2013227607A (en) * | 2012-04-25 | 2013-11-07 | Honda Motor Co Ltd | Steel for belt-type cvt pulley and the belt-type cvt pulley |
| JP2019218585A (en) * | 2018-06-18 | 2019-12-26 | 日本製鉄株式会社 | Steel for carburization and component |
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