JP3240627B2 - Manufacturing method of constant velocity joint parts - Google Patents
Manufacturing method of constant velocity joint partsInfo
- Publication number
- JP3240627B2 JP3240627B2 JP08753891A JP8753891A JP3240627B2 JP 3240627 B2 JP3240627 B2 JP 3240627B2 JP 08753891 A JP08753891 A JP 08753891A JP 8753891 A JP8753891 A JP 8753891A JP 3240627 B2 JP3240627 B2 JP 3240627B2
- Authority
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- Japan
- Prior art keywords
- less
- constant velocity
- hardness
- steel
- velocity joint
- 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.)
- Expired - Fee Related
Links
Description
【０００１】[0001]
【産業上の利用分野】この発明は等速ジョイント部品の
製造方法に関する。BACKGROUND OF THE INVENTION This invention relates to a process for producing a constant velocity joint parts.
【０００２】[0002]
【従来の技術】等速ジョイントの一種にボ−ルを介して
トルク伝達を行うものがあり、自動車，建設車両等の等
速ジョイントとして用いられている。図１はこの等速ジ
ョイントの構成部品を示したものである。図に示してい
るようにこの部品（ケ−ジ）１０は、全体として中空の
太鼓形状を成していて所定複数個所に窓部１２を有し、
この窓部１２にボ−ルを係合させてトルク伝達を行うよ
うになっている。2. Description of the Related Art One type of constant velocity joints transmits torque through a ball, and is used as a constant velocity joint for automobiles, construction vehicles, and the like. FIG. 1 shows the components of this constant velocity joint. As shown in the figure, this part (cage) 10 has a hollow drum shape as a whole and has windows 12 at a plurality of predetermined positions.
A ball is engaged with the window 12 to transmit torque.
【０００３】この太鼓形状の等速ジョイント部品１０
は、従来、表１Ｈに示す組成の鋼材を素材として用い、
これに以下の各種処理を施して最終製品に製造してい
た。具体的には、先ず鋼材を熱間鍛造して基本形状，即
ち中空の太鼓形状に成形し、次いで焼入・焼戻し処理し
た後にショットブラスト処理して表面のスケ−ルを除去
し、更に機械加工を施して内径出しを行う。その後に窓
抜き加工を施して窓部１２を形成し、その後に光輝焼な
らし処理を施した上、表面硬化のための浸炭焼入・焼戻
し処理を行う。[0003] This drum-shaped constant velocity joint part 10
Has conventionally used a steel material having the composition shown in Table 1H as a raw material,
This was subjected to the following various processes to produce a final product. Specifically, first, a steel material is hot forged to form a basic shape, that is, a hollow drum shape, then quenched and tempered, then shot blasted to remove the scale of the surface, and further machined. To obtain the inner diameter. Thereafter, the window portion 12 is formed by performing a window cutting process, and thereafter, a bright normalizing process is performed, and then a carburizing quenching / tempering process for surface hardening is performed.
【０００４】ここで熱間鍛造後に焼入・焼戻し処理を行
うのは、その後の窓抜き加工を良好に行うために、太鼓
形状の中間品を最適な硬さ（ＨＲＢ８５〜９５）とする
ためである。即ちこの窓抜き加工は冷間加工で行うため
に、中間製品の硬さが軟らか過ぎると窓抜き加工時にバ
リが発生したり変形を起こしたりし、また逆に硬すぎる
とバリの発生の問題は生じないものの加工自体が困難と
なる。そこでその硬さを最適硬さに調整する必要がある
のである。The reason for performing the quenching / tempering treatment after the hot forging is to make the drum-shaped intermediate product the optimum hardness (HRB 85-95) in order to perform the subsequent window cutting work well. is there. That is, since the window forming process is performed by cold working, if the hardness of the intermediate product is too soft, burrs are generated or deformed at the time of the window forming process. Although it does not occur, the processing itself becomes difficult. Therefore, it is necessary to adjust the hardness to the optimum hardness.
【０００５】また窓抜き加工後の光輝焼ならし処理は、
窓抜き加工の際に結晶粒が著しく微細化し、また歪が蓄
積された状態となるため、そのまま最終の浸炭焼入・焼
戻し処理を行うとその際に局部的に結晶粒が粗大化して
異常班点を生じ、このことが熱処理歪の増加，疲れ強さ
及び衝撃強さの劣化をもたらすことから、加工歪の開放
とオ−ステナイト初期粒の調整（整粒）を図り、異常班
点の発生を防止するために行うものである。[0005] The bright normalizing process after the window cutting process is as follows.
During the window cutting process, the crystal grains become extremely fine and strain is accumulated, so if the final carburizing quenching / tempering treatment is performed as it is, the crystal grains locally become coarse and abnormal This causes an increase in heat treatment strain, deterioration of fatigue strength and impact strength, so that the work strain is released and the austenite initial grains are adjusted (sizing), and abnormal spots are generated. This is done to prevent
【０００６】更にその後の浸炭焼入・焼戻し処理は、等
速ジョイント部品を実際に使用した時の面疲れ強さを向
上させる目的で行うものである。[0006] Further, the subsequent carburizing quenching / tempering treatment is performed for the purpose of improving the surface fatigue strength when the constant velocity joint parts are actually used.
【０００７】[0007]
【発明が解決しようとする課題】このように従来にあっ
ては、複雑な工程を経て等速ジョイント部品を製造して
おり、このことが等速ジョイント部品のコストを高める
要因となっていた。As described above, in the prior art, constant velocity joint parts are manufactured through complicated steps, which has been a factor of increasing the cost of the constant velocity joint parts.
【０００８】[0008]
【課題を解決するための手段】本発明の等速ジョイント
部品の製造方法は上記工程における熱間鍛造後の硬さ調
整のための焼入・焼戻し処理及び光輝焼ならし処理に着
眼し、これを省略することによって製造工程を簡略化す
る目的の下になされたものである。而して本発明の製造
方法は、重量基準でＣ：0.1〜0.3％，Ｓｉ：0.15％以
下，Ｍｎ：0.2〜1.50％，Ｐ：0.015％以下，Ｓ：0.030
％以下，Ｃｒ：0.2〜1.50％，Ｍｏ：0.2〜1.0％，Ｎ：
0.025％以下，Ｏ：0.0020％以下、Ｎｂ，Ａｌ，Ｔｉの
何れか１種又は２種以上をＮｂ：0.005〜0.050％，Ａ
ｌ：0.020〜0.060％，Ｔｉ：0.01〜0.15％の範囲で含有
し、残部実質的にＦｅから成る組成を有し且つ焼入性を
ＨＲＣで３０＜J ３ ＜４５に調整して成る素材鋼を溶解
し鋼塊とした後ソーキングし、次いで熱間鍛造成形を行
って鍛造後硬さをＨＲＢ８５〜９５となした後、浸炭焼
入・焼戻し処理を行うことにより、ＨＶが５５０以上と
なる有効硬化層深さが0.2〜0.9mm、心部硬さＨＶが４０
０以下、かつ平均結晶粒度が１０以上とすることを特徴
とする（請求項１）。 SUMMARY OF THE INVENTION A constant velocity joint according to the present invention.
The method of manufacturing parts focuses on the quenching / tempering process and the bright normalizing process for adjusting the hardness after hot forging in the above process, with the aim of simplifying the manufacturing process by omitting this. It was done. Thus, the production of the present invention
The method is as follows: C: 0.1 to 0.3%, Si: 0.15% or less, Mn: 0.2 to 1.50%, P: 0.015% or less, S: 0.030 on a weight basis.
%, Cr: 0.2-1.50%, Mo: 0.2-1.0%, N:
0.025% or less, O: 0.0020% or less, Nb, Al, Ti, one or more of Nb: 0.005 to 0.050%, A
l: 0.020~0.060%, Ti: contains at 0.01% to 0.15% range, the and hardenability has a composition comprising the balance substantially Fe
Dissolved 30 <steel material formed by adjusting the J 3 <45 in HRC
And then soaked, then hot forged.
After forging the hardness after HRB85-95, carburizing
The HV is increased to 550 or more by performing the tempering process.
Effective hardened layer depth is 0.2-0.9mm, core hardness HV is 40
0 or less and the average grain size is 10 or more
(Claim 1).
【０００９】上記のような本発明は、熱間鍛造後の焼入
・焼戻し処理及び整粒化のための光輝焼ならし処理を省
略することに着眼し、そして等速ジョイント用鋼の各種
成分及び浸炭焼入れ処理について検討を行った結果到達
し得たものである。かかる本発明は、Ｍｏを鋼中に添加
・含有させるとともにＣｒ等他成分を上記範囲に調整
し、以て熱間鍛造した段階で所定の硬さが出るようにす
るとともに、鋼中にＮｂ，Ａｌ，Ｔｉ等成分を添加し且
つその量を上記所定範囲とすることによって、結晶粒の
粗大化を防止するようになすものである。The present invention as described above focuses on omitting the quenching / tempering treatment after hot forging and the bright normalizing treatment for sizing, and various components of steel for constant velocity joints. Reached as a result of studying carburizing and carburizing
I was able to do it. According to the present invention, Mo is added to and contained in steel, and other components such as Cr are adjusted to the above range so that a predetermined hardness is obtained at the stage of hot forging, and Nb, al, the added and the amount of Ti or the like component by the above-mentioned predetermined range, and constitute so as to prevent coarsening of crystal grains.
【００１０】かかる本発明によれば、熱間鍛造後の段階
で後の窓抜き加工のための最適な硬さが得られるので、
硬さ調整のための焼入・焼戻し処理を省略することがで
き、また冷間加工後において浸炭焼入・焼戻し処理した
時に結晶粒が粗大化するのが抑制されているので、整粒
及び歪取りのために従来必要とされていた光輝焼ならし
処理を省略することができる。これにより等速ジョイン
ト部品の製造工程が簡略化され、コスト低減が達成され
る。According to the present invention, at the stage after the hot forging, the optimal hardness for the subsequent window cutting can be obtained.
Quenching and tempering treatments for adjusting hardness can be omitted, and coarsening of grains during carburizing quenching and tempering after cold working is suppressed. It is possible to omit the bright normalizing process conventionally required for removing. This simplifies the manufacturing process of the constant velocity joint parts and achieves cost reduction.
【００１１】本発明ではまた、焼入れ性をＨＲＣで３０
＜J ３ ＜４５に調整して成る上記組成の鋼を素材として
用い且つ表面硬化のための浸炭焼入・焼戻し処理を行う
ことにより、ＨＶが５５０以上となる有効硬化層深さが
0.2〜0.9ｍｍ、心部硬さＨＶが４００以下且つ平均結晶
粒度を１０以上となす。[0011] In the present invention, the hardenability is 30 or more by HRC.
<Steel of the above composition formed by adjusting the J 3 <45 as a material
Carburizing and tempering for surface hardening
Thereby, the effective hardened layer depth at which the HV becomes 550 or more is increased.
0.2-0.9mm, core hardness HV is 400 or less and average crystal
The particle size is 10 or more .
【００１２】等速ジョイント部品においては、トルク伝
達に際して表面部分におけるマイクロクラックの発生が
問題となり、このようなマクロクラックが発生するとこ
れが成長して疲労破壊の原因となる。In the case of constant velocity joint parts, the generation of microcracks on the surface during torque transmission becomes a problem. When such macrocracks occur, they grow and cause fatigue failure.
【００１３】一方においてかかる等速ジョイント部品
は、耐衝撃強度，靱性も必要とされる。そこでこのよう
な等速ジョイント部品においては、表面硬さが一定硬さ
以上であり、また心部については一定の軟らかさ，靱性
が要求される。On the other hand, such constant velocity joint parts also require impact strength and toughness. Therefore, in such constant velocity joint parts, the surface hardness is not less than a certain hardness, and the core is required to have certain softness and toughness.
【００１４】これら特性は、用いる鋼材の組成とともに
最終の浸炭焼入条件によって左右される。本発明は上記
特定の組成の鋼材を素材として用い且つ表面硬化のため
の浸炭焼入条件を確定したことを特徴とするものであ
り、かかる本発明によると最終製品として必要とされる
表面硬さ、つまり耐疲れ強さと高い衝撃強度が確保でき
る。These properties depend on the final carburizing and quenching conditions as well as the composition of the steel material used. The present invention is characterized in that a steel material having the above specific composition is used as a material and carburizing and quenching conditions for surface hardening are determined. According to the present invention, the surface hardness required as a final product is In other words, fatigue resistance and high impact strength can be secured.
【００１５】ここで焼入性を示すJ３の値が３０〜４５
の範囲となるようにしているのは、J３が３０より小さ
いと鍛造後の硬さが不足する一方、４５より高くなると
等速ジョイント部品の心部硬さが増大して靱性の劣化を
もたらすためである。[0015] The value of J 3 shown here hardenability 30-45
Is the so that the range, while J 3 is insufficient hardness after forging and less than 30, the constant velocity joint component eccentric part hardness of becomes higher than 45 results in deterioration of the increased toughness That's why.
【００１６】また浸炭焼入れの際、ＨＶ＝５５０以上と
なる有効硬化層深さが0.2〜0.9ｍｍとなるようにしてい
るのは、かかる有効硬化層深さが0.2ｍｍよりも少ない
と浸炭後の強度が確保できず、逆に0.9ｍｍより深いと
靱性が劣化してしまうためである。In carburizing and quenching, the effective hardened layer depth at which HV is equal to or more than 550 is set to be 0.2 to 0.9 mm. This is because the strength cannot be secured, and conversely, if it is deeper than 0.9 mm, the toughness is deteriorated.
【００１７】本発明は、更に心部硬さをＨＶ＝４００以
下に規定している。これは等速ジョイント部品としての
靱性を確保し、部品全体としての強度，耐衝撃特性を確
保するには、心部硬さＨＶ＝４００以下である必要があ
るとの知見に基づく。In the present invention, the core hardness is further defined as HV = 400 or less. This is based on the finding that the core hardness HV needs to be 400 or less in order to secure the toughness as a constant velocity joint part and the strength and impact resistance of the whole part.
【００１８】本発明においては、上記等速ジョイント用
鋼に更にＮｉ及びＶの何れか１種又は２種をＮｉ：2.00
％以下，Ｖ：0.5％以下の範囲で含有させることができ
る（請求項２）。これにより浸炭部及び内部の靱性を有
効に向上させることができ、また鍛造後の硬さ調整が行
い易くなる。In the present invention, one or two of Ni and V are further added to the above steel for constant velocity joints with Ni: 2.00.
%, V: 0.5% or less (claim 2) . Thereby, the toughness of the carburized portion and the inside can be effectively improved, and the hardness after forging can be easily adjusted.
【００１９】本発明においては、更にＰｂ，Ｂｉ，Ｃ
ａ，Ｔｅ，Ｂの何れか１種又は２種以上を、Ｐｂ：0.02
〜0.35％，Ｂｉ：0.03〜0.15％，Ｃａ：0.0010〜0.01
％，Ｔｅ：0.005〜0.10％，Ｂ：0.008％以下の範囲で含
有させることができる（請求項３）。これにより、等速
ジョイント用鋼の被削性を良好にすることができる。In the present invention, Pb, Bi, C
any one or more of a, Te, and B, Pb: 0.02
0.35%, Bi: 0.03 to 0.15%, Ca: 0.0010 to 0.01
%, Te: 0.005 to 0.10%, B: 0.008% or less (Claim 3) . Thereby, the machinability of the steel for constant velocity joints can be improved.
【００２０】次に本発明における各種添加成分の限定理
由を説明する。 Ｃ：0.1〜0.3％ Ｃは心部の強度確保に必要な成分である。但し0.1％未
満では効果が少なく、0.3％を超過すると靱性及び被削性
が劣化してしまう。Next, the reasons for limiting various additives in the present invention will be described. C: 0.1 to 0.3% C is a component necessary for securing the strength of the core. However, if it is less than 0.1%, the effect is small, and if it exceeds 0.3%, toughness and machinability deteriorate.
【００２１】 Ｓｉ：0.15％以下 Ｓｉは浸炭時の粒界酸化を助長し、破壊の起点となりや
すい。また冷鍛性を阻害する。本発明ではＳｉを0.15％
以下に抑える必要がある。Si: 0.15% or less Si promotes grain boundary oxidation at the time of carburization and is likely to be a starting point of destruction. In addition, it inhibits cold forgeability. In the present invention, 0.15% of Si
It is necessary to keep it below.
【００２２】 Ｍｎ：0.2〜1.50％ Ｍｎは焼入性向上元素であり、心部の強度を向上させ
る。その効果を発揮させるには0.2％以上が必要であ
る。但し1.50％を超過すると焼入性が過大となり、靱性
が劣化してしまう。Mn: 0.2-1.50% Mn is an element for improving hardenability and improves the strength of the core. 0.2% or more is required to achieve the effect. However, if it exceeds 1.50%, the hardenability becomes excessive and the toughness deteriorates.
【００２３】 Ｃｒ：0.2〜1.50％ Ｃｒは焼入性向上元素であるが、粒界酸化を助長する元
素でもある。またその量が多過ぎるとＭｎと同じく焼入
性が過大となり、靱性を劣化させてしまう。そこで本発
明ではＣｒの量を0.2〜1.50％とする。Cr: 0.2-1.50% Cr is an element that improves hardenability, but also promotes grain boundary oxidation. On the other hand, if the amount is too large, the hardenability becomes excessive as in Mn, and the toughness is deteriorated. Therefore, in the present invention, the amount of Cr is set to 0.2 to 1.50%.
【００２４】 Ｐ：0.015％以下 Ｓ：0.030％以下 Ｐ，Ｓは粒界強度を低下させ、鋼の強度，靱性を劣化さ
せる。従ってその上限値を0.015％，0.030％とする。P: 0.015% or less S: 0.030% or less P and S lower the grain boundary strength and deteriorate the strength and toughness of steel. Therefore, the upper limits are set to 0.015% and 0.030%.
【００２５】 Ｏ：0.0020％以下 Ｏは酸化物系介在物を形成して内部亀裂発生の起点とな
る。そこでこれを0.0020％以下に抑える。O: 0.0020% or less O forms oxide-based inclusions and becomes a starting point of internal crack generation. Therefore, this is suppressed to 0.0020% or less.
【００２６】 Ｎｂ：0.005〜0.050％ Ａｌ：0.020〜0.060％ Ｔｉ：0.01〜0.15％ これら元素は結晶粒を微細化する元素であり、その効果
を充分発揮させるためにそれぞれ0.005％，0.020％，0.
01％以上含有させる。但し含有量が多過ぎると効果が飽
和するのみならず、機械的な強度を低下させてしまう。
そこでそれぞれ上限値を0.050％，0.060％，0.15％とす
る。Nb: 0.005 to 0.050% Al: 0.020 to 0.060% Ti: 0.01 to 0.15% These elements are elements for refining crystal grains. In order to sufficiently exhibit the effect, 0.005%, 0.020%, and 0%, respectively. .
01% or more. However, if the content is too large, not only the effect is saturated, but also the mechanical strength is reduced.
Therefore, the upper limits are set to 0.050%, 0.060%, and 0.15%, respectively.
【００２７】 Ｎ：0.025％以下 Ｎは熱間加工性を阻害し、また地傷等の原因となる。そ
こでこれを0.025％以下とする。N: 0.025% or less N inhibits hot workability and causes ground damage and the like. Therefore, this is set to 0.025% or less.
【００２８】 Ｖ：0.50％以下 Ｖは鍛造後の硬さ調整のために添加する。但しその上限
は0.5％である。V: 0.50% or less V is added for adjusting hardness after forging. However, the upper limit is 0.5%.
【００２９】 Ｎｉ：2.00％以下 Ｎｉは浸炭部及び内部の靱性向上に有効な元素である。
但し2.00％を超過すると微細炭化物の生成を阻害し、ま
た被削性を劣化させる。ここでは上限値を2.00％とす
る。Ni: 2.00% or less Ni is an element effective for improving the toughness of the carburized portion and the inside.
However, if it exceeds 2.00%, the formation of fine carbides is inhibited and the machinability is deteriorated. Here, the upper limit is 2.00%.
【００３０】 Ｍｏ：0.2〜1.0％ ＭｏはＮｉと同様の働きをするもので、0.2％以上の添加
が必要である。但し1.0％を超過すると効果が飽和して
しまう。Mo: 0.2 to 1.0% Mo has the same function as Ni, and needs to be added in an amount of 0.2% or more. However, if it exceeds 1.0%, the effect will be saturated.
【００３１】 Ｐｂ：0.02〜0.35％ Ｂｉ：0.03〜0.15％ Ｃａ：0.0010〜0.01％ Ｔｅ：0.005〜0.10％ Ｂ：0.008％以下 これらは被削性を改善する元素であるが、それぞれ上記
上限値を超過すると効果が飽和する傾向にあり、また熱
間加工性の劣化をもたらす。Pb: 0.02 to 0.35% Bi: 0.03 to 0.15% Ca: 0.0010 to 0.01% Te: 0.005 to 0.10% B: 0.008% or less These are elements that improve machinability. If it exceeds, the effect tends to be saturated and the hot workability is deteriorated.
【００３２】[0032]
【実施例】次に本発明の特徴を更に明確にすべく、以下
にその実施例を詳述する。表１に示す組成の素材鋼５０
ｋｇを溶解し鋼塊とした後ソ−キングし、次いで熱間鍛
造成形してその鍛造硬さ測定を行うとともに、焼入性測
定（ジョミニ−試験）を行った。これと併せて鍛造品
を、焼入・焼戻し処理による硬さ調整を行うことなく機
械加工し、シャルピ−試験片（１０Ｒノッチ）を作成し
た。次いで図２に示す条件下での浸炭焼入及び焼戻し処
理（焼戻しは１６０℃に２時間保持後空冷）を行い、そ
の処理品の硬さ分布測定，結晶粒度測定を行うととも
に、シャルピ−衝撃試験を行った。結果が表２に示して
ある。但し表２中Ｈの各値は従来の工程に従って処理し
たものの結果である。Next, in order to further clarify the features of the present invention, examples thereof will be described in detail below. Material steel 50 having the composition shown in Table 1
After dissolving the kg into a steel ingot, the steel was subjected to soaking, then hot forging and the forging hardness was measured, and the hardenability was measured (Jomini test). At the same time, the forged product was machined without adjusting the hardness by quenching and tempering to prepare a Charpy test piece (10R notch). Next, carburizing and quenching and tempering treatment (tempering was carried out at 160 ° C. for 2 hours followed by air cooling) under the conditions shown in FIG. 2 were carried out, and the hardness distribution and crystal grain size of the treated product were measured. Was done. The results are shown in Table 2. However, each value of H in Table 2 is the result of processing according to the conventional process.
【００３３】[0033]
【表１】 [Table 1]
【００３４】[0034]
【表２】 [Table 2]
【００３５】表１及び表２から分かるように、比較鋼Ｆ
の場合、焼入性が低いために鍛造後の硬さが低く、また
微粒化元素であるＡｌの添加量が少ないために一部結晶
粒の粗大化を引き起こしており、耐衝撃値も低くなって
いる。As can be seen from Tables 1 and 2, the comparative steel F
In the case of, the hardness after forging is low due to low hardenability, and the addition amount of Al, which is an atomizing element, is small, causing partial coarsening of the crystal grains and the impact resistance value is also low ing.
【００３６】また比較鋼Ｇの場合、焼入性が高いために
硬さ調節のための焼入・焼戻し処理の省略が可能である
が、結晶粒粗大化による耐衝撃値の低下がみられる。In the case of comparative steel G, the quenchability and tempering treatment for adjusting the hardness can be omitted because of its high hardenability, but the impact resistance is lowered due to coarsening of the crystal grains.
【００３７】これに対して本発明鋼の場合には、何れも
鍛造後の硬さＨＲＢ８５〜９５を満足しており、焼入・
焼戻し処理の省略が可能であることに加え、結晶粒粗大
化防止元素の添加効果が現れており、結晶粒が細粒であ
り、焼ならし処理を省略することが可能である。また耐
衝撃値は結晶粒の細粒化効果によって何れも従来鋼Ｈ以
上の値が得られている。On the other hand, in the case of the steel of the present invention, the hardness after forging satisfies the hardness HRB 85-95, and
In addition to the fact that tempering treatment can be omitted, the effect of adding a crystal grain coarsening preventing element is exhibited, the crystal grains are fine, and the normalizing treatment can be omitted. In addition, the impact resistance value is higher than that of conventional steel H in all cases due to the effect of grain refinement.
【００３８】以上本発明の実施例を詳述したが、これは
あくまで本発明の一具体例であり、本発明はその主旨を
逸脱しない範囲において、当業者の知識に基づき様々な
変更を加えた形態・態様において実施可能である。Although the embodiment of the present invention has been described in detail above, this is merely a specific example of the present invention, and the present invention is based on the knowledge of those skilled in the art without departing from the gist thereof. The present invention can be implemented in the form and mode.
【００３９】[0039]
【図面の簡単な説明】[Brief description of the drawings]
【図１】本発明に係る等速ジョイント部品の一例を示す
斜視図である。FIG. 1 is a perspective view showing an example of a constant velocity joint component according to the present invention.
【図２】本発明の一実施例工程における浸炭焼入条件を
示す説明図である。FIG. 2 is an explanatory view showing carburizing and quenching conditions in a step of one embodiment of the present invention.
１０ 等速ジョイント部品 １２ 窓部 10 Constant velocity joint parts 12 Window
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ Ｆ１６Ｄ 3/20 Ｆ１６Ｄ 3/20 Ｚ (72)発明者 秦野 敦臣 愛知県名古屋市天白区島田２−301 (72)発明者 並木 邦夫 愛知県名古屋市守山区牛牧字牛牧７−１ (56)参考文献 特開 昭64−39351（ＪＰ，Ａ) 特開 平２−147148（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C21D 9/00 C21D 8/00 C22C 38/00 - 38/60 C23C 8/22 F16D 3/20 ────────────────────────────────────────────────── ─── Continuing on the front page (51) Int.Cl. 7 Identification code FI F16D 3/20 F16D 3/20 Z (72) Inventor Atsushi Hatano 2-301 Shimada, Tenpaku-ku, Nagoya City, Aichi Prefecture (72) Inventor Namiki Kunio 7-1, Ushimaki, Ushimaki, Moriyama-ku, Nagoya-shi, Aichi (56) References JP-A-64-39351 (JP, A) JP-A-2-147148 (JP, A) (58) Fields studied (Int. . 7, DB name) C21D 9/00 C21D 8/00 C22C 38/00 - 38/60 C23C 8/22 F16D 3/20
Claims (3)
％以下，Ｍｎ：0.2〜1.50％，Ｐ：0.015％以下，Ｓ：0.
030％以下，Ｃｒ：0.2〜1.50％，Ｍｏ：0.2〜1.0％，
Ｎ：0.025％以下，Ｏ：0.0020％以下、Ｎｂ，Ａｌ，Ｔ
ｉの何れか１種又は２種以上をＮｂ：0.005〜0.050％，
Ａｌ：0.020〜0.060％，Ｔｉ：0.01〜0.15％の範囲で含
有し、残部実質的にＦｅから成る組成を有し且つ焼入性
をＨＲＣで３０＜J ３ ＜４５に調整して成る素材鋼を溶
解し鋼塊とした後ソーキングし、次いで熱間鍛造成形を
行って鍛造後硬さをＨＲＢ８５〜９５となした後、浸炭
焼入・焼戻し処理を行うことにより、ＨＶが５５０以上
となる有効硬化層深さが0.2〜0.9mm、心部硬さＨＶが４
００以下、かつ平均結晶粒度が１０以上とすることを特
徴とする等速ジョイント部品の製造方法。 1. C: 0.1 to 0.3%, Si: 0.15% by weight
%, Mn: 0.2-1.50%, P: 0.015% or less, S: 0.
030% or less, Cr: 0.2-1.50%, Mo: 0.2-1.0%,
N: 0.025% or less, O: 0.0020% or less, Nb, Al, T
i, Nb: 0.005 to 0.050%,
Al: 0.020~0.060%, Ti: contains at 0.01% to 0.15% range, it has a composition comprising the balance substantially Fe and hardenability
Is adjusted to 30 <J 3 <45 by HRC to melt the material steel.
After soaking it into a steel ingot, soaking, then hot forging
After forging and setting the hardness to HRB85-95 after forging, carburizing
HV of 550 or more by quenching / tempering
Effective hardened layer depth is 0.2-0.9mm and core hardness HV is 4
And an average grain size of 10 or more.
Manufacturing method of constant velocity joint parts.
れか１種又は２種を重量基準でＮｉ：2.00％以下，Ｖ：
0.5％以下の範囲で更に含有した組成となすことを特徴
とする請求項１に記載の等速ジョイント部品の製造方
法。2. The steel composition of the raw material steel, wherein one or two of Ni and V are Ni: 2.00% or less on a weight basis, and V:
CVJ parts manufacturing side of claim 1, wherein the forming the composition further containing from 0.5% or less
Law .
ａ，Ｔｅ，Ｂの何れか１種又は２種以上を、重量基準で
Ｐｂ：0.02〜0.35％，Ｂｉ：0.03〜0.15％，Ｃａ：0.00
10〜0.01％，Ｔｅ：0.005〜0.10％，Ｂ：0.008％以下の
範囲で更に含有した組成とすることを特徴とする請求項
１又は２に記載の等速ジョイント部品の製造方法。3. The steel composition of the material steel is Pb, Bi, C
a, Te or B, one or more of Pb: 0.02 to 0.35%, Bi: 0.03 to 0.15%, and Ca: 0.00 by weight.
10~0.01%, Te: 0.005~0.10%, B: constant velocity joint component manufacturing method according to claim 1 or 2, characterized in that the composition further containing in the range 0.008% or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP08753891A JP3240627B2 (en) | 1991-03-27 | 1991-03-27 | Manufacturing method of constant velocity joint parts |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP08753891A JP3240627B2 (en) | 1991-03-27 | 1991-03-27 | Manufacturing method of constant velocity joint parts |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04297552A JPH04297552A (en) | 1992-10-21 |
| JP3240627B2 true JP3240627B2 (en) | 2001-12-17 |
Family
ID=13917762
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP08753891A Expired - Fee Related JP3240627B2 (en) | 1991-03-27 | 1991-03-27 | Manufacturing method of constant velocity joint parts |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3240627B2 (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH11201168A (en) * | 1998-01-12 | 1999-07-27 | Nippon Seiko Kk | Rolling bearing |
| JP5071038B2 (en) * | 2007-10-22 | 2012-11-14 | 住友金属工業株式会社 | Steel for CVJ ball cage |
| WO2013065718A1 (en) * | 2011-11-01 | 2013-05-10 | 新日鐵住金株式会社 | Method for producing steel part |
| CN103421940B (en) * | 2013-09-05 | 2016-01-20 | 中原特钢股份有限公司 | A kind ofly a thermal cycling is utilized to carry out modified processing method to AISI4140 and AISI4340 structure iron forging |
| BR112017008578A2 (en) * | 2014-11-19 | 2017-12-26 | Nippon Steel & Sumitomo Metal Corp | laser welded joint, vehicle component, manufacturing method laser welded joint and vehicle component manufacturing method |
-
1991
- 1991-03-27 JP JP08753891A patent/JP3240627B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH04297552A (en) | 1992-10-21 |
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