JPH11222650A - Wear resistant alloy steel excellent in cold forgeability and its production - Google Patents
Wear resistant alloy steel excellent in cold forgeability and its productionInfo
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- JPH11222650A JPH11222650A JP3801898A JP3801898A JPH11222650A JP H11222650 A JPH11222650 A JP H11222650A JP 3801898 A JP3801898 A JP 3801898A JP 3801898 A JP3801898 A JP 3801898A JP H11222650 A JPH11222650 A JP H11222650A
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- alloy steel
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、冷間鍛造性に優れ
た耐摩耗合金鋼及びその製造方法に関する。The present invention relates to a wear-resistant alloy steel having excellent cold forgeability and a method for producing the same.
【０００２】[0002]
【従来の技術】従来、農耕用刃物などは、高速度鋼で形
成した薄板を複雑な形状に冷間鍛造することで成形して
いる。2. Description of the Related Art Conventionally, agricultural cutting tools and the like are formed by cold forging a thin plate formed of high-speed steel into a complicated shape.
【０００３】[0003]
【発明が解決しようとする課題】しかし、被加工材であ
る高速度鋼はその硬度が高いこと、特に溶製材の場合は
巨大炭化物を有する等の理由により成形しにくく、寸法
精度が出ない上、金型の寿命も短い。さらには、成形後
に熱処理を実施すると、焼入れ温度が高いため熱処理歪
みにより変形，変寸が起こり、仕上げ加工を必要とする
が、硬度が高いため仕上げ加工が困難である、といった
問題点があった。However, high-speed steel, which is a material to be processed, is difficult to form due to its high hardness, especially in the case of ingot material, because it has a large carbide, and the dimensional accuracy is not high. Also, the mold life is short. Furthermore, when heat treatment is performed after molding, deformation and size change occur due to heat treatment distortion due to high quenching temperature, and finishing is required. However, finishing is difficult due to high hardness, which is a problem. .
【０００４】[0004]
【課題を解決するための手段】本発明は、上記のような
従来の問題点を解決するために成されたもので、高速度
鋼並の耐摩耗性を有し、然も冷間鍛造性に優れた合金鋼
及びその製造方法を提供することを目的としたものであ
り、その要旨は、重量％で、Ｃ：０．５％以下、Ｓｉ：
０．５０％以下、Ｍｎ：０．５０％以下、Ｍｏ又はＷの
一種または二種をＷｅｑ＝２Ｍｏ＋ＷとしてＷｅｑ：１
０．０〜２４．０％、Ｖ：２．０〜１０．０％、残部が
Ｆｅと不可避の不純物からなることを特徴とする鋼で形
成した厚さ５ｍｍ以下の薄板もしくは径６ｍｍ以下の線
材であって、浸炭もしくは浸炭窒化後の表層部に形成し
た浸炭層もしくは浸炭窒化層中にＭＣおよびＭ6 Ｃ型炭
化物もしくはＭＣＮおよびＭ6 ＣＮ型炭窒化物を有して
おり、通常の熱処理もしくは浸炭焼入後のマトリックス
組織がマルテンサイトであることを特徴とする冷間鍛造
性に優れた耐摩耗合金鋼、及び重量％で、Ｃ：０．５％
以下、Ｓｉ：０．５０％以下、Ｍｎ：０．５０％以下、
Ｍｏ又はＷの一種または二種をＷｅｑ＝２Ｍｏ＋Ｗとし
てＷｅｑ：１０．０〜２４．０％、Ｖ：２．０〜１０．
０％、残部がＦｅと不可避の不純物からなることを特徴
とする鋼を冷間鍛造により加工して厚さ５ｍｍ以下の薄
板もしくは径６ｍｍ以下の線材に形成した後、浸炭もし
くは浸炭窒化法により処理し、該浸炭もしくは浸炭窒化
処理により表層部に形成した浸炭層もしくは浸炭窒化層
中にＭＣおよびＭ6 Ｃ型の炭化物もしくはＭＣＮおよび
Ｍ6 ＣＮ型の炭窒化物を析出せしめ、１０００〜１２５
０℃で焼入れすることによりマトリックス組織をマルテ
ンサイトに形成することを特徴とする冷間鍛造性に優れ
た耐摩耗合金鋼の製造方法にある。SUMMARY OF THE INVENTION The present invention has been made to solve the above-mentioned conventional problems, and has a wear resistance equivalent to that of high-speed steel, and has a cold forging property. It is an object of the present invention to provide an alloy steel excellent in the above and a method for producing the same.
0.50% or less, Mn: 0.50% or less, one or two types of Mo or W are set as Weq = 2Mo + W, and Weq: 1.
A thin plate having a thickness of 5 mm or less or a wire having a diameter of 6 mm or less formed of steel, characterized in that 0.0 to 24.0%, V: 2.0 to 10.0%, and the balance consists of Fe and inevitable impurities. And having MC and M 6 C-type carbide or MCN and M 6 CN-type carbonitride in the carburized layer or carbonitrided layer formed on the surface layer after carburizing or carbonitriding, and performing a normal heat treatment or Wear resistant alloy steel excellent in cold forgeability, characterized in that the matrix structure after carburizing and quenching is martensite, and C: 0.5% by weight%
Hereinafter, Si: 0.50% or less, Mn: 0.50% or less,
One or two types of Mo or W are defined as Weq = 2Mo + W, and Weq: 10.0 to 24.0%, and V: 2.0 to 10.
0%, the balance consisting of Fe and unavoidable impurities is processed by cold forging to form a thin plate having a thickness of 5 mm or less or a wire having a diameter of 6 mm or less, and then treated by carburizing or carbonitriding. Then, MC and M 6 C-type carbides or MCN and M 6 CN-type carbonitrides are precipitated in the carburized layer or carbonitrided layer formed on the surface layer by the carburizing or carbonitriding treatment, and 1000 to 125
A method for producing a wear-resistant alloy steel excellent in cold forgeability, characterized in that a matrix structure is formed in martensite by quenching at 0 ° C.
【０００５】[0005]
【発明の実施の形態】以下、本発明を実施例により詳細
に説明するに、本発明に係る合金鋼は、Ｃの少ない組成
からなり、通常の手段で成形した後、浸炭によって硬質
の炭化物を析出させることで高速度鋼並の耐摩耗性を有
するものである。Ｃの少ない組成の合金鋼は成型時には
硬度が低く、粗大炭化物も存在しないことから冷間鍛造
性に優れ、厳しい加工精度が要求される部材に最適であ
るとゝもに、冷間鍛造金型の寿命延長に寄与することが
できる。また、成形，浸炭後の熱処理を低温で実施でき
ることから、熱処理歪みを軽減することが可能である。BEST MODE FOR CARRYING OUT THE INVENTION Hereinafter, the present invention will be described in more detail with reference to Examples. The alloy steel according to the present invention has a composition with a low content of C. By precipitating it, it has the same abrasion resistance as high-speed steel. Alloy steel with a low C composition has low hardness at the time of molding and does not contain coarse carbides, so it has excellent cold forgeability and is ideal for members requiring strict processing accuracy. Can be extended. Further, heat treatment after forming and carburizing can be performed at a low temperature, so that heat treatment distortion can be reduced.
【０００６】すなわち、本発明は、Ｃの少ない後述する
組成の合金鋼を通常の手段で、径６ｍｍ以下の線材もし
くは厚さ５ｍｍ以下の薄板まで加工し、冷間鍛造により
所望の製造形状に鍛造する。この場合、鋼中のＣが少な
いことからマトリックスの延性が高く、破断の起点とな
る巨大炭化物の生成もないため加工性に優れており、冷
間鍛造により成形される部材に最適である。That is, according to the present invention, an alloy steel having a composition described below, which has a low C content, is processed into a wire having a diameter of 6 mm or less or a thin plate having a thickness of 5 mm or less by ordinary means, and is forged into a desired shape by cold forging. I do. In this case, since the C in the steel is small, the matrix has high ductility, and there is no generation of a giant carbide serving as a starting point of fracture.
【０００７】冷間鍛造により所望の製造形状に鍛造した
後、浸炭もしくは浸炭窒化により外部からＣを付与する
ことで、内部まで微細で均一なＭＣおよびＭ6 Ｃ型炭化
物もしくはＭＣＮおよびＭ6 ＣＮ型炭窒化物を生成す
る。これらの浸炭および浸炭窒化処理は、固体，液体，
ガス（浸炭性ガス雰囲気中で浸炭する真空浸炭，プラズ
マ浸炭等を含む）いずれの方法においても実施可能であ
るが、部材の表面性状を良好に保ち、仕上げ加工での研
磨代を少なく、且つコスト的にも安くするにはガス浸炭
が好ましい。本発明者らは、通常行われる肌焼鋼の浸炭
処理条件で、深い硬化層が得られる成分系を見出し、工
業上での製造を可能とした。[0007] After forging into a desired production shape by cold forging, and then adding C from the outside by carburizing or carbonitriding, MC and M 6 C type carbides or MCN and M 6 CN type fine and uniform to the inside. Produces carbonitride. These carburizing and carbonitriding processes are solid, liquid,
It can be carried out by any method (including vacuum carburizing, plasma carburizing, etc., carburizing in a carburizing gas atmosphere), but it maintains good surface properties of the member, reduces polishing allowance in finishing, and costs. Gas carburization is preferable to reduce the cost. The present inventors have found a component system capable of obtaining a deep hardened layer under the ordinary carburizing condition of case hardening steel, and have enabled industrial production.
【０００８】その後、通常の熱処理もしくは浸炭焼入れ
によってマトリックスがマルテンサイトを形成すること
により、線材もしくは薄板に高速度鋼並の硬さと特性を
付与する。この場合、１０００℃付近での焼入れで十分
な硬さを得ることが出来るため、熱処理歪みを低減する
ことが可能であるとゝもに、低温焼戻しが可能であるた
め、熱処理コストの低減を図ることも可能である。Thereafter, the matrix forms martensite by ordinary heat treatment or carburizing and quenching, thereby giving the wire or the thin plate the hardness and properties equivalent to high-speed steel. In this case, sufficient hardness can be obtained by quenching at around 1000 ° C., so that heat treatment distortion can be reduced, and low-temperature tempering can be performed, thereby reducing heat treatment costs. It is also possible.
【０００９】つぎに、合金鋼の成分について以下説明す
るに、Ｃの含有量は０．５％以下とする。浸炭温度下で
マトリックス組織がオーステナイトに変態すると、Ｃの
拡散が阻害されて内部まで浸炭されにくくなるため、Ｃ
は浸炭温度下でマトリックスがフェライトを形成する範
囲内でなければならない。さらに、Ｃを０．５％より多
く含有すると凝固過程で巨大な一次炭化物を生成し、マ
トリックス強度も高くなり冷間鍛造性を阻害するため、
上限を０．５％とする。Next, the components of the alloy steel will be described below. The content of C is set to 0.5% or less. When the matrix structure is transformed into austenite at the carburizing temperature, the diffusion of C is inhibited and the carburizing becomes difficult to reach the inside.
Must be within the range where the matrix forms ferrite at the carburizing temperature. Furthermore, if C is contained in an amount of more than 0.5%, a large primary carbide is generated in the solidification process, and the matrix strength is increased, which impairs cold forgeability.
The upper limit is set to 0.5%.
【００１０】また、Ｓｉの含有量は０．５０％以下とす
る。このＳｉは脱酸剤をして使用するが、少な過ぎると
製造上精錬が困難となる。しかしながら、多量に入れ過
ぎると靭性を低下するため、工業上０．５％以下とす
る。そして、Ｍｎの含有量も０．５０％以下とする。Ｍ
ｎもまた、脱酸，脱硫剤として添加するのであるが、多
量に入れ過ぎると靭性が低下するため、０．５％以下と
する。[0010] The content of Si is set to 0.50% or less. This Si is used as a deoxidizing agent, but if it is too small, refining becomes difficult in production. However, if added in a large amount, the toughness is reduced. And the content of Mn is also set to 0.50% or less. M
n is also added as a deoxidizing and desulfurizing agent, but if added too much, the toughness is reduced, so that the content of n is set to 0.5% or less.
【００１１】２Ｍｏ＋Ｗの含有量は１０．０〜２４．０
％の範囲内とする。Ｍｏ及びＷは浸炭および浸炭窒化に
よりＭ6 Ｃ型もしくはＭ6 ＣＮ型の複炭化物，炭窒化物
を形成するとゝもに、二次硬化により熱処理硬さを高め
て耐摩耗性に寄与する。重量％でＭｏ１％はＷ２％と等
価であり、Ｗ当量（Ｗｅｑ＝２Ｍｏ＋Ｗ）として表され
る。Ｗｅｑは少なくとも１０．０％以上添加させる必要
があるが、高硬度を得るにはＷｅｑに比例して浸炭時の
Ｃ濃度を高くする必要があり、ガス浸炭やガス浸炭窒化
では高硬さが得にくくなるため、上限を２４％とする。[0011] The content of 2Mo + W is 10.0 to 24.0.
%. Mo and W form M 6 C-type or M 6 CN-type double carbides and carbonitrides by carburizing and carbonitriding, and also contribute to abrasion resistance by increasing heat treatment hardness by secondary hardening. Mo1% by weight is equivalent to W2% and is expressed as W equivalent (Weq = 2Mo + W). Weq must be added at least 10.0% or more, but in order to obtain high hardness, it is necessary to increase the C concentration during carburization in proportion to Weq, and high hardness is obtained by gas carburizing or gas carbonitriding. Therefore, the upper limit is set to 24%.
【００１２】更に、Ｖの含有量は２．０〜１０．０％の
範囲内とする。Ｖは浸炭および浸炭窒化により非常に硬
度の高いＭＣ型炭化物及びＭＣＮ型炭窒化物を形成する
とともに、二次硬化により熱処理硬さを高めて耐摩耗性
に寄与する。これらの硬化を得るには少なくとも２．０
％含有させる必要があるが、Ｖ量に比例してファライト
層が残存しやすくなるため浸炭時のＣ濃度を高くする必
要があり、ガス浸炭やガス浸炭窒化では高硬度が得にく
くなる上、生成する炭化物も粗大化しやすく靭性を阻害
するため、上限を１０．０％とする。Further, the content of V is in the range of 2.0 to 10.0%. V forms extremely hard MC-type carbide and MCN-type carbonitride by carburizing and carbonitriding, and also contributes to wear resistance by increasing heat treatment hardness by secondary hardening. To achieve these cures, at least 2.0
However, it is necessary to increase the C concentration at the time of carburizing because the fallite layer tends to remain in proportion to the amount of V, and it is difficult to obtain high hardness by gas carburizing or gas carbonitriding, and to form The upper limit is set to 10.0% because the carbides to be formed are also likely to be coarsened and impair the toughness.
【００１３】Ｃｒの含有量は２．０％以下とする。Ｃｒ
はＣと結合して複炭化物を形成し、耐摩耗性に寄与す
る。しかしながら、Ｃｒ量に比例して浸炭層の硬さが低
下し、多量に添加するとかえって耐摩耗性を低下させる
ため、上限を２％とする。またＣｏの含有量は０．１〜
５．０％の範囲内とする。Ｃｏはマトリックス硬さと耐
熱性の向上に寄与する。しかしながら、添加し過ぎると
靭性を阻害するため、上限を５．０％とする。The content of Cr is set to 2.0% or less. Cr
Combines with C to form a double carbide and contributes to wear resistance. However, the hardness of the carburized layer decreases in proportion to the amount of Cr, and when added in a large amount, the wear resistance is rather reduced. Therefore, the upper limit is set to 2%. The content of Co is 0.1 to
It is within the range of 5.0%. Co contributes to improvement of matrix hardness and heat resistance. However, if added too much, the toughness is impaired, so the upper limit is made 5.0%.
【００１４】そして、Ｔｉ，Ｎｂ，Ｚｒの各含有量は
０．０１〜０．１％の範囲内とする。これらの元素は浸
炭および浸炭窒化によりいずれもＭＣ，ＭＣＮ型の微細
な炭化物，炭窒化物を形成し、安定で成長しにくいため
結晶粒を微細化し、靭性の向上に寄与する。しかし、こ
れらは添加しすぎると金属間化合物を形成し、かえって
靭性を阻害するため上限を０．１％とする。The contents of Ti, Nb and Zr are each in the range of 0.01 to 0.1%. All of these elements form MC and MCN-type fine carbides and carbonitrides by carburizing and carbonitriding, and are stable and difficult to grow, so that crystal grains are refined and contribute to improvement in toughness. However, if these are added too much, they form intermetallic compounds, which rather impair toughness, so the upper limit is made 0.1%.
【００１５】[0015]
【実施例】表１に、本発明に係る素材鋼の代表例（Ｎ
Ｏ．１及びＮＯ．２）と比較鋼（ＮＯ．３）の化学成分
を示す。EXAMPLES Table 1 shows typical examples (N) of the raw steel according to the present invention.
O. 1 and NO. 2) and the chemical composition of comparative steel (NO. 3) are shown.
【００１６】[0016]
【表１】 [Table 1]
【００１７】これらＮＯ．１乃至ＮＯ．３の各成分鋼を
溶製，通常の手段で厚さ３ｍｍの薄板を製造し、外形５
０ｍｍ，内径２０ｍｍのリング形状に打ち抜き加工を実
施した。冷間鍛造金型が廃却になるまでのプッシュ数と
廃却要因を表２に示す。この表２から明らかなように、
本発明に係る素材鋼（ＮＯ．１及びＮＯ．２）は比較鋼
（ＮＯ．３）と比較して冷間鍛造性に優れ、また金型の
寿命を著しく向上させることが可能であることがわか
る。These NO. 1 to NO. 3 was melted, and a thin plate having a thickness of 3 mm was manufactured by ordinary means.
Punching was performed into a ring shape of 0 mm and an inner diameter of 20 mm. Table 2 shows the number of pushes until the cold forging die is discarded and the factors that cause it to be discarded. As is clear from Table 2,
The material steels (NO.1 and NO.2) according to the present invention are excellent in cold forgeability as compared with the comparative steel (NO.3), and can significantly improve the life of the mold. Recognize.
【００１８】[0018]
【表２】 [Table 2]
【００１９】次に、打ち抜き加工後の本発明鋼を、９４
０℃のＣポテンシャルＣｐ＝１．２の雰囲気中でガス浸
炭を実施、比較鋼とともに１０００℃で焼入れ、２００
℃で２回焼戻しを実施した。中心部及び表面における硬
さの測定結果を表３に示す。Next, the steel of the present invention after the punching process was
Gas carburizing was performed in an atmosphere of C potential Cp = 1.2 at 0 ° C., and quenched at 1000 ° C. with comparative steel.
Tempering was performed twice at ° C. Table 3 shows the measurement results of the hardness at the center and the surface.
【００２０】[0020]
【表３】 [Table 3]
【００２１】本発明鋼は、高速度鋼と比較して低温焼入
れ焼戻しで十分な硬さが得られることがわかる。さら
に、６５ＨＲＣを満足する条件で本発明鋼と比較鋼を夫
々熱処理し、変寸率を測定した。それぞれの熱処理条件
と結果を表４に示す。この表４によって明らかなよう
に、本発明鋼は低温での焼入れが可能であるため、熱処
理歪みが小さいことがわかる。It can be seen that the steel of the present invention can obtain sufficient hardness by low-temperature quenching and tempering as compared with high-speed steel. Further, the steel of the present invention and the comparative steel were each heat-treated under the conditions satisfying 65HRC, and the dimensional change was measured. Table 4 shows the respective heat treatment conditions and results. As is clear from Table 4, since the steel of the present invention can be hardened at a low temperature, the distortion of the heat treatment is small.
【００２２】[0022]
【表４】 [Table 4]
【００２３】[0023]
【発明の効果】本発明は、上記のように、Ｃの少ない合
金鋼を用いることにより、成形時には硬度が低く、粗大
炭化物も存在しないことから冷間鍛造性に優れており、
加工精度の要求が厳しい部材の金属材料として最適であ
り、低コストで高速度鋼と同等以上の性能を有する冷間
鍛造部材の製造が可能である。また、本発明鋼はその成
分の適正化により、通常のガス浸炭，浸炭窒化の条件に
より素材内部まで均一に効果層を得ることができ、工業
上での製造が容易であるとゝもに、低温での焼入れ焼戻
しが可能なため、熱処理歪みを小さくし、熱処理コスト
を低減できる、といった諸効果がある。According to the present invention, as described above, the use of an alloy steel with a small amount of C has a low hardness at the time of forming, and is excellent in cold forgeability because there is no coarse carbide.
It is most suitable as a metal material for members requiring strict processing accuracy, and it is possible to manufacture a cold forged member having performance equal to or higher than that of high-speed steel at low cost. In addition, the steel of the present invention can obtain an effective layer even to the inside of the material under ordinary gas carburizing and carbonitriding conditions by optimizing its components, and it is easy to manufacture industrially. Since quenching and tempering can be performed at a low temperature, there are various effects such as a reduction in heat treatment distortion and a reduction in heat treatment cost.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 ＦＩ Ｃ２３Ｃ 8/22 Ｃ２３Ｃ 8/22 8/30 8/30 (72)発明者 中村 活也 富山県新湊市八幡町３丁目10番15号 日本 高周波鋼業株式会社富山製造所内 (72)発明者 西沢 泰二 宮城県仙台市青葉区太白区茂ケ崎１−１− 65 (72)発明者 石田 清仁 宮城県仙台市青葉区上杉３−５−20──────────────────────────────────────────────────続 き Continuation of the front page (51) Int.Cl. 6 Identification code FI C23C 8/22 C23C 8/22 8/30 8/30 (72) Inventor Akiya Nakamura 3-chome, Yawatacho, Shinminato-shi, Toyama Prefecture No. 15 Japan High Frequency Steel Industry Co., Ltd. Toyama Works (72) Inventor Taiji Nishizawa 1-1-65 Mogasaki, Taishiro-ku, Aoba-ku, Sendai-shi, Miyagi Prefecture (72) Inventor Kiyohito Ishida 3 Uesugi, Aoba-ku, Sendai-shi, Miyagi -5-20
Claims (10)
０．５０％以下、Ｍｎ：０．５０％以下、Ｍｏ又はＷの
一種または二種をＷｅｑ＝２Ｍｏ＋ＷとしてＷｅｑ：１
０．０〜２４．０％、Ｖ：２．０〜１０．０％、残部が
Ｆｅと不可避の不純物からなることを特徴とする鋼で形
成した厚さ５ｍｍ以下の薄板もしくは径６ｍｍ以下の線
材であって、浸炭後の表層部に形成した浸炭層中にＭＣ
およびＭ6 Ｃ型炭化物を有しており、通常の熱処理もし
くは浸炭焼入後のマトリックス組織がマルテンサイトで
あることを特徴とする冷間鍛造性に優れた耐摩耗合金
鋼。C .: 0.5% by weight or less, Si:
0.50% or less, Mn: 0.50% or less, one or two types of Mo or W are set as Weq = 2Mo + W, and Weq: 1.
A thin plate having a thickness of 5 mm or less or a wire having a diameter of 6 mm or less formed of steel, characterized in that 0.0 to 24.0%, V: 2.0 to 10.0%, and the balance consists of Fe and inevitable impurities. In the carburized layer formed on the surface layer after carburization, MC
And M 6 has a C-type carbide wear alloy steel matrix tissue of a normal heat treatment or carburizing after turning and excellent cold forgeability, which is a martensitic.
ｏ：０．１〜５．０％のうちの一種又は二種と置換した
組成としたことを特徴とする請求項１記載の冷間鍛造性
に優れた耐摩耗合金鋼。2. A method according to claim 1, wherein part of Fe is Cr: 2.0% or less,
2. A wear-resistant alloy steel having excellent cold forgeability according to claim 1, wherein the composition is replaced by one or two of o: 0.1 to 5.0%.
％、Ｎｂ：０．０１〜０．１％、Ｚｒ：０．０１〜０．
１％のうちの一種又は二種以上と置換した組成としたこ
とを特徴とする請求項１記載の冷間鍛造性に優れた耐摩
耗合金鋼。3. A method according to claim 1, wherein part of Fe is Ti: 0.01 to 0.1.
%, Nb: 0.01-0.1%, Zr: 0.01-0.
2. A wear-resistant alloy steel having excellent cold forgeability according to claim 1, wherein the composition is replaced by one or more of 1%.
ｏ：０．１〜５．０％の一種又は二種、及びＴｉ：０．
０１〜０．１％、Ｎｂ：０．０１〜０．１％、Ｚｒ：
０．０１〜０．１％のうちの一種又は二種以上と置換し
た組成としたことを特徴とする請求項１記載の冷間鍛造
性に優れた耐摩耗合金鋼。4. A method according to claim 1, wherein part of Fe is Cr: 2.0% or less,
o: One or two kinds of 0.1 to 5.0%, and Ti: 0.
01-0.1%, Nb: 0.01-0.1%, Zr:
2. A wear-resistant alloy steel having excellent cold forgeability according to claim 1, wherein the composition is replaced by one or more of 0.01 to 0.1%.
０．５０％以下、Ｍｎ：０．５０％以下、Ｍｏ又はＷの
一種または二種をＷｅｑ＝２Ｍｏ＋ＷとしてＷｅｑ：１
０．０〜２４．０％、Ｖ：２．０〜１０．０％、残部が
Ｆｅと不可避の不純物からなることを特徴とする鋼で形
成した厚さ５ｍｍ以下の薄板もしくは径６ｍｍ以下の線
材であって、浸炭窒化後の表層部に形成した浸炭窒化層
中にＭＣＮおよびＭ6 ＣＮ型炭窒化物を有しており、通
常の熱処理もしくは浸炭焼入後のマトリックス組織がマ
ルテンサイトであることを特徴とする冷間鍛造性に優れ
た耐摩耗合金鋼。5. The method according to claim 1, wherein C: 0.5% or less, Si:
0.50% or less, Mn: 0.50% or less, one or two types of Mo or W are set as Weq = 2Mo + W, and Weq: 1.
A thin plate having a thickness of 5 mm or less or a wire having a diameter of 6 mm or less formed of steel, characterized in that 0.0 to 24.0%, V: 2.0 to 10.0%, and the balance consists of Fe and inevitable impurities. Wherein the carbonitrided layer formed on the surface layer after carbonitriding contains MCN and M 6 CN type carbonitride, and the matrix structure after normal heat treatment or carburizing and quenching is martensite. A wear-resistant alloy steel with excellent cold forgeability characterized by the following characteristics.
ｏ：０．１〜５．０％一種又は二種と置換した組成とし
たことを特徴とする請求項５記載の冷間鍛造性に優れた
耐摩耗合金鋼。6. A method according to claim 1, wherein a part of Fe is Cr: 2.0% or less,
6. The wear-resistant alloy steel having excellent cold forgeability according to claim 5, wherein the composition is a composition in which o: 0.1 to 5.0% is substituted with one or two kinds.
％、Ｎｂ：０．０１〜０．１％、Ｚｒ：０．０１〜０．
１％のうちの一種又は二種以上と置換した組成としたこ
とを特徴とする請求項５記載の冷間鍛造性に優れた耐摩
耗合金鋼。7. A part of Fe, Ti: 0.01 to 0.1.
%, Nb: 0.01-0.1%, Zr: 0.01-0.
6. A wear-resistant alloy steel having excellent cold forgeability according to claim 5, wherein the composition is replaced by one or more of 1%.
ｏ：０．１〜５．０％一種又は二種、及びＴｉ：０．０
１〜０．１％、Ｎｂ：０．０１〜０．１％、Ｚｒ：０．
０１〜０．１％のうちの一種又は二種以上と置換した組
成としたことを特徴とする請求項５記載の冷間鍛造性に
優れた耐摩耗合金鋼。8. A method according to claim 8, wherein part of Fe is Cr: 2.0% or less,
o: 0.1 to 5.0% one or two kinds, and Ti: 0.0
1-0.1%, Nb: 0.01-0.1%, Zr: 0.
The wear-resistant alloy steel excellent in cold forgeability according to claim 5, wherein the composition is one or two or more of 01 to 0.1%.
間鍛造により加工して厚さ５ｍｍ以下の薄板もしくは径
６ｍｍ以下の線材に形成した後、浸炭法により処理し、
該浸炭処理により表層部に形成した浸炭層中にＭＣおよ
びＭ6 Ｃ型の炭化物を析出せしめ、１０００〜１２５０
℃で焼入れすることによりマトリックス組織をマルテン
サイトに形成することを特徴とする冷間鍛造性に優れた
耐摩耗合金鋼の製造方法。9. The steel according to any one of claims 1 to 4, which is formed by cold forging into a thin plate having a thickness of 5 mm or less or a wire having a diameter of 6 mm or less, and then treated by a carburizing method.
MC and M 6 C-type carbides were precipitated in the carburized layer formed on the surface layer by the carburizing treatment, and 1000 to 1250
A method for producing a wear-resistant alloy steel excellent in cold forgeability, characterized in that a matrix structure is formed in martensite by quenching at a temperature of ° C.
冷間鍛造により加工して厚さ５ｍｍ以下の薄板もしくは
径６ｍｍ以下の線材に形成した後、浸炭窒化法により処
理し、該浸炭窒化処理により表層部に形成した浸炭窒化
層中にＭＣＮおよびＭ6 ＣＮ型の炭窒化物を析出せし
め、１０００〜１２５０℃で焼入れすることによりマト
リックス組織をマルテンサイトに形成することを特徴と
する冷間鍛造性に優れた耐摩耗合金鋼の製造方法。10. The steel according to claim 5, which is processed by cold forging to form a thin plate having a thickness of 5 mm or less or a wire rod having a diameter of 6 mm or less, and then the carbon steel is treated by carbonitriding. MCN and M 6 CN type carbonitrides are precipitated in the carbonitrided layer formed on the surface by carbonitriding, and the matrix structure is formed on martensite by quenching at 1000 to 1250 ° C. Manufacturing method of wear-resistant alloy steel with excellent cold forgeability.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3801898A JPH11222650A (en) | 1998-02-04 | 1998-02-04 | Wear resistant alloy steel excellent in cold forgeability and its production |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3801898A JPH11222650A (en) | 1998-02-04 | 1998-02-04 | Wear resistant alloy steel excellent in cold forgeability and its production |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH11222650A true JPH11222650A (en) | 1999-08-17 |
Family
ID=12513845
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3801898A Pending JPH11222650A (en) | 1998-02-04 | 1998-02-04 | Wear resistant alloy steel excellent in cold forgeability and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH11222650A (en) |
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