JP3353698B2 - Method of manufacturing steel for nitrocarburizing and nitrocarburized parts using the steel - Google Patents

Method of manufacturing steel for nitrocarburizing and nitrocarburized parts using the steel

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Publication number
JP3353698B2
JP3353698B2 JP11538898A JP11538898A JP3353698B2 JP 3353698 B2 JP3353698 B2 JP 3353698B2 JP 11538898 A JP11538898 A JP 11538898A JP 11538898 A JP11538898 A JP 11538898A JP 3353698 B2 JP3353698 B2 JP 3353698B2
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Japan
Prior art keywords
steel
hardness
carbosulfide
nitrocarburizing
machinability
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Japanese (ja)
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JPH11302779A (en
Inventor
八寿男 黒川
芳彦 鎌田
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住友金属工業株式会社
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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、軟窒化用鋼材の製
造方法及びその鋼材を用いた軟窒化部品に関し、より詳
しくは耐疲労特性、耐摩耗性、耐ピッチング性や耐スポ
ーリング性に優れた軟窒化部品と、その軟窒化部品の素
材となる被削性に優れた軟窒化用鋼材の製造方法に関す
る。なお、本明細書では、繰り返し面圧の負荷により材
料表面が剥離する疲労現象のうち、剥離が比較的小さい
ものを「ピッチング」、剥離が比較的大きなものを「ス
ポーリング」と呼ぶ。
BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a steel material for nitrocarburizing and a nitrocarburized component using the steel material, and more particularly to a steel sheet having excellent fatigue resistance, wear resistance, pitting resistance and spalling resistance. The present invention relates to a nitrocarburized component and a method for producing a nitrocarburized steel material having excellent machinability, which is a material of the nitrocarburized component. In the present specification, among the fatigue phenomena in which the material surface peels off due to the repetitive surface pressure load, those with relatively small peeling are called "pitting", and those with relatively large peeling are called "spalling".
【0002】[0002]
【従来の技術】自動車や産業機械に使用される多くの部
品、例えば歯車や軸受などには、一般に大きな疲労強度
や耐摩耗性が要求される。そのため前記部品は、所謂
「表面硬化処理」を施して製造されてきた。
2. Description of the Related Art Many parts used in automobiles and industrial machines, such as gears and bearings, generally require large fatigue strength and wear resistance. Therefore, the components have been manufactured by performing a so-called “surface hardening treatment”.
【0003】表面硬化処理としては一般に、浸炭焼入
れ、高周波焼入れ、炎焼入れ、窒化や軟窒化などの処理
が知られている。このうち、浸炭焼入れ、高周波焼入れ
や炎焼入れといったオーステナイト状態の高温域から急
冷(焼入れ)して表面を硬化させる処理では、部品に大
きな焼入れ歪が生じてしまう。更に、場合によっては焼
入れした部品に焼割れが生ずることもある。
As the surface hardening treatment, generally, carburizing quenching, induction quenching, flame quenching, nitriding and nitrocarburizing are known. Of these, in the treatment of hardening the surface by rapid cooling (quenching) from a high temperature region in an austenitic state such as carburizing quenching, induction quenching, or flame quenching, large quenching distortion occurs in components. Further, in some cases, quenched cracks may occur in the quenched parts.
【0004】このため、所要部品に対して特に低歪であ
ることが要求される場合には、窒化や軟窒化処理が施さ
れている。
[0004] For this reason, when a required component is required to have a particularly low strain, nitriding or nitrocarburizing is performed.
【0005】しかし、一般の窒化処理は、アンモニアの
気流中で500〜550℃に20〜100時間加熱後徐
冷する所謂「ガス窒化」処理であるため生産性が低くコ
ストが嵩む。このため、窒化温度が550℃前後の液体
窒化法が開発されているが、この方法の場合にも窒化に
は12時間程度を要するので、必ずしも量産部品を低コ
ストで効率よく製造するのに適した方法とは言えない。
イオン窒化法によれば短時間で窒化が可能ではあるが、
温度測定が困難なことや、陰極となる被処理部品の配置
や形状、質量などによって温度や窒化層が不安定になっ
たりするので、この方法もやはり量産部品の製造に適し
ているとは言い難い。
However, the general nitriding treatment is a so-called "gas nitriding" treatment of heating at 500 to 550 ° C. for 20 to 100 hours in a stream of ammonia and then gradually cooling, resulting in low productivity and high cost. For this reason, a liquid nitriding method at a nitriding temperature of about 550 ° C. has been developed. However, even in this method, nitridation requires about 12 hours, so that it is not necessarily suitable for efficiently producing mass-produced parts at low cost. I can't say that.
According to the ion nitriding method, nitriding is possible in a short time,
This method is not suitable for the production of mass-produced parts because it is difficult to measure the temperature, and the temperature and nitrided layer become unstable depending on the arrangement, shape, and mass of the part to be treated as the cathode. hard.
【0006】一方、軟窒化処理は、570℃程度の温度
のシアン系化合物の塩浴、又はRXガス(RXガスは吸
熱型変成ガスの商標)にアンモニアを添加したガス中に
保持することにより、鋼材表面からN(窒素)とO(酸
素)を鋼中に侵入させて表層部を硬化させる方法で、短
時間処理が可能である。このうち前者のシアン系化合物
の塩浴を用いる方法は、廃液の処理にコストが嵩むた
め、後者のガスを用いる「ガス軟窒化法」が、低歪が要
求される量産品に適した表面硬化処理方法として重用さ
れている。
On the other hand, the nitrocarburizing treatment is carried out by keeping a salt bath of a cyanide compound at a temperature of about 570 ° C. or a gas obtained by adding ammonia to RX gas (RX gas is a trademark of endothermic modified gas). A method in which N (nitrogen) and O (oxygen) penetrate into the steel from the surface of the steel material to harden the surface layer portion enables short-time processing. Of these, the former method using a salt bath of a cyanide compound increases the cost of waste liquid treatment, so the latter gas nitrocarburizing method using gas is a surface hardening method suitable for mass-produced products requiring low distortion. It is heavily used as a processing method.
【0007】従来、軟窒化用鋼としては、例えば、JIS
G 4105に規定されているクロムモリブデン鋼鋼材(SC
M435など)やJIS G 4202のアルミニウムクロムモリ
ブデン鋼鋼材(SACM645)が多く使用されてき
た。
Conventionally, as steel for nitrocarburizing, for example, JIS
Chromium molybdenum steel (SC) specified in G 4105
M435) and aluminum chromium molybdenum steel of JIS G 4202 (SACM645) have been widely used.
【0008】しかし、SCM435を初めとするJIS
に規定されたクロムモリブデン鋼鋼材を素材鋼とした部
品の場合、軟窒化処理後の表面からビッカース硬度(H
v)500の位置までの距離(以下、「有効硬化深さ」
という)は0.05mm程度と小さい。更に、表面から
0.025mmの位置におけるマイクロビッカース硬度
(以下、「表面硬度」という)もHv600以上になら
ない場合が多い。このため、疲労強度や耐摩耗性の点で
充分に満足できるものではなかった。
However, JIS including SCM435
In the case of parts made of chromium molybdenum steel as specified in JIS, the Vickers hardness (H
v) Distance to the position of 500 (hereinafter, "effective hardening depth")
Is as small as about 0.05 mm. Furthermore, the micro Vickers hardness at a position 0.025 mm from the surface (hereinafter, referred to as “surface hardness”) often does not exceed Hv600. For this reason, it was not sufficiently satisfactory in terms of fatigue strength and wear resistance.
【0009】一方、上記の欠点を改良するためにSAC
M645には窒化特性向上元素であるAl及びCrが多
量に添加されている。しかし、SACM645を素材鋼
とした場合も、軟窒化処理によって表面硬度はHvで8
00〜1100と非常に高くなるものの、有効硬化深さ
は0.08mm程度と小さい。したがって、表面部から
芯部(以下、軟窒化処理後の表面硬化されていない部分
を「芯部」という)への硬度勾配が急激になりすぎる。
そのため、高負荷の下で運転される歯車や軸受などで
は、表面硬化部と芯部の境界付近から剥離現象が起きや
すく、耐ピッチング性あるいは耐スポーリング性が劣っ
ていた。更に、SACM645は溶製、鋳造、熱間加工
が比較的困難であるし、冷間加工性が悪く複雑な形状の
部品にはプレス成形が難しいという問題もあった。
On the other hand, in order to improve the above-mentioned disadvantage, SAC
M645 contains a large amount of Al and Cr which are nitriding property improving elements. However, even when SACM645 is used as the material steel, the surface hardness is 8 in Hv by the nitrocarburizing treatment.
Although it is very high as 00 to 1100, the effective hardening depth is as small as about 0.08 mm. Therefore, the hardness gradient from the surface portion to the core portion (hereinafter, the portion that is not surface-hardened after the nitrocarburizing treatment is referred to as “core portion”) is too sharp.
Therefore, in a gear or a bearing operated under a high load, a peeling phenomenon easily occurs near a boundary between a surface hardened portion and a core portion, and the pitting resistance or the spalling resistance is poor. Furthermore, SACM645 has problems that melting, casting, and hot working are relatively difficult, and that cold workability is poor and that parts having complicated shapes are difficult to press-form.
【0010】特開昭58−71357号公報には、JI
S規格鋼の問題点を解決した「軟窒化用鋼」が開示され
ている。この公報で提案された鋼を素材鋼として用いれ
ば、確かに疲労強度、耐摩耗性に優れると共に耐ピッチ
ング性、耐スポーリング性にも優れた軟窒化部品を得る
ことは可能である。しかし、Siなどの強化に有効な元
素の含有量を低減して冷間加工性を向上させた鋼である
ため、軟窒化によって表面部は硬化するものの、逆に芯
部は軟窒化時の加熱で軟化するので、軟窒化後に芯部硬
度が低くなりすぎて疲労特性が劣化する場合もあった。
JP-A-58-71357 discloses JI
"Steel for nitrocarburizing" which solves the problem of S-standard steel is disclosed. If the steel proposed in this publication is used as a material steel, it is possible to obtain a nitrocarburized part having excellent fatigue strength and wear resistance, and also excellent pitting resistance and spalling resistance. However, since the steel is improved in cold workability by reducing the content of elements effective for strengthening such as Si, the surface is hardened by nitrocarburizing, whereas the core is heated during nitrocarburizing. , The core hardness becomes too low after nitrocarburizing, and the fatigue properties are sometimes deteriorated.
【0011】更に、JIS規格鋼であるSCM435な
どのクロムモリブデン鋼やアルミニウムクロムモリブデ
ン鋼のSACM645及び上記の特開昭58−7135
7号公報で提案された鋼の場合には被削性が劣るため、
これを熱間鍛造や冷間鍛造した後に所望の軟窒化部品の
形状に成形するための切削加工のコストが嵩んでしま
う。このため、切削加工を容易にし、低コスト化を図る
ために被削性に優れた軟窒化用鋼材に対する要求がます
ます大きくなっている。
Further, chromium molybdenum steel such as SCM435 which is JIS standard steel, SACM645 of aluminum chromium molybdenum steel and the above-mentioned Japanese Patent Application Laid-Open No. 58-7135.
In the case of steel proposed in Japanese Patent Publication No. 7, the machinability is inferior.
After this is subjected to hot forging or cold forging, the cost of cutting for forming into a desired nitrocarburized component shape increases. For this reason, there is an increasing demand for a nitrocarburizing steel material having excellent machinability in order to facilitate cutting and reduce costs.
【0012】従来、被削性を高めるために、鋼にPb、
Te、Bi、Ca及びSなどの快削元素を単独あるいは
複合添加することが行われてきた。しかし、前記したJ
IS規格鋼や特開昭58−71357号公報で提案され
た鋼に、単に上記の快削元素を添加しただけの場合に
は、所望の機械的性質、なかでも疲労強度を確保できな
いことが多い。
Conventionally, in order to enhance machinability, Pb,
Free-cutting elements such as Te, Bi, Ca and S have been used alone or in combination. However, J
When simply adding the above-mentioned free-cutting elements to IS standard steel or steel proposed in Japanese Patent Application Laid-Open No. 58-71357, it is often impossible to secure desired mechanical properties, especially fatigue strength. .
【0013】鉄と鋼(vol.57(1971年)S4
84)には、脱酸調整快削鋼にTiを添加すれば被削性
が高まる場合のあることが報告されている。しかし、T
iの多量の添加はTiNが多量に生成されることもあっ
て工具摩耗を増大させ、被削性の点からは好ましくない
ことも述べられている。例えば、C:0.45%、S
i:0.29%、Mn:0.78%、P:0.017
%、S:0.041%、Al:0.006%、N:0.
0087%、Ti:0.228%、O:0.004%及
びCa:0.001%を含有する鋼では却ってドリル寿
命が低下して被削性が劣っている。このように、鋼に単
にTiを添加するだけでは被削性は向上するものではな
い。
Iron and steel (vol. 57 (1971) S4)
84) reports that the addition of Ti to deoxidized adjusted free-cutting steel may enhance machinability. But T
It is also described that the addition of a large amount of i increases tool wear due to generation of a large amount of TiN, and is undesirable from the viewpoint of machinability. For example, C: 0.45%, S
i: 0.29%, Mn: 0.78%, P: 0.017
%, S: 0.041%, Al: 0.006%, N: 0.
Steel containing 0087%, Ti: 0.228%, O: 0.004%, and Ca: 0.001%, on the contrary, has a short drill life and poor machinability. Thus, the machinability is not improved simply by adding Ti to steel.
【0014】又、硫黄快削鋼の硫化物形態制御の目的で
Zrが添加されることがあるが、例えば、鉄と鋼(vo
l.62(1976年)p.885)に記されているよ
うに、Zrは被削性に対してはほとんど影響を及ぼさな
い。つまり、鋼に単にZrを添加するだけでは被削性は
向上するものではない。
In some cases, Zr is added for the purpose of controlling the sulfide form of the sulfur free-cutting steel.
l. 62 (1976) p. 885), Zr has little effect on machinability. That is, the machinability is not improved simply by adding Zr to steel.
【0015】[0015]
【発明が解決しようとする課題】本発明は、上記現状に
鑑みなされたもので、被削性と冷間加工性に優れた鋼を
素材とし、冷間加工後に軟窒化処理するだけで優れた疲
労特性、耐摩耗性、耐ピッチング性や耐スポーリング性
を呈する軟窒化部品を提供することを課題とする。更
に、本発明は、上記軟窒化部品の素材となる被削性に優
れた軟窒化用鋼材の製造方法を提供することも課題とす
る。
DISCLOSURE OF THE INVENTION The present invention has been made in view of the above-mentioned circumstances, and is excellent in that it is made of a steel excellent in machinability and cold workability, and is subjected to nitrocarburizing after cold working. An object of the present invention is to provide a nitrocarburized component exhibiting fatigue characteristics, wear resistance, pitting resistance and spalling resistance. Still another object of the present invention is to provide a method for producing a steel material for nitrocarburizing which is excellent in machinability and is used as a material for the nitrocarburized component.
【0016】[0016]
【課題を解決するための手段】本発明の要旨は、下記
(1)及び(2)に示す軟窒化用鋼材の製造方法、並び
に、(3)に示すその鋼材を用いた軟窒化部品にある。
Gist of the present invention SUMMARY OF THE INVENTION The method of producing soft-nitriding steel material shown in the following (1) and (2), the arrangement
Secondly, there is a nitrocarburized component using the steel material shown in (3) .
【0017】(1)重量%で、C:0.15〜0.45
%、Si:0.05〜0.5%、Mn:0.2〜2.5
%、S:0.002〜0.2%、Cu:0.5〜1.5
%、Ni:0.25〜0.75%で、且つ1.8≦Cu
(%)/Ni(%)≦2.2、Cr:0.5〜2%、
V:0.05〜0.5%、Ti:0〜1.0%、Zr:
0〜1.0%で、且つTi(%)+Zr(%):0.0
4〜1.0%、Al:0.01〜0.3%、N:0.0
08%以下、Mo:0.02〜0.3%及びW:0.0
〜0.5%のうちの1種以上を含み、下記式で表さ
れるfn1が0%を超え、残部はFe及び不可避不純物
の化学組成で、更に鋼中のTi炭硫化物及びZr炭硫化
物の最大直径が10μm以下で、且つ、その量の和が清
浄度で0.05%以上である鋼を、熱間加工後に球状化
焼鈍して硬度をHv180以下とし、次いで冷間加工し
て硬度をHv250以上にすることを特徴とする被削性
に優れた軟窒化用鋼材の製造方法。fn1=Ti(%)
+Zr(%)−1.2S(%)・・・・。
(1) In weight%, C: 0.15 to 0.45
%, Si: 0.05 to 0.5%, Mn: 0.2 to 2.5
%, S: 0.002 to 0.2%, Cu: 0.5 to 1.5
%, Ni: 0.25 to 0.75%, and 1.8 ≦ Cu
(%) / Ni (%) ≦ 2.2, Cr: 0.5 to 2%,
V: 0.05 to 0.5%, Ti: 0 to 1.0 %, Zr:
0 to 1.0 % , and Ti (%) + Zr (%): 0.0
4 to 1.0%, Al: 0.01 to 0.3%, N: 0.0
08% or less, Mo: 0.02 to 0.3% and W: 0.0
5 to 0.5% , fn1 represented by the following formula exceeds 0%, the balance is the chemical composition of Fe and unavoidable impurities, and further, Ti carbosulfide and Zr carbon in steel. A steel having a maximum diameter of sulfide of 10 μm or less and the sum of the amounts is 0.05% or more in cleanliness is subjected to spheroidizing annealing after hot working to a hardness of Hv 180 or less, and then to cold working. A method for producing a steel material for nitrocarburizing excellent in machinability, wherein the hardness is Hv 250 or more. fn1 = Ti (%)
+ Zr (%)-1.2S (%) ...
【0018】 2)重量%で、C:0.15〜0.45%、Si:
0.05〜0.5%、Mn:0.2〜2.5%、S:
0.002〜0.2%、Cu:0.5〜1.5%、N
i:0.25〜0.75%で、且つ1.8≦Cu(%)
/Ni(%)≦2.2、Cr:0.5〜2%、V:0.
05〜0.5%、Ti:0〜1.0%、Zr:0〜1.
0%で、且つTi(%)+Zr(%):0.04〜1.
0%、Al:0.01〜0.3%、N:0.008%以
下、Mo:0.02〜0.3%及びW:0.05〜0.
5%のうちの1種以上、並びに、Pb:0.03〜0.
35%及びCa:0.001〜0.01%のうちの1種
以上を含み、下記式で表されるfn1が0%を超え、
残部はFe及び不可避不純物の化学組成で、更に鋼中の
Ti炭硫化物及びZr炭硫化物の最大直径が10μm以
下で、且つ、その量の和が清浄度で0.05%以上であ
る鋼を、熱間加工後に球状化焼鈍して硬度をHv180
以下とし、次いで冷間加工して硬度をHv250以上に
することを特徴とする被削性に優れた軟窒化用鋼材の製
造方法。fn1=Ti(%)+Zr(%)−1.2S
(%)・・・・。 (3)上記(1)又は(2)に記載の化学組成、上記
(1)又は(2)に記載の大きさ及び量のTi炭硫化物
とZr炭硫化物、並びに球状化組織を備え、表面硬度が
Hv600以上、且つ、有効硬化深さが0.1mm以
上、芯部硬度がHv250以上であることを特徴とする
軟窒化部品。
( 2) C: 0.15 to 0.45% by weight, Si:
0.05-0.5%, Mn: 0.2-2.5%, S:
0.002-0.2%, Cu: 0.5-1.5%, N
i: 0.25 to 0.75%, and 1.8 ≦ Cu (%)
/Ni(%)≦2.2, Cr: 0.5-2%, V: 0.
05 to 0.5%, Ti: 0 to 1.0%, Zr: 0 to 1.
0% and Ti (%) + Zr (%): 0.04 to 1.
0%, Al: 0.01-0.3%, N: 0.008% or less
Below, Mo: 0.02-0.3% and W: 0.05-0.
At least one of 5% and Pb: 0.03 to 0.
35% and Ca: one of 0.001 to 0.01%
Including the above, fn1 represented by the following equation exceeds 0%,
The balance is the chemical composition of Fe and unavoidable impurities.
The maximum diameter of Ti and Zr carbosulfides is 10 μm or less
And the sum of the amounts is 0.05% or more in cleanliness.
Steel is subjected to spheroidizing annealing after hot working to have a hardness of Hv180.
And then cold worked to a hardness of Hv250 or more
Of steel for nitrocarburizing with excellent machinability
Construction method. fn1 = Ti (%) + Zr (%)-1.2S
(%) (3) The chemical composition according to (1) or (2) above,
Ti carbosulfide of the size and amount according to (1) or (2)
And Zr carbosulfide, as well as spheroidized structure, surface hardness
Hv600 or more and effective curing depth is 0.1mm or less
The core hardness is not less than Hv250.
Soft nitriding parts.
【0019】なお、本発明でいう「Ti炭硫化物」には
単なるTi硫化物を、又、「Zr炭硫化物」には単なる
Zr硫化物をそれぞれ含むものとする。又、「(Ti及
びZrの炭硫化物の)最大直径」とは「個々のTi及び
Zrの炭硫化物における最も長い径」のことを指す。T
i炭硫化物の清浄度やZr炭硫化物の清浄度は、光学顕
微鏡の倍率を400倍として、JIS G 0555に規定された
「鋼の非金属介在物の顕微鏡試験方法」によって60視
野測定した値をいう。
In the present invention, "Ti carbosulfide" includes simple Ti sulfide, and "Zr carbosulfide" includes simple Zr sulfide. Also, the "maximum diameter (of Ti and Zr carbosulfides)" refers to "the longest diameter of individual Ti and Zr carbosulfides." T
i The cleanliness of carbosulfides and Zr carbosulfides were measured in 60 fields of view using the “microscope test method for nonmetallic inclusions in steel” specified in JIS G 0555, with the magnification of an optical microscope set to 400 times. Value.
【0020】以下において、上記(1)、(2)に記載
製造方法、(3)に記載の部品をそれぞれ(1)の発
明、(2)の発明及び(3)の発明という。
Hereinafter, the manufacturing method described in the above (1) and (2), and the component described in the above (3) are referred to as the invention (1), the invention (2) and the invention (3), respectively .
【0021】本発明者らは、軟窒化部品の素材となる鋼
材の化学組成、各製造工程における適正なミクロ組織や
機械的性質に関して調査・研究を行った。その結果、次
の知見を得るに到った。
The present inventors have investigated and studied the chemical composition of the steel material used as the material for the nitrocarburized parts, the appropriate microstructure and the mechanical properties in each manufacturing process. As a result, the following findings were obtained.
【0022】(a)軟窒化部品の耐疲労特性や耐ピッチ
ング性を向上させるには、いずれも表面硬度と有効硬化
深さを大きくすれば良い。又、耐摩耗性を向上させるに
は、表面硬度を大きくすれば良い。一方、耐スポーリン
グ性を向上させるには、有効硬化深さを大きくすれば良
い。
(A) In order to improve the fatigue resistance and pitting resistance of the nitrocarburized parts, the surface hardness and the effective hardening depth may be increased. In order to improve the wear resistance, the surface hardness may be increased. On the other hand, in order to improve the spalling resistance, the effective hardening depth may be increased.
【0023】(b)軟窒化処理を施し、表面硬度をHv
600以上、有効硬化深さを0.1mm以上とすれば、
軟窒化部品の耐疲労特性、耐摩耗性、耐ピッチング性及
び耐スポーリング性を著しく高めることができる。
(B) A nitrocarburizing treatment is performed to make the surface hardness Hv
600 or more, if the effective curing depth is 0.1 mm or more,
The fatigue resistance, wear resistance, pitting resistance, and spalling resistance of the nitrocarburized component can be significantly improved.
【0024】(c)軟窒化後の芯部硬度がHv250以
上であれば、例えば、自動車のミッションギアのように
高い負荷が加わる部品においても、部品内部を起点とし
て曲げ疲労が生ずることはない。
(C) If the core hardness after nitrocarburizing is Hv250 or more, bending fatigue does not occur from the inside of the component as a starting point even in a component to which a high load is applied such as a transmission gear of an automobile.
【0025】(d)鋼材を球状化焼鈍して硬度をHv1
80以下に低下させれば、冷間加工性が向上して金型寿
命を大幅に改善できる。
(D) A steel material is subjected to spheroidizing annealing to have a hardness of Hv1.
If it is reduced to 80 or less, the cold workability is improved and the mold life can be greatly improved.
【0026】(e)適正量のCuとNiとを含有する鋼
材を球状化焼鈍して硬度をHv180以下にし、冷間鍛
造による加工硬化で硬度をHv250以上に上昇させれ
ば、次に軟窒化処理を施しても、軟窒化時の加熱で軟化
して芯部硬度が低下することはない。すなわち、芯部硬
度を軟窒化前の値に維持、あるいは更に高めることがで
きる。このため、軟窒化部品にはHv250以上の高い
芯部硬度が安定して確保できるので、耐疲労特性、なか
でも耐曲げ疲労特性が大きく向上する。
(E) A steel material containing appropriate amounts of Cu and Ni is subjected to spheroidizing annealing to reduce the hardness to Hv 180 or less, and if the hardness is increased to Hv 250 or more by work hardening by cold forging, then nitrocarburizing is performed. Even when the treatment is performed, the core is not softened by heating during nitrocarburizing and the hardness of the core does not decrease. That is, the core hardness can be maintained at the value before soft nitriding or further increased. For this reason, since a high core hardness of Hv250 or more can be stably secured in the nitrocarburized component, fatigue resistance, especially bending fatigue resistance, is greatly improved.
【0027】なお、特に断らない限り、軟窒化する前の
状態(例えば球状化焼鈍後、冷間加工後)の硬度とは、
軟窒化後の芯部に相当する部分(例えば「中心部」)の
硬度のことをいう。
Unless otherwise specified, the hardness before nitrocarburizing (for example, after spheroidizing annealing and after cold working) means
It refers to the hardness of a portion (for example, “center”) corresponding to the core after soft nitriding.
【0028】(f)上記の(a)〜(e)から、優れた
冷間加工性を有する鋼を素材鋼とし、これに冷間加工を
施して加工硬化により充分な硬度を確保し、次に軟窒化
して硬く深い窒化層を形成させるが、この軟窒化のため
の加熱で前記の加工硬化による硬度(すなわち芯部硬
度)を維持あるいは更に上昇できれば、軟窒化部品に大
きな耐疲労特性、耐摩耗性、耐ピッチング性及び耐スポ
ーリング性を付与できる。
(F) From the above (a) to (e), steel having excellent cold workability is used as a material steel, which is subjected to cold working to secure sufficient hardness by work hardening. To form a hard and deep nitrided layer. If the hardness for the work hardening (that is, the core hardness) can be maintained or further increased by heating for this soft nitriding, large fatigue resistance characteristics of the nitrocarburized component can be obtained. Abrasion resistance, pitting resistance and spalling resistance can be imparted.
【0029】(g)鋼にTiとZrの少なくともいずれ
かを添加し、鋼中の介在物制御として硫化物をTi炭硫
化物やZr炭硫化物に変え、こうした炭硫化物を微細に
分散させれば、鋼材の被削性が飛躍的に向上する。
(G) At least one of Ti and Zr is added to steel, and sulfides are changed to Ti carbosulfides or Zr carbosulfides to control inclusions in the steel, and such carbosulfides are finely dispersed. Then, the machinability of the steel material is dramatically improved.
【0030】そこで、更に研究を続けた結果、下記の事
項を見いだした。
Then, as a result of further study, the following matters were found.
【0031】(h)Sとのバランスを考慮して鋼にTi
とZrのいずれかを積極的に添加して行くと、鋼中にT
i炭硫化物あるいはZr炭硫化物が形成され、Ti及び
Zrを添加すると、鋼中にはTi炭硫化物とZr炭硫化
物とが形成される。
(H) Considering the balance with S, Ti
When either of Zr and Zr is actively added, T
i carbosulfide or Zr carbosulfide is formed, and when Ti and Zr are added, Ti carbosulfide and Zr carbosulfide are formed in the steel.
【0032】(i)鋼中に上記したTi炭硫化物やZr
炭硫化物が生成すると、MnSの生成量が減少する。
(I) The above-mentioned Ti carbosulfide or Zr in steel
When the carbosulfide is formed, the amount of MnS generated decreases.
【0033】(j)鋼中のS含有量が同じ場合には、T
i炭硫化物やZr炭硫化物はMnSよりも大きな被削性
改善効果を有する。これは、Ti炭硫化物やZr炭硫化
物の融点がMnSのそれよりも低いため、切削加工時に
工具のすくい面での潤滑作用が大きくなることに基づ
く。
(J) When the S content in steel is the same, T
i carbosulfide and Zr carbosulfide have a greater machinability improvement effect than MnS. This is based on the fact that the melting point of Ti carbosulfide or Zr carbosulfide is lower than that of MnS, so that the lubricating action on the rake face of the tool during cutting is increased.
【0034】(k)Ti炭硫化物やZr炭硫化物の効果
を充分発揮させるためには、N含有量を低くすることが
重要である。これは、N含有量が多いとTiNやZrN
としてTiやZrが固定されてしまい、Ti炭硫化物や
Zr炭硫化物の生成が抑制されてしまうためである。
(K) In order to sufficiently exert the effects of Ti carbosulfide and Zr carbosulfide, it is important to lower the N content. This is because when the N content is large, TiN or ZrN
This is because Ti and Zr are fixed, and the production of Ti carbosulfide and Zr carbosulfide is suppressed.
【0035】(l)製鋼時に生成したTi炭硫化物やZ
r炭硫化物は、通常の熱間加工のための加熱温度及び焼
準における通常の加熱温度では基地に固溶しない。した
がって、オーステナイト領域において所謂「ピン止め作
用」が発揮されるので、オーステナイト粒の粗大化防止
に有効である。勿論、Ti炭硫化物やZr炭硫化物は、
軟窒化処理の加熱温度でも基地に固溶しない。
(L) Ti carbosulfide and Z produced during steelmaking
r Carbosulfide does not form a solid solution in the matrix at a normal heating temperature for hot working and at a normal heating temperature in normalization. Therefore, a so-called "pinning action" is exhibited in the austenite region, which is effective in preventing austenite grains from becoming coarse. Of course, Ti and Zr carbosulfides are
It does not form a solid solution in the matrix even at the heating temperature of the nitrocarburizing treatment.
【0036】(m)Ti炭硫化物やZr炭硫化物によっ
て被削性を高めるためには、Ti炭硫化物やZr炭硫化
物のサイズと、その清浄度で表される量(以下、単に
「清浄度」という)を適正化しておくことが重要であ
る。
(M) In order to enhance the machinability by Ti carbosulfide or Zr carbosulfide, the size of Ti carbosulfide or Zr carbosulfide and the amount expressed by its cleanliness (hereinafter simply referred to as simply) It is important to optimize “cleanness”.
【0037】本発明は、上記の知見に基づいて完成され
たものである。
The present invention has been completed based on the above findings.
【0038】[0038]
【発明の実施の形態】以下、本発明の各要件について詳
しく説明する。なお、化学成分の含有量の「%」は「重
量%」を意味する。
DESCRIPTION OF THE PREFERRED EMBODIMENTS Each requirement of the present invention will be described in detail below. In addition, “%” of the content of the chemical component means “% by weight”.
【0039】(A)素材鋼の化学組成 C:Cは、SとともにTiやZrと結合してTi炭硫化
物やZr炭硫化物を形成し、被削性を高める作用を有す
る。更に、Cは、静的強度を確保するのにも有効な元素
である。しかし、その含有量が0.15%未満では所望
の静的強度(冷間加工後に軟窒化処理した後の芯部硬
度、すなわち最終製品である軟窒化部品の芯部硬度とし
てHv250以上)が確保できない。一方、0.45%
を超えると芯部の延性、靭性の低下をきたすとともに、
冷間加工性を劣化させてしまう。更に、軟窒化後の表面
硬度及び硬化深さが却って減少するようになる。したが
って、Cの含有量を0.15〜0.45%とした。
(A) Chemical composition of raw steel C: C combines with S and Ti or Zr to form Ti carbosulfide or Zr carbosulfide, and has an effect of enhancing machinability. Further, C is an element effective for securing the static strength. However, if the content is less than 0.15%, the desired static strength (core hardness after nitrocarburizing after cold working, ie, Hv250 or more as the core hardness of the nitrocarburized component as the final product) is secured. Can not. On the other hand, 0.45%
Exceeding this causes a decrease in ductility and toughness of the core,
It degrades cold workability. Further, the surface hardness and hardening depth after nitrocarburizing are rather reduced. Therefore, the content of C is set to 0.15 to 0.45%.
【0040】Si:Siは、鋼の焼入れ性を高めるとと
もに静的強度を向上させる作用を有する。しかし、その
含有量が0.05%未満では、前記した所望の静的強度
が確保できない。一方、0.5%を超えると靭性の劣化
を招いて、冷間加工性に悪影響を及ぼす。したがって、
Siの含有量を0.05〜0.5%とした。
Si: Si has the effect of improving the hardenability of steel and improving the static strength. However, if the content is less than 0.05%, the desired static strength described above cannot be secured. On the other hand, if it exceeds 0.5%, the toughness is degraded, which adversely affects the cold workability. Therefore,
The content of Si was set to 0.05 to 0.5%.
【0041】Mn:Mnは、焼入れ性の向上と芯部強度
の確保に有効な元素である。しかし、その含有量が0.
2%未満では添加効果に乏しく、一方、2.5%を超え
て含有させると偏析を生じて冷間加工性の劣化をもたら
す。したがって、Mnの含有量を0.2〜2.5%とし
た。なお、Mnの含有量は0.5〜1.5%とすること
が好ましい。
Mn: Mn is an element effective for improving hardenability and ensuring core strength. However, when its content is 0.1.
If it is less than 2%, the effect of the addition is poor. On the other hand, if it exceeds 2.5%, segregation occurs and the cold workability deteriorates. Therefore, the content of Mn is set to 0.2 to 2.5%. Note that the content of Mn is preferably set to 0.5 to 1.5%.
【0042】S:Sは、CとともにTiやZrと結合し
てTi炭硫化物やZr炭硫化物を形成し、被削性を高め
る作用を有する。しかし、その含有量が0.002%未
満では所望の効果が得られない。
S: S combines with C with Ti and Zr to form Ti carbosulfide and Zr carbosulfide, and has an effect of improving machinability. However, if the content is less than 0.002%, the desired effect cannot be obtained.
【0043】従来、快削鋼にSを添加する目的は、Mn
Sを形成させて被削性を改善させることにあった。しか
し、本発明者らの検討によると、上記のMnSの被削性
向上作用は、切削時の切り屑と工具表面との潤滑性を高
める機能に基づくことが判明した。しかもMnSは巨大
化し、鋼材本体の地疵を大きくし、欠陥となる場合があ
る。本発明におけるSの被削性改善作用は、適正量のC
とTiやZrとの複合添加によってTi炭硫化物やZr
炭硫化物を形成させることで初めて得られる。このため
には、上記したように0.002%以上のSの含有量が
必要である。一方、Sを0.2%を超えて含有させても
被削性に与える効果に変化はないが、鋼中に粗大なMn
Sが再び生じるようになり、地疵等の問題が生じる。更
に、熱間での加工性が著しく劣化し熱間加工が困難にな
るし、靭性が低下することもある。したがって、Sの含
有量を0.002〜0.2%とした。なお、Sの好まし
い含有量は0.004〜0.1%である。
Conventionally, the purpose of adding S to free-cutting steel is to add Mn
The purpose is to improve the machinability by forming S. However, according to the study of the present inventors, it has been found that the above-described action of improving the machinability of MnS is based on a function of enhancing lubricity between chips and the tool surface during cutting. In addition, MnS increases in size, increases the ground flaw of the steel material main body, and sometimes becomes a defect. In the present invention, the machinability improving action of S is based on an appropriate amount of C
Addition of Ti and Zr to Ti carbosulfide and Zr
Obtained only by forming carbosulfide. For this purpose, the content of S is required to be 0.002% or more as described above. On the other hand, although the effect on machinability is not changed even when S is contained in excess of 0.2%, coarse Mn is contained in steel.
S is generated again, and problems such as ground flaws occur. Further, the hot workability is remarkably deteriorated, so that hot working becomes difficult, and the toughness may be reduced. Therefore, the content of S is set to 0.002 to 0.2%. In addition, the preferable content of S is 0.004 to 0.1%.
【0044】Cu:Cuは、本発明において重要な元素
であって、軟窒化処理時に微細に析出して鋼を硬化させ
る作用を有する。このため被処理鋼材は、軟窒化のため
の加熱で軟化することがなく軟窒化前の硬度を維持で
き、場合によっては逆に硬化する。前記のCuの効果
は、特に、球状化焼鈍して硬度をHv180以下にし、
冷間鍛造による加工効果で硬度をHv250以上に上昇
させた鋼材において大きく発揮される。しかし、その含
有量が0.5%未満では充分な量が微細析出しないので
添加効果に乏しい。一方、1.5%を超えて含有させる
と前記の効果が飽和するばかりか熱間加工性の劣化をも
たらす。したがって、Cu含有量を0.5〜1.5%と
した。
Cu: Cu is an important element in the present invention, and has an effect of finely precipitating during hard nitriding treatment to harden the steel. For this reason, the steel material to be treated can maintain the hardness before the soft nitriding without being softened by heating for the soft nitriding, and in some cases, hardens in reverse. The effect of the Cu is, in particular, spheroidizing annealing to reduce the hardness to Hv180 or less,
It is greatly exhibited in steel materials whose hardness has been increased to Hv250 or more by the working effect of cold forging. However, if the content is less than 0.5%, a sufficient amount is not finely precipitated, so that the effect of addition is poor. On the other hand, when the content exceeds 1.5%, not only the above effect is saturated, but also the hot workability is deteriorated. Therefore, the Cu content is set to 0.5 to 1.5%.
【0045】Ni:Niは、上記のCuを基地に完全に
固溶させて、軟窒化処理に際しCuの析出硬化作用を充
分発揮させる効果を有する。この作用は後述するCu
(%)/Ni(%)の比が1.8〜2.2の場合に顕著
である。しかし、Niの含有量が0.25%未満では添
加効果に乏しく、0.75%を超えて含有させても前記
の効果は飽和する。このため、Niの含有量を0.25
〜0.75%とした。
Ni: Ni has the effect of completely dissolving the above-mentioned Cu in the matrix and sufficiently exerting the precipitation hardening effect of Cu during the nitrocarburizing treatment. This function is described later in Cu
This is remarkable when the ratio of (%) / Ni (%) is 1.8 to 2.2. However, if the content of Ni is less than 0.25%, the effect of addition is poor, and even if the content exceeds 0.75%, the above effect is saturated. Therefore, the content of Ni is set to 0.25.
-0.75%.
【0046】Cu(%)/Ni(%):Cu(%)/N
i(%)の値が1.8〜2.2の場合に、適正量のCu
とNiの複合添加によりCuが基地に完全に固溶して、
軟窒化処理に際し析出硬化するCuの作用の発現が顕著
となる。したがって、Cu(%)/Ni(%)の値を
1.8〜2.2とした。なお、Cu(%)/Ni(%)
の値は1.9〜2.1とすることが好ましい。
Cu (%) / Ni (%): Cu (%) / N
When the value of i (%) is 1.8 to 2.2, an appropriate amount of Cu
Cu is completely dissolved in the matrix by the complex addition of
The effect of Cu that precipitates and hardens during the nitrocarburizing treatment becomes remarkable. Therefore, the value of Cu (%) / Ni (%) was set to 1.8 to 2.2. In addition, Cu (%) / Ni (%)
Is preferably 1.9 to 2.1.
【0047】Cr:Crは、軟窒化時に鋼材表面から侵
入してくるNと結合して、表面硬度を高めるとともに硬
化深さを大きくするのに極めて有効な元素である。しか
し、その含有量が0.5%未満では上記の作用が期待で
きない。一方、Crを2%を超えて含有させると、軟窒
化によって表面硬度が高くなりすぎるために、表面から
芯部にかけての硬度勾配が急激なものとなってしまい、
却って耐スポーリング性や耐ピッチング性が劣化してし
まう。したがって、Crの含有量を0.5〜2%とし
た。
Cr: Cr is an element that is extremely effective in combining with N invading from the steel material surface during soft nitriding to increase the surface hardness and increase the hardening depth. However, if the content is less than 0.5%, the above effects cannot be expected. On the other hand, if Cr is contained in excess of 2%, the surface hardness becomes too high due to soft nitriding, so that the hardness gradient from the surface to the core becomes sharp,
Rather, spalling resistance and pitting resistance are degraded. Therefore, the content of Cr is set to 0.5 to 2%.
【0048】V:Vは、軟窒化処理時に鋼材表面から侵
入してくるN及びCと結合して微細なバナジウム炭窒化
物として析出することにより、表面硬度を高め、更に、
硬化深さを大きくする作用を有する。V添加鋼において
は上記のCr添加の場合に比べて、表面硬度の上昇割合
が小さいのに対して硬化深さの増大割合は極めて大き
く、且つ前記炭窒化物が析出して芯部硬度を高めるた
め、硬化深さの大きい、表面から芯部への硬度勾配が緩
やかな硬化曲線が得られる。しかし、V含有量が0.0
5%未満では添加効果に乏しく、一方、0.5%を超え
て含有させても前記の効果が飽和してコストが嵩むばか
りか、却って脆化現象の発現をきたすようになる。した
がって、V含有量を0.05〜0.5%とした。なお、
V含有量は0.1〜0.3%とすることが好ましい。
V: V combines with N and C invading from the surface of the steel material during the nitrocarburizing treatment to precipitate as fine vanadium carbonitride, thereby increasing the surface hardness.
It has the effect of increasing the curing depth. In the case of V-added steel, the rate of increase in the surface hardness is very small, but the rate of increase in the hardening depth is extremely large, and the carbonitride precipitates to increase the core hardness, as compared with the case of the above Cr addition. Therefore, a hardening curve with a large hardening depth and a gentle hardness gradient from the surface to the core can be obtained. However, when the V content is 0.0
If it is less than 5%, the effect of addition is poor. On the other hand, if it exceeds 0.5%, the above effect is saturated and not only increases the cost but also causes the embrittlement phenomenon. Therefore, the V content is set to 0.05 to 0.5%. In addition,
The V content is preferably 0.1 to 0.3%.
【0049】Ti、Zr:Ti、Zrは本発明において
重要な元素であって、それぞれC及びSと結合してTi
炭硫化物やZr炭硫化物を形成し、被削性を高める作用
を有する。
Ti, Zr: Ti and Zr are important elements in the present invention.
It forms carbosulfides and Zr carbosulfides and has the effect of enhancing machinability.
【0050】上記の効果は、TiとZrの含有量に関
し、Ti(%)+Zr(%)の値が0.04%以上の場
合に確実に得られる。しかし、Ti(%)+Zr(%)
の値で1.0%を超えるTiとZrを含有させても被削
性向上効果は飽和するのでコストが嵩んでしまう。な
お、Ti(%)+Zr(%)の値が0.04〜1.0%
でありさえすれば良いので、必ずしもTiとZrを複合
して含有させる必要はない。Zrを添加しない、つまり
Tiを単独で添加する場合に、Tiを1.0%を超えて
含有させるとTi炭硫化物による被削性向上効果が飽和
してコストが嵩むばかりか、Ti炭硫化物が粗大化して
却って靭性の低下を招いてしまう。逆に、Tiを添加し
ない、つまりZrを単独で添加する場合に、Zrを1.
0%を超えて含有させるとZr炭硫化物による被削性向
上効果が飽和してコストが嵩むばかりか、Zr炭硫化物
が粗大化して却って靭性の低下を招いてしまう。したが
って、TiとZrの含有量をいずれも0〜1.0%で
且つ、Ti(%)+Zr(%)の値を0.04〜1.0
%とした。なお、良好な被削性と靭性を安定して得るた
めには、TiとZrの含有量の上限はそれぞれ0.8%
とすることが好ましい。
The above effect can be surely obtained when the value of Ti (%) + Zr (%) is 0.04% or more with respect to the contents of Ti and Zr. However, Ti (%) + Zr (%)
If the content of Ti and Zr exceeds 1.0%, the effect of improving machinability is saturated, so that the cost increases. The value of Ti (%) + Zr (%) is 0.04 to 1.0%
Therefore, it is not always necessary to include Ti and Zr in combination. When Zr is not added, that is, when Ti is added alone, if the content of Ti exceeds 1.0%, the effect of improving the machinability due to Ti carbosulfide is saturated and the cost is increased. The material is coarsened and the toughness is rather reduced. Conversely, when Ti is not added, that is, when Zr is added alone, Zr is added at 1.
If the content exceeds 0%, the effect of improving the machinability by Zr carbosulfide is saturated and not only the cost is increased, but also the Zr carbosulfide is coarsened and the toughness is reduced. Therefore, the content of both Ti and Zr is 0-1.0 % ,
Further, the value of Ti (%) + Zr (%) is set to 0.04 to 1.0.
%. In order to stably obtain good machinability and toughness, the upper limits of the contents of Ti and Zr are each 0.8%.
It is preferable that
【0051】Al:Alは、鋼の脱酸の安定化及び均質
化を図る作用がある。更に、侵入Nと結合して表面硬度
を高める効果を有する。しかし、その含有量が0.01
%未満では上記の作用が期待できない。一方、0.3%
を超えると硬化深さを小さくしてしまう。したがって、
Alの含有量を0.01〜0.3%とした。なお、Al
含有量は0.01〜0.15とすることが好ましい。
Al: Al has the effect of stabilizing and homogenizing steel deoxidation. Furthermore, it has the effect of increasing the surface hardness by combining with the intrusion N. However, the content is 0.01
%, The above effect cannot be expected. On the other hand, 0.3%
If it exceeds 300, the curing depth will be reduced. Therefore,
The content of Al was set to 0.01 to 0.3%. In addition, Al
The content is preferably set to 0.01 to 0.15.
【0052】N:本発明においてはNの含有量を低くす
ることが極めて重要である。すなわち、NはTiやZr
との親和力が大きいために容易にTiやZrと結合して
TiNやZrNを生成し、TiやZrを固定してしまう
ので、Nを多量に含有する場合には前記したTi炭硫化
物やZr炭硫化物の被削性向上効果が充分に発揮できな
いこととなる。特に、TiやZrの含有量が低めの場合
には、N含有量の影響が顕著となる。更に、粗大なTi
NやZrNは靭性及び被削性を低下させてしまう。した
がって、N含有量を0.008%以下とした。なお、T
i炭硫化物やZr炭硫化物の効果を高めるために、N含
有量の上限は0.006%とすることが好ましい。
N: In the present invention, it is extremely important to reduce the N content. That is, N is Ti or Zr
Has a high affinity with Ti and Zr to easily form TiN and ZrN and fix Ti and Zr. Therefore, when a large amount of N is contained, the above-mentioned Ti carbosulfide or Zr is used. As a result, the effect of improving the machinability of the carbosulfide cannot be sufficiently exhibited. In particular, when the content of Ti or Zr is relatively low, the influence of the N content becomes significant. Furthermore, coarse Ti
N and ZrN decrease toughness and machinability. Therefore, the N content is set to 0.008% or less. Note that T
In order to enhance the effect of i carbosulfide and Zr carbosulfide, the upper limit of the N content is preferably set to 0.006%.
【0053】Mo: Moは、鋼の焼入れ性を高めるとともに軟窒化時の芯部
の軟化抵抗を高める作用を有する。この効果を確実に得
るには、Moは0.02%以上の含有量を必要とする。
しかし、その含有量が0.3%を超えると前記効果が飽
和し、コストが嵩むばかりである。したがって、Moの
含有量を0.02〜0.3%とした。
Mo: Mo has the effect of increasing the hardenability of steel and increasing the softening resistance of the core during soft nitriding. In order to ensure this effect, Mo is that require content of 0.02% or more.
However, if the content exceeds 0.3%, the above effect is saturated and the cost is only increased. Therefore, the content of Mo is set to 0.02 to 0.3%.
【0054】W: Wは、鋼の焼入れ性を高めるとともに軟窒化時の芯部の
軟化抵抗を高める作用を有する。この効果を確実に得る
には、Wは0.05%以上の含有量を必要とする。しか
し、その含有量が0.5%を超えると前記効果が飽和
し、コストが嵩むばかりである。したがって、Wの含有
量を0.05〜0.5%とした。なお、上記した量のM
oとWの少なくとも1種以上が含有されておれば、鋼の
焼入れ性を高めるとともに軟窒化時の芯部の軟化抵抗を
高めることができる。
W: W has the effect of increasing the hardenability of steel and increasing the softening resistance of the core during soft nitriding. In order to ensure this effect, W is that require content of 0.05% or more. However, if the content exceeds 0.5%, the above effect is saturated and the cost is increased. Therefore, the content of W is set to 0.05 to 0.5%. Note that the above amount of M
If at least one of o and W is contained, steel
Improves hardenability and reduces core softening resistance during nitrocarburizing
Can be enhanced.
【0055】Pb: Pbは添加しなくても良い。添加すれば、鋼の被削性を
一段と高める作用を有する。この効果を確実に得るに
は、Pbは0.03%以上の含有量とすることが好まし
い。しかし、Pbを0.35%を超えて含有させると熱
間加工性が劣化して熱間圧延や熱間鍛造などの熱間加工
時に割れの発生を招くことが多くなる。したがって、
加する場合のPbの含有量は0.03〜0.35%と
るのがよい。
Pb: Pb may not be added. If added, it has the effect of further increasing the machinability of the steel. In order to surely obtain this effect, the content of Pb is preferably set to 0.03% or more. However, when Pb is contained in excess of 0.35%, hot workability is deteriorated, and cracks often occur during hot working such as hot rolling and hot forging. Therefore, hydrogenated
The Pb content when added is 0.03 to 0.35% .
Is good.
【0056】Ca: Caは添加しなくても良い。添加すれば、鋼の被削性を
一段と高める作用を有する。この効果を確実に得るに
は、Caは0.001%以上の含有量とすることが好ま
しい。一方、Caを0.01%を超えて含有させるには
特殊な溶製技術や設備を要してコストが嵩む。したがっ
て、添加する場合のCaの含有量は0.0001〜0.
01%とするのがよい。なお、上記した量のPbとCa
の少なくとも1種以上が含有されておれば、鋼の被削性
を一段と高めることができる。
Ca: Ca may not be added. If added, it has the effect of further increasing the machinability of the steel. In order to surely obtain this effect, the content of Ca is preferably set to 0.001% or more. On the other hand, if Ca is contained in an amount exceeding 0.01%, special smelting techniques and equipment are required, which increases the cost. Therefore, when Ca is added, the content of Ca is 0.0001 to 0.1.
It is better to be 01% . The above amounts of Pb and Ca
The machinability of steel as long as it contains at least one of
Can be further increased.
【0057】fn1:本発明においては、N含有量が
0.008%以下で、前述の式で表されるfn1が0
%を超える値(fn1=Ti(%)+Zr(%)−1.
2×S(%)>0%)の場合に前記したTi炭硫化物や
Zr炭硫化物の被削性向上効果が確保できる。fn1が
0%以下の値(fn1≦0%)の場合には、S量が過剰
となるため、その分MnSが過剰生成してTi炭硫化物
やZr炭硫化物による被削性向上効果が低下してしま
う。したがって、式で表されるfn1に関して0%を
超える値(fn1>0%)と規定した。このfn1の値
の上限は特に規定されるものではなく、Ti(%)+Z
r(%)の値が1.0%でSが0.002%の場合の値
であっても良い。
Fn1: In the present invention, when the N content is 0.008% or less, fn1 represented by the above formula is 0%.
% (Fn1 = Ti (%) + Zr (%)-1.
When 2 × S (%)> 0%), the effect of improving the machinability of the above-mentioned Ti carbosulfide or Zr carbosulfide can be secured. When fn1 is a value of 0% or less (fn1 ≦ 0%), the amount of S is excessive, so that MnS is excessively generated and the effect of improving the machinability by Ti carbosulfide or Zr carbosulfide. Will drop. Therefore, the value of fn1 represented by the formula is defined as a value exceeding 0% (fn1> 0%). The upper limit of the value of fn1 is not particularly defined, and Ti (%) + Z
It may be a value when the value of r (%) is 1.0% and S is 0.002%.
【0058】(B)Ti炭硫化物、Zr炭硫化物のサイ
ズと量 上記の化学組成を有する鋼材の被削性をTi炭硫化物や
Zr炭硫化物によって高めるとともに大きな強度をも確
保するためには、Ti炭硫化物やZr炭硫化物のサイズ
と清浄度(TiとZrを複合添加する場合にはTi炭硫
化物とZr炭硫化物の清浄度の和)で表される量を適正
化しておくことが重要である。
(B) Size and amount of Ti carbosulfide and Zr carbosulfide In order to increase the machinability of the steel material having the above chemical composition by Ti carbosulfide and Zr carbosulfide, and to secure a large strength. In the case, the amount expressed by the size and cleanliness of Ti carbosulfide or Zr carbosulfide (the sum of the cleanliness of Ti carbosulfide and Zr carbosulfide when Ti and Zr are added in combination) is appropriate. It is important to keep it.
【0059】鋼中のTi炭硫化物及びZr炭硫化物の最
大直径が10μmを超えると疲労強度が低下してしま
う。なお、Ti炭硫化物及びZr炭硫化物の最大直径は
いずれも7μm以下とすることが好ましい。Ti炭硫化
物とZr炭硫化物は、それらの最大直径が小さすぎると
被削性向上効果が小さくなってしまう。したがって、T
i炭硫化物とZr炭硫化物の最大直径の下限値は0.5
μm程度とすることが好ましい。
If the maximum diameter of Ti carbosulfide and Zr carbosulfide in steel exceeds 10 μm, the fatigue strength is reduced. Note that the maximum diameter of each of the Ti carbosulfide and the Zr carbosulfide is preferably 7 μm or less. If the maximum diameter of Ti carbosulfide and Zr carbosulfide is too small, the effect of improving machinability is reduced. Therefore, T
The lower limit of the maximum diameter of i carbosulfide and Zr carbosulfide is 0.5
It is preferable that the thickness be about μm.
【0060】最大直径が10μm以下のTi炭硫化物及
びZr炭硫化物の量の和が清浄度で0.05%未満の場
合には、Ti炭硫化物及びZr炭硫化物による被削性向
上効果が発揮できない。したがって、Ti炭硫化物及び
Zr炭硫化物の最大直径が10μm以下で、且つその量
の和を清浄度で0.05%以上とした。なお、前記の清
浄度の和は0.08%以上とすることが好ましい。上記
のTi炭硫化物とZr炭硫化物の清浄度の和の値が大き
すぎると疲労強度が低下してしまうので、上記の清浄度
の和の上限値は2.0%程度とすることが好ましい。
When the sum of the amounts of Ti carbosulfide and Zr carbosulfide having a maximum diameter of 10 μm or less is less than 0.05% in cleanliness, the machinability is improved by Ti carbosulfide and Zr carbosulfide. No effect. Therefore, the maximum diameter of Ti carbosulfide and Zr carbosulfide was 10 μm or less, and the sum of the amounts was 0.05% or more in terms of cleanliness. It is preferable that the sum of the cleanliness is 0.08% or more. If the sum of the cleanliness of the Ti and Zr carbosulfides is too large, the fatigue strength is reduced. Therefore, the upper limit of the sum of the cleanliness is set to about 2.0%. preferable.
【0061】上記したようなTi炭硫化物とZr炭硫化
物の形態は基本的にはTi、Zr、S及びNの含有量で
決定される。しかし、Ti炭硫化物やZr炭硫化物のサ
イズと清浄度(清浄度の和)を上述の値とするために
は、TiやZrの酸化物が過剰に生成することを防ぐこ
とが重要である。このためには、鋼が前記(A)項で述
べた化学組成を有しているだけでは充分でない場合があ
るので、例えば、Si及びAlで充分脱酸し、最後にT
iやZrを添加する製鋼法を採れば良い。
The form of Ti carbosulfide and Zr carbosulfide as described above is basically determined by the contents of Ti, Zr, S and N. However, in order to set the size and cleanliness (sum of cleanliness) of Ti carbosulfides and Zr carbosulfides to the above-mentioned values, it is important to prevent the oxides of Ti and Zr from being excessively generated. is there. In some cases, it is not sufficient for the steel to have the chemical composition described in the above item (A). For example, the steel is sufficiently deoxidized with Si and Al, and finally T
A steelmaking method in which i or Zr is added may be employed.
【0062】なお、Ti炭硫化物とZr炭硫化物は、鋼
材から採取した試験片を鏡面研磨し、その研磨面を被検
面として倍率400倍以上で光学顕微鏡観察すれば、色
と形状から容易に他の介在物と識別できる。すなわち、
前記の条件で光学顕微鏡観察すれば、Ti炭硫化物及び
Zr炭硫化物の「色」は極めて薄い灰色で、「形状」は
JISのB系介在物やC系介在物に相当する粒状(球
状)として認められる。Ti炭硫化物及びZr炭硫化物
の詳細判定は、前記の被検面をEDX(エネルギー分散
型X線分析装置)などの分析機能を備えた電子顕微鏡で
観察することによって行うこともできる。
It should be noted that Ti carbosulfide and Zr carbosulfide can be obtained from the color and the shape by polishing a specimen taken from a steel material by mirror polishing and observing the polished surface as a test surface with an optical microscope at a magnification of 400 or more. It can be easily distinguished from other inclusions. That is,
Observation under an optical microscope under the above conditions shows that the “color” of Ti carbosulfide and Zr carbosulfide is extremely light gray, and the “shape” is a granular (spherical) equivalent to JIS B-based inclusion or C-based inclusion. ). The detailed determination of Ti carbosulfide and Zr carbosulfide can also be performed by observing the test surface with an electron microscope equipped with an analysis function such as EDX (energy dispersive X-ray analyzer).
【0063】前記のTi炭硫化物やZr炭硫化物の清浄
度は、既に述べたように、光学顕微鏡の倍率を400倍
として、JIS G 0555に規定された「鋼の非金属介在物の
顕微鏡試験方法」によって60視野測定した値をいう。
なお、Ti炭硫化物やZr炭硫化物の最大直径も、倍率
が400倍の光学顕微鏡で60視野観察して調査すれば
良い。
As described above, the cleanliness of the Ti carbosulfide and the Zr carbosulfide is determined by setting the magnification of the optical microscope to 400 times, as described in JIS G 0555. It refers to the value measured in 60 visual fields by the "test method".
In addition, the maximum diameter of Ti carbosulfide or Zr carbosulfide may be investigated by observing 60 visual fields with an optical microscope having a magnification of 400 times.
【0064】(C)球状化焼鈍 球状化焼鈍は前記(A)に示した化学組成と、上記
(B)に示したサイズと量のTi炭硫化物やZr炭硫化
物をもつ鋼材を、熱間加工(例えば熱間圧延や熱間鍛造
など)した後に、その硬度を低下させて冷間加工性を高
めるとともに、それによって金型寿命を大幅に改善し、
最終製品である所要の軟窒化部品の製造コストを低く抑
えるのに必須の処理である。
(C) Spheroidizing Annealing The spheroidizing annealing is performed by heat-treating a steel material having the chemical composition shown in (A) and the size and amount of Ti carbosulfide or Zr carbosulfide shown in (B) above. After hot working (for example, hot rolling or hot forging), the hardness is reduced to increase cold workability, thereby significantly improving the mold life,
This is an indispensable process to keep the production cost of the required nitrocarburized component as a final product low.
【0065】球状化焼鈍後の硬度がHvで180を超え
ると、金型の寿命が大幅に低下してしまうため、最終製
品である所望の軟窒化部品の製造コストが著しく高くな
る。したがって、球状化焼鈍後の硬度はHv180以下
としなければならない。なお、球状化焼鈍の硬度の下限
値については、特に制限する必要はない。
If the hardness after spheroidizing annealing exceeds 180 in Hv, the life of the mold is greatly reduced, and the production cost of the desired nitrocarburized component as the final product is significantly increased. Therefore, the hardness after spheroidizing annealing must be Hv180 or less. The lower limit of the hardness of the spheroidizing annealing does not need to be particularly limited.
【0066】この球状化焼鈍は、通常の方法で行えば良
い。
The spheroidizing annealing may be performed by a usual method.
【0067】(D)冷間加工 球状化焼鈍して硬度をHv180以下に調整した上記
(C)の鋼材を、次に冷間加工して所望の軟窒化部品の
粗形状に仕上げ、更に切削加工して所望の軟窒化部品の
形状に仕上げる。勿論、精密冷間加工して切削加工せず
に所望の軟窒化部品の形状に仕上げても良いし、球状化
焼鈍後に冷間加工の前あるいは前後で切削加工を行って
所望の軟窒化部品の形状に仕上げても良い。
(D) Cold working The steel material of (C), whose hardness has been adjusted to Hv 180 or less by spheroidizing annealing, is then cold worked to finish it into a rough shape of a desired nitrocarburized part, and further cut. To form the desired nitrocarburized component. Of course, precision cold working may be performed to finish the desired nitrocarburized component without cutting, or after spheroidizing annealing, cutting may be performed before or after cold working to obtain the desired nitrocarburized component. It may be finished in a shape.
【0068】なお、(1)及び(2)の発明にかかわる
「軟窒化用鋼材」とは、前記冷間加工と切削加工(ある
いは精密冷間加工)によって所望形状に成形されたもの
のことで、軟窒化される前のものをいう。
The “soft-nitriding steel material” according to the inventions (1) and (2) is formed by cold working and cutting (or precision cold working) into a desired shape. It is the one before soft nitriding.
【0069】上記の冷間加工は、例えば、冷間鍛造、冷
間転造や冷間引き抜きなど、通常の方法で行えば良い
が、加工した部品の硬度をHv250以上にする必要が
ある。なぜならば、硬度をHv180以下に調整された
上記(C)の鋼材は、冷間での加工を受けて硬度がHv
250以上に上昇すれば、これに軟窒化処理を施しても
芯部硬度は低下せず軟窒化前の硬度が維持でき、あるい
は軟窒化前の硬度を高めることさえできるからである。
The above cold working may be performed by a usual method such as cold forging, cold rolling or cold drawing, but the hardness of the worked part must be Hv250 or more. This is because the steel material (C) whose hardness has been adjusted to Hv180 or less has a hardness of Hv180 due to cold working.
If the hardness is increased to 250 or more, the hardness of the core portion does not decrease even if the nitrocarburizing treatment is performed, and the hardness before nitrocarburizing can be maintained or the hardness before nitrocarburizing can be increased.
【0070】軟窒化後の芯部硬度がHv250以上であ
れば、既に述べたように、例えば、自動車のミッション
ギアのように高い負荷が加わる部品においても、部品内
部を起点として曲げ疲労を生ずることはない。
If the core hardness after nitrocarburizing is equal to or higher than Hv250, as described above, bending fatigue may occur from the inside of the part even in a part to which a high load is applied, such as a transmission gear of an automobile. There is no.
【0071】上記(C)に示した球状化焼鈍して硬度を
Hv180以下に調整した鋼材を冷間加工して、硬度を
Hv250以上とするには、減面率で20%以上の加工
が加わるように寸法調整しておけば良い。
In order to cold-work a steel material whose hardness has been adjusted to Hv 180 or less by spheroidizing annealing as shown in (C) above and to have a hardness of Hv 250 or more, a work of 20% or more in reduction of area is added. The dimensions should be adjusted as follows.
【0072】なお、冷間加工後の硬度の上限値は特に制
限する必要はない。すなわち、設備上加えることが可能
な最高の減面率で加工して、極めて大きな硬度となって
も良い。
The upper limit of the hardness after cold working does not need to be particularly limited. In other words, processing may be performed with the maximum reduction in area that can be added to the equipment to achieve extremely high hardness.
【0073】これまでに述べた製造方法によって、
(1)及び(2)の発明に係る「軟窒化用鋼材」が得ら
れる。この鋼材は、次に述べる軟窒化処理を受けて、
(3)の発明に係る軟窒化部品となる。
According to the manufacturing method described above,
The "steel material for nitrocarburizing" according to the inventions of (1) and (2) is obtained. This steel material is subjected to the following soft nitriding treatment,
The nitrocarburized component according to the invention of (3) is obtained.
【0074】(E)軟窒化 上記(D)の冷間加工を行って、あるいは、冷間加工と
その前又は/及びその後で切削加工を行って所要形状に
成形した部品(軟窒化用鋼材)には、この後更に、軟窒
化処理が施される。この軟窒化の方法は何ら制限しなく
ても良く、通常の方法で行えば良い。軟窒化処理を施
し、表面硬度をHv600以上、有効硬化深さを0.1
mm以上とすれば、軟窒化部品の耐疲労特性、耐摩耗
性、耐ピッチング性及び耐スポーリング性を著しく高め
ることができるのである。
(E) Soft nitriding A part formed into a required shape by performing the cold working of the above (D), or performing the cold working and cutting work before and / or after the cold working (steel material for soft nitriding) Is further subjected to a soft nitriding treatment thereafter. This nitrocarburizing method need not be limited at all, and may be performed by a normal method. Carbide nitriding treatment, surface hardness Hv600 or more, effective hardening depth 0.1
If it is not less than mm, the fatigue resistance, wear resistance, pitting resistance and spalling resistance of the nitrocarburized component can be significantly improved.
【0075】上記(D)に示した冷間加工、あるいは、
冷間加工とその前又は/及びその後で切削加工を施され
た部品(軟窒化用鋼材)を軟窒化して表面硬度をHv6
00以上、有効硬化深さを0.1mm以上、芯部硬度を
Hv250以上とするには、例えば、当該部品を570
℃程度の温度の、RXガスにアンモニアを添加したガス
中に3〜9時間保持し、その後油中に冷却すれば良い。
The cold working shown in the above (D), or
The part (steel material for nitrocarburizing) that has been subjected to cold working and before or / and after that is nitrocarburized to have a surface hardness of Hv6.
In order to set the effective hardening depth to 0.1 mm or more and the core hardness to Hv 250 or more,
What is necessary is just to hold for 3 to 9 hours in a gas obtained by adding ammonia to RX gas at a temperature of about ° C., and then cool in oil.
【0076】なお、軟窒化後の表面硬度、有効硬化深さ
及び芯部硬度の上限値は特に制限しなくても良い。しか
し、軟窒化後の表面硬度については、Hv900程度を
上限とすることが好ましい。
The upper limits of the surface hardness after nitrocarburizing, the effective hardening depth, and the core hardness need not be particularly limited. However, the upper limit of the surface hardness after soft nitriding is preferably about Hv900.
【0077】(3)の発明に係る軟窒化部品は、素材鋼
材である前記(A)の化学組成と(B)に示すサイズと
量のTi炭硫化物やZr炭硫化物をもつ鋼材を、例え
ば、通常の方法によって溶製した後、熱間で圧延又は鍛
造し、必要に応じて焼準を施し、(C)に示した球状化
焼鈍を行い、次いで(D)に示した冷間加工によって、
あるいは、(D)に示した冷間加工とその前又は/及び
その後の切削加工によって、所望の部品形状に成形して
から、軟窒化処理し、この後更に必要に応じて研削や研
磨を施して製造される。
The nitrocarburized part according to the invention of (3) is a steel material having the chemical composition of (A), which is a material steel, and the size and amount of Ti carbosulfide or Zr carbosulfide shown in (B). For example, after smelting by a normal method, hot rolling or forging, normalizing as necessary, spheroidizing annealing shown in (C), and then cold working shown in (D) By
Alternatively, after forming into a desired part shape by the cold working shown in (D) and the cutting work before and / or after that, nitrocarburizing treatment is performed, and then grinding and polishing are further performed as necessary. Manufactured.
【0078】ここで、本発明が対象とする化学組成を有
する素材鋼材においては、熱間加工後に焼準して、少な
くとも表層から0.5mmを超える深さまでの領域の組
織をベイナイトを含む組織(ベイナイト単相組織、ある
いはベイナイト、並びに、フェライト、パーライト及び
マルテンサイトの1種以上の混合組織)とすれば、球状
化焼鈍後の炭化物(主としてセメンタイト)の球状化率
が向上する。したがって、球状化焼鈍で冷間加工前の硬
度を大きく低下させることができる。冷間加工前の鋼材
の硬度を下げることは、冷間加工性の向上につながり、
金型寿命が延びて金型コストの削減が図れる。更に、球
状化焼鈍時間を短縮することができて、生産性の向上と
製造コストの低減が図れる。このため、(1)及び
(2)の発明の軟窒化用鋼材の製造方法においては、熱
間加工後に焼準してから球状化焼鈍することが好まし
い。
Here, in the material steel material having the chemical composition which is the object of the present invention, after normalizing after hot working, the structure of at least the region from the surface to a depth exceeding 0.5 mm is changed to the structure containing bainite ( A bainite single-phase structure or a mixed structure of at least one of bainite and ferrite, pearlite, and martensite) improves the spheroidization rate of carbide (mainly cementite) after spheroidizing annealing. Therefore, the hardness before cold working can be greatly reduced by spheroidizing annealing. Reducing the hardness of steel before cold working leads to improvement of cold workability,
The life of the mold is extended, and the cost of the mold can be reduced. Further, the spheroidizing annealing time can be shortened, so that productivity can be improved and manufacturing cost can be reduced. For this reason, (1) and
In the method for producing a steel material for nitrocarburizing of the invention (2) , it is preferable to perform normalizing after hot working and then spheroidizing annealing.
【0079】[0079]
【実施例】表1、表2に示す化学組成の鋼を180kg
真空溶解炉を用いて溶製した。なお、鋼7及び鋼8を除
いて、Ti酸化物及びZr酸化物の生成を防ぐために、
Si及びAlで充分脱酸し種々の元素を添加した最後に
Ti、Zrを添加して、Ti炭硫化物とZr炭硫化物の
サイズと清浄度(清浄度の和)を調整するようにした。
鋼7と鋼8については、Si及びAlで脱酸する際に同
時にTi、Zrを添加した。
EXAMPLE 180 kg of steel having the chemical composition shown in Tables 1 and 2 was used.
It was melted using a vacuum melting furnace. In addition, except for steel 7 and steel 8, in order to prevent generation of Ti oxide and Zr oxide,
After sufficiently deoxidizing with Si and Al and adding various elements, Ti and Zr were added at the end to adjust the size and cleanliness (sum of cleanliness) of Ti and Zr carbosulfides. .
For Steel 7 and Steel 8, Ti and Zr were added simultaneously when deoxidizing with Si and Al.
【0080】表1における鋼1〜10は化学組成が本発
明で規定する範囲内にある本発明例、表2における鋼1
1〜20は成分のいずれかが本発明で規定する含有量の
範囲から外れた比較例である。比較例に係る鋼のうち鋼
19及び鋼20はそれぞれJIS規格のSCM435及
びSACM645に相当する鋼にTiやZrを添加した
ものである。
Steels 1 to 10 in Table 1 are examples of the present invention in which the chemical composition is within the range specified in the present invention.
Nos. 1 to 20 are comparative examples in which any of the components was out of the range of the content specified in the present invention. Among the steels according to the comparative examples, steels 19 and 20 are steels corresponding to JIS-standard SCM435 and SACM645, respectively, to which Ti and Zr are added.
【0081】[0081]
【表1】 [Table 1]
【0082】[0082]
【表2】 [Table 2]
【0083】次いで、これらの鋼を通常の方法によって
鋼片にした後、1250℃に加熱してから、1250〜
950℃の温度で熱間鍛造して、直径30mm及び38
mmの丸棒とした。この後、C含有量に応じて870〜
925℃で焼準し、次いで図1に示すヒートパターンで
球状化焼鈍した。
Next, these steels were made into billets by a usual method, heated to 1250 ° C.
Hot forging at a temperature of 950 ° C., diameter 30 mm and 38
mm round bar. Thereafter, 870 to 870 depending on the C content.
Normalizing was performed at 925 ° C., and then spheroidizing annealing was performed according to the heat pattern shown in FIG.
【0084】なお、鋼3、鋼7及び鋼9については、比
較のために、熱間鍛造のままで、すなわち熱間鍛造後に
焼準を行わないで球状化焼鈍したものも準備した。
For comparison, steel 3, steel 7, and steel 9 were also prepared as hot forged, that is, spheroidized and annealed without normalizing after hot forging.
【0085】(実施例1)上記のようにして得られた直
径が30mmの丸棒を用いて、下記の各種調査を行っ
た。
(Example 1) The following various investigations were carried out using the round bar having a diameter of 30 mm obtained as described above.
【0086】すなわち、熱間鍛造のままの丸棒から、JI
S G 0555の図1に則って試験片を採取し、鏡面研磨した
幅が15mmで高さが20mmの被検面を、倍率が40
0倍の光学顕微鏡で60視野観察して、Ti炭硫化物及
びZr炭硫化物を他の介在物と区分しながらその清浄度
(清浄度の和)を測定した。Ti炭硫化物及びZr炭硫
化物の最大直径も、倍率が400倍の光学顕微鏡で60
視野観察して調査した。
That is, the hot forged round bar was replaced with JI
A test piece was sampled according to FIG. 1 of SG 0555, and a mirror-polished test surface having a width of 15 mm and a height of 20 mm was placed at a magnification of 40.
By observing 60 visual fields with a 0-magnification optical microscope, the cleanliness (sum of cleanliness) was measured while separating Ti and Zr carbosulfides from other inclusions. The maximum diameters of Ti and Zr carbosulfides were also 60
The field of view was examined.
【0087】焼準のままの丸棒からは、直径が30mm
で厚さが20mmの試験片を切り出し、ナイタルで腐食
して倍率400倍の光学顕微鏡による組織観察を行っ
た。
From the as-normalized round bar, the diameter was 30 mm.
, A test piece having a thickness of 20 mm was cut out, corroded with nital, and observed under an optical microscope with a magnification of 400 times.
【0088】球状化焼鈍後の各丸棒からは、直径が30
mmで厚さが20mmの硬度試験片と直径が10mmで
長さが15mmの冷間加工用試験片を作製した。
From each round bar after the spheroidizing annealing, a diameter of 30
A 20 mm thick, 20 mm thick hardness test piece and a 10 mm diameter, 15 mm long cold test piece were prepared.
【0089】上記の硬度試験片を用いて、マイクロビッ
カース硬度計により中央部のHv硬度測定を行った。
Using the above-mentioned hardness test piece, the Hv hardness of the central portion was measured by a micro Vickers hardness meter.
【0090】又、上記の冷間加工用試験片を用いて、5
00t高速プレス機による通常の方法で冷間(室温)拘
束型据え込み試験を行い、限界据え込み率を測定した。
なお、各条件ごとに3回の据え込み試験を行い、3個の
試験片のすべてに割れが発生しない最大加工率(減面
率)を限界据え込み率として評価した。
Further, using the test piece for cold working described above,
A cold (room temperature) constrained upsetting test was performed by a normal method using a 00t high-speed press machine, and the limit upsetting ratio was measured.
In addition, three upsetting tests were performed for each condition, and the maximum working rate (area reduction rate) at which cracks did not occur in all three test pieces was evaluated as the limit upsetting rate.
【0091】一方、前記のようにして得られた球状化焼
鈍後の直径30mmの各丸棒を、直径25mmにピーリ
ング加工し、この後、通常の方法によって冷間(室温)
で直径20.9mm(減面率30.1%)までドローベ
ンチを用いて引き抜き加工した。次いで、RXガスにア
ンモニアガスを1:1の割合で添加した温度が570℃
のガス中で6時間保持して軟窒化処理を施し、その後油
中へ冷却した。
On the other hand, each round bar having a diameter of 30 mm after the spheroidizing annealing obtained as described above was subjected to a peeling process to a diameter of 25 mm, and thereafter, was subjected to cold (room temperature) by an ordinary method.
To 20.9 mm in diameter (30.1% reduction in area) using a draw bench. Next, the temperature at which ammonia gas was added to the RX gas at a ratio of 1: 1 was 570 ° C.
, A soft nitriding treatment was carried out for 6 hours, and then cooled into oil.
【0092】引き抜きままの丸棒からは、直径が20.
9mmで厚さが20mmの硬度試験片を作製し、マイク
ロビッカース硬度計を用いて中央部の硬度測定を行っ
た。又、軟窒化処理した丸棒からも、直径が20.9m
mで厚さが20mmの硬度試験片を作製し、マイクロビ
ッカース硬度計により表面硬度(表面から0.025m
mの位置におけるHv硬度)、有効硬化深さ(表面から
Hv500の位置までの距離)及び中央部硬度の測定を
行った。
From the as-pulled round bar, a diameter of 20.
A hardness test piece having a thickness of 9 mm and a thickness of 20 mm was prepared, and the hardness of the center portion was measured using a micro Vickers hardness tester. The diameter is 20.9m from the soft-nitrided round bar.
m and a hardness test piece having a thickness of 20 mm were prepared, and the surface hardness (0.025 m from the surface) was measured using a micro Vickers hardness tester.
m), the effective hardening depth (distance from the surface to the position of Hv500), and the center hardness were measured.
【0093】被削性評価のため、ドリル穿孔試験も実施
した。すなわち、既に述べた球状化焼鈍後の直径30m
mの丸棒及び引き抜き加工後の直径20.9mmの丸棒
を25mmの長さに輪切りにしたものを用いて、R/2
部(Rは丸棒の半径)についてその長さ方向に貫通孔を
あけ、刃先摩損により穿孔不能となったときの貫通孔の
個数を数え、被削性の評価を行った。穿孔条件は、JI
S高速度工具鋼SKH51のφ5mmストレートシャン
クドリルを使用し、水溶性の潤滑剤を用いて、送り0.
15mm/rev、回転数980rpmで行った。
[0093] For the evaluation of machinability, a drilling test was also performed. That is, the diameter 30 m after spheroidizing annealing already described.
m and a round bar having a diameter of 20.9 mm after drawing were cut into 25 mm lengths, and R / 2 was used.
Through holes were made in the length direction of the portion (R is the radius of the round bar), and the number of through holes when drilling was impossible due to abrasion of the cutting edge was counted to evaluate the machinability. The drilling conditions are JI
Using a φ5 mm straight shank drill made of S high speed tool steel SKH51 and using a water-soluble lubricant, the feed rate is set to 0.
The measurement was performed at 15 mm / rev and a rotation speed of 980 rpm.
【0094】表3に各種の試験結果をまとめて示す。な
お、表の「Ti、Zr炭硫化物」とした欄において、T
iとZrとを複合添加した場合には「最大直径」はいず
れか大きい方の炭硫化物の値であり、清浄度は清浄度の
和を意味する。
Table 3 summarizes the results of various tests. In the column of “Ti, Zr carbosulfide” in the table, T
When i and Zr are added in combination, the “maximum diameter” is the value of the larger one of the carbosulfides, and the cleanliness means the sum of the cleanliness.
【0095】[0095]
【表3】 [Table 3]
【0096】表3から、化学組成及び最大直径が10μ
m以下の「Ti、Zr炭硫化物」の清浄度が本発明で規
定する範囲内にある本発明例に係る鋼1〜10を素材と
するものは、球状化焼鈍後の硬度はいずれもHvで18
0を下回るもので、限界据え込み率は80%を超えてい
るし、被削性も良好である。そして、減面率30.1%
の冷間加工(引き抜き加工)によって、容易にHv25
0を超える硬度が得られているし、冷間引き抜き後の被
削性も良好である。更に、軟窒化後にはHv600を超
える表面硬度と、0.1mmを超える有効硬化深さが得
られており、しかも軟窒化のための570℃での6時間
の熱処理を受けても、中央部硬度(芯部硬度)は軟窒化
前のレベルに維持されているか、あるいは軟窒化前の硬
度より高くなっている。
Table 3 shows that the chemical composition and the maximum diameter were 10 μm.
m, the hardness after spheroidizing annealing is Hv for each of the steels 1 to 10 according to the present invention in which the cleanliness of “Ti, Zr carbosulfide” of not more than m is within the range specified in the present invention. At 18
Since it is less than 0, the critical upsetting ratio exceeds 80%, and the machinability is also good. And 30.1% of area reduction rate
Hv25 easily by cold working (drawing)
Hardness exceeding 0 is obtained, and machinability after cold drawing is also good. Furthermore, after nitrocarburizing, a surface hardness of more than Hv600 and an effective hardening depth of more than 0.1 mm are obtained. (Core hardness) is maintained at a level before nitrocarburizing or higher than that before nitrocarburizing.
【0097】これに対して比較例に係る鋼11〜20を
素材とする場合には、(イ)球状化焼鈍後の硬度がHv
180を超える、(ロ)冷間加工後の硬度が低いために
軟窒化後の芯部硬度も低い、(ハ)冷間加工後の硬度は
Hv250を超えるものの軟窒化後の芯部硬度はHv2
50を下回る、(ニ)軟窒化後の表面硬度がHv600
を下回る、(ホ)軟窒化後の有効硬化深さが0.1mm
を下回る、(ヘ)ドリル穿孔試験における貫通孔個数が
100を大きく下回り被削性に劣る、のいずれか1つ以
上に該当する。このため、冷間鍛造時の金型寿命が短く
て金型コストが嵩むし、所望の軟窒化部品の形状に成形
するための切削加工のコストも嵩むので、所望の軟窒化
部品の製造コストは極めて高いものとなってしまう。あ
るいは、製造コストは低くても軟窒化部品の耐疲労特
性、耐摩耗性、耐ピッチング性及び耐スポーリング性は
劣ったものとなってしまう。
On the other hand, when the steels 11 to 20 according to the comparative example are used as materials, (a) the hardness after spheroidizing annealing is Hv
(B) Core hardness after soft nitriding is low due to low hardness after cold working. (C) Hardness after cold working exceeds Hv250, but core hardness after soft nitriding is Hv2.
(D) surface hardness after nitrocarburizing is less than 50
(E) Effective hardening depth after nitrocarburizing is 0.1mm
And (f) the number of through holes in the drilling test is significantly less than 100 and the machinability is inferior. For this reason, the mold life at the time of cold forging is short, the mold cost increases, and the cutting cost for forming into a desired nitrocarburized part shape also increases. It will be extremely expensive. Alternatively, the fatigue resistance, wear resistance, pitting resistance, and spalling resistance of the nitrocarburized parts are inferior even though the manufacturing cost is low.
【0098】(実施例2)前記のようにして得られた直
径が38mmの丸棒を用いて、下記の各種調査を行っ
た。
(Example 2) The following various investigations were conducted using the round bar having a diameter of 38 mm obtained as described above.
【0099】すなわち、実施例1の場合と同様に、熱間
鍛造のままの丸棒から、JIS G 0555の図1に則って試験
片を採取し、鏡面研磨した幅が15mmで高さが20m
mの被検面を、倍率が400倍の光学顕微鏡で60視野
観察して、Ti炭硫化物及びZr炭硫化物を他の介在物
と区分しながらその清浄度(清浄度の和)を測定した。
Ti炭硫化物及びZr炭硫化物の最大直径も、倍率が4
00倍の光学顕微鏡で60視野観察して調査した。
That is, as in the case of Example 1, a test piece was sampled from a hot-forged round bar in accordance with JIS G 0555 in FIG.
The surface to be inspected for m is observed with an optical microscope having a magnification of 400 times in 60 visual fields, and its cleanliness (sum of cleanliness) is measured while distinguishing Ti and Zr carbosulfides from other inclusions. did.
The maximum diameter of Ti and Zr carbosulfides is also 4
Investigation was performed by observing 60 visual fields with an optical microscope of 00 times.
【0100】球状化焼鈍後の各丸棒からは、直径が38
mmで厚さが20mmの硬度試験片を作製し、これを用
いて、マイクロビッカース硬度計により中央部のHv硬
度測定を行った。
From each round bar after spheroidizing annealing, a diameter of 38
A hardness test piece having a thickness of 20 mm and a thickness of 20 mm was prepared, and the Hv hardness of the center portion was measured using a micro Vickers hardness meter.
【0101】更に、球状化焼鈍後の直径38mmの各丸
棒を、直径36mmにピーリング加工し、この後、通常
の方法によって冷間(室温)で直径30mm(減面率3
0.6%)までドローベンチを用いて引き抜き加工し
た。この後、図2に示す転動疲労試験片(小ローラー)
と環状半円溝付きの小野式回転曲げ疲労試験片(JIS Z2
274のD=10mm、d=8mm、ρ=t=1mm、D0
=12mmの試験片)を作製した。
Further, each round bar having a diameter of 38 mm after the spheroidizing annealing was peeled to a diameter of 36 mm, and thereafter, was cold (room temperature) with a diameter of 30 mm (area reduction rate of 3) by an ordinary method.
0.6%) using a draw bench. Thereafter, the rolling fatigue test piece (small roller) shown in FIG.
Ono-type rotating bending fatigue test piece with JIS Z2
274 D = 10 mm, d = 8 mm, ρ = t = 1 mm, D 0
= 12 mm test piece).
【0102】次いで、前記の各試験片を、RXガスにア
ンモニアガスを1:1の割合で添加した温度が570℃
のガス中で6時間保持して軟窒化処理を施し、その後油
中へ冷却した。なお、直径30mm×長さ100mmの
冷間引き抜きままのものに対しても、同時に上記の処理
を施した。
Next, each of the test pieces was heated to a temperature of 570 ° C. by adding ammonia gas to RX gas at a ratio of 1: 1.
, A soft nitriding treatment was carried out for 6 hours, and then cooled into oil. In addition, the above-mentioned process was also performed simultaneously with the thing of 30 mm in diameter x 100 mm in length as it was drawn cold.
【0103】引き抜きままの丸棒からは、直径が30m
mで厚さが20mmの硬度試験片を作製し、マイクロビ
ッカース硬度計を用いて中央部の硬度測定を行った。
又、軟窒化処理した丸棒からも、直径が30mmで厚さ
が20mmの硬度試験片を作製し、マイクロビッカース
硬度計により表面硬度(表面から0.025mmの位置
におけるHv硬度)、有効硬化深さ(表面からHv50
0の位置までの距離)及び中央部硬度の測定を行った。
From the round bar as drawn, the diameter is 30 m.
A hardness test piece having a thickness of 20 mm and a thickness of 20 mm was prepared, and the hardness of the central portion was measured using a micro Vickers hardness meter.
A hardness test piece having a diameter of 30 mm and a thickness of 20 mm was also prepared from the soft-nitrided round bar, and the surface hardness (Hv hardness at a position of 0.025 mm from the surface) and the effective hardening depth were measured with a micro Vickers hardness meter. Sa (Hv50 from the surface
0) and the hardness at the center.
【0104】一方、軟窒化処理した小野式回転曲げ疲労
試験片と転動疲労試験片を用いて、疲労特性を調査し
た。
On the other hand, fatigue characteristics were investigated using the Ono-type rotating bending fatigue test piece and the rolling fatigue test piece subjected to the nitrocarburizing treatment.
【0105】すなわち、常温(室温)、大気中、回転数
3000rpmの条件で小野式回転曲げ疲労試験を行
い、曲げ疲労強度(疲労限)を求めた。
That is, an Ono-type rotating bending fatigue test was performed at room temperature (room temperature) and in the atmosphere at a rotation speed of 3000 rpm, and the bending fatigue strength (fatigue limit) was determined.
【0106】又、回転数1000rpm、潤滑油の温度
80℃、すべり率40%の条件でローラーピッチング試
験機を用いて、面疲労強度を求めた。なお、相手材とな
る大ローラーには、JISのSUJ2を用いて硬度をロ
ックウェルC硬度(HRC)で61に調整し、外径13
0mm、内径45mm、厚さ18mmに加工したものを
使用した。そして、前記の試験条件で107 回の回転が
可能な面圧を「面疲労強度」として評価した。
The surface fatigue strength was determined using a roller pitching tester under the conditions of a rotation speed of 1,000 rpm, a lubricating oil temperature of 80 ° C., and a slip ratio of 40%. The hardness of the mating roller is adjusted to 61 by Rockwell C hardness (HRC) using JIS SUJ2, and the outer diameter is 13 mm.
One processed to 0 mm, an inner diameter of 45 mm, and a thickness of 18 mm was used. Then, the surface pressure capable of rotating 10 7 times under the test conditions described above was evaluated as “surface fatigue strength”.
【0107】表4に各種の試験結果をまとめて示す。な
お、この表についても、「Ti、Zr炭硫化物」とした
欄において、TiとZrとを複合添加した場合には「最
大直径」はいずれか大きい方の炭硫化物の値であり、清
浄度は清浄度の和を意味する。
Table 4 summarizes the results of various tests. Also in this table, in the column of “Ti, Zr carbosulfide”, when the combination of Ti and Zr is added, the “maximum diameter” is the value of the larger carbosulfide, and Degree means the sum of cleanliness.
【0108】[0108]
【表4】 [Table 4]
【0109】表4から、化学組成及び最大直径が10μ
m以下の「Ti、Zr炭硫化物」の清浄度が本発明で規
定する範囲内にある本発明例に係る鋼1〜10を素材と
するものは、前記の実施例1におけると同様に、球状化
焼鈍後の硬度はいずれもHvで180を下回っている。
そして、減面率で30.6%の冷間加工(引き抜き加
工)によって、容易にHv250を超える硬度が得られ
ている。更に、軟窒化後にはHv600を超える表面硬
度と、0.1mmを超える有効硬化深さが得られてお
り、しかも軟窒化のための570℃での6時間の熱処理
を受けても、中央部硬度(芯部硬度)は軟窒化前のレベ
ルに維持されているか、あるいは軟窒化前の硬度より高
くなっている。
Table 4 shows that the chemical composition and the maximum diameter were 10 μm.
m and the steels 1 to 10 according to the present invention in which the cleanliness of “Ti, Zr carbosulfide” is within the range specified in the present invention, as in the above-mentioned Example 1, The hardness after spheroidizing annealing is less than 180 in Hv.
Then, a hardness exceeding Hv250 is easily obtained by cold working (drawing processing) with a surface reduction rate of 30.6%. Furthermore, after nitrocarburizing, a surface hardness of more than Hv600 and an effective hardening depth of more than 0.1 mm are obtained. (Core hardness) is maintained at a level before nitrocarburizing or higher than that before nitrocarburizing.
【0110】更に、曲げ疲労強度は55kgf/mm2
以上の値を有し、面疲労強度も245kgf/mm2
超える値が得られている。
Further, the bending fatigue strength is 55 kgf / mm 2
It has the above values, and the surface fatigue strength is also a value exceeding 245 kgf / mm 2 .
【0111】これに対して比較例に係る鋼11〜20を
素材とする場合には、(イ)球状化焼鈍後の硬度がHv
180を超える、(ロ)冷間加工後の硬度が低いために
軟窒化後の芯部硬度も低い、(ハ)冷間加工後の硬度は
Hv250を超えるものの軟窒化後の芯部硬度はHv2
50を下回る、(ニ)軟窒化後の表面硬度がHv600
を下回る、(ホ)軟窒化後の有効硬化深さが0.1mm
を下回る、のいずれか1つ以上に該当する。更に、曲げ
疲労強度も高々46kgf/mm2 で、本発明例の鋼材
を素材とする場合と比較して明らかに劣っている。
On the other hand, when the steels 11 to 20 according to the comparative example are used as the material, (a) the hardness after the spheroidizing annealing is Hv
(B) The hardness of the core after soft-nitriding is low because the hardness after cold working is low.
(D) surface hardness after nitrocarburizing is less than 50
(E) Effective hardening depth after nitrocarburizing is 0.1mm
, And falls under any one or more of the following. Furthermore, the bending fatigue strength is at most 46 kgf / mm 2 , which is clearly inferior to the case where the steel material of the present invention is used as a material.
【0112】[0112]
【発明の効果】本発明の軟窒化部品は、耐疲労特性、耐
摩耗性、耐ピッチング性及び耐スポーリング性に優れる
ことから、自動車用や産業機械用の歯車など大きな疲労
強度や耐摩耗性が要求される部品として利用することが
できる。なお、Hv250以上の高い芯部硬度が安定し
て確保できるので、特に大きな曲げ疲労強度が要求され
る部品にも用いることができる。この軟窒化部品の素材
となる被削性に優れた軟窒化用鋼材は、本発明の方法に
よって比較的容易に製造することができる。
The nitrocarburized parts of the present invention are excellent in fatigue resistance, wear resistance, pitting resistance and spalling resistance, so that they have great fatigue strength and wear resistance such as gears for automobiles and industrial machines. Is required. In addition, since a high core hardness of Hv250 or more can be stably ensured, it can also be used for parts requiring particularly high bending fatigue strength. The steel material for nitrocarburizing, which is excellent in machinability and is used as the material for the nitrocarburized component, can be produced relatively easily by the method of the present invention.
【図面の簡単な説明】[Brief description of the drawings]
【図1】実施例における球状化焼鈍のヒートパターンを
示す図である。
FIG. 1 is a diagram showing a heat pattern of spheroidizing annealing in an example.
【図2】実施例で用いた転動疲労試験片の形状を示す図
である。
FIG. 2 is a view showing the shape of a rolling fatigue test piece used in an example.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 平5−59488(JP,A) 特開 平9−256045(JP,A) 特開 昭55−6456(JP,A) 特開 昭55−152175(JP,A) 特開 平11−181518(JP,A) 特開 平10−298704(JP,A) 特開 平11−293390(JP,A) (58)調査した分野(Int.Cl.7,DB名) C22C 38/00 - 38/60 ────────────────────────────────────────────────── ─── Continuation of the front page (56) References JP-A-5-59488 (JP, A) JP-A-9-256045 (JP, A) JP-A-55-6456 (JP, A) JP-A-55-456 152175 (JP, A) JP-A-11-181518 (JP, A) JP-A-10-298704 (JP, A) JP-A-11-293390 (JP, A) (58) Fields investigated (Int. Cl. 7 , DB name) C22C 38/00-38/60

Claims (3)

    (57)【特許請求の範囲】(57) [Claims]
  1. 【請求項1】重量%で、C:0.15〜0.45%、S
    i:0.05〜0.5%、Mn:0.2〜2.5%、
    S:0.002〜0.2%、Cu:0.5〜1.5%、
    Ni:0.25〜0.75%で、且つ1.8≦Cu
    (%)/Ni(%)≦2.2、Cr:0.5〜2%、
    V:0.05〜0.5%、Ti:0〜1.0%、Zr:
    0〜1.0%で、且つTi(%)+Zr(%):0.0
    4〜1.0%、Al:0.01〜0.3%、N:0.0
    08%以下、Mo:0.02〜0.3%及びW:0.0
    〜0.5%のうちの1種以上を含み、下記式で表さ
    れるfn1が0%を超え、残部はFe及び不可避不純物
    の化学組成で、更に鋼中のTi炭硫化物及びZr炭硫化
    物の最大直径が10μm以下で、且つ、その量の和が清
    浄度で0.05%以上である鋼を、熱間加工後に球状化
    焼鈍して硬度をHv180以下とし、次いで冷間加工し
    て硬度をHv250以上にすることを特徴とする被削性
    に優れた軟窒化用鋼材の製造方法。 fn1=Ti(%)+Zr(%)−1.2S(%)・・・・
    C. 0.15 to 0.45% by weight, S
    i: 0.05 to 0.5%, Mn: 0.2 to 2.5%,
    S: 0.002-0.2%, Cu: 0.5-1.5%,
    Ni: 0.25 to 0.75%, and 1.8 ≦ Cu
    (%) / Ni (%) ≦ 2.2, Cr: 0.5 to 2%,
    V: 0.05 to 0.5%, Ti: 0 to 1.0 %, Zr:
    0 to 1.0 % , and Ti (%) + Zr (%): 0.0
    4 to 1.0%, Al: 0.01 to 0.3%, N: 0.0
    08% or less, Mo: 0.02 to 0.3% and W: 0.0
    5 to 0.5% , fn1 represented by the following formula exceeds 0%, the balance is the chemical composition of Fe and unavoidable impurities, and further, Ti carbosulfide and Zr carbon in steel. A steel having a maximum diameter of sulfide of 10 μm or less and the sum of the amounts is 0.05% or more in cleanliness is subjected to spheroidizing annealing after hot working to a hardness of Hv 180 or less, and then to cold working. A method for producing a steel material for nitrocarburizing excellent in machinability, wherein the hardness is Hv 250 or more. fn1 = Ti (%) + Zr (%)-1.2S (%)
  2. 【請求項2】重量%で、C:0.15〜0.45%、S
    i:0.05〜0.5%、Mn:0.2〜2.5%、
    S:0.002〜0.2%、Cu:0.5〜1.5%、
    Ni:0.25〜0.75%で、且つ1.8≦Cu
    (%)/Ni(%)≦2.2、Cr:0.5〜2%、
    V:0.05〜0.5%、Ti:0〜1.0%、Zr:
    0〜1.0%で、且つTi(%)+Zr(%):0.0
    4〜1.0%、Al:0.01〜0.3%、N:0.0
    08%以下、Mo:0.02〜0.3%及びW:0.0
    5〜0.5%のうちの1種以上、並びに、Pb:0.0
    3〜0.35%及びCa:0.001〜0.01%のう
    ちの1種以上を含み、下記式で表されるfn1が0%
    を超え、残部はFe及び不可避不純物の化学組成で、更
    に鋼中のTi炭硫化物及びZr炭硫化物の最大直径が1
    0μm以下で、且つ、その量の和が清浄度で0.05%
    以上である鋼を、熱間加工後に球状化焼鈍して硬度をH
    v180以下とし、次いで冷間加工して硬度をHv25
    0以上にすることを特徴とする被削性に優れた軟窒化用
    鋼材の製造方法。 fn1=Ti(%)+Zr(%)−1.2S(%)・・・・
    2. C: 0.15 to 0.45% by weight, S
    i: 0.05 to 0.5%, Mn: 0.2 to 2.5%,
    S: 0.002-0.2%, Cu: 0.5-1.5%,
    Ni: 0.25 to 0.75%, and 1.8 ≦ Cu
    (%) / Ni (%) ≦ 2.2, Cr: 0.5 to 2%,
    V: 0.05 to 0.5%, Ti: 0 to 1.0%, Zr:
    0 to 1.0%, and Ti (%) + Zr (%): 0.0
    4 to 1.0%, Al: 0.01 to 0.3%, N: 0.0
    08% or less, Mo: 0.02 to 0.3% and W: 0.0
    One or more of 5 to 0.5%, and Pb: 0.0
    3 to 0.35% and Ca: 0.001 to 0.01%
    Fn1 represented by the following formula containing 0% or more
    The remainder is the chemical composition of Fe and unavoidable impurities.
    The maximum diameter of Ti and Zr carbosulfides in steel is 1
    0 μm or less, and the sum of the amounts is 0.05% in cleanliness
    The above steel is subjected to spheroidizing annealing after hot working to have a hardness of H
    v180 or less, then cold worked to a hardness of Hv25
    For nitrocarburizing with excellent machinability characterized by being 0 or more
    Method of manufacturing steel. fn1 = Ti (%) + Zr (%)-1.2S (%)
  3. 【請求項3】(3) 請求項1又は2に記載の化学組成、請求項The chemical composition according to claim 1 or 2,
    1又は2に記載の大きさ及び量のTi炭硫化物とZr炭Ti carbosulfide and Zr charcoal of the size and amount described in 1 or 2
    硫化物、並びに球状化組織を備え、表面硬度がHv60It has a sulfide and a spheroidized structure, and has a surface hardness of Hv60.
    0以上、且つ、有効硬化深さが0.1mm以上、芯部硬0 or more, effective hardening depth of 0.1 mm or more, core hardness
    度がHv250以上であることを特徴とする軟窒化部Nitrocarburized part having a degree of Hv250 or more
    品。Goods.
JP11538898A 1998-04-24 1998-04-24 Method of manufacturing steel for nitrocarburizing and nitrocarburized parts using the steel Expired - Fee Related JP3353698B2 (en)

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WO2011114775A1 (en) 2010-03-16 2011-09-22 新日本製鐵株式会社 Steel for nitrocarburization, nitrocarburized components, and production method for same

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WO2002077309A1 (en) * 2001-03-23 2002-10-03 Sumitomo Metal Industries, Ltd. Cast steel and metal mold for casting
WO2009119388A1 (en) * 2008-03-27 2009-10-01 日立金属株式会社 Piston ring material for internal combustion engine

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JPS556456A (en) * 1978-06-29 1980-01-17 Daido Steel Co Ltd Blank for surface hardened material having less heat treatment strain
JPS55152175A (en) * 1979-05-18 1980-11-27 Daido Steel Co Ltd Low-strain high strength gear
JPH0559488A (en) * 1991-09-02 1993-03-09 Kobe Steel Ltd Precipitation hardening type high strength steel for soft-nitriding excellent in machinability
JPH09256045A (en) * 1996-03-22 1997-09-30 Sumitomo Metal Ind Ltd Production of steel for soft-nitriding and soft-nitrided parts using the same steel
JP3489655B2 (en) * 1997-02-27 2004-01-26 住友金属工業株式会社 High-strength, high-toughness free-cut non-heat treated steel
JP3855418B2 (en) * 1997-12-19 2006-12-13 住友金属工業株式会社 Method of manufacturing nitrocarburizing steel material and nitrocarburized component using the steel material
JP3489434B2 (en) * 1998-04-10 2004-01-19 住友金属工業株式会社 High-strength free-cut non-heat treated steel

Cited By (3)

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Publication number Priority date Publication date Assignee Title
WO2011114775A1 (en) 2010-03-16 2011-09-22 新日本製鐵株式会社 Steel for nitrocarburization, nitrocarburized components, and production method for same
US9284632B2 (en) 2010-03-16 2016-03-15 Nippon Steel & Sumitomo Metal Corporation Steel for nitrocarburizing, nitrocarburized steel part, and producing method of nitrocarburized steel part
US10196720B2 (en) 2010-03-16 2019-02-05 Nippon Steel & Sumitomo Metal Corporation Steel for nitrocarburizing, nitrocarburized steel part, and producing method of nitrocarburized steel part

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