JP2737386B2 - Carburized case hardened steel with excellent wear resistance - Google Patents
Carburized case hardened steel with excellent wear resistanceInfo
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- JP2737386B2 JP2737386B2 JP2285473A JP28547390A JP2737386B2 JP 2737386 B2 JP2737386 B2 JP 2737386B2 JP 2285473 A JP2285473 A JP 2285473A JP 28547390 A JP28547390 A JP 28547390A JP 2737386 B2 JP2737386 B2 JP 2737386B2
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Description
【発明の詳細な説明】 〈産業上の利用分野〉 この発明は、自動車，土木建設機械，産業機械等の摩
耗が生じやすい部位に使用される部品（歯車，シャフ
ト，ブッシュ等）用素材として好適な、耐摩耗性に優れ
た浸炭肌焼鋼に関するものである。DETAILED DESCRIPTION OF THE INVENTION <Industrial Application Field> The present invention is suitable as a material for parts (gears, shafts, bushes, etc.) used in parts where wear is likely to occur, such as automobiles, civil engineering and construction machines, and industrial machines. And a carburized case hardened steel having excellent wear resistance.
〈従来技術とその課題〉 浸炭肌焼鋼は、本来、母材炭素量を0.15〜0.25％（以
降、成分割合を表わす％は重量％とする）に調整して靭
性を確保すると共に、浸炭処理により表層部のみを炭素
量を0.8〜0.9％程度に高めて表面硬さを増加させ、所望
靭性と耐摩耗性を兼ね備えしめることを目的として案出
された鋼であるが、現在、一般的にはJIS規格のSCr415,
SCr420,SCM420,SNCM420等がこの目的で多く使用され、
歯車，シャフト，ブッシュ等に供されている。<Prior art and its problems> Carburized case-hardened steel originally has a base material carbon content of 0.15 to 0.25% (hereinafter,% representing the component ratio is referred to as% by weight) to ensure toughness and carburizing treatment. The steel was devised for the purpose of increasing the surface hardness by increasing the carbon content of only the surface layer to about 0.8 to 0.9%, thereby providing the desired toughness and wear resistance. Is JIS standard SCr415,
SCr420, SCM420, SNCM420 etc. are often used for this purpose,
Used for gears, shafts, bushes, etc.
しかし、最近、前記機械・装置類に対する性能や耐久
性の向上要求が一段と高まる中で、十分な靭性を備えた
ままで従来の浸炭肌焼鋼よりも更に耐摩耗性の優れた材
料の開発が強く求められるようになってきた。However, recently, as the demand for improving the performance and durability of the machines and devices has been further increased, the development of materials having more excellent wear resistance than conventional carburized case hardening steel with sufficient toughness has been strongly developed. It has become required.
そこで、このような要望に応えるべく、鋼中のCr含有
量を増加させ、かつ浸炭雰囲気の炭素ポテンシャルを1.
3〜1.5％と言う高い値にして表層部に球状炭化物を生成
させる“過剰浸炭”が提案され、そのための“過剰浸炭
用鋼”の開発もなされた。Therefore, in order to meet such a demand, the Cr content in steel was increased, and the carbon potential of the carburizing atmosphere was increased by 1.
"Excess carburizing" was proposed, which produces spherical carbides in the surface layer at a high value of 3 to 1.5%, and "excess carburizing steel" was developed for that purpose.
ところが、“過剰浸炭”には、処理時にスーチング
（すすの発生）を起こして作業性を低下させる上、環境
を悪化させると言う問題もあることから、“通常浸炭”
によっても耐摩耗性を十分に向上できる浸炭肌焼鋼の開
発が望まれている。However, "excess carburization" has the problem of causing sooting (formation of soot) during processing to lower workability and deteriorating the environment.
Therefore, development of carburized case hardening steel which can sufficiently improve wear resistance is desired.
〈課題を解決するための手段〉 本発明者等は、上述のような観点から、通常浸炭でも
十分に満足できる優れた耐摩耗性を付与することのでき
る浸炭肌焼鋼を実現すべく、特に従来の浸炭肌焼高を達
成する成分個々の作用について基礎的な再検討を加えつ
つ研究を重ねた結果、「Crには鋼の浸炭特性を向上させ
て浸炭層を深くする効果があるが、通常浸炭の条件下で
は耐摩耗性の改善に有効な球状炭化物を生成させる効果
は認められない。ところが、一般には快削性向上元素と
して快削鋼に添加される。“Pb"は、それのみでは鋼の
浸炭特性を向上させる効果はないものの、その所定量を
Crの所定量と共に添加した場合には両者の相乗的効果が
発揮され、通常浸炭の条件下であっても表層部での球状
炭化物の安定生成を可能とし、耐摩耗性の著しい向上を
もたらす」との知見を得るに至ったのである。<Means for Solving the Problems> The present inventors, from the viewpoints described above, in order to realize a carburized case hardening steel capable of imparting excellent wear resistance sufficiently satisfactory even in normal carburization, As a result of repeated studies with basic reexamination on the effects of individual components that achieve conventional carburizing case hardening height, `` Cr has the effect of improving the carburizing characteristics of steel and deepening the carburized layer, Normally, under carburizing conditions, there is no effect of forming spherical carbides that are effective in improving wear resistance, but it is generally added to free-cutting steel as a free-cutting property improving element. Does not have the effect of improving the carburizing properties of steel,
When added together with a predetermined amount of Cr, a synergistic effect of the two is exhibited, enabling stable generation of spherical carbides in the surface layer even under normal carburizing conditions, and significantly improving wear resistance. '' That led to the finding.
本発明は、上記知見事項等に基づいてなされたもの
で、 「浸炭肌焼鋼を、 C:0.10〜0.30％,Si:0.50以下， Mn:2.00以下,Cr:1.2超〜5.0％ Pb:0.06超〜0.50％ を含有すると共に、更に Cu:1.0％以下,Ni:3.50以下， Mo:2.00％以下,Al:0.010〜0.100％， Ti:0.010〜0.100％,V:0.01〜0.30％， B:0.0003〜0.0050％,Nb:0.010〜0.100％ の１種以上をも含み、残部がFe及び不可避的不純物から
成る化学成分組成に構成することにより、通常浸炭によ
っても表層部に球状炭化物が安定して生成され、その耐
摩耗性が顕著に向上されるようにした点」 に大きな特徴を有している。The present invention has been made based on the above findings and the like. "Carburized case hardening steel is C: 0.10 to 0.30%, Si: 0.50 or less, Mn: 2.00 or less, Cr: more than 1.2 to 5.0% Pb: 0.06% In addition to containing up to 0.50%, Cu: 1.0% or less, Ni: 3.50 or less, Mo: 2.00% or less, Al: 0.010 to 0.100%, Ti: 0.010 to 0.100%, V: 0.01 to 0.30%, B: 0.0003 to 0.0050%, Nb: 0.010 to 0.100% or more, and the balance is composed of a chemical composition composed of Fe and unavoidable impurities. It is produced and its wear resistance is remarkably improved.
このように、本発明は鋼中に所定量のCr及びPbを共存
させると同時に、鋼全体の化学成分を厳密に共存するこ
とによって通常浸炭で表層部に球状炭化物が生成される
ようにし、その耐摩耗性を著しく向上させ得るようにし
たことを骨子とするものであるが、以下、本発明に係る
浸炭肌焼鋼において、その化学成分組成を前記の如くに
限定した理由を各成分の作用と共に説明する。As described above, the present invention allows a predetermined amount of Cr and Pb to coexist in the steel, and at the same time, strictly coexists the chemical components of the entire steel, so that a spherical carbide is generated on the surface layer by ordinary carburization, The main point is that the wear resistance can be significantly improved.However, in the carburized case hardening steel according to the present invention, the reason why the chemical component composition is limited as described above is described below. It is explained together with.
〈作用〉 ａ）Ｃ Ｃは鋼に所定の静的強度を付与するのに必要な成分で
あるが、一方で靭性を劣化させる元素でもある。特に、
浸炭処理を施す肌焼鋼においては静的強度と靭性の好適
なバランスが必要であるため、Ｃ含有量の調整は非常に
重要である。ここで、Ｃ含有量が0.10％未満では所望の
静的強度を確保することができず、一方、0.30％を超え
てＣを含有させると所望靭性の確保が困難となることか
ら、Ｃ含有量が0.10〜0.30％と定めた。<Operation> a) C C is a component necessary for imparting a predetermined static strength to steel, but is also an element that deteriorates toughness. Especially,
Adjustment of the C content is very important in case hardening steel to be carburized because a suitable balance between static strength and toughness is required. Here, if the C content is less than 0.10%, the desired static strength cannot be ensured. On the other hand, if the C content exceeds 0.30%, it becomes difficult to secure the desired toughness. Was determined to be 0.10 to 0.30%.
ｂ）Si Siは鋼の脱酸に必要な元素であり、また鋼に所望の静
的強度を付与するのに必要な成分でもある。しかし、0.
50％を超えてSiを含有させると浸炭性が劣化し、浸炭処
理を条件とする肌焼鋼としては不利になる上、浸炭異常
層の生成が著しくなって最表面の硬度低下を招く。この
ようなことから、Si含有量の上限を0.50％と定めた。b) Si Si is an element necessary for deoxidizing steel and also a component necessary for imparting a desired static strength to steel. But 0.
If Si is contained in excess of 50%, the carburizing property is deteriorated, which is disadvantageous for case hardening steel subject to carburizing treatment, and the formation of an abnormal carburizing layer is remarkable, leading to a decrease in the hardness of the outermost surface. For these reasons, the upper limit of the Si content is set to 0.50%.
ｃ）Mn Mnも、Siと同様、鋼の脱酸に必要な元素であり、また
焼入れ性を付与するのに必要な元素でもある。しかし、
2.00％を超えてMnを含有させると高温軟化抵抗が低下
し、静的強度の低下をもたらす。従って、Mnを含有量の
上限を2.00％と定めた。c) Mn Mn, like Si, is an element necessary for deoxidizing steel and also an element necessary for imparting hardenability. But,
When Mn is contained in excess of 2.00%, the high-temperature softening resistance decreases, and the static strength decreases. Therefore, the upper limit of the content of Mn is set to 2.00%.
ｄ）Cr Crは鋼に焼入性を付与するのに有効な元素であると共
に、浸炭性を向上させる作用を有していることから、一
般の肌焼鋼においても必須成分として用いられることが
多い元素である。本発明においてもCrが有する前記作用
が利用されるが、これに加え、Pbとの共存で発揮される
「通常浸炭で表層部に球状炭化物を生成する作用」が最
大限に利用される。この場合、Cr含有量が1.2％を超え
ると上記作用による十分な効果が得られるが、5.0％を
超えてCrを含有させるとCr酸化物が生成して浸炭性の低
下を招くようになることから、Cr含有量は1.2超〜5.0％
と定めた。d) Cr Cr is an element effective for imparting hardenability to steel, and has an effect of improving carburizing properties. Therefore, it may be used as an essential component in general case hardening steel. Many elements. In the present invention, the above-mentioned action of Cr is used, but in addition to this, the "action to form spherical carbide in the surface layer by normal carburization" exhibited in coexistence with Pb is used to the maximum. In this case, if the Cr content exceeds 1.2%, a sufficient effect can be obtained by the above-mentioned action. However, if the Cr content exceeds 5.0%, Cr oxide is generated and the carburizing property is reduced. Therefore, Cr content is more than 1.2 to 5.0%
It was decided.
ｅ）Pb 前述した如く、一般的にはPbは切削性を向上させる元
素として知られ、快削鋼に添加される成分である。しか
し、本発明者等の研究により、Pbは切削性の向上作用の
みでなく、Crとの共存下では浸炭層に球状炭化物の生成
を促進させる働きのあることが判明した。ここで、通常
浸炭で鋼の表層部に球状炭化物を生成させるためには、
所定量のCrの存在下でPb量を0.06％超に調整すれば十分
であるが、0.50％を超えて含有させると鋼の静的強度及
び靭性が共に低下する。従って、Pb含有量は0.06超〜0.
50％と定めた。e) Pb As described above, Pb is generally known as an element for improving machinability, and is a component added to free-cutting steel. However, studies by the present inventors have revealed that Pb not only has an effect of improving machinability, but also has a function of promoting the formation of spherical carbides in a carburized layer in the presence of Cr. Here, in order to form spherical carbides on the surface layer of steel by normal carburizing,
It is sufficient to adjust the amount of Pb to more than 0.06% in the presence of a predetermined amount of Cr, but if it exceeds 0.50%, both the static strength and the toughness of the steel decrease. Therefore, the Pb content is more than 0.06 to 0.
It was set at 50%.
ｆ）Cu,Ni,Mo,V及びＢ これらの元素には何れも鋼の静的強度を向上させる作
用があるので、必要により１種又は２種以上添加される
ものであるが、個々の含有量を前記の如くに限定した理
由をその他の作用と共に説明する。f) Cu, Ni, Mo, V and B Each of these elements has an effect of improving the static strength of steel, so one or more of these elements may be added as necessary. The reason why the amount is limited as described above will be described together with other effects.
Cu Cuには鋼の焼入性と静的強度を上昇させる作用がある
が、1.0％を超えて含有させると熱間加工性の低下や静
的強度の低下を招くようになることから、Cu含有量は1.
0以下と定めた。Cu Cu has the effect of increasing the hardenability and static strength of steel.However, if it is contained in excess of 1.0%, the hot workability is reduced and the static strength is reduced. Content is 1.
0 or less.
Ni NiもCuと同様に鋼の焼入性と静的強度を上昇させる作
用を有している上、鋼の靭性向上にも有効な元素である
が、3.50％を超えて含有させてもその効果が飽和するこ
とから、経済性を考慮してNi含有量の上限を3.50％と定
めた。Ni Ni, like Cu, has the effect of increasing the hardenability and static strength of steel, and is also an effective element for improving the toughness of steel. Since the effect is saturated, the upper limit of the Ni content is set to 3.50% in consideration of economic efficiency.
Mo Moは、鋼の焼入性，静的強度及び靭性を向上させる作
用のほか、球状炭化物生成を促進させる作用を有してい
る。しかし、2.00％を超えて含有させてもその効果が飽
和することから、経済性を考慮してMo含有量の上限を2.
00％と定めた。Mo Mo has an effect of improving the hardenability, static strength and toughness of steel, and an effect of promoting the formation of spherical carbides. However, the effect saturates even if it exceeds 2.00%, the upper limit of the Mo content is set to 2.
It was set to 00%.
Ｖ Ｖは鋼中で炭窒化物を析出させ、鋼の高温強度を高め
るのに有効な元素である。例えば、高出力エンジンの歯
車として使用された場合、所望の熱間静的強度を発揮さ
せるためには0.01％以上含有させることが必要である。
しかし、0.30％を超えて含有させると熱間加工性の低下
を招く。従って、Ｖ含有量は0.01〜0.30％と定めた。VV is an element effective for precipitating carbonitride in steel and increasing the high-temperature strength of steel. For example, when used as a gear of a high-power engine, it is necessary to contain 0.01% or more in order to exhibit a desired hot static strength.
However, when the content exceeds 0.30%, the hot workability is reduced. Therefore, the V content was determined to be 0.01 to 0.30%.
Ｂ Ｂには、鋼の焼入性を向上させ静的強度を上昇させる
作用があるが、その含有量が0.0003％未満では前記作用
による所望の効果が得られず、一方、0.0050％を超えて
含有させると鋼の結晶粒を粗大化させて靭性の劣化を招
くようになることから、Ｂ含有量は0.0003〜0.0050％と
定めた。BB has the effect of improving the hardenability of steel and increasing the static strength. However, if the content is less than 0.0003%, the desired effect due to the above-mentioned effects cannot be obtained. When B is contained, the crystal grains of the steel are coarsened and the toughness is deteriorated. Therefore, the B content is set to 0.0003 to 0.0050%.
ｇ）Al,Ti及びNb これらの元素には何れも鋼の靭性を改善する作用があ
るので、必要により１種又は２種以上添加されるもので
るが、個々の含有量を前記の如くに限定した理由をその
他の作用と共に説明する。g) Al, Ti and Nb Each of these elements has an effect of improving the toughness of steel, so one or more of these elements may be added as necessary, but the content of each element is limited as described above. The reason for this will be described together with other actions.
Al,Ti Al,Tiには、それぞれ高温状態の鋼の結晶粒を微細化
して靭性を向上させる作用があるが、その含有量が各々
0.010％未満では、前記作用による所望の効果が得られ
ず、一方、0.100％を超えて含有させると鋼の清浄度が
悪化して切削性を損なわせ、また鋼の結晶粒を粗大化さ
せて靭性を低下させるようになることから、Al,Tiの含
有量はそれぞれ0.010〜0.100％と定めた。Al, Ti Al and Ti have the effect of improving the toughness by refining the crystal grains of the steel in the high-temperature state.
If the content is less than 0.010%, the desired effect cannot be obtained by the above-mentioned action. On the other hand, if the content exceeds 0.100%, the cleanliness of the steel is deteriorated, the machinability is impaired, and the crystal grains of the steel are coarsened. Since the toughness is reduced, the contents of Al and Ti are set to 0.010 to 0.100%, respectively.
Nb Nbは、Ti等と同様に鋼の結晶粒を微細化し靭性を向上
させる作用を有すると共に、球状化炭化物の生成を促進
させる作用も認められるが、その含有量が0.010％未満
では前記作用による所望の効果が得られず、一方、0.10
0％を超えて含有させると機械加工時の切削性を損なう
ほか、結晶粒を粗大化させて靭性を劣化するようになる
ことから、Nb含有量は0.010〜0.100％と定めた。Nb Nb has the effect of refining the crystal grains of steel and improving the toughness similarly to Ti and the like, and also has the effect of accelerating the generation of spheroidized carbides. The desired effect was not obtained, while 0.10
If the Nb content exceeds 0%, the machinability during machining is impaired, and the crystal grains are coarsened to deteriorate the toughness. Therefore, the Nb content is determined to be 0.010 to 0.100%.
次いで、本発明の効果を実施例によって更に具体的に
説明する。Next, the effects of the present invention will be described more specifically with reference to examples.
〈実施例〉 まず、150kg真空溶解炉にて第１表に示した各化学成
分組成の鋼を溶製した後、得られた鋼塊を1250℃に１時
間加熱し、30mmφに鍛伸し て得た材料について、各々浸炭後の耐摩耗性，浸炭特性
（最高硬さ，浸炭深さ，球状炭化物の有無，異常組織の
深さ，静的曲げ強度），浸炭後の衝撃特性，及びオース
テナイト粒度番号を調査した。<Example> First, after smelting steel of each chemical composition shown in Table 1 in a 150 kg vacuum melting furnace, the obtained steel ingot was heated to 1250 ° C for 1 hour and forged to 30 mmφ. Wear resistance after carburizing, carburizing properties (maximum hardness, carburizing depth, presence or absence of spherical carbide, abnormal microstructure depth, static bending strength), impact properties after carburizing, and austenite The particle size number was investigated.
なお、「耐摩耗性」については、前記鍛伸材を925℃
×１時間で焼準した後10φ×100Lの寸法に加工し、続い
て第１図に示すヒートパターンにて浸炭処理した後、ガ
ウジング摩耗試験により摩耗量を測定する手法で調査し
た。ガウジング摩耗試験条件は、面圧:2.8kg/cm2,摩耗
速度:33m/min,摩耗距離:500m一定，研磨剤:SiCであっ
た。In addition, about "abrasion resistance", the said forged material
After normalizing for × 1 hour, working to a size of 10φ × 100 L , followed by carburizing treatment with the heat pattern shown in FIG. 1, and then investigating by a method of measuring the amount of wear by a gouging wear test. The gouging wear test conditions were as follows: surface pressure: 2.8 kg / cm 2 , wear rate: 33 m / min, wear distance: 500 m, abrasive: SiC.
また、「浸炭特性」については、前記鍛伸材を925℃
×１時間で焼準した後、これら焼準材を30φ×15Lに加
工し，続いて第１図に示すヒートパターンにて浸炭処理
したものにつき、浸炭層の硬度分布測定，球状炭化物観
察，異常組織観察を行って調査した。なお、静的曲げ試
験では、上記焼準材から第２図に示す形状・寸法の試験
片を切り出した後、第１図に示すヒートパターンにて浸
炭処理し、10-2/sの速度で静的曲げ強度を調査する手法
を採用したが、静的曲げ強度は破断荷重にて評価した。Regarding the “carburizing properties”, the forged material was heated at 925 ° C.
After normalizing for × 1 hour, these normalized materials were processed to 30φ × 15 L , and then carburized by the heat pattern shown in FIG. 1 to measure the hardness distribution of the carburized layer, observe spherical carbides, An abnormal tissue was observed and investigated. In the static bending test, a test piece having the shape and dimensions shown in Fig. 2 was cut out from the above-mentioned normalized material, and then carburized by the heat pattern shown in Fig. 1, and at a rate of 10 -2 / s. A method of examining the static bending strength was adopted, but the static bending strength was evaluated based on the breaking load.
「衝撃特性」については、前記鍛伸材を925℃×１時
間で焼準した後、25mmφに切削し、次いで925℃×１時
間水焼入れ,170℃×１時間焼戻しを施し、しかる後JIS3
号（2mmUノッチ）シャルピー試験片に加工してから常温
にて衝撃特性を測定する手法で調査した。Regarding the “impact characteristics”, the forged material was normalized at 925 ° C. × 1 hour, cut into 25 mmφ, then water-quenched at 925 ° C. × 1 hour, tempered at 170 ° C. × 1 hour, and then JIS3
No. (2mm U notch) was processed into a Charpy test piece, and the impact characteristics were measured at room temperature.
「オーステナイト粒径」については、前記鍛伸材を92
5℃×１時間で焼準した後、これら焼準材を30φ×15Lに
加工し、続いて第１図に示すヒートパターンにて浸炭処
理したものにつき内部のオーステナイト結晶粒を測定し
た。Regarding the “austenite grain size”,
After normalizing at 5 ° C. × 1 hour, these normalized materials were processed into 30φ × 15 L , and then the austenite crystal grains inside were measured for those carburized by the heat pattern shown in FIG.
これらの結果を第２表に示す。 Table 2 shows the results.
第２表に示される結果からも明らかなように、本発明
鋼は浸炭特性及び衝撃特性が共に非常に良好で、通常浸
炭にて優れた耐摩耗性並びに靭性を兼備するようになる
のに対して、比較鋼及び従来鋼では十分な特性を示さな
いことが分かる。特に、Cr含有量が本発明で規定する範
囲の上下限を外れていたり、Pb含有量が本発明で規定す
る範囲の下限を外れた鋼種では、浸炭後の最高硬さが低
く、かつ浸炭深さが浅いことを確認できる。As is clear from the results shown in Table 2, the steel of the present invention has both excellent carburizing characteristics and impact characteristics, and usually has excellent wear resistance and toughness by carburizing. Thus, it is understood that the comparative steel and the conventional steel do not show sufficient characteristics. In particular, for steel types whose Cr content is outside the upper and lower limits of the range specified by the present invention and whose Pb content is outside the lower limit of the range specified by the present invention, the maximum hardness after carburizing is low and the carburizing depth is low. You can see that it is shallow.
〈効果の総括〉 以上に説明した如く、この発明によれば、通常浸炭に
よっても優れた耐摩耗性を発揮するようになる、靭性の
良好な浸炭肌焼鋼を提供できるようになるなど、産業上
極めて有用な効果がもたらされる。<Summary of Effects> As described above, according to the present invention, it becomes possible to provide a carburized case hardening steel having excellent toughness and good toughness even by normal carburization. In addition, a very useful effect is provided.
なお、浸炭時のスーチングを無視して過剰浸炭を実施
すれば、炭化物の生成量が増大し、硬さ，硬化層深さが
増加するため、耐摩耗性は更に向上する。If excessive carburization is performed ignoring sooting during carburization, the amount of carbide generated increases, the hardness and the depth of the hardened layer increase, and the wear resistance further improves.
第１図は、実施例で採用された浸炭処理のヒートパター
ンである。 第２図は、静的曲げ試験で採用した試験片の形状・寸法
を示した概略図である。FIG. 1 is a heat pattern of a carburizing treatment adopted in the embodiment. FIG. 2 is a schematic diagram showing the shape and dimensions of a test piece employed in a static bending test.
Claims (4)
特徴とする、耐摩耗性に優れた浸炭肌焼鋼。(1) C: 0.10 to 0.30%, Si: 0.50 or less, Mn: 2.00 or less, Cr: more than 1.2 to 5.0%, Pb: more than 0.06 to 0.50% by weight, the balance being Fe and unavoidable Carburized case-hardened steel with excellent wear resistance, characterized by being composed of chemical impurities.
ら成ることを特徴とする、耐摩耗性に優れた浸炭肌焼
鋼。2. The composition contains, by weight, C: 0.10 to 0.30%, Si: 0.50 or less, Mn: 2.00 or less, Cr: more than 1.2 to 5.0%, Pb: more than 0.06 to 0.50, and further Cu: 1.0% or less. , Ni: 3.50% or less, Mo: 2.00% or less, V: 0.01 to 0.30%, B: 0.0003 to 0.0050%, and the balance consists of Fe and inevitable impurities. Carburized case hardened steel with excellent wear resistance.
成ることを特徴とする、耐摩耗性に優れた浸炭肌焼鋼。(3) In a weight ratio, C: 0.10 to 0.30%, Si: 0.50 or less, Mn: 2.00 or less, Cr: more than 1.2 to 5.0%, Pb: more than 0.06 to 0.50%, and Al: 0.010 to 0.50%. A carburized case hardening steel with excellent wear resistance, characterized in that it contains at least one of 0.100%, Ti: 0.010 to 0.100%, and Nb: 0.010 to 0.100%, with the balance being Fe and inevitable impurities.
ら成ることを特徴とする、耐摩耗性に優れた浸炭肌焼
鋼。4. In a weight ratio, C: 0.10 to 0.30%, Si: 0.50 or less, Mn: 2.00 or less, Cr: more than 1.2 to 5.0%, Pb: more than 0.06 to 0.50%, and further Cu: 1.0% Ni, 3.50% or less, Mo: 2.00% or less, V: 0.01 to 0.30%, B: 0.0003 to 0.0050%, Al: 0.010 to 0.100%, Ti: 0.010 to 0.100%, Nb: 0.010 A carburized case hardening steel having excellent wear resistance, characterized by containing at least one of 0.100% or more, and the balance being Fe and unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2285473A JP2737386B2 (en) | 1990-10-23 | 1990-10-23 | Carburized case hardened steel with excellent wear resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2285473A JP2737386B2 (en) | 1990-10-23 | 1990-10-23 | Carburized case hardened steel with excellent wear resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04160136A JPH04160136A (en) | 1992-06-03 |
| JP2737386B2 true JP2737386B2 (en) | 1998-04-08 |
Family
ID=17691976
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2285473A Expired - Lifetime JP2737386B2 (en) | 1990-10-23 | 1990-10-23 | Carburized case hardened steel with excellent wear resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2737386B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2943519B2 (en) * | 1992-07-31 | 1999-08-30 | 日本鋼管株式会社 | Case hardened steel with excellent impact resistance |
| CN102978515B (en) * | 2012-11-09 | 2016-01-20 | 宁波嘉达精密铸造有限公司 | Excavator toothholder and preparation method thereof |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5433206A (en) * | 1977-08-20 | 1979-03-10 | Tokuriki Honten Kk | Silver based composite materials and method of making same |
| JP2615126B2 (en) * | 1988-03-28 | 1997-05-28 | 大同特殊鋼株式会社 | Gear steel |
-
1990
- 1990-10-23 JP JP2285473A patent/JP2737386B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH04160136A (en) | 1992-06-03 |
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