JPH0762203B2 - High strength, high toughness, hot forged non-heat treated steel - Google Patents
High strength, high toughness, hot forged non-heat treated steelInfo
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- JPH0762203B2 JPH0762203B2 JP63022059A JP2205988A JPH0762203B2 JP H0762203 B2 JPH0762203 B2 JP H0762203B2 JP 63022059 A JP63022059 A JP 63022059A JP 2205988 A JP2205988 A JP 2205988A JP H0762203 B2 JPH0762203 B2 JP H0762203B2
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Description
【発明の詳細な説明】 ［産業上の利用分野］ 本発明は高強度高靱性熱間鍛造非調質鋼にかかわり、さ
らに詳しくは、自動車用部品、建設機械部品等のなか
で、高強度・高靱性を必要とする熱間鍛造品の製造に際
して、熱間鍛造後、調質処理をすることなく、十分な強
度と靱性、特に低温靱性を製品に付与することを可能に
した高強度高靱性熱間鍛造非調質鋼に関するものであ
る。DETAILED DESCRIPTION OF THE INVENTION [Industrial field of application] The present invention relates to a high-strength, high-toughness hot forged non-heat treated steel, and more specifically, it has high strength / high strength among automobile parts and construction machine parts. When manufacturing a hot forged product that requires high toughness, it is possible to give the product sufficient strength and toughness, especially low temperature toughness, without heat treatment after hot forging. The present invention relates to hot forged non-heat treated steel.
［従来の技術］ 従来、自動車用部品、建設機械部品等のなかで、高強度
・高靱性を必要とする熱間鍛造品は、主として調質、即
ち、焼入れ焼きもどしをして使用されている。しかしな
がら、調質処理のコストは近年のエネルギ高騰とともに
これらの機械部品の製造コストのなかで大きなウェイト
を占めるようになってきている。したがって、製造コス
ト低減の観点から、調質処理を省略する事が出来る鋼
材、即ち熱間鍛造のままで調質材以上の強度と靱性を確
保し得るいわゆる熱間鍛造非調質鋼が必要になってきて
いる。[Prior Art] Conventionally, among automobile parts, construction machine parts, etc., hot forged products requiring high strength and high toughness are mainly used for tempering, that is, quenching and tempering. . However, the cost of refining treatment has come to occupy a large weight in the manufacturing cost of these mechanical parts due to the recent increase in energy. Therefore, from the viewpoint of manufacturing cost reduction, it is necessary to use a steel material that does not require heat treatment, that is, a so-called hot-forged non-heat-treated steel that can secure strength and toughness higher than that of the heat-treated material as hot forged. It has become to.
一般に、鋼材の靱性を無視して、強度のみ高くすること
は、非調質であっても、比較的容易であるけれども、こ
のような鋼材は、用途が限定され、従来の調質鋼に代替
できるものではない。Generally, it is relatively easy to ignore the toughness of steel materials and increase only the strength even if they are non-tempered, but such steel materials have limited applications and can be replaced by conventional tempered steels. Not something you can do.
これに対して、特開昭56−38448公報には、Si、Mn等を
多くすることによる地鉄の強化と、Ti、V,Nbによる析出
強化による鋼材の高強度化を図るとともに、鋼中のＮを
0.29Ti％以上と多くして、窒化物主体のTi、V,Nbの析出
物を生成させることにより、旧オーステナイト粒径を微
細化して、鋼材の高靱性化を図り、熱間鍛造のままで優
れた強度と靱性の確保を可能にした材料が示されてい
る。On the other hand, in Japanese Patent Laid-Open No. 56-38448, strengthening the base iron by increasing Si, Mn, etc., and increasing the strength of the steel material by precipitation strengthening with Ti, V, Nb, N of
By increasing the content to 0.29Ti% or more to generate Ti, V, and Nb precipitates mainly composed of nitride, the former austenite grain size is refined, the toughness of the steel material is increased, and hot as-forged Materials have been shown that have made it possible to ensure excellent strength and toughness.
［発明が解決しようとする課題］ しかしながら、このような材料を用いてもなおかつ、従
来の調質材以上の強度と靱性、特に低温靱性の保温には
未だ十分であるとは言えないのが現状である。[Problems to be Solved by the Invention] However, even if such a material is used, the strength and toughness of a conventional heat-treated material, particularly the low temperature toughness, cannot be said to be still sufficient. Is.
本発明の目的は、熱間鍛造のままで従来の調質材以上の
強度と靱性、特に低温靱性の保証を可能にした、高強度
高靱性熱間鍛造非調質鋼を提供しようとするものであ
る。An object of the present invention is to provide a high-strength, high-toughness hot forged non-tempered steel capable of guaranteeing strength and toughness as compared with conventional heat-treated materials, particularly low-temperature toughness, while being hot forged. Is.
［課題を解決するための手段、作用］ 本発明者らは、熱間鍛造のままで従来の調質材以上の強
度と靱性、特に低温靱性の保証を可能にした高強度高靱
性熱間鍛造用鋼を実現するために、鋭意検討を行なった
結果、高Si化による固溶体硬化の活用及びパーライト分
率増加元素の添加によって高強度化をはかり、Ｓ、Ｖ、
Ｎの多量添加によるフェライト・パーライト組織の微細
化によって高靱性化をはかった鋼材を用いれば、熱間鍛
造のままで従来の調質材以上の強度と低温靱性の保証が
可能であるという新規な知見を得て、本発明をなしたも
のである。[Means and Actions for Solving the Problems] The inventors of the present invention have high-strength, high-toughness hot forging capable of guaranteeing strength and toughness superior to that of conventional tempered materials, particularly low-temperature toughness, while hot forging. As a result of earnest studies to realize a steel for use, as a result of utilizing solid solution hardening due to high Si content and adding a pearlite fraction increasing element to increase strength, S, V,
The use of steel that has been made tougher by refining the ferrite / pearlite structure by adding a large amount of N makes it possible to guarantee the strength and low temperature toughness of conventional tempered materials with hot forging. The present invention has been made based on knowledge.
即ち、本発明は以上の知見にもとずいてなされたもので
あって、その要旨とするところは、重量比として、 C:0.10〜0.60％、 Si:1.0超〜3.0％、 Mn:1.2超〜3.0％、 S:0.05超〜0.30％、 V:0.03〜0.30％ N:0.010超〜0.060％ Al:0.005〜0.100％を含有し、 Cr:3.0％以下、 Ni:3.0％以下、 Mo:1.0％以下、 Cu:2.0％以下、 の１種又は２種以上を（0.4−Ｃ％）＜（Mn％）/5＋（C
r％）/9＋（Ni％）/30＋（Mo％）/4＋（Cu％）/13＜
（0.7−Ｃ％）の範囲で含有し、 P:0.03％以下に制限し、残部がFe及び不可避的不純物か
らなることを特徴とする高強度高靱性熱間鍛造非調質鋼
にある。また、さらに必要に応じて、 Ti:0.001〜0.050％、 Nb:0.005〜0.10％のうちの少なくとも一方を含有するも
のである。That is, the present invention was made based on the above findings, and the gist thereof is, as a weight ratio, C: 0.10 to 0.60%, Si: more than 1.0 to 3.0%, Mn: more than 1.2. ~ 3.0%, S:> 0.05 to 0.30%, V: 0.03 to 0.30%, N:> 0.010 to 0.060%, Al: 0.005 to 0.100%, Cr: 3.0% or less, Ni: 3.0% or less, Mo: 1.0 % Or less, Cu: 2.0% or less, one or more of (0.4-C%) <(Mn%) / 5 + (C
r%) / 9+ (Ni%) / 30+ (Mo%) / 4+ (Cu%) / 13 <
A high-strength, high-toughness hot forged non-heat treated steel characterized by being contained in the range of (0.7-C%), P: 0.03% or less, and the balance being Fe and inevitable impurities. Further, if necessary, at least one of Ti: 0.001 to 0.050% and Nb: 0.005 to 0.10% is contained.
以下に、本発明を詳細に説明する。The present invention will be described in detail below.
まず、Ｃは鍛造品の強度を増加させるのに有効な元素で
あるが、0.10％未満では強度が不足し、また0.6％を超
えると、靱性の劣化を招くため、含有量を0.10〜0.60％
とした。First, C is an element effective for increasing the strength of the forged product, but if it is less than 0.10%, the strength is insufficient, and if it exceeds 0.6%, the toughness is deteriorated, so the content is 0.10 to 0.60%.
And
次に、Siは固溶体硬化による強度の増加を図ることを目
的として添加するが、1.00％以下ではそれの硬化は不十
分であり、一方、3.0％を超えるとその硬化は飽和し、
むしろ靱性の劣化を招くので、その含有量を1.00超〜3.
0％とした。Next, Si is added for the purpose of increasing the strength by solid solution hardening, but if it is 1.00% or less, its hardening is insufficient, while if it exceeds 3.0%, its hardening is saturated,
Rather, it causes deterioration of toughness, so its content exceeds 1.00 to 3.
It was set to 0%.
また、Mnはパーライト分率を高めるのに有効な元素であ
り、1.2％超を添加するが、多量に添加した場合、コス
トがかかるため上限を3.0％以下に限定する。Further, Mn is an element effective for increasing the pearlite fraction, and is added in an amount of more than 1.2%. However, if added in a large amount, it will be costly, so the upper limit is limited to 3.0% or less.
また、Ｓは鋼中でMnSとして存在し、フェライト・パー
ライト組織の微細化に寄与するが、0.05％以下ではその
効果は不十分である。一方、0.30％を超えるとその効果
は飽和し、むしろ靱性の劣化及び異方性の増加を招く。
以上の理由から、Ｓの含有量を0.05超〜0.30％とした。Further, S exists as MnS in the steel and contributes to the refinement of the ferrite-pearlite structure, but the effect is insufficient if the content is 0.05% or less. On the other hand, if it exceeds 0.30%, the effect is saturated and rather the toughness deteriorates and the anisotropy increases.
For the above reason, the S content is set to more than 0.05 to 0.30%.
さらに、Ｖ、ＮはVNの析出挙動を通じて、フェライト・
パーライト組織の微細化に寄与するが、V:0.03％未満、
N:0.010％以下ではその効果は不十分であり、一方、V:
0.30％超、N:0.060％超では、その効果は飽和し、むし
ろ析出脆化による靱性の劣化を招くので、その含有量を
V:0.03〜0.30％、N:0.010超〜0.060％とした。In addition, V and N are ferrite
Contributes to the refinement of pearlite structure, but V: less than 0.03%,
If N: 0.010% or less, the effect is insufficient, while V:
If the content exceeds 0.30% and N: 0.060%, the effect is saturated, and rather the toughness deteriorates due to precipitation embrittlement.
V: 0.03 to 0.30%, N: more than 0.010 to 0.060%.
次に、Alは脱酸元素として添加するが、0.005％未満で
はその効果は不十分であり、一方、0.100％を超えると
その効果は飽和し、むしろ靱性を劣化させるので、その
含有量を0.005〜0.100％とした。Next, Al is added as a deoxidizing element, but if its content is less than 0.005%, its effect is insufficient, while if it exceeds 0.100%, its effect saturates and rather deteriorates toughness, so its content is 0.005%. It was set to ~ 0.100%.
次に本発明においては、Cr、Ni、Mo、Cuの１種又は２種
以上を必須元素として含有させる。これらの元素は焼入
れ性の増加によりパーライト分率を増加させ、鍛造品の
強度を増加させるために添加する。ここでパーライト分
率は、第１図に示すように、次式で表わされる炭素当量
に比例する。Next, in the present invention, one or more of Cr, Ni, Mo and Cu are contained as essential elements. These elements are added in order to increase the pearlite fraction due to the increase in hardenability and the strength of the forged product. Here, the pearlite fraction is proportional to the carbon equivalent represented by the following equation, as shown in FIG.
Ceq＝（Ｃ％）＋（Mn％）/5＋（Cr％）/9＋ （Ni％）/30＋（Mo％）/4＋（Cu％）/13 さらに、炭素当量が0.4未満では強度が不足し、一方、
炭素当量が0.7を超えると靱性の劣化を招くので、炭素
当量は0.4〜0.7の範囲に限定する必要がある。以上の理
由で、Cr、Ni、Mo、Cuの含有量を、Ｃ量とMn量に応じ
て、（0.4−Ｃ％）＜（Mn％）/5＋（Cr％）/9＋（Ni
％）/30＋（Mo％）/4＋（Cu％）/13＜（0.7−Ｃ％）の
範囲に限定した。なお、Cr、Ni、Mo、Cuの個々の含有量
をそれぞれ、3.0％以下、3.0％以下、1.0％以下、2.0％
以下としたのは、各元素とも、上限値以上の多量添加
は、経済性の点で好ましくないためである。C eq = (C%) + (Mn%) / 5+ (Cr%) / 9+ (Ni%) / 30+ (Mo%) / 4+ (Cu%) / 13 Furthermore, if the carbon equivalent is less than 0.4, the strength is insufficient. ,on the other hand,
When the carbon equivalent exceeds 0.7, toughness is deteriorated, so the carbon equivalent needs to be limited to the range of 0.4 to 0.7. For the above reasons, the contents of Cr, Ni, Mo, and Cu are set to (0.4−C%) <(Mn%) / 5+ (Cr%) / 9+ (Ni depending on the C content and the Mn content.
%) / 30+ (Mo%) / 4+ (Cu%) / 13 <(0.7-C%). The individual contents of Cr, Ni, Mo, and Cu are 3.0% or less, 3.0% or less, 1.0% or less, and 2.0%, respectively.
The reason for the following is that it is not preferable to add a large amount of each element above the upper limit in terms of economy.
一方、Ｐは鋼中で粒界偏析や中心偏析を起こし、靱性劣
化の原因となる。特にＰが0.03％を超えると靱性の劣化
が顕著となるため、0.03％を上限とした。On the other hand, P causes grain boundary segregation or center segregation in the steel and causes deterioration of toughness. In particular, when P exceeds 0.03%, deterioration of toughness becomes remarkable, so 0.03% was made the upper limit.
以上が本発明鋼の基本組成であるが、この他本発明鋼に
おいては、粒度調整の目的で、Ti、Nbの一方又は両方を
必要に応じて含有させることが出来る。しかしながら、
Ti含有量が0.001％未満、Nb含有量が0.005％未満ではそ
の効果は不十分であり、一方、Ti:0.050％超、Nb:0.10
％超では、その効果は飽和し、むしろ靱性を劣化させる
ので、Tiの含有量を0.001〜0.050％、Nbの含有量を0.00
5〜0.10％とした。The above is the basic composition of the steel of the present invention. In addition to this, in the steel of the present invention, one or both of Ti and Nb can be contained as necessary for the purpose of grain size adjustment. However,
If the Ti content is less than 0.001% and the Nb content is less than 0.005%, the effect is insufficient, while Ti: more than 0.050%, Nb: 0.10.
%, The effect saturates and rather deteriorates the toughness. Therefore, the Ti content is 0.001 to 0.050%, and the Nb content is 0.00%.
It was set to 5 to 0.10%.
以下に、本発明の効果を実施例により、さらに具体的に
示す。Hereinafter, the effects of the present invention will be described more specifically by way of examples.
［実施例］ 第１表に示す直径50mmの鋼材を、1250℃加熱の後、直径
25mmの熱間鍛造し、得られた鍛造品の強度と靱性（−50
℃及び20℃における襲撃値）の評価を行った。これらの
結果を第１表に併せて示す。[Example] A steel material having a diameter of 50 mm shown in Table 1 was heated at 1250 ° C.
The strength and toughness of the forged product obtained by hot forging of 25 mm (-50
The attack value at ℃ and 20 ℃) was evaluated. The results are also shown in Table 1.
なお、熱間鍛造のままで従来の調質材以上の強度と靱性
の確保が可能か否かについて、次の基準により判断し
た。強度:80kgf/mm2以上、且つ低温靱性（−50℃に
おける衝撃値）：強度に応じて、2UE-50＝13.6−0.115
×T.S.kgf−m/cm2以上、常温靱性（20℃における衝撃
値）：強度に応じて、2UE20＝17.1−0.115×T.S.kgf−m
/cm2以上（調質用高強度鍛造用鋼として、一般に用いら
れている、SMn鋼の焼入れ焼戻し（500℃焼戻し）材の強
度と靱性をその化学成分と併せて第２表に示したが、低
温靱性（2UE-50）及び常温靱性（2UE20）を強度（T.S）
について、回帰分析すると、2UE-50＝13.6−0.115×T.
S.、及び2UE20＝17.1−0.115×T.S.kgf−m/cm2となるた
め。） 第１表から明らかなように、本発明の鋼は、いずれも熱
間鍛造のままで、80kgf/mm2以上の強度と、強度に応じ
て、2UE-50＝13.6−0.115×T.S.kgf−m/cm2以上の低温
靱性、及び2UE20＝17.1−0.115×T.S.kgf−m/cm2以上の
常温靱性を有することがわかる。The following criteria were used to judge whether or not the strength and toughness of the conventional heat-treated material could be secured with hot forging. Strength: 80kgf / mm 2 or more, and low temperature toughness (impact value at -50 ° C): 2U E -50 = 13.6-0.115 depending on strength
× TSkgf-m / cm 2 or more, normal temperature toughness (impact value at 20 ° C): Depending on strength, 2U E 20 = 17.1-0.115 × TSkgf-m
/ cm 2 or more (Table 2 shows the strength and toughness of the quenched and tempered (500 ° C tempered) material of SMn steel, which is commonly used as a high-strength forging steel for tempering, together with its chemical composition. Strength (TS), low temperature toughness ( 2U E -50 ) and room temperature toughness ( 2U E 20 ).
Regression analysis of 2U E -50 = 13.6−0.115 × T.
S. and 2U E 20 = 17.1−0.115 × TSkgf−m / cm 2 ) As is clear from Table 1, the steels of the present invention were both hot forged and had a strength of 80 kgf / mm 2 or more and, depending on the strength, 2U E -50 = 13.6-0.115 × TSkgf- m / cm 2 or more low-temperature toughness, and 2U E 20 = 17.1-0.115 × TSkgf- m / cm 2 or more can be seen to have a room temperature toughness.
一方、比較例６と８は、Ｃ、SiおよびMnの含有量がそれ
ぞれ本発明の範囲を下回った場合であり、ともに強度が
不足している。比較例７、９、18、25、26は、Mnの含有
量が本発明の範囲にあるかあるいは下回っているが、
Ｃ、Si、Ti、ＰあるいはNbの含有量がそれぞれ本発明の
範囲を上回っており、いずれも所定の低温及び常温靱性
が得られていない。また、比較例10、12、14、16は、
Ｓ、Ｖ、Ｎ、AlあるいはMnの含有量が本発明の範囲を下
回った場合であり、比較列11、13、15、17は、Ｓ、Ｖ、
Ｎ、Alの含有量が本発明の範囲を上回り、あるいはMnが
下回った場合であり、いずれも所定の低温及び常温靱性
が得られていない。さらに、比較例19、20、21は、Mn、
Cr、Ni、Mo、Cuの１種または２種以上の含有量が本発明
の範囲を下回った場合であり、いずれも強度が不足して
いる。比較例22、23、24は、炭素当量が本発明の範囲を
上回った場合であり、いずれも所定の低温及び常温靱性
が得られていない。On the other hand, Comparative Examples 6 and 8 are cases in which the contents of C, Si and Mn were below the respective ranges of the present invention, and both had insufficient strength. Comparative Examples 7, 9, 18, 25 and 26 have Mn contents within or below the range of the present invention,
The contents of C, Si, Ti, P, and Nb each exceed the range of the present invention, and none of them has a predetermined low temperature and normal temperature toughness. In addition, Comparative Examples 10, 12, 14, and 16,
When the content of S, V, N, Al or Mn is below the range of the present invention, the comparative columns 11, 13, 15, 17 are S, V,
This is the case where the contents of N and Al exceed the range of the present invention or fall below Mn, and neither of the prescribed low temperature and normal temperature toughness is obtained. Furthermore, Comparative Examples 19, 20, and 21 are Mn,
This is the case where the content of one or more of Cr, Ni, Mo and Cu is below the range of the present invention, and the strength is insufficient in each case. Comparative Examples 22, 23, and 24 are cases where the carbon equivalent exceeds the range of the present invention, and none of the predetermined low temperature and room temperature toughness is obtained.
［発明の効果］ 以上述べたごとく、本発明の鋼を用いれば、熱間鍛造の
ままで従来の調質材以上の強度と靱性の確保が可能であ
り、従来必要とした調質処理の省略とそれにともなう製
造コスト低減が可能となり、産業上の効果は極めて顕著
なるものがある。 [Effects of the Invention] As described above, by using the steel of the present invention, it is possible to secure strength and toughness higher than those of conventional heat-treated materials by hot forging, and the heat-treatment required conventionally is omitted. Therefore, the manufacturing cost can be reduced, and the industrial effect is extremely remarkable.
第１図は、炭素当量とパーライト分率の関係を示した図
である。FIG. 1 is a diagram showing the relationship between carbon equivalent and pearlite fraction.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 高田 啓督 北海道室蘭市仲町12番地 新日本製鐵株式 会社室蘭製鐵所内 (72)発明者 前田 千芳利 愛知県豊田市トヨタ町１番地 トヨタ自動 車株式会社内 (72)発明者 安田 茂 愛知県豊田市トヨタ町１番地 トヨタ自動 車株式会社内 (72)発明者 杉本 繁利 愛知県豊田市トヨタ町１番地 トヨタ自動 車株式会社内 (56)参考文献 特開 昭55−138056（ＪＰ，Ａ) 特開 昭62−196359（ＪＰ，Ａ) ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Keisuke Takada 12 Nakamachi, Muroran-shi, Hokkaido Inside Nippon Steel Co., Ltd. Muroran Works (72) Inventor Chihori Maeda 1 Toyota-cho, Toyota-shi, Aichi Toyota Auto Car Co., Ltd. (72) Inventor Shigeru Yasuda 1 Toyota Town, Toyota City, Aichi Prefecture Toyota Motor Co., Ltd. (72) Inventor Shigetoshi Sugimoto 1 Toyota Town, Toyota City, Aichi Prefecture Toyota Motor Co., Ltd. (56) Reference References JP 55-138056 (JP, A) JP 62-196359 (JP, A)
Claims (2)
r％）/9＋（Ni％）/30＋（Mo％）/4＋（Cu％）/13＜
（0.7−Ｃ％）の範囲で含有し、 P:0.03％以下に制限し、残部がFe及び不可避的不純物か
らなることを特徴とする高強度高靱性熱間鍛造非調質
鋼。1. A weight ratio of C: 0.10 to 0.60%, Si: more than 1.0 to 3.0%, Mn: more than 1.2 to 3.0%, S: more than 0.05 to 0.30%, V: 0.03 to 0.30%, N: 0.010. More than 0.060%, Al: 0.01 to 0.100%, and Cr: 3.0% or less, Ni: 3.0% or less, Mo: 1.0% or less, Cu: 2.0% or less, one or more of (0.4-C%) <(Mn%) / 5+ (C
r%) / 9+ (Ni%) / 30+ (Mo%) / 4+ (Cu%) / 13 <
A high-strength, high-toughness hot-forged non-heat treated steel, characterized by being contained in the range of (0.7-C%), limited to P: 0.03% or less, and the balance being Fe and inevitable impurities.
r％）/9＋（Ni％）/30＋（Mo％）/4＋（Cu％）/13＜
（0.7−Ｃ％）の範囲で含有し、さらにまた、 Ti:0.001〜0.050％、 Nb:0.005〜0.10％のうち少なくとも一方を含有し、 P:0.03％以下に制限し、残部がFe及び不可避的不純物か
らなることを特徴とする高強度高靱性熱間鍛造非調質
鋼。2. A weight ratio of C: 0.10 to 0.60%, Si: more than 1.0 to 3.0%, Mn: more than 1.2 to 3.0%, S: more than 0.05 to 0.30%, V: 0.03 to 0.30%, N: 0.010. More than 0.060%, Al: 0.01 to 0.100%, and Cr: 3.0% or less, Ni: 3.0% or less, Mo: 1.0% or less, Cu: 2.0% or less, one or more of (0.4-C%) <(Mn%) / 5+ (C
r%) / 9+ (Ni%) / 30+ (Mo%) / 4+ (Cu%) / 13 <
(0.7-C%), Ti: 0.001 to 0.050% and Nb: 0.005 to 0.10%, and P: 0.03% or less. The balance is Fe and unavoidable. High-strength, high-toughness hot forged non-heat treated steel characterized by being composed of mechanical impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63022059A JPH0762203B2 (en) | 1988-02-03 | 1988-02-03 | High strength, high toughness, hot forged non-heat treated steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63022059A JPH0762203B2 (en) | 1988-02-03 | 1988-02-03 | High strength, high toughness, hot forged non-heat treated steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH01198450A JPH01198450A (en) | 1989-08-10 |
| JPH0762203B2 true JPH0762203B2 (en) | 1995-07-05 |
Family
ID=12072338
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63022059A Expired - Lifetime JPH0762203B2 (en) | 1988-02-03 | 1988-02-03 | High strength, high toughness, hot forged non-heat treated steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0762203B2 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100428581B1 (en) * | 1999-12-28 | 2004-04-30 | 주식회사 포스코 | A non qt steel having superior strength and toughness and a method for manufacturing wire rod by using it |
| KR20010066065A (en) * | 1999-12-31 | 2001-07-11 | 이계안 | Manufacturing method of quenching and trenching crank shaft for the diesel engine |
| JP5620336B2 (en) | 2011-05-26 | 2014-11-05 | 新日鐵住金株式会社 | Steel parts for high fatigue strength and high toughness machine structure and manufacturing method thereof |
| CN103201401B (en) | 2011-05-26 | 2014-07-02 | 新日铁住金株式会社 | Steel component for mechanical structural use and manufacturing method for same |
| KR20130083925A (en) | 2011-05-26 | 2013-07-23 | 신닛테츠스미킨 카부시키카이샤 | Steel component for mechanical structural use and manufacturing method for same |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5853709B2 (en) * | 1979-04-12 | 1983-11-30 | 住友金属工業株式会社 | As-forged high-strength forging steel |
| JPS62196359A (en) * | 1986-02-24 | 1987-08-29 | Sumitomo Metal Ind Ltd | Non-heattreated steel for hot forging and production thereof |
-
1988
- 1988-02-03 JP JP63022059A patent/JPH0762203B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH01198450A (en) | 1989-08-10 |
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