JPS61238941A - Untempered steel for hot forging - Google Patents
Untempered steel for hot forgingInfo
- Publication number
- JPS61238941A JPS61238941A JP8088385A JP8088385A JPS61238941A JP S61238941 A JPS61238941 A JP S61238941A JP 8088385 A JP8088385 A JP 8088385A JP 8088385 A JP8088385 A JP 8088385A JP S61238941 A JPS61238941 A JP S61238941A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- forging
- hot forging
- strength
- soluble
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Links
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- Heat Treatment Of Steel (AREA)
- Forging (AREA)
Abstract
Description
【発明の詳細な説明】
〈産業上の利用分野〉
本発明は、鍛造後の焼入れ一焼戻し等の熱処理が不要な
熱間鍛造用の非調質鋼に関する。DETAILED DESCRIPTION OF THE INVENTION <Industrial Application Field> The present invention relates to a non-tempered steel for hot forging that does not require heat treatment such as quenching and tempering after forging.
〈従来の技術〉
従来、自動車や建設機械に用いられる機械構造用部品は
、機械構造用炭素鋼や合金鋼を素材鋼として、これを熱
間鍛造した後、再加熱し、焼入れ一焼戻し等の調質処理
を施して、目的、用途に応じた強度特性を付与して製造
されている。しかし、１肥熱処理における多大の熱エネ
ルギーのための費用、処理工程の増加、仕掛り品の増大
等のために、上記機械構造用部品の製造費用が高くなら
ざるを得ない。<Conventional technology> Conventionally, mechanical structural parts used in automobiles and construction machinery have been made of mechanical structural carbon steel or alloy steel, which is hot forged, reheated, quenched and tempered, etc. It is manufactured by applying heat treatment to give it strength characteristics depending on the purpose and use. However, due to the cost of a large amount of thermal energy in the 1-fertilization treatment, an increase in the number of processing steps, an increase in the number of products in progress, etc., the manufacturing cost of the above-mentioned mechanical structural parts inevitably increases.
そこで、近年、鍛鋼品の製造において、製造工程を簡略
化、特に、焼入れ一焼戻し工程を省略するために、ＪＩ
ＳＧ４０５１に規定された機械構造用炭素鋼やＪＩＳＧ
４１０６に規定された機械構造用マンガン鋼及びマンガ
ンクロム鋼に微量のＶ、Ｎｂ 、Ｔｉ等の析出硬化型合
金元素を添加したいわゆる熱間鍛造用非調質鋼を素材と
し、熱間鍛造時の加熱と鍛造およびその後の冷却によっ
て、調質処理がいらずそのままで所要の特性を得ること
ができる非調質鍛鋼品が注目されており、一部では既に
実用化されている。Therefore, in recent years, in the manufacture of forged steel products, JI
Carbon steel for mechanical structures specified in SG4051 and JISG
The material is so-called non-thermal steel for hot forging, which is made by adding trace amounts of precipitation hardening alloy elements such as V, Nb, and Ti to manganese steel and manganese chromium steel for machine structures specified in 4106. Non-thermal forged steel products, which can obtain the desired properties without the need for heat treatment through heating, forging, and subsequent cooling, are attracting attention, and some have already been put into practical use.
通常、このような非調質鍛鋼品は、１１００〜１３５０
℃の温度から鍛造し始め、１０００〜１３００℃の温度
で鍛造を終了した後、大気中放冷、衝風冷却または噴水
冷却して製造されている。Normally, such non-thermal forged steel products have a temperature of 1100 to 1350
Forging is started at a temperature of 1,000 to 1,300 degrees Celsius, and after the forging is finished at a temperature of 1,000 to 1,300 degrees Celsius, it is manufactured by cooling in the atmosphere, blast cooling, or fountain cooling.
〈発明が解決しようとする問題点〉
ところが、既に実用化されている重連の熱間鍛造用非調
質鋼を素材として製造されている非調質鍛鋼品は、調質
鍛鋼品に比較すると同一の強度は確保されるが、靭性や
延性は劣る。これは、非調質鍛鋼品の強度が主にパーラ
イトの強度とＶやＮｂ等の炭窒化物の析出による強度に
よって確保されていることと、組織が粗いオーステナイ
ト粒から変態したフェライト・パーライトであることに
起因する。このため、素材鋼のＣ，ＭｎおよびＶ等の化
学成分比率の最適化や鍛造温度の低温化等により、靭性
や延性の改善が試みられているが、調質鍛鋼品と同等の
靭性や延性を確保できるまでには至っていない。特に、
従来の熱間鍛造用非調質鋼を素材とした場合、引張強さ
が９０ ｋｇｆ／ｍｍ２以上になると室温における２ｍ
ｍＵノツチシャルピー衝撃試験の吸収エネルギーは３．
２ ｋｇｆ−ｍ以下にまで極端に低下し、構造用材料と
して十分な靭性を発揮し得ない。<Problems to be solved by the invention> However, non-tempered forged steel products manufactured using non-tempered steel for continuous hot forging, which has already been put into practical use, are inferior to heat-treated forged steel products. The same strength is ensured, but the toughness and ductility are inferior. This is because the strength of non-thermal forged steel products is mainly ensured by the strength of pearlite and the strength due to the precipitation of carbonitrides such as V and Nb, and the structure is ferrite and pearlite transformed from coarse austenite grains. This is due to this. For this reason, attempts have been made to improve the toughness and ductility by optimizing the ratio of chemical components such as C, Mn, and V in the raw steel and by lowering the forging temperature. We have not yet reached the point where we can secure this. especially,
When using conventional non-temperature steel for hot forging as a material, if the tensile strength is 90 kgf/mm2 or more, the
The absorbed energy in the mU Notch Charpy impact test is 3.
The toughness decreases extremely to 2 kgf-m or less, and cannot exhibit sufficient toughness as a structural material.
そこで、本発明の目的は、添加元素を有効に含み、鍛造
後の調質熱処理が不要で、高強度でしかも優れた靭性と
延性を有し、さらに焼入性や切削性の良い熱間鍛造用非
調質鋼を提供することである。Therefore, the object of the present invention is to provide a hot forged material that effectively contains additive elements, does not require tempering heat treatment after forging, has high strength, excellent toughness and ductility, and has good hardenability and machinability. The objective is to provide non-thermal treated steel for use in the manufacturing industry.
く問題点を解決するための手段〉
発明者らは、従来の非調質鋼に高強度と優れた靭性およ
び延性を付与する元素を種々の成分比率で添加して供試
鋼とし、これらの供試鋼について引張試験やシャルピー
衝撃試験等を行ない、研究を重ねた結果、熱間鍛造後冷
却された状態で供試鋼の組織がベイナイトあるいはフェ
ライト・ベイナイトを呈するような最適の化学成分比率
を見出し、本発明を構成するに至った。この第１の発明
の熱間鍛造用非調質鋼は、Ｃ：０．０５〜０．１５重量
％（以下重量％）、Ｓ ｉ： ０．０５〜１．００％、
Ｍｎ： １．３０〜２．５０％、Ｃｒ： ０．３０〜２
．００％、酸可溶Ａ、９： ０．０１５〜０．０６０％
、Ｔｉ： Ｏ，０１０〜０．１００％、Ｂ： ０．
０００３〜０．００５０％を含み、残部Ｆｅおよび不可
避的不純物からなることを特徴とする。Means for Solving Problems〉 The inventors added elements that impart high strength and excellent toughness and ductility to conventional non-tempered steel in various component ratios to make test steels, and As a result of conducting tensile tests, Charpy impact tests, etc. on the test steel, and conducting repeated research, it was possible to find the optimum chemical composition ratio so that the structure of the test steel exhibits bainite or ferrite-bainite when cooled after hot forging. This heading constitutes the present invention. The non-tempered steel for hot forging of the first invention contains C: 0.05 to 0.15% by weight (hereinafter referred to as weight%), Si: 0.05 to 1.00%,
Mn: 1.30-2.50%, Cr: 0.30-2
．． 00%, acid soluble A, 9: 0.015-0.060%
, Ti: O, 010-0.100%, B: 0.
0003 to 0.0050%, with the remainder consisting of Fe and unavoidable impurities.
また、この第２の発明の焼入性向上を図った熱間鍛造用
非調質鋼は、上記第１の発明のＣからＢまでの各元素を
同一比率範囲で含み、さらにＮｂ＝≦０．２０％、Ｍｏ
：≦０．５０％、Ｖ：５０．３０％の少なくとも一種を
含み、残部Ｆｅおよび不可避的不純物からなることを特
徴とする。Further, the non-temperature steel for hot forging with improved hardenability of the second invention contains each element from C to B of the first invention in the same ratio range, and furthermore, Nb=≦0 .20%, Mo
:≦0.50%, V:50.30%, and the balance is Fe and inevitable impurities.
また、この第３の発明の切削性改善を図った熱間鍛造用
非調質鋼は、上記第１の発明のＣからＢまでの各元素を
同一比率範囲で含み、さらにＳ ：≦０１２％、Ｐｂ
≦０．３０％、 Ｃａ： ≦０．０１％、 Ｔｅ：５
０．１０％の少なくとも一種を含み、残部Ｆｅおよび不
可避的不純物からなることを特徴とする。Further, the non-tempered steel for hot forging with improved machinability of the third invention contains each element from C to B of the first invention in the same ratio range, and further has S: ≦012%. , Pb
≦0.30%, Ca: ≦0.01%, Te: 5
It is characterized by containing 0.10% of at least one kind, with the remainder consisting of Fe and unavoidable impurities.
また、この第４の発明の焼入性向上と切削性改傅を図っ
た熱間鍛造用非調質鋼は、上記第２の発明のＣからＶま
での各元素を同一比率範囲で含むとともに、上記第３の
発明のＳからＴｅまでの各元素を同一比率範囲で含み、
残部Ｆｅおよび不可避的不純物からなることを特徴とす
る。In addition, the non-temperature steel for hot forging with improved hardenability and modified machinability of the fourth invention contains each element from C to V of the second invention in the same ratio range, and , containing each element from S to Te of the third invention in the same ratio range,
The balance is characterized by consisting of Fe and unavoidable impurities.
以下、本発明の化学成分限定理由について述べる。The reasons for limiting the chemical components of the present invention will be described below.
Ｃは、Ｖ、Ｎｂなどの炭窒化物の析出強化を利用する従
来の熱間鍛造用非調質鋼においては、鍛造のままで所要
の強度を確保するために０．２５〜０．６０％程度含有
させる必要があった。これは強度の確保を主としてパー
ライトの強度と炭窒化物の析出による強度に依存してい
るためである。しかし、本発明鋼においては、主として
ベイナイト析出による強化で鍛造後の強度を確保してい
るため低炭素化が可能である。靭性の向上に対してはＣ
含有量を少なくする程効果があるが、０．０５％よりも
少ないと、ベイナイト析出させるためにＭｎやＯｒなど
の焼入性向上元素を多く添加する必要があり、不経済な
ので、下限を０．０５％とする。一方、０ｏ１５％を越
えて含有させると、所要の強度は得やすいが、靭性の劣
化が増大するので、上限を０゜１５％とする。C is 0.25 to 0.60% in conventional non-annealed steel for hot forging that utilizes precipitation strengthening of carbonitrides such as V and Nb to ensure the required strength as forged. It was necessary to contain some amount. This is because securing strength mainly depends on the strength of pearlite and the strength due to carbonitride precipitation. However, in the steel of the present invention, the strength after forging is ensured mainly by strengthening by bainite precipitation, so it is possible to reduce carbon. C for improved toughness
The lower the content, the more effective it is, but if it is less than 0.05%, it is necessary to add a large amount of hardenability-improving elements such as Mn and Or to precipitate bainite, which is uneconomical, so the lower limit is set to 0. .05%. On the other hand, if the content exceeds 0°15%, it is easy to obtain the required strength, but the deterioration of toughness increases, so the upper limit is set at 0°15%.
Ｓｉは、脱酸とフェライト地の強化のため０．０５％以
上含有させる必要があるが、１．００％を越えて多量に
含有さけると靭性と切削性が低下するので、上限を１，
００％とする。It is necessary to contain 0.05% or more of Si to deoxidize and strengthen the ferrite base, but if it is avoided in a large amount exceeding 1.00%, toughness and machinability will decrease, so the upper limit should be set to 1.
00%.
Ｍｎは、焼入性向上に大きく寄与する元素で、本発明鋼
には必須の元素である。鍛造後冷却された状態で組織の
主体を低炭素のベイナイトにするためには、他の元素の
添加量にもよるが少なくとも１．３０％の含有量は必要
である。しかし、２．５０％を越えて含有させると、鍛
鋼品の端部などの冷却速度が速くなるところではマルテ
ンサイトが生成することもあるので上限を２．５０％と
した。Mn is an element that greatly contributes to improving hardenability and is an essential element for the steel of the present invention. In order to make the structure mainly composed of low carbon bainite in a cooled state after forging, a content of at least 1.30% is required, although it depends on the amount of other elements added. However, if the content exceeds 2.50%, martensite may be formed in areas where the cooling rate is high, such as at the ends of forged steel products, so the upper limit was set at 2.50%.
Ｃｒも、Ｍｎと同様に焼入性向上元素であり、同様にベ
イナイト組織を適切に得るために、含有量を０３０〜２
．００％の範囲に限定した。Cr is also an element that improves hardenability like Mn, and in order to obtain a bainite structure appropriately, the content should be adjusted to 0.30 to 2.
．． 00% range.
酸可溶ＡｊＪは、脱酸効果と結晶粒度の微細化に有効で
あるが、この効果を有効に発揮させるためには少なくと
も０．０１５％を含有させる必要がある。Acid-soluble AjJ is effective in deoxidizing effect and refining crystal grain size, but in order to effectively exhibit this effect, it is necessary to contain at least 0.015%.
しかし、０．０６０％を越えて多量に含有させてもその
効果が飽和し、また被削性に関しても有害な影響を与え
るので、含有量を０．０１５〜０．０６０％の範囲に限
定した。However, even if the content exceeds 0.060%, the effect will be saturated and it will also have a detrimental effect on machinability, so the content was limited to a range of 0.015 to 0.060%. .
Ｔｉは、強力な炭窒化物形成元素であり、遊離［くの固
定に有効である。本発明鋼はＢの含有を必須としており
、Ｂの焼入性向上効果を十分に発揮させるには、鋼中の
Ｎを固定し、遊離Ｎができる限り存在しないようにしな
ければならない。また、Ｔｉの炭窒化物は鍛造時のオー
ステナイト結晶粒の粗大化を抑制するので、鍛造後生と
して析出したベイナイト組織も微細化され、靭性が向上
する。Ti is a strong carbonitride-forming element and is effective in fixing free Ti. The steel of the present invention must contain B, and in order to fully exhibit the hardenability-improving effect of B, it is necessary to fix N in the steel and prevent free N from existing as much as possible. Further, since Ti carbonitride suppresses coarsening of austenite crystal grains during forging, the bainite structure precipitated as a result of forging is also refined, improving toughness.
このような効果を発揮させるためには、０．０１％以上
含有させる必要があるが、０．１００％を越えて含有さ
せると被削性を低下させるので、上限を０．１００％と
する。In order to exhibit such an effect, it is necessary to contain 0.01% or more, but since containing more than 0.100% reduces machinability, the upper limit is set to 0.100%.
Ｂは、周知の如く微量添加で亜共析鋼の焼入性を大幅に
向上させるため、低炭素のベイナイト組織を得るのに特
に有効な元素である。焼入性の向上は、Ｍｏ 、Ｍｎ
、Ｃｒ 、Ｎｉ 、Ｃｕ等の焼入性向上元素を多量に含
有させることによっても可能であるが、その場合、これ
らの合金元素添加によって鋼材費が、通常の焼入れ・焼
戻し処理を施した調質の機械構造用鋼や低合金鋼の価格
を上廻り、非調質馴化のメリットが失われてしまう。そ
のため、Ｂの添加は必須であり、安定した焼入性向上効
果を得るために、その含有量を０．０００３〜０．００
５０％の範囲に限定した。B is an element that is particularly effective in obtaining a low carbon bainite structure because, as is well known, B can greatly improve the hardenability of hypo-eutectoid steel when added in a small amount. Hardenability is improved by Mo, Mn
It is also possible to add large amounts of hardenability-improving elements such as Cr, Ni, Cu, etc.; however, in that case, the addition of these alloying elements reduces the cost of the steel material compared to that of conventional hardening and tempering treatments. The price exceeds that of mechanical structural steel and low-alloy steel, and the benefits of non-thermal conditioning are lost. Therefore, the addition of B is essential, and in order to obtain a stable hardenability improvement effect, the content should be adjusted to 0.0003 to 0.000.
It was limited to a range of 50%.
Ｎｂ 、Ｍｏ 、Ｖは、いずれも鍛造前の加熱でオース
テナイト組織中に固溶し、少量の含有量でも焼入性向上
に有効なので、必要に応じて添加するものとし、夫々の
含有量の上限を０．２０％、 ０．５０％。Nb, Mo, and V all form a solid solution in the austenite structure when heated before forging, and are effective in improving hardenability even in small amounts. Therefore, they should be added as necessary, and the upper limit of each content should be set. 0.20%, 0.50%.
０．３０％とした。It was set to 0.30%.
Ｓ、Ｐｂ、Ｃａ 、Ｔｅは、いずれも鋼の被削性（切削
性）を改善するため、鍛造後の製品を機械加工する場合
、必要に応じて添加するものとし、夫々の含有量の上限
を、０．１２％、 ０．３０％、００１％、０゜１０％
とした。S, Pb, Ca, and Te all improve the machinability of steel, so when machining products after forging, they shall be added as necessary, and the upper limit of each content shall be , 0.12%, 0.30%, 001%, 0°10%
And so.
〈発明の効果〉
本発明の熱間鍛造用非調質鋼は、熱間鍛造後冷却された
状態でその組織がベイナイトあるいはフェライト・ベイ
ナイトを呈すべく添加元素を最適に含有するとともに、
焼入性向上元素や切削性改善元素を必要に応じて添加す
るようにしているので、鍛造後の調質熱処理が不要で従
来の調質鋼より安価に製造でき、しかも鍛造後冷却のま
まで、従来の調質鋼に劣らぬ高強度と優れた靭性および
延性を具備し、さらに良好な焼入性や切削性を仔する。<Effects of the Invention> The non-tempered steel for hot forging of the present invention optimally contains additive elements so that its structure exhibits bainite or ferrite-bainite when cooled after hot forging, and
Since hardenability-improving elements and machinability-improving elements are added as necessary, there is no need for tempering heat treatment after forging, making it cheaper to manufacture than conventional tempered steel, and it can be left cooled after forging. It has high strength, excellent toughness and ductility comparable to conventional tempered steel, and also has good hardenability and machinability.
〈実施例〉 以下、本発明を実施例により詳細に説明する。<Example> Hereinafter, the present invention will be explained in detail with reference to Examples.
末尾に掲げた第１表は、引張り試験とシャルピー衝撃試
験に供した供試鋼の化学組成、熱処理条件および上記試
験の結果を示している。これらの供試鋼は、成分を調整
して溶製され、７２開φに圧延された。そして、上記供
試鋼を、まず長さ２５０ｍｍに切断し、その後１２５０
°Ｃに加熱して、ハンマーで直径５０ｍｍの丸棒に鍛伸
した。仕上成形時の終了温度は１１５０℃で、その後、
大気中で放冷した。供試ｗ４Ｎｏ、１３は、調質鋼の一
例としての５５３Ｃ鋼で、熱間鍛造後、従来どおり再加
熱して、焼入れ焼戻し処理を施している。鍛伸された丸
棒の中央部より１手方向にＪＩＳ４号（平行部径１４ｍ
ｍφ）引張試験片ＴＳおよび月Ｓ３号（２ｍｍＵノツチ
）衝撃試験片ＣＨを採取し、鍛伸材の機械的性質を調査
した。第１表中、供試ｊｌ！Ｎｏ、Ｉ〜７は本特許請求
の範囲内の発明鋼、供試１１ｉＮｏ、８〜１３は上記発
明鋼に対する比較鋼である。表から明らかなように、本
発明鋼は、比較鋼に比べて、概してＣの含有量が少ない
一方、Ｍｎの含有量が多く、比較間にないＮｂを含有し
ている。Table 1 listed at the end shows the chemical composition, heat treatment conditions, and results of the above tests of the test steels subjected to the tensile test and Charpy impact test. These test steels were melted with adjusted components and rolled to a diameter of 72 mm. The above test steel was first cut to a length of 250 mm, and then cut to a length of 1250 mm.
It was heated to °C and forged into a round bar with a diameter of 50 mm using a hammer. The finishing temperature during final molding was 1150°C, and then
It was left to cool in the air. Sample w4 No. 13 is 553C steel as an example of tempered steel, and after hot forging, it is reheated as usual and subjected to quenching and tempering treatment. JIS No. 4 (parallel part diameter 14 m) in one direction from the center of the forged round bar.
mφ) tensile test piece TS and Tsuki S3 (2 mm U notch) impact test piece CH were taken to investigate the mechanical properties of the forged and drawn material. In Table 1, test jl! Nos. I to 7 are inventive steels within the scope of the claims of the present invention, and Samples 11iNo. 8 to 13 are comparative steels for the above-mentioned inventive steels. As is clear from the table, the steels of the present invention generally have a lower C content and a higher Mn content than the comparative steels, and contain Nb, which is not found in the comparison steels.
表中の引張試験と衝撃試験結果について述べれば、本発
明鋼（Ｎｏ、１〜７）は、従来の非調質鋼（Ｎｏ、１３
）と比較して何ら劣らぬ強度と靭性を具備している。こ
れに対して、本特許請求の範囲外にある比較鋼のうち、
供試鋼Ｎ０１８〜ｌＯは高炭素化によって所要の強度は
確保できるが、靭性値が低い。また、供試鋼Ｎｏ、１１
は低炭素化によって所要の靭性値は得られるが、強度が
不足している。本発明鋼の中でも、供試鋼Ｎｏ、 ５
、７は、ベイナイト１柑の組織を呈し、引張強さが９７
４ｋｇｆ／ ｍｍ’。Regarding the tensile test and impact test results in the table, the present invention steels (Nos. 1 to 7) are different from conventional non-tempered steels (No. 13).
) has strength and toughness that are comparable to those of On the other hand, among the comparative steels that are outside the scope of the claims,
Although the required strength can be ensured by increasing the carbon content of the test steels N018 to IO, their toughness values are low. In addition, test steel No. 11
Although the required toughness value can be obtained by reducing the carbon content, the strength is insufficient. Among the steels of the present invention, test steel No. 5
, 7 exhibits a bainite structure and has a tensile strength of 97.
4kgf/mm'.
１．０２．Ｏｋｇｆ／ ｍｍ”と高いばかりでなく、靭
性にも優れている。このことから、本発明の非調質鋼を
素材鋼とすることにより、従来熱間鍛造後再加熱。1.02. It not only has a high Okgf/mm" but also excellent toughness. For this reason, by using the non-tempered steel of the present invention as a raw material steel, it can be reheated after conventional hot forging.
焼入れ焼戻しなどの費用のかかる調質処理を経て製造さ
れていた例えばステアリングナックル、フロントアクス
ル等の部品を、熱間鍛造後冷却するだけで安価に製造す
ることができる。For example, parts such as steering knuckles and front axles, which were previously manufactured through expensive heat treatment such as quenching and tempering, can be manufactured at low cost by simply cooling after hot forging.
Claims (4)
Ｓｉ：０．０５〜１．００％、Ｍｎ：１．３０〜２．５
０％、Ｃｒ：０．３０〜２．００％、酸可溶Ａｌ：０．
０１５〜０．０６０％、Ｔｉ：０．０１０〜０．１００
％、Ｂ：０．０００３〜０．０００５％を含み、残部Ｆ
ｅおよび不可避的不純物からなる熱間鍛造用の非調質鋼
。(1) C: 0.05 to 0.15% by weight (hereinafter referred to as weight%),
Si: 0.05-1.00%, Mn: 1.30-2.5
0%, Cr: 0.30-2.00%, acid-soluble Al: 0.
015-0.060%, Ti: 0.010-0.100
%, B: 0.0003 to 0.0005%, the remainder F
Non-thermal steel for hot forging consisting of e and inevitable impurities.
．００％、Ｍｎ：１．３０〜２．５０％、Ｃｒ：０．３
０〜２．００％、酸可溶Ａｌ：０．０１５〜０．０６０
％、Ｔｉ：０．０１０〜０．１００％、Ｂ：０．０００
３〜０．０００５％を含み、さらにＮｂ：≦０．２０％
、Ｍｏ：≦０．５０％、Ｖ：≦０．３０％の少なくとも
一種を含み、残部Ｆｅおよび不可避的不純物からなる焼
入性向上を図った熱間鍛造用の非調質鋼。(2) C: 0.05-0.15%, Si: 0.05-1
．． 00%, Mn: 1.30-2.50%, Cr: 0.3
0-2.00%, acid-soluble Al: 0.015-0.060
%, Ti: 0.010-0.100%, B: 0.000
Contains 3 to 0.0005%, and further includes Nb: ≦0.20%
, Mo:≦0.50%, V:≦0.30%, and the remainder consists of Fe and unavoidable impurities.
．００％、Ｍｎ：１．３０〜２．５０％、Ｃｒ：０．３
０〜２．００％、酸可溶Ａｌ：０．０１５〜０．０６０
％、Ｔｉ：０．０１０〜０．１００％、Ｂ：０．０００
３〜０．０００５％を含み、さらにＳ：≦０．１２％、
Ｐｂ：≦０．３０％、Ｃａ：≦０．０１％、Ｔｅ：≦０
．１０％の少なくとも一種を含み、残部Ｆｅおよび不可
避的不純物からなる切削性改善を図った熱間鍛造用の非
調質鋼。(3) C: 0.05-0.15%, Si: 0.05-1
．． 00%, Mn: 1.30-2.50%, Cr: 0.3
0-2.00%, acid-soluble Al: 0.015-0.060
%, Ti: 0.010-0.100%, B: 0.000
Contains 3 to 0.0005%, further S: ≦0.12%,
Pb:≦0.30%, Ca:≦0.01%, Te:≦0
．． A non-tempered steel for hot forging with improved machinability, containing at least 10% of Fe and unavoidable impurities.
．００％、Ｍｎ：１．３０〜２．５０％、Ｃｒ：０．３
０〜２．００％、酸可溶Ａｌ：０．０１５〜０．０６０
％、Ｔｉ：０．０１０〜０．１００％、Ｂ：０．０００
３〜０．０００５％を含み、さらにＮｂ：≦０．２０％
、Ｍｏ：≦０．５０％、Ｖ：≦０．３０％の少なくとも
一種を含むとともに、Ｓ：≦０．１２％、Ｐｂ：≦０．
３０％、Ｃａ：≦０．０１％、Ｔｅ：０．１０％の少な
くとも一種を含み、残部Ｆｅおよび不可避的不純物から
なる焼入性向上と切削性改善を図った熱間鍛造用の非調
質鋼。(4) C: 0.05-0.15%, Si: 0.05-1
．． 00%, Mn: 1.30-2.50%, Cr: 0.3
0-2.00%, acid-soluble Al: 0.015-0.060
%, Ti: 0.010-0.100%, B: 0.000
Contains 3 to 0.0005%, and further includes Nb: ≦0.20%
, Mo:≦0.50%, V:≦0.30%, S:≦0.12%, Pb:≦0.
Non-thermal treatment for hot forging with improved hardenability and machinability, containing at least one of the following: 30%, Ca: ≦0.01%, Te: 0.10%, with the remainder being Fe and unavoidable impurities. steel.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60080883A JPH0772323B2 (en) | 1985-04-15 | 1985-04-15 | Non-heat treated steel bar for hot forging |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60080883A JPH0772323B2 (en) | 1985-04-15 | 1985-04-15 | Non-heat treated steel bar for hot forging |
Related Child Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP20571896A Division JP2667386B2 (en) | 1996-08-05 | 1996-08-05 | Unheated steel bars for hot forging |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61238941A true JPS61238941A (en) | 1986-10-24 |
| JPH0772323B2 JPH0772323B2 (en) | 1995-08-02 |
Family
ID=13730740
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60080883A Expired - Lifetime JPH0772323B2 (en) | 1985-04-15 | 1985-04-15 | Non-heat treated steel bar for hot forging |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0772323B2 (en) |
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63111159A (en) * | 1986-10-30 | 1988-05-16 | Nkk Corp | High strength and high toughness non-heattreated steel for hot forging |
| JPS63130748A (en) * | 1986-11-21 | 1988-06-02 | Daido Steel Co Ltd | Non-heattreated tough and hard steel having high strength |
| JPS63130749A (en) * | 1986-11-21 | 1988-06-02 | Daido Steel Co Ltd | Hot-forging and hardening steel combining high strength with high toughness |
| JPS63166949A (en) * | 1986-12-27 | 1988-07-11 | Aichi Steel Works Ltd | Non-heattreated steel for hot forging |
| JPS63312949A (en) * | 1987-06-15 | 1988-12-21 | Kobe Steel Ltd | Non-refining steel for hot forging having high toughness |
| JPH01129953A (en) * | 1987-11-16 | 1989-05-23 | Kobe Steel Ltd | High strength non-heat treated steel and its manufacture |
| JPH0288748A (en) * | 1988-09-27 | 1990-03-28 | Nkk Corp | Steel for machine structural use having excellent machinability |
| JPH0448029A (en) * | 1990-06-14 | 1992-02-18 | Nissan Motor Co Ltd | Production of carriage parts for automobile use with high strength |
| JPH04141548A (en) * | 1990-09-28 | 1992-05-15 | Aichi Steel Works Ltd | High strength and high toughness non-heat treated steel for forging |
| JPH04210449A (en) * | 1990-12-12 | 1992-07-31 | Toa Steel Co Ltd | High toughness non-heat treated steel for hot forging |
| US5362338A (en) * | 1990-07-27 | 1994-11-08 | Aichi Steel Works Ltd. | Non-heat treating steel for hot forging |
| CN114317923A (en) * | 2021-12-31 | 2022-04-12 | 无锡透平叶片有限公司 | Hot working process for improving short transverse impact performance of X5CrNiCuNb16-4 turbine blade |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5351121A (en) * | 1976-10-20 | 1978-05-10 | Sumitomo Metal Ind Ltd | Production of medium or low carbn high tensile wire rod |
| JPS54134019A (en) * | 1978-04-11 | 1979-10-18 | Kawasaki Steel Co | Production of nonnrefined highhtensile hottrolled steel beltfor use in processing |
| JPS5983719A (en) * | 1982-11-02 | 1984-05-15 | Nippon Steel Corp | Preparation of unnormalized high strength steel |
-
1985
- 1985-04-15 JP JP60080883A patent/JPH0772323B2/en not_active Expired - Lifetime
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5351121A (en) * | 1976-10-20 | 1978-05-10 | Sumitomo Metal Ind Ltd | Production of medium or low carbn high tensile wire rod |
| JPS54134019A (en) * | 1978-04-11 | 1979-10-18 | Kawasaki Steel Co | Production of nonnrefined highhtensile hottrolled steel beltfor use in processing |
| JPS5983719A (en) * | 1982-11-02 | 1984-05-15 | Nippon Steel Corp | Preparation of unnormalized high strength steel |
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63111159A (en) * | 1986-10-30 | 1988-05-16 | Nkk Corp | High strength and high toughness non-heattreated steel for hot forging |
| JPS63130748A (en) * | 1986-11-21 | 1988-06-02 | Daido Steel Co Ltd | Non-heattreated tough and hard steel having high strength |
| JPS63130749A (en) * | 1986-11-21 | 1988-06-02 | Daido Steel Co Ltd | Hot-forging and hardening steel combining high strength with high toughness |
| JPS63166949A (en) * | 1986-12-27 | 1988-07-11 | Aichi Steel Works Ltd | Non-heattreated steel for hot forging |
| JPS63312949A (en) * | 1987-06-15 | 1988-12-21 | Kobe Steel Ltd | Non-refining steel for hot forging having high toughness |
| JPH01129953A (en) * | 1987-11-16 | 1989-05-23 | Kobe Steel Ltd | High strength non-heat treated steel and its manufacture |
| JPH0288748A (en) * | 1988-09-27 | 1990-03-28 | Nkk Corp | Steel for machine structural use having excellent machinability |
| JPH0448029A (en) * | 1990-06-14 | 1992-02-18 | Nissan Motor Co Ltd | Production of carriage parts for automobile use with high strength |
| US5362338A (en) * | 1990-07-27 | 1994-11-08 | Aichi Steel Works Ltd. | Non-heat treating steel for hot forging |
| JPH04141548A (en) * | 1990-09-28 | 1992-05-15 | Aichi Steel Works Ltd | High strength and high toughness non-heat treated steel for forging |
| JPH04210449A (en) * | 1990-12-12 | 1992-07-31 | Toa Steel Co Ltd | High toughness non-heat treated steel for hot forging |
| CN114317923A (en) * | 2021-12-31 | 2022-04-12 | 无锡透平叶片有限公司 | Hot working process for improving short transverse impact performance of X5CrNiCuNb16-4 turbine blade |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0772323B2 (en) | 1995-08-02 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| EXPY | Cancellation because of completion of term |