JPH07109021B2 - Tool steel for hot working - Google Patents
Tool steel for hot workingInfo
- Publication number
- JPH07109021B2 JPH07109021B2 JP60290176A JP29017685A JPH07109021B2 JP H07109021 B2 JPH07109021 B2 JP H07109021B2 JP 60290176 A JP60290176 A JP 60290176A JP 29017685 A JP29017685 A JP 29017685A JP H07109021 B2 JPH07109021 B2 JP H07109021B2
- Authority
- JP
- Japan
- Prior art keywords
- less
- steel
- toughness
- present
- effect
- 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.)
- Expired - Lifetime
Links
Landscapes
- Heat Treatment Of Steel (AREA)
- Forging (AREA)
Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は高い高温強度、耐摩耗性を有するとともに、き
わめて大きい焼入性とすぐれた靭性を有し、使用時の昇
温温度が高く、併せて過酷な摩耗作用、熱衝撃を受け、
かつ大きい衝撃応力を受ける各種寸法の熱間鍛造型など
熱間工具用途に適用し、長寿命を与える型材料に関する
ものである。DETAILED DESCRIPTION OF THE INVENTION [Industrial field of application] The present invention has high high temperature strength and wear resistance, has extremely high hardenability and excellent toughness, and has a high temperature rise during use. In addition, it is subjected to severe wear and thermal shock,
In addition, the present invention relates to a die material which is applied to hot tool applications such as hot forging dies of various sizes which are subjected to large impact stress and which has a long life.
使用中の型面温度の上昇が激しく、高度の熱間強度なら
びに熱間耐摩耗性を要求される用途に対しては、従来最
も高温強度の高い材料として高Ｗ−Ｖ−Co系のAISI H19
系鋼が使用されていた。AISI H19 of high WV-Co type is conventionally used as the material with the highest high-temperature strength for applications where the die surface temperature rises sharply during use and high levels of hot strength and hot wear resistance are required.
Steels were used.
しかしこれは、高温強度が高い反面靭性が低く、用途に
より使用中早期割れ発生をまねく場合があり、また焼入
性が小さいため、焼入冷却速度の僅かな低下により、上
部ベイナイト組織の多量の生成をまねき、この結果靭性
が大幅に低下するため、中〜大寸法の型への適用が困難
であった。However, this has high high temperature strength but low toughness, which may lead to early cracking during use depending on the application.Because the hardenability is small, a small decrease in the quenching cooling rate may result in a large amount of the upper bainite structure. It has been difficult to apply to medium- to large-sized molds, since it causes the formation and the toughness is significantly reduced as a result.
本発明鋼の化学組成は、中Ｃ−中Cr−Ni−中（Ｗ・Mo）
−中〜Ｖ−Ｎを基本成分とし、靭性低下の要因の一つで
ある粗大なVC炭化物の生成を抑制し、また基地の焼入組
織を半冷30min程度の徐冷焼入の場合にもマルテンサイ
ト組織主体の組織となるよう十分な焼入性を付与するた
め、Ｃ、Cr、Ni、Mnを主体とした合金組成を適切に組合
せ、併せて凝固組織の微細化、オーステナイト結晶粒径
の微細化による靭性向上効果を与え、大寸法の型でもす
ぐれた靭性が得られる特性を付与したものである。The chemical composition of the steel of the present invention is medium C-medium Cr-Ni-medium (W · Mo).
-Medium to VN is used as a basic component to suppress the formation of coarse VC carbides, which is one of the factors that reduce the toughness, and also when the quenching structure of the matrix is annealed for about 30 min. In order to impart sufficient hardenability so that the structure is mainly composed of martensite structure, the alloy composition mainly composed of C, Cr, Ni and Mn is appropriately combined, and at the same time, the refinement of the solidification structure and the austenite grain size It has the effect of improving the toughness by miniaturization and imparts the property of obtaining excellent toughness even in a large-sized mold.
また、Ｃ、Ｗ、Mo、Ｖ量の適切な組合せにより、すぐれ
た高温強度と高温耐摩耗性を付与するとともに、Cr、C
o、Niの添加、Si量の調整により、使用時の昇温により
型面に緻密で固着性が大きく適度の厚みを有する酸化被
膜を形成させ、この面からも高度の高温耐摩耗性、焼付
性を付与したものである。Also, by combining C, W, Mo, and V in an appropriate amount, excellent high-temperature strength and high-temperature wear resistance are imparted, and Cr, C
By adding o and Ni, and adjusting the amount of Si, a dense oxide film with a large amount of adhesion and a proper thickness is formed on the mold surface due to temperature rise during use, and from this surface also high temperature wear resistance and baking It is the one to which sex is given.
すなわち本願発明は、 重量％でC0.36〜0.50％、Si1.00％以下、Mn1.50％以
下、Ni0.50〜2.30％、Cr4.05〜6.50％、（1/2W＋Mo）1.
90〜3.50％、V0.50％以上1.00％未満、N0.025〜0.15
％、残部Feおよび通常の不純物からなることを特徴とす
る熱間加工用工具鋼、 重量％でC0.36〜0.50％、Si1.00％以下、Mn1.50％以
下、Ni0.50〜2.30％、Cr4.05〜6.50％、（1/2W＋Mo）1.
90〜3.50％、V0.50％以上1.00％未満、N0.025〜0.15
％、Co0.50〜4.00％、残部Feおよび通常の不純物からな
ることを特徴とする熱間加工用工具鋼、 重量％でC0.36〜0.50％、Si1.00％以下、Mn1.50％以
下、Ni0.50〜2.30％、Cr4.05〜6.50％、（1/2W＋Mo）1.
90〜3.50％、V0.50％以上1.00％未満、N0.025〜0.15
％、Nb0.02〜0.15％、残部Feおよび通常の不純物からな
ることを特徴とする熱間加工用工具鋼、および、 重量％でC0.36〜0.50％、Si1.00％以下、Mn1.50％以
下、Ni0.50〜2.30％、Cr4.05〜6.50％、（1/2W＋Mo）1.
90〜3.50％、V0.50％以上1.00％未満、N0.025〜0.15
％、Co0.50〜4.00％、Nb0.02〜0.15％、残部Feおよび通
常の不純物からなることを特徴とする熱間加工用工具鋼
である。That is, the present invention is C0.36-0.50%, Si1.00% or less, Mn1.50% or less, Ni0.50-2.30%, Cr4.05-6.50%, (1 / 2W + Mo) 1.
90 to 3.50%, V0.50% to less than 1.00%, N0.025 to 0.15
%, Balance Fe and normal impurities, hot work tool steel, C0.36 ~ 0.50% by weight%, Si1.00% or less, Mn1.50% or less, Ni0.50 ~ 2.30% , Cr4.05-6.50%, (1 / 2W + Mo) 1.
90 to 3.50%, V0.50% to less than 1.00%, N0.025 to 0.15
%, Co 0.50 to 4.00%, balance Fe and ordinary impurities, hot work tool steel, C0.36 to 0.50% by weight, Si 1.00% or less, Mn 1.50% or less , Ni0.50 to 2.30%, Cr4.05 to 6.50%, (1 / 2W + Mo) 1.
90 to 3.50%, V0.50% to less than 1.00%, N0.025 to 0.15
%, Nb0.02 to 0.15%, balance Fe and ordinary impurities, and hot working tool steel, and C0.36 to 0.50% by weight, Si1.00% or less, Mn1.50 % Or less, Ni0.50 to 2.30%, Cr4.05 to 6.50%, (1 / 2W + Mo) 1.
90 to 3.50%, V0.50% to less than 1.00%, N0.025 to 0.15
%, Co 0.50 to 4.00%, Nb 0.02 to 0.15%, the balance Fe and ordinary impurities, and is a hot work tool steel.
次に本発明鋼の成分限定の理由について述べる。 Next, the reasons for limiting the components of the steel of the present invention will be described.
Ｃは、本発明鋼のすぐれた焼入性、焼もどし硬さ、およ
び高温硬さを維持し、またＷ、Mo、Ｖ、NbおよびCrなど
の炭化物生成元素と結合して炭化物を形成し、結晶粒の
微細化、耐摩耗性、焼もどし軟化抵抗、高温硬さを与え
るために添加するものである。C maintains excellent hardenability, tempering hardness, and high temperature hardness of the steel of the present invention, and forms a carbide by combining with a carbide-forming element such as W, Mo, V, Nb and Cr, It is added in order to give finer crystal grains, wear resistance, temper softening resistance, and high temperature hardness.
多すぎると靭性が低下するので、含有量を0.50％以下と
し、低すぎると上記添加の効果が得られないので、含有
量を0.36％以上とする。If the amount is too large, the toughness is lowered, so the content is made 0.50% or less, and if it is too low, the effect of the above addition cannot be obtained, so the content is made 0.36% or more.
SiはA1変態点を高めるため、および用途に応じた耐酸化
特性を付与するために添加される。Si is added to increase the A 1 transformation point and to impart oxidation resistance characteristics depending on the application.
多量の添加は靭性の点で不利であり、また使用時の保護
性酸化被膜が形成されにくくなり、また熱伝導性の低下
をまねくので1.00％以下とする。Addition of a large amount is disadvantageous in terms of toughness, a protective oxide film is less likely to be formed during use, and thermal conductivity is deteriorated.
Mnは、本発明鋼の特徴である特にすぐれた焼入性を付与
するために添加される。Mn is added to impart the particularly excellent hardenability characteristic of the steel of the present invention.
多量の添加は焼なまし硬さを上げ、被切削性を低下さ
せ、またA1変態点の低下をまねくので、1.50％以下とす
る。Addition of a large amount raises the annealing hardness, reduces the machinability, and lowers the A 1 transformation point, so it should be 1.50% or less.
NiはＣ、Cr、Mn、Mo、Ｗなどとともに本発明鋼にすぐれ
た焼入性を付与し、緩やかな焼入冷却速度の場合にも、
マルテンサイト主体の組織を形成し、靭性の低下を防ぐ
ための重要な添加元素である。また基地の本質的な靭性
改善を与える。Ni, together with C, Cr, Mn, Mo, W, etc., imparts excellent hardenability to the steel of the present invention, and even in the case of a slow quenching cooling rate,
It is an important additive element for forming a structure mainly composed of martensite and preventing a decrease in toughness. It also provides an essential toughness improvement for the base.
Niは上記効果を得るために添加されるが、多すぎるとA1
変態点を過度に低下させ、耐摩耗寿命の低下をまねき、
また焼きなまし硬さを過度に高くして機械加工性を低下
させるので2.30％以下とし、低すぎると上記添加の効果
が得られないので0.50％以上とする。Ni is added to obtain the above effect, but if too much is added A 1
Excessively lowering the transformation point will lead to a decrease in wear resistance life,
Further, since the annealing hardness is excessively increased to deteriorate the machinability, it is set to 2.30% or less, and if it is too low, the effect of the above addition cannot be obtained, so it is set to 0.50% or more.
Crは本発明鋼の特徴である焼入性の向上を目的として添
加されるもので、Niとともに本発明鋼における最も重要
な元素の一つであり、Cr量の設定はきわめて重要であ
る。またCrは焼もどし軟化抵抗および高温強度の向上、
また適度の酸化被膜特性の付与、Ｃと結合して炭化物を
形成することによる耐摩耗性向上効果、A1変態点向上効
果を得るために添加される。Cr is added for the purpose of improving the hardenability, which is a feature of the steel of the present invention, and is one of the most important elements in the steel of the present invention, together with Ni, and the setting of the Cr amount is extremely important. Also, Cr improves temper softening resistance and high temperature strength,
Further, it is added for the purpose of imparting an appropriate oxide film characteristic, the effect of improving wear resistance by combining with C to form a carbide, and the effect of improving the A 1 transformation point.
低すぎると本発明鋼の特徴である特にすぐれた焼入性を
保持することが困難となり、また耐酸化性が不足し、使
用時肌あれを生じ易く、A1変態点の低下、昇温時の軟化
抵抗の劣化、残留炭化物の減少等により、良好な靭性を
耐摩耗性を兼備させるのが困難となるので4.05％以上と
し、高すぎると昇温時凝集しやすい炭化物を形成し、高
温強度、軟化抵抗を低下させるので6.50％以下とする。
徐冷焼入によっても十分な焼入性を得るためには、4.50
〜6.50％添加させるのがより望ましい。If it is too low, it becomes difficult to maintain particularly excellent hardenability, which is a feature of the steel of the present invention, and also the oxidation resistance is insufficient, and it is easy for rough skin to occur during use, lowering of A 1 transformation point, and at the time of heating It becomes difficult to combine good toughness with wear resistance due to deterioration of softening resistance, decrease of residual carbides, etc., so it is 4.05% or more. Since it lowers the softening resistance, it should be 6.50% or less.
To obtain sufficient hardenability even with slow cooling quenching, 4.50
It is more desirable to add ~ 6.50%.
Ｗは焼入加熱時に固溶しにくい炭化物を多量に形成し
て、耐摩耗性向上に独得の効果をもたらすものであり、
また焼もどし時、凝集しにくい微細な炭化物を析出して
高温耐力を高め、また昇温時の軟化抵抗を特に高くし、
さらに使用中の昇温時に形成される表面酸化被膜の緻密
性を向上させるために添加するものである。Ｗは、多す
ぎると従来鋼と同様粗大な炭化物を形成する傾向が大と
なり、靭性の低下をまねく。W forms a large amount of carbide that does not easily form a solid solution during quenching and heating, and has a unique effect in improving wear resistance,
Also, during tempering, fine carbides that do not easily agglomerate are deposited to increase the high temperature proof stress, and the softening resistance at the time of temperature rise is particularly increased.
Further, it is added to improve the denseness of the surface oxide film formed when the temperature is raised during use. If the W content is too large, the tendency to form coarse carbides becomes large as in the case of conventional steel, leading to a decrease in toughness.
Moは炭化物を形成し、耐摩耗性を高め、基地に固溶して
焼入性を向上させ、また焼もどし時、微細な炭化物を形
成して高温強度および昇温時の軟化に対する抵抗性を高
め、また使用中の保護性酸化被膜の生成容易性を向上さ
せる効果をもたらすものである。Mo forms carbides, enhances wear resistance, forms a solid solution in the matrix to improve hardenability, and forms fine carbides during tempering to improve high-temperature strength and resistance to softening at elevated temperatures. It also has the effect of improving the easiness of forming a protective oxide film during use.
Ｗ、Moは上記効果を得るために添加するが、多すぎると
粗大炭化物の形成や、炭化物量の増大などにより靭性を
低下させ、本発明鋼の特徴であるすぐれた靭性を保持さ
せることが困難となるので、（1/2W＋Mo）で3.50％以下
とし、低すぎると上記添加の効果が得られないので1.90
％以上とする。W and Mo are added in order to obtain the above effect, but if they are too much, the toughness is lowered due to the formation of coarse carbides or the increase of the amount of carbides, and it is difficult to maintain the excellent toughness which is a feature of the steel of the present invention. Therefore, if (1 / 2W + Mo) is 3.50% or less, if it is too low, the effect of the above addition cannot be obtained.
% Or more.
なお、ＷとMoの添加効果は類似しているが、高温強度、
耐摩耗性に関してはＷの方が有利であり、靭性に関して
はMoの方が有利で、目的、用途により単独または複合添
加を行なうものである。Although the effect of adding W and Mo is similar,
W is more advantageous in terms of wear resistance, and Mo is more advantageous in terms of toughness, and they may be added individually or in combination depending on the purpose and application.
Ｖは固溶しにくい炭化物を多量に形成して耐摩耗性およ
び耐焼付性向上効果をもたらすものであり、かつ焼入加
熱時基地に固溶して、焼もどし時微細な凝集しにくい炭
化物を析出し、高い温度領域における軟化抵抗を向上さ
せる。V forms a large amount of carbides that are hard to form a solid solution to bring about the effects of improving wear resistance and seizure resistance, and forms a solid solution in the base during quenching and heating to form fine carbides that are hard to agglomerate during tempering. Precipitates and improves the softening resistance in the high temperature region.
また焼入時の結晶粒微細化効果をもたらし靭性を向上さ
せ、またA1変態点をあげ高温強度向上効果とあいまっ
て、耐ヒートクラック性を向上させる。多すぎると粗大
な炭化物に生成し、本発明鋼の特徴であるすぐれた靭性
を保持させることが困難となるので1.00％未満とし、低
すぎると上記添加の効果が得られないので0.50％以上と
する。Further, it brings about an effect of refining crystal grains at the time of quenching and improves toughness, and also improves heat crack resistance together with an effect of improving high temperature strength by raising A 1 transformation point. If it is too large, coarse carbides are formed, and it becomes difficult to maintain the excellent toughness that is a characteristic of the steel of the present invention, so less than 1.00%, and if it is too low, the effect of the above addition cannot be obtained, so 0.50% or more. To do.
ＮはNbとともに凝固組織を微細化し、また焼入時に結晶
粒を微細化させ、徐冷焼入においても粗大な上部ベイナ
イトの生成を防止して、高い靭性を保持させ、本発明鋼
の効果を達成させるための不可欠の重要な添加元素であ
る。N refines the solidification structure together with Nb, and also refines the crystal grains during quenching, prevents the formation of coarse upper bainite even during slow quenching, and retains high toughness, thereby achieving the effect of the steel of the present invention. It is an indispensable important additional element to achieve.
Ｎは上記効果を得るために添加されるが多量の添加は必
要なく、固溶限からの制約もあり0.15％以下とし、低す
ぎると上記添加の効果が得られないので0.025％以上と
する。N is added in order to obtain the above effect, but it is not necessary to add a large amount and is limited to 0.15% or less due to the limitation from the solid solution limit. If it is too low, the effect of the above addition cannot be obtained, so N is set to 0.025% or more.
Coは本発明鋼において、きわめて大きい高温耐摩耗性を
付与するための添加元素である。これはCoの添加によ
り、使用中の昇温時きわめて緻密で密着性のよい保護性
酸化被膜を形成し、これにより、相手材との間の金属接
触を防ぎ、本発明鋼の温度上昇を防ぐとともにすぐれた
耐摩耗性をもたらすものである。Co is an additive element for imparting extremely high temperature wear resistance in the steel of the present invention. This is because the addition of Co forms a protective oxide film that is extremely dense and has good adhesion when the temperature rises during use, which prevents metal contact with the mating material and prevents the temperature rise of the steel of the present invention. It also provides excellent wear resistance.
Coのこの効果は、Cr、Niをはじめ、Ｗ、Moその他の添加
元素量との関係において異なってくるもので、本発明鋼
の場合、多量の添加を必要としない。多すぎると靭性を
低下させるので4.00％以下とし、低すぎると上記添加の
効果が得られないので0.50％以上とする。This effect of Co is different in relation to the amounts of added elements such as Cr, Ni, W, Mo and the like, and in the case of the steel of the present invention, it is not necessary to add a large amount. If it is too large, the toughness is lowered, so it is set to 4.00% or less, and if it is too low, the effect of the above addition cannot be obtained, so it is made 0.50% or more.
Nbは焼もどし時、微細で特に凝集しにくい炭化物を形成
し、昇温時の軟化抵抗を特に高め、また焼入時の結晶粒
の微細化のために添加される。Nb forms carbides that are fine and does not easily agglomerate at the time of tempering, particularly enhances the softening resistance at the time of temperature rise, and is added for refining the crystal grains during quenching.
またＮ、Ｃと結び付いて凝固時の初晶生成時の核作用に
より、凝固組織を微細化し、靭性向上の効果をもたら
す。In addition, by combining with N and C, the solidification structure is refined by the nuclear action at the time of primary crystal formation during solidification, and the effect of improving toughness is brought about.
Nbは上記効果を得るために添加されるが、多すぎると粗
大な炭化物を形成し、靭性を低下させるので0.15％以下
とし、低すぎると上記添加の効果が得られないので0.02
％以下とする。Nb is added to obtain the above effect, but if it is too much, coarse carbides are formed and the toughness is reduced, so it is 0.15% or less, and if it is too low, the effect of the above addition cannot be obtained, so 0.02
% Or less.
以下本発明を実施例に基づき詳細に説明する。 Hereinafter, the present invention will be described in detail based on examples.
第１表に本発明鋼および従来の熱間加工用工具鋼の化学
組成を示す。Table 1 shows the chemical compositions of the steel of the present invention and the conventional tool steel for hot working.
第２表は第１表に示す本発明鋼および従来鋼の熱処理条
件（目標硬さＨRC45）および高温強度を示したもので、
本発明鋼は従来鋼と同等ないしこれに準ずる高温強度を
備えていることがわかる。 Table 2 shows heat treatment conditions (target hardness HRC45) and high temperature strength of the steels of the present invention and conventional steels shown in Table 1.
It can be seen that the steel of the present invention has high temperature strength equivalent to or comparable to that of conventional steel.
第３表は、第１表に示す本発明鋼および従来鋼試料を半
冷30min（焼入温度と室温との中間温度または降温する
までの所要時間が30minとなるような冷却速度）で焼入
冷却後、ＨRC45に焼もどした場合の破壊靭性値（KIC）
を示す。 Table 3 shows quenching of the steels of the present invention and conventional steels shown in Table 1 by semi-cooling for 30 min (intermediate temperature between quenching temperature and room temperature or cooling rate such that the time required to cool down is 30 min). Fracture toughness value (KIC) when tempered to HRC45 after cooling
Indicates.
従来鋼Ｋの場合は、半冷30minの焼入で上部ベイナイト
主体の組織となるため、焼もどし後十分な靭性が得られ
ない。 In the case of the conventional steel K, the structure mainly composed of upper bainite is obtained by quenching for 30 minutes in semi-cooling, so that sufficient toughness cannot be obtained after tempering.
一方本発明鋼の場合、焼入性が大きく、半冷30minの焼
入冷却の場合にもマルテンサイト主体の組織を生成し、
焼もどし後高い靭性値を示している。On the other hand, in the case of the present invention steel, the hardenability is large, and a structure mainly composed of martensite is generated even in the case of quenching and cooling for half-cooling 30 min.
It shows a high toughness value after tempering.
このように本発明鋼は、徐冷焼入の場合にも十分な靭性
値が得られるため、大寸法の金型でも空冷焼入で十分な
靭性を維持することができる点に大きな特徴がある。As described above, since the steel of the present invention can obtain a sufficient toughness value even in the case of slow cooling and quenching, there is a great feature in that it is possible to maintain sufficient toughness by air cooling and quenching even in a large-sized die. .
第４表に本発明鋼の耐ヒートチェック性を示す。試験片
は、第２表に示した各オーステナイト化温度より、半冷
30minで焼入後、ＨRC45に焼もどしを行なった。Table 4 shows the heat check resistance of the steel of the present invention. The test piece was semi-cooled from each austenitizing temperature shown in Table 2.
After quenching for 30 minutes, HRC45 was tempered.
試験片を15mmφ×25mmで660℃に急熱し、水中で20℃に
急冷する操作を3,000回繰返した結果である。 It is the result of repeating the operation of rapidly heating the test piece with 15 mmφ × 25 mm to 660 ° C. and then rapidly cooling it to 20 ° C. in water 3,000 times.
本発明鋼は従来鋼よりクラック個数はやや多いが、平均
および最大深さが小さく格段にすぐれた耐ヒートチェッ
ク性を備えていることがわかる。It can be seen that the steel of the present invention has a slightly larger number of cracks than the conventional steel, but the average and maximum depths are small and the heat check resistance is remarkably excellent.
これは、本発明鋼が従来鋼と同等ないしこれに準ずるす
ぐれた高温強度を有しており、かつ焼入性が大きく、半
冷30minの焼入においても、上部ベイナイトの生成が抑
制され、高い靭性を維持すること、また合金組成および
凝固時の初晶の核生成効果により、凝固時に粗大な炭化
物を生成する傾向が小さいことによる靭性改善の効果、
などによるものである。This is because the steel of the present invention has excellent high-temperature strength equivalent to or comparable to that of conventional steel, and has high hardenability, and even in the quenching of half-cooled 30 min, the formation of upper bainite is suppressed and high. By maintaining toughness, and by the alloy composition and the nucleation effect of primary crystals during solidification, the effect of improving toughness due to the small tendency to form coarse carbides during solidification,
Etc.
以上説明したように、本発明鋼は半冷時間30min程度、
あるいはこれより冷却速度の遅い徐冷焼入の場合にも靭
性の低下を生ぜず、また合金組織の適切な組合せ、凝固
組織の微細化とあいまって大寸法工具の場合でもすぐれ
た高温強度と高いレベルの靭性を保持することを特徴と
する新しい熱間加工用工具鋼である。As described above, the steel of the present invention has a half-cooling time of about 30 minutes,
Alternatively, slow cooling quenching with a slower cooling rate does not cause deterioration in toughness, and due to the appropriate combination of alloy structures and refinement of solidification structure, excellent high temperature strength and high strength even in the case of large size tools. It is a new tool steel for hot working characterized by maintaining a level of toughness.
Claims (4)
n1.50％以下、Ni0.50〜2.30％、Cr4.05〜6.50％、（1/2
W＋Mo）1.90〜3.50％、V0.50％以上1.00％未満、N0.025
〜0.15％、残部Feおよび通常の不純物からなることを特
徴とする熱間加工用工具鋼。1. C0.36-0.50% by weight%, Si 1.00% or less, M
n1.50% or less, Ni0.50 to 2.30%, Cr4.05 to 6.50%, (1/2
W + Mo) 1.90 to 3.50%, V0.50% or more and less than 1.00%, N0.025
Tool steel for hot working, characterized by ~ 0.15%, balance Fe and normal impurities.
n1.50％以下、Ni0.50〜2.30％、Cr4.05〜6.50％、（1/2
W＋Mo）1.90〜3.50％、V0.50％以上1.00％未満、N0.025
〜0.15％、Co0.50〜4.00％、残部Feおよび通常の不純物
からなることを特徴とする熱間加工用工具鋼。2. C0.36-0.50% by weight%, Si 1.00% or less, M
n1.50% or less, Ni0.50 to 2.30%, Cr4.05 to 6.50%, (1/2
W + Mo) 1.90 to 3.50%, V0.50% or more and less than 1.00%, N0.025
Tool steel for hot working, characterized in that it consists of ~ 0.15%, Co0.50 ~ 4.00%, balance Fe and usual impurities.
n1.50％以下、Ni0.50〜2.30％、Cr4.05〜6.50％、（1/2
W＋Mo）1.90〜3.50％、V0.50％以上1.00％未満、N0.025
〜0.15％、Nb0.02〜0.15％、残部Feおよび通常の不純物
からなることを特徴とする熱間加工用工具鋼。3. C0.36-0.50% by weight%, Si 1.00% or less, M
n1.50% or less, Ni0.50 to 2.30%, Cr4.05 to 6.50%, (1/2
W + Mo) 1.90 to 3.50%, V0.50% or more and less than 1.00%, N0.025
~ 0.15%, Nb 0.02 ~ 0.15%, balance Fe and ordinary impurities, characterized in that it is a tool steel for hot working.
n1.50％以下、Ni0.50〜2.30％、Cr4.05〜6.50％、（1/2
W＋Mo）1.90〜3.50％、V0.50％以上1.00％未満、N0.025
〜0.15％、Co0.50〜4.00％、Nb0.02〜0.15％、残部Feお
よび通常の不純物からなることを特徴とする熱間加工用
工具鋼。4. C0.36-0.50% by weight%, Si 1.00% or less, M
n1.50% or less, Ni0.50 to 2.30%, Cr4.05 to 6.50%, (1/2
W + Mo) 1.90 to 3.50%, V0.50% or more and less than 1.00%, N0.025
~ 0.15%, Co 0.50 ~ 4.00%, Nb 0.02 ~ 0.15%, balance Fe and ordinary impurities, characterized in that it is a tool steel for hot working.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60290176A JPH07109021B2 (en) | 1985-12-23 | 1985-12-23 | Tool steel for hot working |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60290176A JPH07109021B2 (en) | 1985-12-23 | 1985-12-23 | Tool steel for hot working |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS62149852A JPS62149852A (en) | 1987-07-03 |
| JPH07109021B2 true JPH07109021B2 (en) | 1995-11-22 |
Family
ID=17752730
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60290176A Expired - Lifetime JPH07109021B2 (en) | 1985-12-23 | 1985-12-23 | Tool steel for hot working |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07109021B2 (en) |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2746919B2 (en) * | 1988-06-30 | 1998-05-06 | 日立金属株式会社 | Tool steel for warm and hot working |
| JP2953663B2 (en) * | 1988-08-03 | 1999-09-27 | 日立金属株式会社 | Tool steel for hot working |
| JP2662291B2 (en) * | 1989-03-28 | 1997-10-08 | 川崎製鉄株式会社 | Steel for hot press tools |
| JP2004169177A (en) * | 2002-11-06 | 2004-06-17 | Daido Steel Co Ltd | Alloy tool steel, its manufacturing method, and die using it |
| WO2015140235A1 (en) * | 2014-03-18 | 2015-09-24 | Innomaq 21, Sociedad Limitada | Extremely high conductivity low cost steel |
| JP5744300B1 (en) * | 2014-11-11 | 2015-07-08 | 日本高周波鋼業株式会社 | Hot work tool steel |
| JP6227076B2 (en) * | 2015-10-16 | 2017-11-08 | 株式會社三共合金鑄造所 | Iron-based heat-resistant alloy and method for producing iron-based heat-resistant alloy |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5521548A (en) * | 1978-08-01 | 1980-02-15 | Hitachi Metals Ltd | Hot processing tool steel |
| JPS6059053A (en) * | 1983-09-09 | 1985-04-05 | Daido Steel Co Ltd | Hot working tool steel |
-
1985
- 1985-12-23 JP JP60290176A patent/JPH07109021B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPS62149852A (en) | 1987-07-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5929963B2 (en) | Hardening method of steel | |
| JP7172275B2 (en) | Hot stamping die steel, hot stamping die and manufacturing method thereof | |
| JPH07109021B2 (en) | Tool steel for hot working | |
| JPH07179985A (en) | High strength suspension spring excellent in corrosion resistance and its production | |
| JPH06212253A (en) | Production of cold tool steel | |
| JP6903507B2 (en) | Hot tool steel with excellent hardenability and toughness | |
| JP6913291B2 (en) | Hot tools Steel and hot tools | |
| WO2021187484A1 (en) | Steel for hot working die, die for hot working, and manufacturing method for same | |
| JP2755301B2 (en) | Tool steel for hot working | |
| JP2953663B2 (en) | Tool steel for hot working | |
| JPS62161942A (en) | Tool steel for hot working | |
| JP2746919B2 (en) | Tool steel for warm and hot working | |
| US4116685A (en) | Tool steel for warm and hot working | |
| JPS6366386B2 (en) | ||
| JP2602903B2 (en) | Tool steel for warm and hot working | |
| KR20150077660A (en) | Using the gear manufacturing method of high frequency heat material | |
| JPH0688163A (en) | Hot tool steel | |
| JP3191008B2 (en) | Hot tool steel | |
| JPS62112761A (en) | Tool steel for warm and hot working | |
| JPS5925026B2 (en) | mold steel | |
| JP4347033B2 (en) | Manufacturing method of steel for pre-hardened mold | |
| JP2784128B2 (en) | Precipitation hardening type hot work tool steel | |
| JP3750835B2 (en) | High hardness corrosion resistant powder die steel excellent in mirror finish and method for producing the same | |
| JPH02298234A (en) | Tool steel for warm and hot working | |
| KR810001656B1 (en) | Bake hardening hot rolled toal steel |