JPS62149852A - Tool steel for hot working - Google Patents
Tool steel for hot workingInfo
- Publication number
- JPS62149852A JPS62149852A JP29017685A JP29017685A JPS62149852A JP S62149852 A JPS62149852 A JP S62149852A JP 29017685 A JP29017685 A JP 29017685A JP 29017685 A JP29017685 A JP 29017685A JP S62149852 A JPS62149852 A JP S62149852A
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- steel
- toughness
- temperature
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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] [Field of Industrial Application] The present invention has high high temperature strength and wear resistance, as well as extremely high hardenability and excellent toughness, and the heating temperature during use is high. At the same time, it is subjected to severe abrasion and thermal shock,
The present invention also relates to a mold material that can be applied to hot tools such as hot forging molds of various sizes that are subjected to large impact stress, and provides 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、従来量
も高温強度の高い材料として高W−V −G o系のA
l5I +119系鋼が使用されていた。For applications where the mold surface temperature rises rapidly during use and a high degree of hot strength and hot wear resistance is required, high W-V-G o-based materials are used as materials with high high temperature strength. A
l5I +119 series steel was 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(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。However, although it has high high-temperature strength, it has low toughness and may cause early cracking during use depending on the application. formation, resulting in a significant decrease in toughness.
中〜大寸法の型への適用が困難であった。It was difficult to apply to medium to large size molds.
本発明鋼の化学組成は、中C−中Cr−N i−中(W
・M o )−中〜高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30m1n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
・M o )-Medium to high V-N is the basic component, suppressing the formation of coarse VC carbides, which is one of the causes of reduction in toughness,
In addition, in order to provide sufficient hardenability so that the quenched structure of the base becomes a martensite-based structure even in the case of slow cooling quenching of about 30 m1n, C, Cr, Ni, and Mn are mainly used. The alloy composition is appropriately combined, and the toughness is improved by making the solidification structure finer and the austenite crystal grain size finer, giving it the ability to obtain excellent toughness even in large-sized molds.
また、C,W、Mo、■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
、Co−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。In addition, by appropriately combining the amounts of C, W, Mo, and ■, it provides excellent high temperature strength and high temperature wear resistance, and
By adding Co--Ni and adjusting the amount of Si, a dense oxide film with high adhesion and appropriate thickness is formed on the mold surface by increasing the temperature during use.
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。From this point of view as well, it provides a high degree of high-temperature wear resistance and seizure resistance.
すなわち本願発明は、
重量%でC0.36〜0.50%、 Si 1.00%
以下、Mn1.50%以下、Ni 0.50〜2.30
%、 Cr 4.05−6.50%、(1/2W +
Mo) 1.90−3.50%、V 0.50〜1.6
0%。That is, in the present invention, C0.36 to 0.50% and Si 1.00% in weight%.
Below, Mn 1.50% or less, Ni 0.50 to 2.30
%, Cr 4.05-6.50%, (1/2W +
Mo) 1.90-3.50%, V 0.50-1.6
0%.
N 0.025〜0.15%、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%、Si 1.00%以下、
Mn1.50%以下、 Ni 0.50〜2.30%、
Cr 4.05−6.50%、(1/2W+Mo)
1.90〜3.50%、 V 0.50〜1.60%。Hot working tool steel characterized by consisting of N 0.025-0.15%, balance Fe and normal impurities, C 0.36-0.50% by weight, Si 1.00% or less,
Mn 1.50% or less, Ni 0.50-2.30%,
Cr 4.05-6.50%, (1/2W+Mo)
1.90-3.50%, V 0.50-1.60%.
N 0.025〜0.15%、 Co 0.50−4.
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。N 0.025-0.15%, Co 0.50-4.
A tool steel for hot working, characterized in that the remainder consists of 0.00% Fe and normal impurities.
重量%でC0.36〜0.50%、Si 1.00%以
下、Mn 1.50%以下、 Ni 0.50〜2.3
0%、 Cr 4.05−6.502、(]/2W +
Mo) 1.90−3.50%、 V 0.5
0〜1.60%、N 0.025〜0.15%、 Nb
0.02〜0.1’5%、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%、Si 1.00%以
下、Mn 1.50%以下、Ni 0.50〜2.30
%、 Cr 4.05−6.50%、(1/2W +
Mo) 1.90−3.50%、V 0.50〜1.6
0%。C0.36 to 0.50% by weight, Si 1.00% or less, Mn 1.50% or less, Ni 0.50 to 2.3
0%, Cr 4.05-6.502, (]/2W +
Mo) 1.90-3.50%, V 0.5
0-1.60%, N 0.025-0.15%, Nb
A tool steel for hot working characterized by consisting of 0.02-0.1'5%, balance Fe and normal impurities, and C0.36-0.50%, Si 1.00% by weight% Below, Mn 1.50% or less, Ni 0.50 to 2.30
%, Cr 4.05-6.50%, (1/2W +
Mo) 1.90-3.50%, V 0.50-1.6
0%.
N 0.025〜0.15%、Co 0.50〜4.0
0%、Nb 0.02〜0.15%、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。N 0.025-0.15%, Co 0.50-4.0
0%, Nb 0.02 to 0.15%, the balance Fe and normal impurities.
次に本発明鋼の成分限定の理由について述にる。 Next, the reason for limiting the composition 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、■、NbおよびC
r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 the excellent hardenability, tempering hardness, and high-temperature hardness of the steel of the present invention, and also contains W, Mo, ■, Nb, and C.
It combines with carbide-forming elements such as r to form carbides, and is added to refine crystal grains, provide 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0.502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 it is too large, the toughness will decrease, so the content should be 0.502 or less, and if it is too low, the effect of the above addition cannot be obtained.
The content shall be 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 A1 transformation point and to provide oxidation resistance 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, makes it difficult to form a protective oxide film during use, and causes a decrease in thermal conductivity, so the content should be 1.00% or less.
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 particularly excellent hardenability, which is a 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
、またへ〇変態点の低下をまねくので、1.50%以下
とする。Addition of a large amount increases annealing hardness, reduces machinability, and lowers the 〇 transformation point, so the content 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
的な靭性改害を与える。Ni, together with C, Cr, Mn, Mo, W, etc., gives the steel of the present invention excellent hardenability, and forms a martensite-based structure even at a slow quenching cooling rate, preventing a decrease in toughness. It is an important additive element to prevent It also gives an essential toughness modification to 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
へ〇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 effects, but if it is too large, it will excessively lower the 〇 transformation point, leading to a decrease in wear resistance life, and will also excessively increase annealing hardness, decreasing machinability. Therefore, the content should be 2.30% or less, and if it is too low, the effect of the above addition cannot be obtained, so the content should be 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、N1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 characteristic of the steel of the present invention, and is one of the most important elements in the steel of the present invention, along with N1, and setting the amount of Cr is extremely important. Cr is added to improve temper softening resistance and high-temperature strength, provide appropriate oxide film properties, improve wear resistance by combining with C to form carbides, and improve A1 transformation point. Ru.
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
と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6.5部以下
とする。If the temperature is too low, it will be difficult to maintain the particularly excellent hardenability that is a characteristic of the steel of the present invention, and the oxidation resistance will be insufficient, the surface roughness will easily occur during use, the A1 transformation point will decrease, and the 4.05% because it becomes difficult to achieve both good toughness and wear resistance due to deterioration of softening resistance, reduction of residual carbides, etc.
The content should be 6.5 parts or less, since if the content is too high, carbides that tend to aggregate when the temperature rises will be formed, reducing high-temperature strength and softening resistance.
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。In order to obtain sufficient hardenability even by slow cooling quenching, 4.
It is more desirable to add 50 to 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 carbides that are difficult to dissolve in the solid state during quenching and heating, which has a unique effect on improving wear resistance, and during tempering, it precipitates fine carbides that are difficult to aggregate, increasing high-temperature yield strength. It is added to particularly increase the softening resistance when the temperature rises, and further to improve the density of the surface oxide film formed when the temperature rises during use. If too much W is present, there is a strong tendency to form coarse carbides similar to conventional steels, 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 to improve wear resistance, dissolves 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 ease 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 to obtain the above effects, but if they are too large, the toughness decreases due to the formation of coarse carbides and an increase in the amount of carbides, making it difficult to maintain the excellent toughness that is the characteristic of the steel of the present invention. Therefore, (1/2W+Mo) is 3
.. The content should be 50% or less, and if it is too low, the effect of the above addition cannot be obtained, so the content should be 1.90% 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 effects of adding W and Mo are similar, W is more advantageous in terms of high-temperature strength and wear resistance, and MO is more advantageous in terms of toughness. It is something to do.
■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。(2) Forms a large amount of carbides that are difficult to dissolve in solid solution, resulting in the effect of improving wear resistance and seizure resistance, and also forms a solid solution in the matrix during quenching and heating, and produces fine carbides that are difficult to aggregate during tempering. Precipitates and improves softening resistance in high temperature ranges.
またパワ人時の結晶粒微細化効果をもたらし靭性を向上
させ、またA□変態点をあげ高温強度向上効果とあいま
って、耐ヒートクラツク性を向上させる。多すぎると粗
大な炭化物を生成し、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1.6は以下とし
、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。It also brings about the effect of grain refinement during power operation, improving toughness, and also increases the A□ transformation point, which together with the effect of improving high-temperature strength, improves heat crack resistance. If it is too high, coarse carbides will be formed and it will be difficult to maintain the excellent toughness that is a characteristic of the steel of the present invention, so the value should be 1.6 or less. If it is too low, the effect of the above addition cannot be obtained, so 0. 50
% or more.
N l−t、 N h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1〜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。Together with Nlt and Nh, the solidified structure is made finer, and the crystal grains are made finer during quenching, and even during slow cooling quenching, the formation of coarse upper bainii 1~ is prevented, and high toughness is maintained. It is an essential and important additive element for achieving the effects of the steel of the present invention.
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0.02
5%以上とする。Although N is added to obtain the above effect, it is not necessary to add a large amount, and due to restrictions from the solid solubility limit, it should be 0.15% or less. If it is too low, the above effect of addition cannot be obtained, so it is 0.02
5% 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 high temperature wear resistance to the steel of the present invention. The addition of Co forms an extremely dense and highly adhesive protective oxide film when the temperature rises during use, thereby preventing metal contact with the other material and preventing the steel of the present invention from rising in temperature. It also provides excellent wear resistance.
COのこの効果は、Cr、Niをはしめ、W、M。This effect of CO can be applied to Cr, Ni, W, M.
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1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。It differs depending on the relationship with the amount of other added elements, 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 will decrease, so the content should be 4.00% or less, and if it is too low, the effect of the above addition cannot be obtained, so the content should be 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 fine carbides that are particularly difficult to agglomerate during tempering, particularly increases softening resistance during temperature rise, and is added to refine crystal grains during quenching.
またN、Cと結び付いて凝固時の初品生成時の核作用に
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, it combines with N and C and acts as a nucleus during initial product formation during solidification, thereby refining the solidified structure and improving toughness.
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%以下とするゆ〔実施例〕
以下本発明を実施例に基づき詳細に説明する。Nb is added to obtain the above effect, but if it is too large, it will form coarse carbides and reduce toughness, so it should be added to 0.15
% or less, and if it is too low, the effect of the above addition cannot be obtained, so it should be 0.02% or less. [Example] The present invention will be explained in detail below 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する高温強
度を備えていることがわかる。Table 2 shows the heat treatment conditions (target hardness HRC45) and high-temperature strength of the inventive steel and conventional steel shown in Table 1. The inventive steel has high-temperature strength equivalent to or similar to the conventional steel. You can see that
第2表
第3表は、第1表に示す本発明鋼および従来鋼試料を半
途30m1n (焼入温度と室温との中間温度まで降温
するまでの所要時間が30m1n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。Tables 2 and 3 show that the inventive steel and conventional steel samples shown in Table 1 were cooled at a cooling rate of 30 m1n (cooling rate such that the time required to lower the temperature to an intermediate temperature between the quenching temperature and room temperature is 30 m1n). The fracture toughness value (KIC) when tempered to HRC45 after quenching and cooling is shown.
第3表
従来鋼にの場合は、半途30m1n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 in Table 3, the structure becomes mainly upper bainite after being quenched halfway through 30 ml, so sufficient toughness cannot be obtained after tempering.
一方本発明鋼の場合、焼入性が大きく、半途30m1n
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 steel of the present invention, the hardenability is large and
Even in the case of quenching and cooling, a martensite-based structure is generated and shows high toughness 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力り人で十分
な靭性を維持することができる点に大きな特徴がある。In this way, the steel of the present invention can obtain sufficient toughness even when slowly quenched, so a major feature of the steel is that it can maintain sufficient toughness even in large-sized molds by air-cooling. be.
第4表に本発明鋼の耐ヒートチェック性を示す。Table 4 shows the heat check resistance of the steel of the present invention.
試験片は、第2表に示した各オーステナイト化温度によ
り、半途30m1nで焼入後、HRC45に焼もどしを
行なった。The test pieces were quenched at each austenitizing temperature shown in Table 2 at 30 ml, and then tempered to HRC45.
第4表
試験片を15mmφX25rrrnで660°C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。Table 4 shows the results of 3,000 repetitions of rapidly heating a test piece to 660°C with a diameter of 15mm x 25rrrn and rapidly cooling it to 20°C in water 3,000 times.
本発明鋼は従来鋼よりクラン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 although the steel of the present invention has a slightly larger number of cranks than the conventional steel, the average and maximum depths are smaller and it has significantly better heat check resistance.
これは、本発明鋼が従来鋼と同等ないしこれに錦するす
ぐれた高温強度を有しており、かつ焼入性が大きく、半
途30m1n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
よび凝固時の初品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 equal to or superior to that of conventional steel, and has high hardenability, suppressing the formation of upper bainite even in half-way hardening of 30 ml. This is due to the effect of maintaining toughness and improving toughness due to the small tendency to form coarse carbides during solidification due to the alloy composition and the nucleation effect of the initial product during solidification.
以上説明したように、本発明鋼は半途時間30m1n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 explained above, the steel of the present invention does not cause a decrease in toughness even when slow quenching is performed for a half-time of about 30 m1n or at a slower cooling rate, and also has an appropriate combination of alloy structures.
This is a new tool steel for hot working, which is characterized by its fine solidification structure, which allows it to maintain excellent high-temperature strength and high-level toughness even in the case of large-sized tools.
Claims (1)
以下、Mn1.50%以下、Ni0.50〜2.30%
、Cr4.05〜6.50%、(1/2W+Mo)1.
90〜3.50%、V0.50〜1.60%、N0.0
25〜0.15%、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。 2 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%、V0.50〜1.60%、N0.0
25〜0.15%、Co0.50〜4.00%、残部F
e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 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%、V0.50〜1.60%、N0.0
25〜0.15%、Nb0.02〜0.15%、残部F
e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 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%、V0.50〜1.60%、N0.0
25〜0.15%、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。[Claims] 1% by weight: C 0.36-0.50%, Si 1.00%
Below, Mn 1.50% or less, Ni 0.50-2.30%
, Cr4.05-6.50%, (1/2W+Mo)1.
90-3.50%, V0.50-1.60%, N0.0
A tool steel for hot working, characterized in that it consists of 25 to 0.15%, the balance being Fe and normal impurities. 2% by weight: C0.36-0.50%, Si1.00%
Below, Mn 1.50% or less, Ni 0.50-2.30%
, Cr4.05-6.50%, (1/2W+Mo)1.
90-3.50%, V0.50-1.60%, N0.0
25-0.15%, Co0.50-4.00%, balance F
A tool steel for hot working, characterized in that it consists of e and normal impurities. 3 Weight%: C0.36-0.50%, Si1.00%
Below, Mn 1.50% or less, Ni 0.50-2.30%
, Cr4.05-6.50%, (1/2W+Mo)1.
90-3.50%, V0.50-1.60%, N0.0
25-0.15%, Nb0.02-0.15%, balance F
A tool steel for hot working, characterized in that it consists of e and normal impurities. 4 C0.36-0.50%, Si1.00% by weight%
Below, Mn 1.50% or less, Ni 0.50-2.30%
, Cr4.05-6.50%, (1/2W+Mo)1.
90-3.50%, V0.50-1.60%, N0.0
25-0.15%, Co0.50-4.00%, Nb0
.. A tool steel for hot working, characterized in that the steel comprises 0.02 to 0.15%, the balance being Fe and normal impurities.
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 true JPS62149852A (en) | 1987-07-03 |
JPH07109021B2 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) |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0211736A (en) * | 1988-06-30 | 1990-01-16 | Hitachi Metals Ltd | Tool steel for warm and hot workings |
JPH0243346A (en) * | 1988-08-03 | 1990-02-13 | Hitachi Metals Ltd | Tool steel for hot working |
JPH02254135A (en) * | 1989-03-28 | 1990-10-12 | Kawasaki Steel Corp | Steel for hot press tool |
CN100357476C (en) * | 2002-11-06 | 2007-12-26 | 大同特殊钢株式会社 | Alloy tool steel and its producing method and mold using it |
JP2017075392A (en) * | 2015-10-16 | 2017-04-20 | 株式會社三共合金鑄造所 | Iron-based heat resistant alloy and manufacturing method of iron-based heat resistant alloy |
US20170327933A1 (en) * | 2014-11-11 | 2017-11-16 | Nippon Koshuha Steel Co., Ltd. | Hot work tool steel |
EP4219783A1 (en) * | 2014-03-18 | 2023-08-02 | Innomaq 21, Sociedad Limitada | Extremely high conductivity low cost steel |
Citations (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
Patent Citations (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 |
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0211736A (en) * | 1988-06-30 | 1990-01-16 | Hitachi Metals Ltd | Tool steel for warm and hot workings |
JPH0243346A (en) * | 1988-08-03 | 1990-02-13 | Hitachi Metals Ltd | Tool steel for hot working |
JPH02254135A (en) * | 1989-03-28 | 1990-10-12 | Kawasaki Steel Corp | Steel for hot press tool |
CN100357476C (en) * | 2002-11-06 | 2007-12-26 | 大同特殊钢株式会社 | Alloy tool steel and its producing method and mold using it |
EP4219783A1 (en) * | 2014-03-18 | 2023-08-02 | Innomaq 21, Sociedad Limitada | Extremely high conductivity low cost steel |
US20170327933A1 (en) * | 2014-11-11 | 2017-11-16 | Nippon Koshuha Steel Co., Ltd. | Hot work tool steel |
US10829841B2 (en) * | 2014-11-11 | 2020-11-10 | Nippon Koshuha Steel Co., Ltd. | Hot work tool steel |
JP2017075392A (en) * | 2015-10-16 | 2017-04-20 | 株式會社三共合金鑄造所 | Iron-based heat resistant alloy and manufacturing method of iron-based heat resistant alloy |
Also Published As
Publication number | Publication date |
---|---|
JPH07109021B2 (en) | 1995-11-22 |
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