JPH07116550B2 - Low alloy high speed tool steel and manufacturing method thereof - Google Patents
Low alloy high speed tool steel and manufacturing method thereofInfo
- Publication number
- JPH07116550B2 JPH07116550B2 JP63077310A JP7731088A JPH07116550B2 JP H07116550 B2 JPH07116550 B2 JP H07116550B2 JP 63077310 A JP63077310 A JP 63077310A JP 7731088 A JP7731088 A JP 7731088A JP H07116550 B2 JPH07116550 B2 JP H07116550B2
- Authority
- JP
- Japan
- Prior art keywords
- less
- speed tool
- tool steel
- high speed
- alloy high
- 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 - Fee Related
Links
- 229910045601 alloy Inorganic materials 0.000 title claims description 27
- 239000000956 alloy Substances 0.000 title claims description 27
- 229910001315 Tool steel Inorganic materials 0.000 title claims description 22
- 238000004519 manufacturing process Methods 0.000 title claims description 5
- 229910000831 Steel Inorganic materials 0.000 claims description 45
- 239000010959 steel Substances 0.000 claims description 45
- 238000010438 heat treatment Methods 0.000 claims description 14
- 238000009792 diffusion process Methods 0.000 claims description 11
- 229910052746 lanthanum Inorganic materials 0.000 claims description 11
- 229910052684 Cerium Inorganic materials 0.000 claims description 10
- 229910052727 yttrium Inorganic materials 0.000 claims description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims description 7
- 229910052782 aluminium Inorganic materials 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 6
- 229910052760 oxygen Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 3
- 230000001105 regulatory effect Effects 0.000 claims description 3
- 229910052717 sulfur Inorganic materials 0.000 claims description 3
- 150000001247 metal acetylides Chemical class 0.000 description 13
- 230000000694 effects Effects 0.000 description 11
- 239000000126 substance Substances 0.000 description 8
- 238000005242 forging Methods 0.000 description 7
- 238000007792 addition Methods 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- 238000005204 segregation Methods 0.000 description 6
- 229910052721 tungsten Inorganic materials 0.000 description 6
- 229910052720 vanadium Inorganic materials 0.000 description 6
- 239000011159 matrix material Substances 0.000 description 5
- 238000005496 tempering Methods 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 230000001771 impaired effect Effects 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 229910000997 High-speed steel Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000008094 contradictory effect Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000002829 reductive effect Effects 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000008207 working material Substances 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Forging (AREA)
- Heat Treatment Of Steel (AREA)
Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は、圧造工具などに使用される塑性加工用の低合
金高速度工具鋼に関するものである。Description: TECHNICAL FIELD The present invention relates to a low alloy high speed tool steel for plastic working, which is used for a forging tool or the like.
一般に圧造工具など塑性加工用高速度工具鋼には次のよ
うな特性が要求される。Generally, high-speed tool steels for plastic working such as forging tools are required to have the following characteristics.
（１） 耐摩耗性の面からHRC60以上の高い焼もどし硬
さが得られること。(1) From the viewpoint of wear resistance, a high temper hardness of HRC60 or higher should be obtained.
（２） 耐衝撃性の面から、優れた機械的破壊強さを有
すること。(2) It has excellent mechanical fracture strength in terms of impact resistance.
これらの要求特性に対して特公昭42−20619号、特公昭5
0−10808号、特公昭55−49148号、特公昭57−24063号、
特公昭62−8503号など低合金高速度工具鋼の改良が行な
われてきた。For these required characteristics, Japanese Patent Publication No. 42-20619 and Japanese Patent Publication No. 5
0-10808, JP-B-55-49148, JP-B-57-24063,
Improvements have been made to low alloy high speed tool steel such as Japanese Examined Patent Publication No. 62-8503.
しかしながら最近、被加工材の難加工化に伴い、より高
い耐摩耗性が工具に要求され、焼もどし後の硬さがHRC6
0程度では不足で、HRC62〜64が必要となってきている。
しかも塑性加工用工具では十分な靱性も必要であるの
で、HRC62〜64で高い靱性を有する材質を開発する必要
性が高くなった。従来の低合金高速度工具鋼に関する公
知例では、熱処理後HRC62以上の硬さが得られるものは
限られており、また仮に高硬度を有していても靱性不足
により耐衝撃性が不十分であった。However, due to the recent difficulty in working materials, higher wear resistance is required for tools, and the hardness after tempering is HRC6.
About 0 is insufficient, and HRC62 to 64 are needed.
Moreover, since plastic working tools also require sufficient toughness, it became necessary to develop materials with high toughness in HRC62-64. In the known examples of conventional low-alloy high-speed tool steel, there are only a few that can obtain hardness of HRC62 or higher after heat treatment, and even if it has high hardness, its impact resistance is insufficient due to lack of toughness. there were.
本発明はかかる点に鑑み、圧造工具用の特性を十分に満
足させるため、さらに優れた耐摩耗性、耐衝撃性を兼ね
備えた低合金高速度工具鋼を提供するものである。In view of such a point, the present invention provides a low alloy high speed tool steel having excellent wear resistance and impact resistance in order to sufficiently satisfy the properties for a forging tool.
本発明鋼は、熱処理後安定してHRC62〜64の硬さが得ら
れ、優れた耐摩耗性を有することを１つの特徴とする。
一般に低合金高速度工具鋼は合金量が低いため、経済的
ではあるが、焼もどし後、あまり高硬度が得られない。
本発明では、従来の低合金高速度工具鋼よりＣ、Si量を
増やし鋼の基地（マトリックス）の硬さを高めている。The steel of the present invention is characterized in that the hardness of HRC62 to 64 is stably obtained after heat treatment and that it has excellent wear resistance.
In general, low alloy high speed tool steels are economical because they have a low alloy content, but after tempering, they do not have very high hardness.
In the present invention, the hardness of the matrix of steel is increased by increasing the amounts of C and Si as compared with the conventional low alloy high speed tool steel.
本発明鋼は同時に高靱性を有し、耐衝撃性が優れている
ことを特徴とする。一般に工具鋼においては硬さと靱性
とは相反した性質を持っており、硬さの高いものは靱性
が低くなる相互関係にある。加えて靱性をさらに阻害す
る原因の一つにミクロ組織上の要因として、 （１）炭化物の縞状偏析、 （２）10μｍ以上の巨大炭化物、 （３）粗大なオーステナイト結晶粒、 （４）非金属介在物の偏析、 等が考えられる。本発明ではかかる問題点を解決すべく
靱性を阻害するミクロ組織要因を化学成分あるいは製造
上できるだけ排除し、HRC62〜64の硬さ領域で優れた耐
衝撃性を有する新規な低合金高速度鋼を提供するもので
ある。The steel of the present invention is characterized by having high toughness and excellent impact resistance at the same time. Generally, in tool steel, hardness and toughness have contradictory properties, and those having high hardness have a mutual relationship in which toughness decreases. In addition, one of the factors that further hinder the toughness is as follows: (1) Stripe segregation of carbides, (2) Giant carbides of 10 μm or more, (3) Coarse austenite grains, (4) Non- Segregation of metal inclusions is possible. The present invention eliminates as much as possible the microstructural factors that inhibit toughness in terms of chemical composition or manufacturing in order to solve such problems, and provides a novel low alloy high speed steel having excellent impact resistance in the hardness region of HRC62 to 64. It is provided.
以下、本発明の成分限定理由について説明する。Hereinafter, the reasons for limiting the components of the present invention will be described.
C:0.7％を越え0.85％以下 ＣはCr、Ｗ、Mo、Ｖ、Nbなどの炭化物形成元素と結合し
て、硬い複炭化物を生成し、工具として必要な耐摩耗性
の向上に著しく効果があり、また一部基地中に固溶して
基地を強化する。0.7％以上では焼もどし硬さが低下
し、0.85％を越えると靱性が低下するためにＣは0.7％
を越え0.85％以下とした。C: more than 0.7% and 0.85% or less C combines with carbide forming elements such as Cr, W, Mo, V, and Nb to form hard double carbide, and is remarkably effective in improving wear resistance required as a tool. Yes, some solid solution in the base to strengthen the base. If it exceeds 0.7%, the temper hardness decreases, and if it exceeds 0.85%, the toughness decreases, so C is 0.7%.
Over 0.85%.
Si:0.8〜2.2％ Ｃ含有量が低く、かつＷ、Mo、Ｖ等の炭化物形成元素含
有量が低い低合金高速度工具鋼では、Ｗ、Mo、Ｖによる
２次硬化があまり期待できないので、高い焼もどし硬さ
と軟化抵抗を得るためには必須の元素である。Siは基地
中に固溶し、固溶強化により基地の硬さを高める効果が
ある。0.8％未満では焼もどし硬さを上げる効果が不十
分で、2.2％以上添加すると靱性が阻害されるので上限
は2.2％とし、望ましくは安定した硬さを確保するため
に1.2〜2.2％、さらに望ましくは、より安定した硬さお
よび靱性を確保するために1.6〜2.0％とした。Si: 0.8 to 2.2% In a low alloy high speed tool steel having a low C content and a low content of carbide forming elements such as W, Mo and V, secondary hardening due to W, Mo and V cannot be expected so much. It is an essential element for obtaining high temper hardness and softening resistance. Si dissolves in the matrix and has the effect of increasing the hardness of the matrix by strengthening the solution. If it is less than 0.8%, the effect of increasing the tempering hardness is insufficient, and if 2.2% or more is added, the toughness is impaired, so the upper limit is 2.2%, preferably 1.2 to 2.2% to secure stable hardness, and Desirably, it is 1.6 to 2.0% in order to secure more stable hardness and toughness.
Mn:0.6％以下 Mnは主に脱酸剤として添加される元素で上限を0.6％と
した。Mn: 0.6% or less Mn is an element mainly added as a deoxidizer, and the upper limit was set to 0.6%.
Cr:3.0〜5.0％ Crは焼入性と耐摩耗性の向上に有効な元素であるが、5.
0％を越えると炭化物の縞状偏析や巨大炭化物の生成を
助長し、靱性を低下させるので5.0％以下とする。また
3.0％未満では焼入性が不足するので下限は3.0％とし
た。Cr: 3.0-5.0% Cr is an element effective in improving hardenability and wear resistance, but 5.
If it exceeds 0%, it promotes the striped segregation of carbides and the formation of giant carbides and reduces the toughness, so it is made 5.0% or less. Also
If it is less than 3.0%, the hardenability is insufficient, so the lower limit was made 3.0%.
Ｗ＋2Mo:5.0〜10.0％ Ｗと２倍量のMoは共にＣと結合して複炭化物を形成し、
耐摩耗性を向上させる有効な元素であるが、同時に炭化
物の縞状偏析や巨大炭化物の生成を助長し、靱性を阻害
する元素でもある。硬さと靱性とのバランスやＷ、Moが
高価な元素であることから、Ｗ＋2Moは5.0〜10.0％とし
た。W + 2Mo: 5.0 to 10.0% W and double amount of Mo both combine with C to form a double carbide,
Although it is an effective element for improving wear resistance, it is also an element for promoting the striped segregation of carbides and the formation of giant carbides, and at the same time inhibiting toughness. Since W and Mo are expensive elements because of the balance between hardness and toughness, W + 2Mo is set to 5.0 to 10.0%.
V:0.5〜1.5％ ＶはＣと結合して高硬度の炭化物を形成して耐摩耗性を
増し、また基地に固溶して２次硬化性を増大する元素で
あるため、0.5％以上は必要であるが、1.5％を越えると
巨大炭化物が発生し、かつそれが縞状に偏析して靱性を
阻害するので上限を1.5％以下とした。さらに望ましく
は、安定した耐摩耗性を確保するために1.2〜1.5％がよ
い。V: 0.5-1.5% V is an element that combines with C to form a high-hardness carbide to increase wear resistance, and to form a solid solution in the matrix to increase the secondary hardening property. Although it is necessary, if it exceeds 1.5%, large carbides are generated and segregate in stripes to impair the toughness, so the upper limit was made 1.5% or less. More preferably, 1.2 to 1.5% is preferable to ensure stable wear resistance.
Nb:0.1％を越え1.0％以下 Nbは本発明では高靱性を得るために必須の元素である。Nb: more than 0.1% and 1.0% or less Nb is an essential element for obtaining high toughness in the present invention.
NbはＶと同じようにＣと結合しやすく硬い炭化物をつく
り、耐摩耗性を向上させる。また結晶粒を微細化し、靱
性を向上させるのに有効な元素である。0.1％未満で
は、Nb添加の効果が小さいので0.1％を越えて添加す
る。1.0％を越えると炭化物が縞状に偏析し靱性を阻害
するので上限を1.0％とした。Similar to V, Nb easily bonds with C to form hard carbides and improve wear resistance. Further, it is an element effective for refining crystal grains and improving toughness. If it is less than 0.1%, the effect of Nb addition is small, so it is added in excess of 0.1%. If it exceeds 1.0%, carbide segregates in stripes and impairs toughness, so the upper limit was made 1.0%.
Co:8.0％以下 本発明鋼において、望ましくはCoを添加する。Co: 8.0% or less Co is preferably added to the steel of the present invention.
Coは基地に固溶し、耐熱強度を高める元素であり、高速
摩耗領域での耐摩耗性改善に効果がある。しかし、高価
な元素であることから上限を8.0％以下とした。Co is an element that forms a solid solution in the matrix and enhances heat resistance, and is effective in improving wear resistance in the high-speed wear region. However, since it is an expensive element, the upper limit was made 8.0% or less.
Al、La、Ce、Y:0.02〜0.2％ Al、La、Ce、Ｙの一種または二種以上を組合せて添加す
ると粗大なＶを主体としたMC型炭化物を微細化ならし
め、靱性を向上させるのに効果がある。0.02％より少な
いとこれらの効果が少なく、0.2％を越えると炭化物微
細化の効果に影響を及ぼすので、0.02〜0.2％とした。Al, La, Ce, Y: 0.02 to 0.2% Addition of one or more of Al, La, Ce and Y in combination to coarsen the MC type carbide mainly composed of V to improve the toughness. Is effective. If it is less than 0.02%, these effects are small, and if it exceeds 0.2%, it has an effect on the effect of refining the carbide, so the content was made 0.02 to 0.2%.
Ti≦0.02％ Tiは、凝固時に高温でＮ、Ｃと結合し、TiN、TiCを形成
する。これらは、VC炭化物の晶出核となるやすい性質を
有するため、VC炭化物を高温で量出せしめ、上記のAl、
La、Ce、Ｙの添加による効果を損なう。そのため、上限
を0.02％とした。Ti ≦ 0.02% Ti combines with N and C at high temperature during solidification to form TiN and TiC. Since these have a property of easily becoming crystallization nuclei of VC carbide, VC carbide can be quantified at a high temperature, and the above Al,
The effect of the addition of La, Ce, Y is impaired. Therefore, the upper limit was made 0.02%.
Ｎ≦0.006％ Ｎは本発明鋼の不純物である。Ｎ量が、0.006％を越え
るとAl、La、Ce、Ｙの添加による効果を損なうために、
上限を0.006％とした。N ≦ 0.006% N is an impurity in the steel of the present invention. If the amount of N exceeds 0.006%, the effect due to the addition of Al, La, Ce, Y is impaired.
The upper limit was made 0.006%.
Ｓ≦0.004％、Ｏ≦40ppm Ｓ、Ｏも本発明鋼の不純物であり、これらはAl、La、C
e、Ｙと結合力が強く、これらの添加による効果を損な
うだけでなく、La、Ce、Ｙと結合して鋼中に介在物とし
てとどまり、製品の靱性を下げるため、Ｓ≦0.004％、
Ｏ≦40ppmに規制した。S ≦ 0.004%, O ≦ 40 ppm S, O are also impurities in the steel of the present invention, and these are Al, La, C.
The bond strength with e and Y is strong, and not only the effects of these additions are impaired, but also with La, Ce, and Y to remain as inclusions in the steel and reduce the toughness of the product, S ≦ 0.004%,
O was regulated to 40ppm.
本発明鋼の製造に当っては、偏析を改善し靱性を高める
目的で、分塊前後いずれかの段階において鋼塊または鋼
材の拡散熱処理を行なう。高速度工具鋼の炭化物はCr、
Mo、Ｗ、Ｖの炭窒化物を主体としており、拡散熱処理を
行なうことにより、非平衡炭化物を分解し平衡炭化物に
する。また、それに伴い炭化物の球状化、縞状偏析の軽
減などが進み靱性を向上させる。拡散熱処理温度は、11
50℃未満だと十分な元素の拡散、均質化が行なわれない
ため1150℃とした。1190℃を越えると一部炭化物が溶融
し始めるため上限を1190℃とした。In the production of the steel of the present invention, the diffusion heat treatment of the steel ingot or the steel material is performed at any stage before or after the slabbing for the purpose of improving segregation and increasing toughness. Carbide of high speed tool steel is Cr,
Mainly composed of Mo, W, and V carbonitrides, the non-equilibrium carbides are decomposed into equilibrium carbides by performing diffusion heat treatment. Further, along with this, spheroidization of carbides and reduction of striped segregation are promoted to improve toughness. Diffusion heat treatment temperature is 11
If the temperature is lower than 50 ° C, sufficient diffusion and homogenization of elements will not be performed, so the temperature was set to 1150 ° C. When the temperature exceeds 1190 ° C, some carbides start to melt, so the upper limit was made 1190 ° C.
（実施例１） 以下、本発明を実施例により説明する。 Example 1 Hereinafter, the present invention will be described with reference to examples.
第１表に示す組成の鋼を小鋼塊にて試作した。鋳造の後
鋼塊を1170℃×20Hで拡散熱処理を行ない、その後に鍛
造して断面が18mm×18mmの鋼材に仕上げた。これらの試
料につき、第２表に示す熱処理条件で焼入、焼もどしを
行なって、各種の機械的性質を調べた。焼もどし硬さ、
大越式迅速摩耗試験、シャルピー衝撃試験の結果を第２
表に示す。試料No.1〜No.3は従来鋼の値、試料No.7〜N
o.10は比較鋼の値である。A steel having the composition shown in Table 1 was trial-produced as a small steel ingot. After casting, the steel ingot was subjected to diffusion heat treatment at 1170 ° C × 20H, and then forged to finish a steel material having a cross section of 18 mm × 18 mm. These samples were subjected to quenching and tempering under the heat treatment conditions shown in Table 2 to investigate various mechanical properties. Tempering hardness,
Second result of Ogoshi-type rapid wear test and Charpy impact test
Shown in the table. Sample No.1 to No.3 are the values of conventional steel, Sample No.7 to N
o.10 is the value of comparative steel.
本発明鋼に比較して従来鋼１は靱性がやや低く、従来鋼
２は目標とする硬さが不十分であり、従来鋼３（SKH9）
は高硬度であるが、靱性が著しく低下する。Conventional steel 1 has slightly lower toughness than conventional steel, and conventional steel 2 has insufficient target hardness. Conventional steel 3 (SKH9)
Has a high hardness, but its toughness is significantly reduced.
本発明鋼は、Si含有量が多いことを特徴の１つとする
が、No.7のようにSi量が低い場合は焼もどし硬さが低
い。またNo.8のようにSiを過度に添加すると靱性が低下
する。One of the features of the steel of the present invention is that it has a high Si content, but when the Si content is low as in No. 7, the temper hardness is low. Further, if Si is excessively added as in No. 8, the toughness decreases.
本発明鋼は同時にNbの微量添加を特徴とする。No.9また
はNo.10のようにNb無添加鋼では、靱性が低くなる。No.
11〜No.28は本発明鋼の特許請求の範囲の化学成分であ
る。No.11、No.12、No.13はそれぞれ特許請求の範囲第
１項、第２項、第３項に相当する化学成分であるが、第
２表より明らかなようにSi含有量が多くなるにつれ、焼
もどし硬さ、耐摩耗性が向上し、靱性も十分大きい。N
o.14、No.15、No.16はＶ量を低めに添加した鋼である。
これらはNo.13（特許請求の範囲の第３項の化学成分に
相当）に比べ耐摩耗性はやや低いが、靱性が大きくなっ
ている。 The steel according to the invention is also characterized by a trace addition of Nb. In Nb-free steels such as No. 9 or No. 10, the toughness is low. No.
No. 11 to No. 28 are chemical compositions in the claims of the steel of the present invention. No. 11, No. 12, and No. 13 are chemical components corresponding to the first, second, and third claims, respectively, but as shown in Table 2, the Si content is high. As a result, temper hardness and wear resistance are improved, and toughness is sufficiently high. N
o.14, No.15 and No.16 are steels added with a lower V content.
These have slightly lower wear resistance than No. 13 (corresponding to the chemical composition of claim 3), but have high toughness.
No.17、No.18は本特許請求の範囲内でＷ当量を低く抑え
た化学成分であり、靱性が高いものである。No.19、No.
20はCoを添加した例であるが、第２表のようにCoを添加
することにより耐摩耗性が大きく向上する。No. 17 and No. 18 are chemical components whose W equivalents are kept low within the scope of the claims of the present invention, and have high toughness. No.19, No.
Although 20 is an example in which Co is added, the wear resistance is greatly improved by adding Co as shown in Table 2.
No.21はCoを添加し、さらにLa、Ceを添加した例である
が、耐摩耗性、靱性ともにLa、Ceを添加しないNo.19に
比べ向上する。No.22〜No.28は特許請求の範囲第１項な
いし第３項に相当する化学成分にLa、Ce、Al、Ｙを添加
した例であるが、いずれも耐摩耗性、靱性ともに大きく
向上する。No. 21 is an example in which Co and La and Ce are further added, but both the wear resistance and toughness are improved compared to No. 19 in which La and Ce are not added. No.22 to No.28 are examples in which La, Ce, Al, and Y are added to the chemical components corresponding to claims 1 to 3, but both are greatly improved in wear resistance and toughness. To do.
本発明鋼はいずれも、靱性が比較鋼と同等以上でありな
がら、耐摩耗性が比較鋼より大きいことが特徴である。All of the steels of the present invention are characterized in that the toughness is equal to or higher than that of the comparative steel, but the wear resistance is higher than that of the comparative steel.
（実施例２） 第３表は、実際に本発明鋼を実用鋼塊で試作した際の化
学組成および比較に用いた鋼種の化学組成を掲げる。(Example 2) Table 3 lists the chemical composition when the steel of the present invention was actually produced as a trial in a practical steel ingot and the chemical composition of the steel species used for comparison.
本発明鋼は高周波炉で溶解し、実用鋼塊に鋳込んだ後、
ハンマーで断面が100mm×100mmとなるように鍛造した。
鍛造前に1170℃×10Hの拡散熱処理処理を行なった。鍛
造後圧延を行ない、直径20mmに仕上げた。The steel of the present invention is melted in a high frequency furnace and cast into a practical steel ingot,
It was forged with a hammer so that the cross section was 100 mm x 100 mm.
Before forging, a diffusion heat treatment of 1170 ° C x 10H was performed. After forging, it was rolled to a diameter of 20 mm.
また製造上での拡散熱処理の効果を調べるために、鍛造
前に拡散熱処理を行なわないで製造したものを比較鋼と
して供した。Further, in order to examine the effect of the diffusion heat treatment on the production, the one produced without performing the diffusion heat treatment before forging was used as a comparative steel.
第１図は、本発明鋼と他鋼種のHRC62以上でシャルピー
衝撃値を比較したものであるが、図のようにこの硬さ領
域で本発明鋼の耐衝撃性が優れているのがわかる。ま
た、拡散熱処理を行なうことにより、耐衝撃性が向上す
る。 FIG. 1 is a comparison of the Charpy impact value between the present invention steel and other steel grades of HRC62 or higher. As shown in the figure, it can be seen that the present invention steel has excellent impact resistance in this hardness region. Moreover, impact resistance is improved by performing the diffusion heat treatment.
第２図は本発明鋼と他鋼種の耐摩耗性を比較したもので
あるが、同一硬さレベルで比較した場合、他鋼種に比べ
本発明鋼の耐摩耗性は優れている。FIG. 2 compares the wear resistance of the present invention steel with other steel grades, but when compared at the same hardness level, the wear resistance of the present invention steel is superior to other steel grades.
〔発明の効果〕 以上説明したように本発明鋼は、熱処理後HRC62〜64の
硬さが安定して得られ、耐摩耗性に優れ、かつ高靱性を
有するため、圧造工具の寿命の大幅な向上が達成でき
る。[Effects of the Invention] As described above, the steel of the present invention has a stable hardness of HRC62 to 64 after heat treatment, is excellent in wear resistance, and has high toughness, so that the life of the forging tool is significantly increased. Improvement can be achieved.
第１図は、HRC62以上における本発明合金と比較合金と
の衝撃値を比較したグラフ、第２図は本発明合金と比較
合金との耐摩耗性を比較したグラフである。FIG. 1 is a graph comparing impact values of the present invention alloy and comparative alloy at HRC62 or higher, and FIG. 2 is a graph comparing wear resistance of the present invention alloy and comparative alloy.
Claims (13)
〜2.2％、Mn0.6％以下、Cr3.0〜5.0％、W3.0以下、Mo1.
0〜5.0％（ただしＷ＋2Mo5〜10％）、V0.5〜1.5％、Nb
0.1％を越え1.0％以下を含有し、残部Feおよび不純物元
素からなることを特徴とする低合金高速度工具鋼。1. A weight percent content of C0.7% to 0.85% or less, Si0.8.
~ 2.2%, Mn0.6% or less, Cr3.0-5.0%, W3.0 or less, Mo1.
0 to 5.0% (however W + 2Mo5 to 10%), V0.5 to 1.5%, Nb
A low-alloy high-speed tool steel containing more than 0.1% and 1.0% or less, and the balance being Fe and impurity elements.
の範囲第１項に記載の低合金高速度工具鋼。2. The low alloy high speed tool steel according to claim 1, which contains Si 1.2 to 2.2% by weight.
有する特許請求の範囲第１項に記載の低合金高速度工具
鋼。3. A low alloy high speed tool steel according to claim 1, containing Si1.6 to 2.0% and V1.2 to 1.5% by weight.
〜2.2％、Mn0.6％以下、Cr3.0〜5.0％、W3.0％以下、Mo
1.0〜5.0％（ただしＷ＋2Mo5〜10％）、V0.5〜1.5％、N
b0.1％を越え1.0％以下,Co8％以下を含有し、残部Feお
よび不純物元素からなることを特徴とする低合金高速度
工具鋼。4. The weight percentage of C exceeds 0.7% and 0.85% or less, Si0.8.
~ 2.2%, Mn0.6% or less, Cr3.0-5.0%, W3.0% or less, Mo
1.0 to 5.0% (however W + 2Mo5 to 10%), V0.5 to 1.5%, N
b Low-alloy high-speed tool steel containing more than 0.1% and 1.0% or less and Co8% or less, and the balance Fe and impurity elements.
の範囲第４項に記載の低合金高速度工具鋼。5. The low alloy high speed tool steel according to claim 4, which contains Si 1.2 to 2.2% by weight.
有する特許請求の範囲第４項に記載の低合金高速度工具
鋼。6. A low alloy high speed tool steel according to claim 4, which contains Si1.6 to 2.0% and V1.2 to 1.5% by weight.
〜2.2％、Mn0.6％以下、Cr3.0〜5.0％、W3.0％以下、Mo
1.0〜5.0％（ただしＷ＋2Mo5〜10％）、V0.5〜1.5％、N
b0.1％を越え1.0％以下を含み、さらにAl、La、Ce、Ｙ
の一種または二種以上を0.02〜0.2％含み、残部Feおよ
び不純物元素からなり、Ti≦0.02％、Ｎ≦0.006％、Ｓ
≦0.004％、Ｏ≦40ppmに規制したことを特徴とする低合
金高速度工具鋼。7. The weight percentage of C exceeds 0.7% and 0.85% or less, Si0.8.
~ 2.2%, Mn0.6% or less, Cr3.0-5.0%, W3.0% or less, Mo
1.0 to 5.0% (however W + 2Mo5 to 10%), V0.5 to 1.5%, N
b over 0.1% and up to 1.0%, including Al, La, Ce, Y
0.02 to 0.2% of one or more of the above, and the balance Fe and impurity elements, Ti ≦ 0.02%, N ≦ 0.006%, S
Low alloy high speed tool steel characterized by being regulated to ≤0.004% and O≤40ppm.
の範囲第７項に記載の低合金高速度工具鋼。8. The low alloy high speed tool steel according to claim 7, which contains Si 1.2 to 2.2% by weight.
有する特許請求の範囲第７項に記載の低合金高速度工具
鋼。9. The low alloy high speed tool steel according to claim 7, which contains Si1.6 to 2.0% and V1.2 to 1.5% by weight.
8〜2.2％、Mn0.6％以下、Cr3.0〜5.0％、W3.0％以下、M
o1.0〜5.0％（ただしＷ＋2Mo5〜10％）、V0.5〜1.5％、
Nb0.1％を越え1.0％以下、Co8％以下を含み、さらにA
l、La、Ce、Ｙの一種または二種以上を0.02〜0.2％含
み、残部Feおよび不純物元素からなり、Ti≦0.02％、Ｎ
≦0.006％、Ｓ≦0.004％、Ｏ≦40ppmに規制したことを
特徴とする低合金高速度工具鋼。10. A weight percentage of C is more than 0.7% and 0.85% or less.
8-2.2%, Mn0.6% or less, Cr3.0-5.0%, W3.0% or less, M
o1.0-5.0% (W + 2Mo5-10%), V0.5-1.5%,
Nb 0.1% to 1.0% or less, Co 8% or less, and A
l, La, Ce, Y, one or more, containing 0.02 to 0.2%, balance Fe and impurity elements, Ti ≤ 0.02%, N
Low alloy high speed tool steel characterized by being regulated to ≤0.006%, S≤0.004% and O≤40ppm.
求の範囲第９項に記載の低合金高速度工具鋼。11. The low alloy high speed tool steel according to claim 9, which contains Si 1.2 to 2.2% by weight.
含有する特許請求の範囲第９項に記載の低合金高速度工
具鋼。12. The low alloy high speed tool steel according to claim 9, which contains Si1.6 to 2.0% and V1.2 to 1.5% by weight.
において、1150〜1190℃で５〜40時間加熱保持して拡散
熱処理することを特徴とする特許請求の範囲第１項ない
し第11項記載のいずれか１項に記載の低合金高速度工具
鋼の製造方法。13. The diffusion heat treatment as claimed in claim 1, wherein the steel ingot is heated and held at 1150 to 1190 ° C. for 5 to 40 hours before and after the hot working to perform diffusion heat treatment. Item 6. A method for producing a low alloy high speed tool steel according to any one of items.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63077310A JPH07116550B2 (en) | 1987-09-24 | 1988-03-30 | Low alloy high speed tool steel and manufacturing method thereof |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23942687 | 1987-09-24 | ||
| JP62-239426 | 1987-09-24 | ||
| JP63077310A JPH07116550B2 (en) | 1987-09-24 | 1988-03-30 | Low alloy high speed tool steel and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH01159349A JPH01159349A (en) | 1989-06-22 |
| JPH07116550B2 true JPH07116550B2 (en) | 1995-12-13 |
Family
ID=26418410
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63077310A Expired - Fee Related JPH07116550B2 (en) | 1987-09-24 | 1988-03-30 | Low alloy high speed tool steel and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07116550B2 (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100331962B1 (en) * | 1996-05-08 | 2002-11-27 | 기아특수강 주식회사 | Method for manufacturing high cleanliness tool steel with improved macro/micro-solidification structure |
| BRPI0601679B1 (en) * | 2006-04-24 | 2014-11-11 | Villares Metals Sa | FAST STEEL FOR SAW BLADES |
| BRPI0603856A (en) * | 2006-08-28 | 2008-04-15 | Villares Metals Sa | hard alloys of lean composition |
| EP2570507A1 (en) | 2011-09-19 | 2013-03-20 | Sandvik Intellectual Property AB | A method for producing high speed steel |
| JP6529234B2 (en) * | 2014-09-22 | 2019-06-12 | 山陽特殊製鋼株式会社 | High speed tool steel with high toughness and softening resistance |
| CN104328346A (en) * | 2014-11-08 | 2015-02-04 | 江苏天舜金属材料集团有限公司 | Processing process of wear-resisting anti-impact type pile foundation steel protective barrel |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5010808A (en) * | 1973-05-19 | 1975-02-04 | ||
| JPS5168421A (en) * | 1974-12-10 | 1976-06-14 | Michio Takeda | REIKANATSUZOKOGUKEISEIZAIRYOYOTOKUSHUKO |
| JPS58174555A (en) * | 1982-04-02 | 1983-10-13 | Nippon Koshuha Kogyo Kk | Alloy tool steel |
-
1988
- 1988-03-30 JP JP63077310A patent/JPH07116550B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH01159349A (en) | 1989-06-22 |
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