JPS645100B2 - - Google Patents
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- Publication number
- JPS645100B2 JPS645100B2 JP5478683A JP5478683A JPS645100B2 JP S645100 B2 JPS645100 B2 JP S645100B2 JP 5478683 A JP5478683 A JP 5478683A JP 5478683 A JP5478683 A JP 5478683A JP S645100 B2 JPS645100 B2 JP S645100B2
- Authority
- JP
- Japan
- Prior art keywords
- weight
- tempering
- toughness
- hardness
- temperature
- 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
Links
- 238000005496 tempering Methods 0.000 claims description 19
- 229910000831 Steel Inorganic materials 0.000 claims description 16
- 239000010959 steel Substances 0.000 claims description 16
- 230000000694 effects Effects 0.000 claims description 14
- 230000000171 quenching effect Effects 0.000 claims description 7
- 239000012535 impurity Substances 0.000 claims description 5
- 239000000463 material Substances 0.000 description 7
- 238000010791 quenching Methods 0.000 description 6
- 238000005520 cutting process Methods 0.000 description 5
- 150000001247 metal acetylides Chemical class 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 238000009760 electrical discharge machining Methods 0.000 description 4
- 238000005482 strain hardening Methods 0.000 description 4
- 238000005452 bending Methods 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 238000010273 cold forging Methods 0.000 description 2
- 229910052745 lead Inorganic materials 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 230000013011 mating Effects 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910052721 tungsten Inorganic materials 0.000 description 2
- 229910052726 zirconium Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000822 Cold-work tool steel Inorganic materials 0.000 description 1
- 229910001315 Tool steel Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 229910052797 bismuth Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000003009 desulfurizing effect Effects 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000005240 physical vapour deposition Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
Description
本発明は使用条件が苛酷な冷間加工あるいは工
具に加工する際ワイヤーカツト等の放電加工等に
使用するのに特に好適な高硬度でしかも高靭性を
有する冷間ダイス鋼に関する。
従来、冷間鍛造用ダイスおよびポンチ、抜型用
途等に使用される冷間加工用合金工具鋼としては
JIS SKD11が汎用されている。これらSKD11は
熱処理法として1000〜1050℃から焼入れ後、150
〜200℃で焼もどしし、HRC61以上で用いられる
のが一般的である。しかし、これら従来の
SKD11は硬度は高いものの靭性が充分でなく、
近時の冷間加工法の苛酷化、またはワイヤーカツ
ト加工等の放電加工法の普及に伴い、SKD11で
は対処しきれない場合が増大している。例えば冷
間鍛造用ダイスでは焼付による工具寿命の低下、
抜型では前記ワイヤーカツトによる放電加工時の
割れ発生等が問題となつている。
このような状況に対し、SKD11の組成をベー
スに種々の成分を添加する等各種の冷間工具鋼が
提案されている。しかし、これらは前述の如き苛
酷な冷間加工あるいは放電加工に使用する工具と
して充分な硬度と靭性を兼ね備えたものとはいい
難い。
本発明者らは、近時の苛酷な使用条件に充分に
対応し得、強度低下、割れをきたすことなく長期
間に亘つて安定して使用し得る高硬度でしかも高
靭性を備え、放電加工性に優れた冷間ダイス鋼を
提供することを目的とし、種々検討を重ねた。そ
の結果、炭素および炭化物形成元素間に適切なバ
ランスを保持せしめて一次の共晶炭化物を少くす
ることによつて靭性を高い状態にするとともに、
各成分組成範囲を特定し、これを450℃以上の高
温焼もどし処理を施して二次硬化硬さを増大させ
ることにより、冷間ダイス鋼の寿命と放電加工性
が大巾に改善されるという知見を得、本発明に至
つた。
すなわち、本発明は
0.9<C<1.3
0.5<Si≦2.0
0.1≦Mn≦2.0
5.0≦Cr<11.0
1.3≦Mo≦4.0
0.1≦V<0.35(各重量%)
を含有し、さらに必要に応じて
0.001≦REM≦0.5
0.1≦Cu≦2.0
0.1≦W≦3.0
0.1≦Co≦5.0
0<Ti≦2.0
0<Zr≦2.0(各重量%)
のうちの1種又は2種以上と、必要に応じてさら
に
0<S≦0.20
0<Pb≦0.40
0<Se≦0.30
0<Bi≦0.50
0<Te≦0.30
0.002≦Ca≦0.010(各重量%)
のうち1種又は2種以上を含有し、残部Feおよ
び不純物よりなり、1060℃以下での高温で焼入れ
効果が生じ、450〜550℃で焼戻し効果が生じる冷
間ダイス鋼である。
本発明における各成分組成範囲の限定理由は以
下の通りである。
C:Cはマルテンサイトの硬さを高め、高温焼も
どしにより特殊炭化物を形成して2次硬化に寄
与し、またさらにCr、Mo、Vと炭化物を形成
して耐摩耗性に寄与する必須元素である。この
C量はCr量と相関をもつが、0.90%以下では焼
入焼もどし硬さが低く且つ耐摩耗性が低下し、
逆に1.3%以上だと靭性が低下するため0.9<C
<1.3とする。
Si:Siは高温焼もどし硬さの増大に有効であり、
また硬さを低下させることなく靭性を向上させ
る。これら効果を得るためには0.5%を越えた
量で含有させることが必要であるが、2.0%を
越えると熱間加工性、靭性を低下させる。
Mn:Mnは脱酸および脱硫剤として作用し、鋼
の清浄度を向上させるとともに焼入性を良好に
する。そのために、0.1%以上含有させるが、
2%を越えると加工性を害する。
Cr:Crは焼入時に基地中に固溶して焼入性を高
めるとともにCr炭化物を形成し、耐摩耗性を
向上させるが、5%未満ではこのような効果が
小さく、逆に11%以上になると靭性を劣化させ
る。
Mo:Moは焼入時に基地中に固溶するとともに
炭化物を形成して耐摩耗性を向上させ、焼入れ
および焼もどし抵抗性を高めるのに有効な元素
である。このような効果を発揮し、特に高温焼
もどしでHRC62以上の高硬度を得るためには
1.3%以上含有させる必要があるが、5%を越
えてもその効果の増大はそれ程ではなく熱間加
工性を劣化させるようになる。
V:Vは基地のオーステナイト系結晶粒の粗大化
を防止し、微細な炭化物を形成して耐摩耗性お
よび焼入性の向上に寄与する。これら効果は
0.1%未満では期待できず、また0.35%以上に
なると加工性が劣化する。
REM、Cu、W、Co、Ti、Zr:これら各元素は
強度および靭性の向上に寄与するものである
が、多量に含有すると熱間加工性や靭性を低下
させるため、それぞれREM:0.001〜5%、
Cu:0.1〜2.0%、W:0.1〜3.0%、Co:0.1〜
5.0%、Ti:2.0%以下、Zr:2%以下とする。
これら各元素は1種でもあるいは2種以上含有
させてもよい。
S、Pb、Se、Bi、Te、Ca:これら各元素はいず
れも被削性を向上させるのに有効なものであ
り、機械加工および塑性加工(鍛造等)後の仕
上加工の際の加工性を良好となすが、多すぎる
と熱間加工性や靭性を低下させるため、それぞ
れS:0.20%以下、Pb:0.40%以下、Se:0.30
%以下、Bi:0.50%以下、Te:0.30%以下、
Ca:0.002〜0.010%とする。これら各元素は1
種でもあるいは2種以上含有させてもよい。
これら各成分組成を上記範囲に特定した鋼材は
焼なましされた後高温で焼入され、しかる後に高
温焼もどしされる。
本発明は、1060℃以下の高温で焼入れし、450
〜550℃の温度からなる高温焼もどし処理により
すぐれた物性を発揮する冷間ダイス鋼であり、こ
のような高温焼もどしにより、焼入れ時の残留応
力が除去されて安定組織となるとともに二次硬化
硬さが増大し、硬さおよび靭性が共に優れ、工具
としての使用時のかじりを起し、あるいは放電加
工等により工具に熱が生ずる場合にも割れを生ず
ることなく工具寿命が延長され、加工性が大巾に
向上するようになる。またさらに工具表面にTiC
等を物理蒸着する場合の表面処理性も良好とな
る。これら高温焼もどしによる利点は焼もどし温
度が450℃未満では充分に発揮されない。
次に本発明を実施例により詳細に説明する。
実施例
第1表に示す成分組成の本発明鋼および比較鋼
として従来から用いられているJIS SKD11、
SKD12その他を溶製し、硬さ、シヤルピー衝撃
値、曲げ抗折力、焼付荷重、比摩耗量、残留応力
およびワイヤーカツト性につき試験した。それら
特性値の試験結果を第2表に示す。
なお、各試験条件は次のとおりである。
(イ) 曲げ抗折力……φ8×130mmの試験片につき、
支点間距離100mm、中央1点荷重とし試験片が
破断する際の破断荷重で示す。
(ロ) 比摩耗量……大越式迅速摩耗試験機により相
手材SCM415(HB190)、摩擦速度2.9m/sec、
摩擦距離200mm、摩擦荷重6.5Kgとした。
(ハ) 焼付荷重……相手材としてSCM415(焼なま
し)を用い、摩擦速度30〜100mm/sec、接触面
圧5〜50Kgf/mm2、潤滑油として油脂系とした。
(ニ) ワイヤーカツト性……ワイヤーカツトにより
10mm長さ切断し、切断面における100μ長さ以
上の割れ数で示す。
The present invention relates to a cold die steel having high hardness and high toughness, which is particularly suitable for use in severe cold working conditions or electrical discharge machining of wire cuts and the like when processing into tools. Traditionally, cold working alloy tool steel used for cold forging dies, punches, cutting dies, etc.
JIS SKD11 is commonly used. These SKD11 are heat treated from 1000 to 1050℃ and then heated to 150℃.
It is generally tempered at ~200℃ and used with an HRC of 61 or higher. However, these conventional
Although SKD11 has high hardness, it does not have sufficient toughness.
As cold working methods become more severe in recent years and electric discharge machining methods such as wire cutting become more widespread, there are an increasing number of cases that cannot be handled with SKD11. For example, with dies for cold forging, tool life may be reduced due to seizure.
With cutting dies, cracking during electrical discharge machining due to the wire cut has become a problem. In response to this situation, various cold work tool steels have been proposed, such as those based on the composition of SKD11 and with the addition of various ingredients. However, these tools cannot be said to have sufficient hardness and toughness as tools used in severe cold working or electrical discharge machining as described above. The present inventors have developed a material with high hardness and high toughness that can fully cope with today's harsh usage conditions and can be used stably for a long period of time without decreasing strength or cracking. With the aim of providing cold die steel with excellent properties, various studies were conducted. As a result, by maintaining an appropriate balance between carbon and carbide-forming elements and reducing the amount of primary eutectic carbides, toughness is increased, and
By identifying the composition range of each component and subjecting it to high-temperature tempering at 450°C or higher to increase secondary hardening hardness, the lifespan and electrical discharge machinability of cold die steel can be greatly improved. This knowledge led to the present invention. That is, the present invention contains 0.9<C<1.3 0.5<Si≦2.0 0.1≦Mn≦2.0 5.0≦Cr<11.0 1.3≦Mo≦4.0 0.1≦V<0.35 (each % by weight), and further contains 0.001 as necessary. ≦REM≦0.5 0.1≦Cu≦2.0 0.1≦W≦3.0 0.1≦Co≦5.0 0<Ti≦2.0 0<Zr≦2.0 (each weight%) One or more of the following, and further as necessary. Contains one or more of the following: 0<S≦0.20 0<Pb≦0.40 0<Se≦0.30 0<Bi≦0.50 0<Te≦0.30 0.002≦Ca≦0.010 (each weight%), with the remainder being Fe and It is a cold die steel that consists of impurities and has a hardening effect at high temperatures below 1060°C and a tempering effect at 450 to 550°C. The reason for limiting the composition range of each component in the present invention is as follows. C: C is an essential element that increases the hardness of martensite, forms special carbides through high-temperature tempering, and contributes to secondary hardening, and also forms carbides with Cr, Mo, and V, contributing to wear resistance. It is. The amount of C has a correlation with the amount of Cr, but if it is less than 0.90%, the hardness after quenching and tempering will be low and the wear resistance will decrease.
On the other hand, if it exceeds 1.3%, the toughness decreases, so 0.9<C
<1.3. Si: Si is effective in increasing high temperature tempering hardness.
It also improves toughness without reducing hardness. In order to obtain these effects, it is necessary to contain more than 0.5%, but if it exceeds 2.0%, hot workability and toughness will decrease. Mn: Mn acts as a deoxidizing and desulfurizing agent, improving the cleanliness of steel and improving hardenability. For this purpose, it is made to contain 0.1% or more, but
If it exceeds 2%, workability will be impaired. Cr: During quenching, Cr dissolves into the matrix to improve hardenability and forms Cr carbide, improving wear resistance. However, if it is less than 5%, this effect is small, and conversely if it is 11% or more When this happens, the toughness deteriorates. Mo: Mo is an effective element for improving wear resistance by forming a solid solution in the matrix during quenching and forming carbides, and for increasing quenching and tempering resistance. In order to exhibit such effects and obtain a high hardness of HRC62 or higher through high-temperature tempering,
It is necessary to contain 1.3% or more, but even if it exceeds 5%, the effect will not increase much and hot workability will deteriorate. V: V prevents the austenitic crystal grains of the matrix from becoming coarser, forms fine carbides, and contributes to improving wear resistance and hardenability. These effects are
If it is less than 0.1%, it cannot be expected, and if it is more than 0.35%, workability deteriorates. REM, Cu, W, Co, Ti, Zr: Each of these elements contributes to improving strength and toughness, but if contained in large amounts, hot workability and toughness decrease, so REM: 0.001 to 5 %,
Cu: 0.1~2.0%, W: 0.1~3.0%, Co: 0.1~
5.0%, Ti: 2.0% or less, Zr: 2% or less.
Each of these elements may be contained alone or in combination. S, Pb, Se, Bi, Te, Ca: All of these elements are effective in improving machinability, and improve workability during finishing after machining and plastic working (forging, etc.) However, if it is too large, it will reduce hot workability and toughness, so S: 0.20% or less, Pb: 0.40% or less, and Se: 0.30.
% or less, Bi: 0.50% or less, Te: 0.30% or less,
Ca: 0.002 to 0.010%. Each of these elements is 1
A species or two or more kinds may be contained. Steel materials whose component compositions are specified within the above ranges are annealed, quenched at a high temperature, and then tempered at a high temperature. The present invention is quenched at a high temperature of 1060℃ or less, and
It is a cold die steel that exhibits excellent physical properties through high-temperature tempering treatment at a temperature of ~550°C.This high-temperature tempering removes residual stress during quenching and creates a stable structure, as well as secondary hardening. The hardness increases, and both hardness and toughness are excellent, and the tool life is extended without causing galling when used as a tool, or cracking when the tool is heated due to electrical discharge machining, etc., and the tool life is extended. Sexuality will greatly improve. Furthermore, TiC on the tool surface
Surface treatment properties are also improved when physical vapor deposition is performed. These advantages of high-temperature tempering are not fully exhibited when the tempering temperature is lower than 450°C. Next, the present invention will be explained in detail with reference to examples. Example Inventive steel with the composition shown in Table 1 and JIS SKD11, which has been conventionally used as comparative steel,
SKD12 and other materials were melted and tested for hardness, shear py impact value, bending transverse rupture strength, seizure load, specific wear amount, residual stress, and wire cuttability. The test results of these characteristic values are shown in Table 2. The test conditions are as follows. (a) Bending transverse rupture strength...for a φ8×130mm test piece,
The distance between the supporting points is 100mm, and the load is applied at one point at the center.The breaking load is shown when the test piece breaks. (b) Specific wear amount...Mating material SCM415 (HB190), friction speed 2.9m/sec, by Okoshi type rapid wear tester.
The friction distance was 200 mm and the friction load was 6.5 kg. (c) Seizing load: SCM415 (annealed) was used as the mating material, the friction speed was 30 to 100 mm/sec, the contact surface pressure was 5 to 50 Kgf/mm 2 , and the lubricant was oil-based. (d) Wire cutting property... due to wire cutting
Cut to a length of 10mm, and indicate the number of cracks with a length of 100μ or more on the cut surface.
【表】【table】
【表】
第2表より、本発明鋼はいずれもHRC62以上
の硬さを有するとともに高靭性を有し、しかも曲
げ強さ、耐摩耗性、焼付荷重およびワイヤーカツ
ト性ともに優れていることがわかる。
次に、供試材No.1、6、および12(SKD11)を
用いて二次硬化硬さおよびシヤルピー衝撃値に及
ぼす高温焼入れ後の焼もどし温度の影響を調べ
た。その結果を第3表に示す。[Table] From Table 2, it can be seen that all of the steels of the present invention have hardness of HRC62 or higher, high toughness, and are excellent in bending strength, wear resistance, seizure load, and wire cuttability. . Next, using test materials No. 1, 6, and 12 (SKD11), the influence of the tempering temperature after high-temperature quenching on the secondary hardening hardness and Shapey impact value was investigated. The results are shown in Table 3.
【表】
この第3表より、本発明鋼に係るNo.1およびNo.
6において焼もどし温度が200℃、300℃、400℃
の場合の二次硬化硬さは充分でなく、500℃で所
望の硬さとなり、また500℃における衝撃値は400
℃の場合に比べてわずかに低下するが依然として
高靭性を保有している。これらのことから高硬度
および高靭性をともに具備させるための焼もどし
温度は450℃以上とすることが必要といえる。こ
れに対し、従来材では高温焼もどしを施したとし
ても硬さおよび衝撃値とも本発明鋼に比べてかな
り劣るものであることがわかる。[Table] From this Table 3, No. 1 and No. 1 regarding the steel of the present invention.
In 6, the tempering temperature is 200℃, 300℃, 400℃
In the case of
Although the toughness is slightly lower than that at ℃, it still maintains high toughness. From these facts, it can be said that it is necessary to set the tempering temperature to 450°C or higher in order to provide both high hardness and high toughness. On the other hand, it can be seen that even if the conventional material is subjected to high-temperature tempering, both the hardness and the impact value are considerably inferior to the steel of the present invention.
Claims (1)
℃以下での高温で焼入れ効果が生じ、450℃〜550
℃で焼戻し効果が生じる冷間ダイス鋼。 2 0.9<C<1.3 0.5<Si≦2.0 0.1≦Mn≦2.0 5.0≦Cr<11.0 1.3≦Mo≦4.0 0.1≦V<0.35(各重量%) を含有し、さらに 0.001≦REM≦0.5 0.1≦Cu≦2.0 0.1≦W≦3.0 0.1≦Co≦5.0 0<Ti≦2.0 0<Zr≦2.0(各重量%) のうちの1種又は2種以上を含有し、残部Feお
よび不純物よりなり、1060℃以下での高温で焼入
れ効果が生じ、450℃〜550℃で焼戻し効果が生じ
る冷間ダイス鋼。 3 0.9<C<1.3 0.5<Si≦2.0 0.1≦Mn≦2.0 5.0≦Cr<11.0 1.3≦Mo≦4.0 0.1≦V<0.35(各重量%) を含有し、さらに 0<S≦0.20 0<Pb≦0.40 0<Se≦0.30 0<Bi≦0.50 0<Te≦0.30 0.002≦Ca≦0.010(各重量%) のうち1種又は2種以上を含有し、残部Feおよ
び不純物よりなり、1060℃以下での高温で焼入れ
効果が生じ、450℃〜550℃で焼戻し効果が生じる
冷間ダイス鋼。 4 0.9<C<1.3 0.5<Si≦2.0 0.1≦Mn≦2.0 5.0≦Cr<11.0 1.3≦Mo≦4.0 0.1≦V<0.35(各重量%) を含有し、さらに 0.001≦REM≦0.5 0.1≦Cu≦2.0 0.1≦W≦3.0 0.1≦Co≦5.0 0<Ti≦2.0 0<Zr≦2.0(各重量%) のうちの1種又は2種以上と 0<S≦0.20 0<Pb≦0.40 0<Se≦0.30 0<Bi≦0.50 0<Te≦0.30 0.002≦Ca≦0.010(各重量%) のうちの1種又は2種以上を含有し、残部Feお
よび不純物よりなり、1060℃以下での高温で焼入
れ効果が生じ、450℃〜550℃で焼戻し効果が生じ
る冷間ダイス鋼。[Claims] 1 Contains the following: 1 0.9<C<1.3 0.5<Si≦2.0 0.1≦Mn≦2.0 5.0≦Cr<11.0 1.3≦Mo≦4.0 0.1≦V<0.35 (each weight%), with the remainder being Fe and impurities More than 1060
Quenching effect occurs at high temperature below ℃, 450℃~550℃
Cold die steel with tempering effect at ℃. 2 Contains 0.9<C<1.3 0.5<Si≦2.0 0.1≦Mn≦2.0 5.0≦Cr<11.0 1.3≦Mo≦4.0 0.1≦V<0.35 (each weight%), and further contains 0.001≦REM≦0.5 0.1≦Cu≦ Contains one or more of the following: 2.0 0.1≦W≦3.0 0.1≦Co≦5.0 0<Ti≦2.0 0<Zr≦2.0 (each weight%), with the remainder consisting of Fe and impurities, and is resistant to temperatures below 1060℃ Cold die steel that has a hardening effect at a high temperature of , and a tempering effect at a temperature of 450℃ to 550℃. 3 Contains 0.9<C<1.3 0.5<Si≦2.0 0.1≦Mn≦2.0 5.0≦Cr<11.0 1.3≦Mo≦4.0 0.1≦V<0.35 (each weight%), and further contains 0<S≦0.20 0<Pb≦ Contains one or more of the following: 0.40 0<Se≦0.30 0<Bi≦0.50 0<Te≦0.30 0.002≦Ca≦0.010 (each weight%), with the remainder consisting of Fe and impurities, Cold die steel that has a hardening effect at high temperatures and a tempering effect at 450℃~550℃. 4 Contains 0.9<C<1.3 0.5<Si≦2.0 0.1≦Mn≦2.0 5.0≦Cr<11.0 1.3≦Mo≦4.0 0.1≦V<0.35 (each weight%), and further contains 0.001≦REM≦0.5 0.1≦Cu≦ 2.0 0.1≦W≦3.0 0.1≦Co≦5.0 0<Ti≦2.0 0<Zr≦2.0 (each weight%) One or more of the following and 0<S≦0.20 0<Pb≦0.40 0<Se≦ Contains one or more of the following: 0.30 0<Bi≦0.50 0<Te≦0.30 0.002≦Ca≦0.010 (each weight%), with the balance consisting of Fe and impurities, and has a hardening effect at high temperatures below 1060℃ Cold die steel with a tempering effect at 450℃~550℃.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP5478683A JPS59179762A (en) | 1983-03-30 | 1983-03-30 | Cold tool steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP5478683A JPS59179762A (en) | 1983-03-30 | 1983-03-30 | Cold tool steel |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS59179762A JPS59179762A (en) | 1984-10-12 |
JPS645100B2 true JPS645100B2 (en) | 1989-01-27 |
Family
ID=12980437
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP5478683A Granted JPS59179762A (en) | 1983-03-30 | 1983-03-30 | Cold tool steel |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS59179762A (en) |
Families Citing this family (18)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH01111818A (en) * | 1987-07-14 | 1989-04-28 | Japan Casting & Forging Corp | Production of forged steel roll for cold rolling |
JPS6428344A (en) * | 1987-07-24 | 1989-01-30 | Dai Ichi High Frequency Co Ltd | Roll for scale breaker |
US4929288A (en) * | 1988-01-04 | 1990-05-29 | Borges Robert J | Corrosion and abrasion resistant alloy |
JP2710941B2 (en) * | 1988-02-08 | 1998-02-10 | 日立金属株式会社 | Rolling die steel |
JPH01208437A (en) * | 1988-02-13 | 1989-08-22 | Kanto Tokushu Seiko Kk | High chrome-typed roll steel having improved grindability for rolling |
JPH02200783A (en) * | 1989-01-30 | 1990-08-09 | Daido Steel Co Ltd | Surface hardened die material |
US5270124A (en) * | 1989-06-30 | 1993-12-14 | The Broken Hill Proprietary Co., Ltd. | Composite roll |
JPH089045B2 (en) * | 1990-11-05 | 1996-01-31 | 住友金属工業株式会社 | Cavity roll for cold tube rolling mill and method for manufacturing the same |
JP2631262B2 (en) * | 1993-03-30 | 1997-07-16 | 大同特殊鋼株式会社 | Manufacturing method of cold die steel |
SI1511873T1 (en) * | 2002-06-13 | 2011-12-30 | Uddeholms Ab | Cold work steel and cold work tool |
FR2870546B1 (en) * | 2004-05-21 | 2006-09-01 | Industeel Creusot | STEEL WITH HIGH MECHANICAL RESISTANCE AND WEAR |
US8920296B2 (en) | 2011-03-04 | 2014-12-30 | Åkers AB | Forged roll meeting the requirements of the cold rolling industry and a method for production of such a roll |
WO2012121630A1 (en) * | 2011-03-04 | 2012-09-13 | Åkers AB | A forged roll meeting the requirements of the cold rolling industry and a method for production of such a roll |
CN103898415B (en) * | 2014-04-18 | 2015-09-23 | 北京科技大学 | A kind of modified version Cr8 Steel Roll and preparation method thereof |
CN104087867B (en) * | 2014-07-31 | 2016-08-24 | 宁国市宁武耐磨材料有限公司 | A kind of ball mill high abrasion antioxidant wear-resistant ball |
CN112410684A (en) * | 2020-10-14 | 2021-02-26 | 河冶科技股份有限公司 | Die steel and preparation method thereof |
CN112430781A (en) * | 2020-10-14 | 2021-03-02 | 河冶科技股份有限公司 | Alloy tool steel for thread rolling wheel and preparation method thereof |
CN113215482B (en) * | 2021-03-22 | 2022-05-20 | 武汉钜能科技有限责任公司 | Wear-resistant cold-work tool steel |
Family Cites Families (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS51146316A (en) * | 1975-06-11 | 1976-12-15 | Hitachi Metals Ltd | Tool steel for brazed cutter |
JPS5237511A (en) * | 1975-09-22 | 1977-03-23 | Hitachi Metals Ltd | Alloy tool steel for cold working |
JPS52138008A (en) * | 1976-05-14 | 1977-11-17 | Hitachi Metals Ltd | Impact resistance steel having good burn out resistance |
JPS5377821A (en) * | 1976-12-22 | 1978-07-10 | Kanto Special Steel Works Ltd | Roll for cold rolling metal |
JPS54124819A (en) * | 1978-03-22 | 1979-09-28 | Hitachi Metals Ltd | Steel for woodworking knife |
JPS5675554A (en) * | 1979-11-22 | 1981-06-22 | Sanyo Tokushu Seikou Kk | Mandrel steel for cold pilger press drawing machine |
JPS5723049A (en) * | 1980-07-14 | 1982-02-06 | Daido Steel Co Ltd | Conveying roll |
JPS5747849A (en) * | 1980-09-04 | 1982-03-18 | Kobe Steel Ltd | Work roll for cold rolling |
JPS5773177A (en) * | 1980-10-23 | 1982-05-07 | Seiko Epson Corp | Formation of white surface |
JPS5773170A (en) * | 1980-10-24 | 1982-05-07 | Daido Steel Co Ltd | Tool steel |
JPS59145763A (en) * | 1983-02-10 | 1984-08-21 | Nippon Koshuha Kogyo Kk | Alloy tool steel |
-
1983
- 1983-03-30 JP JP5478683A patent/JPS59179762A/en active Granted
Also Published As
Publication number | Publication date |
---|---|
JPS59179762A (en) | 1984-10-12 |
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