JPS608298B2 - Forged steel quenching roll for cold rolling - Google Patents

Forged steel quenching roll for cold rolling

Info

Publication number
JPS608298B2
JPS608298B2 JP8264979A JP8264979A JPS608298B2 JP S608298 B2 JPS608298 B2 JP S608298B2 JP 8264979 A JP8264979 A JP 8264979A JP 8264979 A JP8264979 A JP 8264979A JP S608298 B2 JPS608298 B2 JP S608298B2
Authority
JP
Japan
Prior art keywords
roll
cold rolling
hardness
amount
forged steel
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
Application number
JP8264979A
Other languages
Japanese (ja)
Other versions
JPS569328A (en
Inventor
雅之 江良
公彦 赤堀
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Hitachi Ltd
Original Assignee
Hitachi Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Hitachi Ltd filed Critical Hitachi Ltd
Priority to JP8264979A priority Critical patent/JPS608298B2/en
Publication of JPS569328A publication Critical patent/JPS569328A/en
Publication of JPS608298B2 publication Critical patent/JPS608298B2/en
Expired legal-status Critical Current

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Classifications

    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D9/00Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/38Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for roll bodies

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  • 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)
  • Reduction Rolling/Reduction Stand/Operation Of Reduction Machine (AREA)
  • Heat Treatment Of Articles (AREA)

Description

【発明の詳細な説明】 本発明は、冷間圧延用鍛鋼焼入れロールに係り、特にセ
ンジマー圧延機のワークロールに使用するのに好適な鍬
鋼焼入れロールに関する。
DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a forged steel quench roll for cold rolling, and more particularly to a hoe steel quench roll suitable for use as a work roll of a Sendzimer rolling mill.

冷間圧延用ロールに要求される性質は、一般に高硬度で
耐摩耗性および轍性にすぐれていることである。センジ
マー圧延機のワークロールでは、さらに耐熱衝撃性や光
沢性にすぐれていることが要求される。従来、センジマ
ー圧延機のワークロールは、クロム(Cr)、モリブデ
ン(Mo)、タングステン(W)、バナジウム(V)お
よびコバルト(Co)を含有する高速度工具鋼で作られ
てきた。
The properties required of cold rolling rolls are generally high hardness and excellent wear resistance and rutting resistance. Work rolls for Sendzimer rolling mills are required to have excellent thermal shock resistance and gloss. Traditionally, Sendzimer mill work rolls have been made of high speed tool steel containing chromium (Cr), molybdenum (Mo), tungsten (W), vanadium (V) and cobalt (Co).

前記ワークロールに一般に使用されている組成は、重量
%で、炭素(C)を1.3〜1.6%、Crを4〜6%
、Moを4〜6%、Wを4〜6%、Vを3.5〜6%、
Coを3.5〜6%、けし、素(Si)およびマンガン
(Mn)各0.6%以下、残部鉄(Fe)および不純物
である。組織は、焼入れおよび焼もどしの熱処理を施す
ことによって、暁もどしマルテンサイトと残留オーステ
ナィトと炭化物からなる組織が得られている。このワー
クロールは、硬さがロックウェル硬さでHRc64斗上
、ショァ硬さでHs8肌〆上と極めて高硬度であり、ま
た、デンドラィトを含まない微細な組織を有するので、
光沢性がすぐれている。したがって、ステンレス鋼板の
冷間圧延において、きわめて光沢のある鋼板を得ること
ができる。また、このワークロールは、靭性すなわち曲
げ強さが大きく、さらに熱衝撃にも強いので、圧延中に
被圧延板がワークロールに巻き付き、摩擦熱によってワ
ークロール表面が700〜800℃に加熱される事故が
生じても、クラックが生じにくく且つ進展しにくい効果
を有する。前記靭性および耐熱衝撃性がすぐれる効果は
、Coの含有によるところが大きい。これはCoを入れ
ることによって、基地が強化されたためと考えられる。
しかし、前記ワークロールは、産出量が少なく入手困難
なCoを含有するので、顧客の注文にただちに応じられ
ないという欠点があった。本発明の目的は、入手困難な
Coを含有しなくても、従来のCoを含有する高速度工
具鋼ロールよりも高硬度、高耐摩耗性を有し、鋤性も同
等ないしはすぐれている冷間圧延用ロ−ルを提供するに
ある。
The composition generally used for the work roll is 1.3 to 1.6% carbon (C) and 4 to 6% Cr by weight.
, Mo 4-6%, W 4-6%, V 3.5-6%,
Co is 3.5 to 6%, poppy, elemental (Si) and manganese (Mn) are each 0.6% or less, and the balance is iron (Fe) and impurities. A structure consisting of tempered martensite, retained austenite, and carbide is obtained by heat treatment of quenching and tempering. This work roll has extremely high hardness, exceeding HRc64 on the Rockwell hardness and Hs8 on the Shore hardness, and has a fine structure that does not contain dendrites.
Excellent gloss. Therefore, in cold rolling a stainless steel plate, an extremely glossy steel plate can be obtained. In addition, this work roll has high toughness, that is, bending strength, and is also resistant to thermal shock, so the rolled plate wraps around the work roll during rolling, and the surface of the work roll is heated to 700 to 800°C by frictional heat. Even if an accident occurs, it has the effect of making it difficult for cracks to form and propagate. The excellent toughness and thermal shock resistance are largely due to the inclusion of Co. This is thought to be because the base was strengthened by the addition of Co.
However, since the work roll contains Co, which is produced in small quantities and is difficult to obtain, it has the disadvantage that it is not possible to immediately respond to customer orders. The object of the present invention is to provide a cold roll that has higher hardness and wear resistance than conventional high-speed tool steel rolls containing Co, and has the same or better plowability, even without containing Co, which is difficult to obtain. To provide a roll for inter-rolling.

本発明は、Cを1.3〜1.亀重量%含み、CrとMo
とWとVを含有し、Coを含有しない高速度工具鋼に、
Siを1.3〜2.5重量%含有させ、これに鍛造およ
び暁入れ焼もどし処理を施して、競もどしマルテンサィ
トと残留オーステナィトと炭化物からZなる組織を与え
たものである。
In the present invention, C is 1.3 to 1. Contains turtle weight%, Cr and Mo
and high speed tool steel containing W and V but not containing Co,
It contains 1.3 to 2.5% by weight of Si, and is forged and tempered to give it a Z structure consisting of competitively tempered martensite, retained austenite, and carbide.

本発明のロールは、前記従来のCoを含有する高速度工
具鋼ロールよりも高硬度を有し、摩耗量が少ない。
The roll of the present invention has higher hardness and less wear than the conventional Co-containing high-speed tool steel roll.

また、鞠性も同等ないいまそれ以上である。耐熱衝撃性
もSi量が好適な範囲にあるのでZ従来のロールよりも
すぐれる。したがって、冷間圧延用ロールとして適して
おり、特にセンジマー圧延機のワークロールに最適であ
る。本発明の。ールの好ましい組成は、CI.3〜1.
6%、Mno.6%以下、Cr4〜6%、Mo4〜6%
、W42〜6%、V3.5〜6%及びSil.3〜2.
1%からなるものである。Cは耐摩耗性および硬さを高
めるために必要とされるが、1.3%よりも少ないと焼
入れの効果が十分に与えられないために高硬度が得られ
ず、従2来のCo入り高速度工具鋼ロールよりも劣った
ものになる。
Also, the ballability is the same or even better. Thermal shock resistance is also superior to that of conventional Z rolls because the amount of Si is within a suitable range. Therefore, it is suitable as a cold rolling roll, and is particularly suitable as a work roll for a Sendzimer rolling mill. of the present invention. A preferred composition of the CI. 3-1.
6%, Mno. 6% or less, Cr4-6%, Mo4-6%
, W42-6%, V3.5-6% and Sil. 3-2.
It consists of 1%. C is required to increase wear resistance and hardness, but if it is less than 1.3%, the hardening effect will not be sufficient and high hardness will not be obtained. It becomes inferior to high speed tool steel rolls.

1.6%よりも多いと材質が脆くなって鍛造が困難にな
り、また焼き割れが生じやすくなる。
When the content is more than 1.6%, the material becomes brittle, making forging difficult and prone to quench cracking.

Cr,Mo,WおよびVは、いずれもCと結合し3て炭
化物を形成し、耐摩耗性を高める。
Cr, Mo, W, and V all combine with C to form carbide and improve wear resistance.

またCr,MoおよびWは、焼入れ時に一部基地に固溶
し、基地の耐摩耗性を高める。Cr,MoおよびWの量
がいずれも4%よりも少なく、またVの量が3.5%よ
りも少ないと、耐摩耗性が顕著に改善さ3れず、いずれ
も6%よりも多いと、靭性が悪くなって焼入れ時や圧延
中にロール表面にクラックが入りやすくなる。Mnは脱
酸剤であり、一般の高速度工具鋼に通常含まれている量
を含有することができる。
Furthermore, Cr, Mo, and W partially form a solid solution in the matrix during quenching, thereby increasing the wear resistance of the matrix. When the amounts of Cr, Mo and W are all less than 4%, and when the amount of V is less than 3.5%, the wear resistance is not significantly improved, and when any of them are more than 6%, The toughness deteriorates and cracks tend to form on the roll surface during quenching or rolling. Mn is a deoxidizing agent and can be contained in an amount normally contained in general high-speed tool steel.

本発4明の場合、0.6%以下ならば支障がない。Sj
の量は1.3〜2.5%であり、この範囲にすることに
より従来のCo入りロールよりも硬さ、耐摩耗性および
耐熱衝撃性を高めることができる。特に好ましいSi量
は1.3〜2.1%であり、この範囲であると、硬さ、
耐摩耗性、靭性および耐熱衝撃性のすべてにおいて、従
釆のCo入り高速度工具鋼ロールよりもすぐれるように
なる。本発明のロールの前記した成分を除く残りは、F
eと溶解製造時に混入するりん(P)、硫黄(S)、銅
(Cu)などの不純物である。
In the case of the fourth invention of the present invention, there is no problem if it is 0.6% or less. Sj
The amount is 1.3 to 2.5%, and by setting it within this range, the hardness, abrasion resistance, and thermal shock resistance can be improved compared to conventional Co-containing rolls. A particularly preferable amount of Si is 1.3 to 2.1%, and within this range, hardness,
It is superior to the conventional Co-containing high-speed tool steel roll in terms of wear resistance, toughness, and thermal shock resistance. The remainder of the roll of the present invention other than the above-mentioned components is F
e and impurities such as phosphorus (P), sulfur (S), and copper (Cu) that are mixed in during melting and manufacturing.

これら不純物の量は、一般の高速度工具鋼で通常、規制
されている量すなわちP,Sは各0.03%以下、Cu
は0.25%以下に抑えるべきである。Cuが0.25
%よりも多いとィンゴットを鍛造するときに割れが生じ
やすくなる。本発明のロールは、前記した鋼を鍛造し、
焼入れおよび焼もどし処理を施して作られる。
The amounts of these impurities are normally regulated for general high-speed tool steel, namely P and S are each 0.03% or less, Cu
should be kept below 0.25%. Cu is 0.25
%, cracks tend to occur when forging ingots. The roll of the present invention is produced by forging the above-mentioned steel,
Made by hardening and tempering.

焼入れおよび暁もどいこよって、焼もどしマルテンサイ
トと残留オーステナィトと炭化物からなる組織が得られ
る。残留オーステナィトは少なくできればそれにこした
ことはない。なお、嫁もどし温度がおよそ500〜58
0ooの範囲内にあるときには、焼もどしによって二次
硬化し、硬さが増大することがある。これはSi量を多
くしたことによる効果である。ロールの製造工程は、圧
延ロールの一般的な製造工程と同じである。
By quenching and reheating, a structure consisting of tempered martensite, residual austenite, and carbide is obtained. It would be better if the residual austenite could be reduced. In addition, the bride temperature is approximately 500-58
When it is within the range of 0oo, secondary hardening may occur due to tempering, and the hardness may increase. This is an effect of increasing the amount of Si. The manufacturing process for the roll is the same as the general manufacturing process for rolling rolls.

すなわち、インゴツトー焼なまし処理−鍛造−焼なまし
処理−加工−焼入れ暁もどし処理−加工の工程を経て製
造することができる。鍛造後および最終の加工後には、
磁気探傷や染色検査ならびに寸法検査などを行なう。実
施例第1表に示す化学組成を有する試料を高周波溶解炉
で溶解し、鍛造後、糠なまし処理を施して各種試験片に
加工した。
That is, it can be manufactured through the steps of ingot annealing treatment, forging, annealing treatment, processing, quenching and resetting treatment, and processing. After forging and final processing,
We perform magnetic flaw detection, dye inspection, and dimensional inspection. Examples Samples having the chemical compositions shown in Table 1 were melted in a high-frequency melting furnace, forged, and then processed into various test pieces by being annealed with bran.

その後、焼入れおよび焼もどし処理を施し、硬さ試験、
摩耗試験、曲げ試験および熱衝撃試験を行なった。第2
表に試験結果を示す。なお、暁なまし処理は88000
で5時間保持することにより行ない、焼入れは1200
℃で1時間保持後に油冷、焼もどいま520qoで1時
間保持後に空冷する処理を3回くり返すことにより行な
った。本発明はNo.4〜7である。第2表 硬さ試験は、15仰角の試験片を用いてロックゥェル硬
さ計で測定した。
After that, it is hardened and tempered, hardness tested,
Abrasion tests, bending tests and thermal shock tests were conducted. Second
The test results are shown in the table. In addition, Akatsuki annealing processing is 88000
The quenching is done by holding for 5 hours at 1200℃.
The process was carried out by repeating three times the process of holding at a temperature of 520 qo for 1 hour, cooling with oil, holding at a temperature of 520 qo for 1 hour, and then cooling in air. The present invention is No. 4 to 7. The hardness test in Table 2 was measured using a Rockwell hardness meter using a test piece at an elevation angle of 15.

従来のCo入り高速度工具鋼試験片No.1は、HRc
66(ショア硬さHS約92)であり、本発明の試験片
No.4〜7はこれより若干硬いことが明らかである。
摩耗試験は、回転数60仇.p.m.で回転する直径2
0肌◇のターンテーブル上にェメリーベーパを張り、そ
の上に18肋少、高さ15伽の試験片の円形断面部を荷
重800夕で押し付け、2分2現砂間摩耗させることに
よって行ない、試験前後の重量差をもって耐摩耗性を評
価した。
Conventional Co-containing high-speed tool steel test piece No. 1 is HRc
66 (Shore hardness HS approximately 92), and test piece No. 66 of the present invention. It is clear that samples 4 to 7 are slightly harder than this.
The wear test was performed at a rotation speed of 60 m.p.m. p. m. Rotating diameter 2
The test was carried out by placing emery vapor on a turntable with 0 skin ◇, pressing a circular section of a test piece of 18 ribs and 15 heights onto it under a load of 800 mm, and causing it to wear between 2 minutes and 2 minutes. Wear resistance was evaluated based on the difference in weight before and after.

Si量が1.3%以上のものは、従来のCo入り高速度
工具鋼試験片No.1よりも耐摩耗性がすぐれることは
明らかであ。曲げ試験は、縦と横の寸法が4肌と5側で
長さが55柳の角柱状試験片を、4仇奴の間隔を有する
支点上に載せ、中央の一点に荷重をかけてたわませ、破
断させることにより行ない、破断したときの荷重とたわ
み量を測定した。本発明によるものは、従釆のCo入り
高速度工具鋼試験片No.1よりもた・.」み量が多く
、また破断荷重も同程度か或はNo.1より大きいこと
が明らかにされた。熱衝撃試験は、直径2仇眺め、長さ
5仇舵の試験片を、周波数450KHZで間欠的に高周
波誘導加熱して試験片にヒートクラツクを発生させるこ
とにより行なった。試験片は700℃まで8秒加熱した
ら直ちに水冷し、割れが発生するまでこの熱衝撃をくり
返し与えた。試験片表面には白金−白金ロジウム熱電対
を溶接し、試験片表面の温度を常時測定した。耐熱衝撃
特酸ま、割れ発生までの熱衝撃回数によって評価した。
Siを1.3%以上含む本発明の試験片は、従来のNo
.1よりも耐熱衝撃性がすぐれていることが明らかにさ
れた。図は、第2表に示す試験結果をグラフで表したも
のである。
Those with a Si content of 1.3% or more are conventional Co-containing high-speed tool steel test piece No. It is clear that the wear resistance is superior to that of No. 1. In the bending test, a prismatic specimen of willow with vertical and horizontal dimensions of 4 sides and 5 sides and a length of 55 mm was placed on fulcrums spaced 4 times apart, and a load was applied to one point in the center. The test was carried out by bending and breaking, and the load and deflection at the time of breakage were measured. The specimen according to the present invention is a secondary Co-containing high-speed tool steel test piece No. More than 1. It has a large amount of damage, and the breaking load is about the same or No. was found to be greater than 1. The thermal shock test was conducted by intermittently high-frequency induction heating a test piece with a diameter of 2 views and a length of 5 views at a frequency of 450 KHz to generate heat cracks in the test piece. The test piece was heated to 700° C. for 8 seconds, immediately cooled with water, and subjected to this thermal shock repeatedly until cracking occurred. A platinum-platinum rhodium thermocouple was welded to the surface of the test piece, and the temperature of the surface of the test piece was constantly measured. Thermal shock resistance was evaluated by the number of thermal shocks until cracking occurred.
The test piece of the present invention containing 1.3% or more of Si is different from the conventional No.
.. It was revealed that the thermal shock resistance was superior to that of No. 1. The figure is a graphical representation of the test results shown in Table 2.

横軸にSi量をとり、縦軸に各種特性をとった。これよ
りSi量の影響をつかむことができる。図中、Sio.
5%の線上に記録されている特性はCo入り高速度工具
鋼試験片No.1のものである。硬さは、Si量が2.
1%まではSi量の増加につれて増加し、それ以後は減
少する懐向にある。No.1より高い硬さはSil%以
上で得られている。耐摩耗性も前記硬さのときと同じ傾
向があり、Sj2.1%までは摩耗量が減少するが、そ
れ以上になると増加する。Sil%でNo.1と同じ摩
耗量が得られ、それ以上であればNo.1よりも少なく
なる。曲げ試験における破断荷重とたわみ量は互に密接
に結びついている。破断荷重がいくら大きくてもたわみ
量が少なければ曲げ強さが大きいとは言えず、したがっ
て戦性がすぐれるとは言えない。図から、Si量が1〜
2.5%であればNo.1とほぼ同等の勤性が得られ、
特に1.3〜2.1%であればNo.1よりもすぐれた
鞠性が得られることが明らかである。耐熱衝撃性もSi
l%のときにNo.1と同等であり、Sil.3%以上
でNo.1よりもすぐれる。
The amount of Si is plotted on the horizontal axis, and various characteristics are plotted on the vertical axis. From this, the influence of the amount of Si can be grasped. In the figure, Sio.
The properties recorded on the 5% line are for Co-containing high-speed tool steel specimen no. 1. The hardness is determined when the amount of Si is 2.
It increases as the amount of Si increases up to 1%, and after that it tends to decrease. No. Hardnesses higher than 1 have been obtained at Sil% or higher. The abrasion resistance also shows the same tendency as in the case of the above-mentioned hardness, and the amount of wear decreases up to Sj 2.1%, but increases when it exceeds that. No. in Sil%. If the same amount of wear as No. 1 is obtained and it is greater than No. It will be less than 1. The breaking load and the amount of deflection in bending tests are closely related to each other. No matter how large the breaking load is, if the amount of deflection is small, it cannot be said that the bending strength is large, and therefore it cannot be said that the warpability is excellent. From the figure, the amount of Si is 1~
If it is 2.5%, it is No. Almost the same work efficiency as 1 can be obtained,
In particular, if it is 1.3 to 2.1%, it is No. It is clear that better ballability than No. 1 can be obtained. Thermal shock resistance is also Si
When 1%, No. 1 and is equivalent to Sil. No. 3% or more. Better than 1.

以上の実施例から明らかなように、本発明によれば従来
のCo入り高速度工具鋼ロールよりも高硬度、高耐塵性
を有し、鋤性も同等ないいますぐれているものを得るこ
とができる。特にSi量が1.3〜2.1%のときには
、靭性および耐熱衝撃性のうえでもCo入り高速度工具
鋼ロールよりもすぐれたものにすることができる。した
がって、本発明は冷間圧延用ロール、特にセンジマー圧
延機のワークロールとして最適である。
As is clear from the above examples, according to the present invention, it is possible to obtain a roll that has higher hardness and dust resistance than the conventional Co-containing high-speed tool steel roll, and has equivalent plowability. can. In particular, when the Si content is 1.3 to 2.1%, the roll can be made superior to Co-containing high-speed tool steel rolls in terms of toughness and thermal shock resistance. Therefore, the present invention is most suitable as a cold rolling roll, particularly as a work roll for a Sendzimer rolling mill.

【図面の簡単な説明】[Brief explanation of the drawing]

図は、冷間圧延用ロ・‐ルに要求される各種性質とSi
量との関係を示すグラフである。
The figure shows various properties required for cold rolling rolls and Si
It is a graph showing the relationship with quantity.

Claims (1)

【特許請求の範囲】[Claims] 1 重量%で炭素1.3〜1.6%、マンガン0.6%
以下、クロム4〜6%、モリブデン4〜6%、タングス
テン4〜6%、バナジウム3.5〜6%、けい素1.3
〜2.5%、残部鉄からなり、鍛造および焼入れ焼もど
し処理を施して焼もどしマルテンサイトと残留オーステ
ナイトおよび炭化物からなる組織とした鍛鋼によって一
体に構成されたことを特徴とする冷間圧延用鍛鋼焼入ロ
ール。
1% by weight: carbon 1.3-1.6%, manganese 0.6%
Below, chromium 4-6%, molybdenum 4-6%, tungsten 4-6%, vanadium 3.5-6%, silicon 1.3
~2.5%, the balance being iron, for cold rolling, characterized by being integrally constructed of forged steel that has been forged, quenched and tempered to have a structure consisting of tempered martensite, retained austenite and carbides. Forged steel hardened roll.
JP8264979A 1979-07-02 1979-07-02 Forged steel quenching roll for cold rolling Expired JPS608298B2 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP8264979A JPS608298B2 (en) 1979-07-02 1979-07-02 Forged steel quenching roll for cold rolling

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP8264979A JPS608298B2 (en) 1979-07-02 1979-07-02 Forged steel quenching roll for cold rolling

Publications (2)

Publication Number Publication Date
JPS569328A JPS569328A (en) 1981-01-30
JPS608298B2 true JPS608298B2 (en) 1985-03-01

Family

ID=13780269

Family Applications (1)

Application Number Title Priority Date Filing Date
JP8264979A Expired JPS608298B2 (en) 1979-07-02 1979-07-02 Forged steel quenching roll for cold rolling

Country Status (1)

Country Link
JP (1) JPS608298B2 (en)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2015521235A (en) * 2012-05-07 2015-07-27 ヴァルス ベジッツ ゲーエムベーハー Low temperature hard steel with excellent machinability

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS59153869A (en) * 1983-02-21 1984-09-01 Kanto Tokushu Seikou Kk Material for roll for rolling amorphous metal
JP2567166Y2 (en) * 1991-05-08 1998-03-30 理研機器開発株式会社 Boil and fry equipment
US5355932A (en) * 1992-03-06 1994-10-18 Hitachi Metals, Ltd. Method of producing a compound roll
JP7328606B2 (en) * 2021-08-03 2023-08-17 日本製鉄株式会社 Forged steel roll for cold rolling

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2015521235A (en) * 2012-05-07 2015-07-27 ヴァルス ベジッツ ゲーエムベーハー Low temperature hard steel with excellent machinability

Also Published As

Publication number Publication date
JPS569328A (en) 1981-01-30

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