JP2002273506A - Work roll for cold rolling - Google Patents
Work roll for cold rollingInfo
- Publication number
- JP2002273506A JP2002273506A JP2001077363A JP2001077363A JP2002273506A JP 2002273506 A JP2002273506 A JP 2002273506A JP 2001077363 A JP2001077363 A JP 2001077363A JP 2001077363 A JP2001077363 A JP 2001077363A JP 2002273506 A JP2002273506 A JP 2002273506A
- Authority
- JP
- Japan
- Prior art keywords
- rolling
- roll
- outer layer
- work roll
- cold rolling
- 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.)
- Withdrawn
Links
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- Reduction Rolling/Reduction Stand/Operation Of Reduction Machine (AREA)
Abstract
Description
【0001】[0001]
【発明の属する技術分野】本発明は、鉄鋼の冷間圧延に
用いられる冷間圧延用ワークロールに関するものであ
る。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a work roll for cold rolling used for cold rolling of steel.
【0002】[0002]
【従来の技術】従来、鉄鋼の冷間圧延用ワークロールと
しては、エレクトロ・スラグ再溶解法にて単一材質の鋼
塊を製造し、鍛造工程を経て焼入れ焼戻し熱処理を実施
した所謂鍛造ロールが多く使用されていた。しかしなが
ら、前記従来の鍛造ロールにおいては、実ロールとし
て、主に耐摩耗性、研削性、および圧延トラブル時の耐
亀裂性等が生じ未だに十分なものでなく課題を有してい
た。かかる課題を解決する技術として、例えば特開平1
1−302777号公報に開示されている、この技術の
概要は、従来の製造法であるエレクトロ・スラグ再溶解
・鍛造法での製法に替えて連続鋳掛肉盛法を採用し、凝
固速度の緻密な制御により晶出炭化物の結晶粒径を微細
化して圧延中のロール表面の粗度保持を格段と向上させ
ると共に、化学成分であるCのCbalをある範囲に規
定することにより、研削性を一段と向上させるものであ
る。2. Description of the Related Art Conventionally, as a work roll for cold rolling of iron and steel, a so-called forging roll in which a steel ingot of a single material is manufactured by an electro-slag remelting method and then subjected to a quenching and tempering heat treatment through a forging process. Used a lot. However, in the conventional forging roll, as an actual roll, mainly abrasion resistance, grindability, crack resistance at the time of a rolling trouble, and the like are generated, which is still insufficient and has a problem. As a technique for solving such a problem, for example, Japanese Patent Application Laid-Open
The outline of this technique disclosed in Japanese Patent Application Laid-Open No. 1-302777 is that a continuous casting overlay method is adopted in place of the conventional manufacturing method of electro-slag remelting and forging, and the solidification rate is increased. By making the crystal grain size of the crystallized carbide finer by appropriate control, the roughness maintenance of the roll surface during rolling is remarkably improved, and the Cbal of C, which is a chemical component, is defined in a certain range, so that the grindability is further improved. It is to improve.
【0003】[0003]
【発明が解決しようとする課題】前記の通り、特開平1
1−302777号公報に記載の技術では、従来の技術
に対して圧延中のロール表面の粗度保持性および研削性
が大幅に向上し、実ロールとして大幅な性能向上を図れ
るものである。しかしながら、前記の特開平11−30
2777号公報に記載の技術においても、例えば要求さ
れる表面品質の高い材料を圧延する場合や圧延条件が一
段と過酷である圧延機で使用するには、更なる耐摩耗
性、耐粗度保持性および研削性が望まれている。かかる
従来技術の課題に鑑み、本発明の目的は、圧延条件が過
酷な圧延においても耐摩耗性、圧延中のロール表面の耐
粗度保持性および研削性を具備する冷間圧延用ワークロ
ールを提供することである。As described above, as described above,
According to the technology described in JP-A-1-302777, the roughness retention and the grindability of the roll surface during rolling are significantly improved as compared with the conventional technology, and the performance of the actual roll can be significantly improved. However, Japanese Patent Application Laid-Open No.
In the technology described in Japanese Patent No. 2777, for example, when rolling a material having a high required surface quality or using it in a rolling mill in which rolling conditions are more severe, further wear resistance and roughness retention are required. And grindability is desired. In view of the above problems of the prior art, an object of the present invention is to provide a work roll for cold rolling having abrasion resistance even in severe rolling conditions, resistance to roughness of the roll surface during rolling, and grindability. To provide.
【0004】[0004]
【課題を解決するための手段】上述したような問題を解
消するため、発明者らは鋭意検討した結果、圧延条件が
過酷な圧延においても耐摩耗性、圧延中のロール表面の
耐粗度保持性および研削性を具備する冷間圧延用ワーク
ロールの製造を可能とした。その発明の要旨とするとこ
ろは、以下の通りである。 (1)鋳鋼または鍛鋼からなる芯材の周囲に、連続鋳掛
肉盛法にて外層を形成してなり、前記外層材の化学成分
が重量%で、C:0.8〜2.0%、Si:0.2〜
2.0%、Mn:0.2〜2.0%、Cr:4.0〜1
0.0%、Mo:1.0〜6.0%、V:0.5〜3.
0%、W:0.5〜3.0%からなり、残部がFeおよ
び不可避的成分であり、かつ下記式のCbalを0.1
〜1.0からなる冷間圧延用ワークロールにおいて、前
記外層に、さらにTi,B,Mgの1種以上を0.02
〜0.50%含有したことを特徴とする冷間圧延用ワー
クロール。Cbal=C−(0.060Cr+0.06
3Mo+0.033W+0.235V)Means for Solving the Problems In order to solve the above-mentioned problems, the present inventors have conducted intensive studies. As a result, the present inventors have found that wear resistance is maintained even in rolling under severe rolling conditions, and that the surface roughness of the roll during rolling is maintained. It is possible to manufacture a cold rolled work roll having good grindability and grindability. The gist of the invention is as follows. (1) An outer layer is formed around a core material made of cast steel or forged steel by a continuous casting overlay method, wherein the chemical composition of the outer layer material is% by weight, C: 0.8 to 2.0%, Si: 0.2-
2.0%, Mn: 0.2-2.0%, Cr: 4.0-1
0.0%, Mo: 1.0-6.0%, V: 0.5-3.
0%, W: 0.5 to 3.0%, the balance being Fe and unavoidable components, and Cbal of the following formula being 0.1
1.0 or more of Ti, B, and Mg in the outer layer.
A work roll for cold rolling, characterized in that the work roll contains 0.50% to 0.50%. Cbal = C- (0.060Cr + 0.06
3Mo + 0.033W + 0.235V)
【0005】(2)外層の化学成分として、さらに質量
%で、Ni:0.1〜5.0%を含有したことを特徴と
する前記(1)記載の冷間圧延用ワークロール。 (3)外層表面が750以上のビッカース硬度と、70
0MPa以下の圧縮残留応力を有することを特徴とする
前記(1)または(2)記載の冷間圧延用ワークロール
である。(2) The work roll for cold rolling according to the above (1), wherein the outer layer further contains Ni: 0.1 to 5.0% by mass% as a chemical component. (3) The outer layer surface has a Vickers hardness of 750 or more;
The work roll for cold rolling according to the above (1) or (2), having a compressive residual stress of 0 MPa or less.
【0006】[0006]
【発明の実施の形態】ここで外層の成分を限定した理由
を以下に述べる。Cは硬さを得るための重要な元素であ
る。C量が0.8%より少ないと耐久性を向上させるた
めに有効な炭化物の晶出が少なく、さらに基地に固溶す
るCが不足し、焼入れによっても十分な基地硬さが得ら
れなくなると同時に、高合金化が難しくなる。一方、
2.0%を超えると炭化物が粗大化しその晶出量も過大
となり冷間圧延用ワークロールとして必要な均質性が保
てず、特に研削むらや研削時の引っ掻き状の小さな傷で
あるスクラッチ傷が生ずるため、その上限を2.0%と
した。DESCRIPTION OF THE PREFERRED EMBODIMENTS The reasons for limiting the components of the outer layer are described below. C is an important element for obtaining hardness. If the C content is less than 0.8%, the crystallization of carbides effective for improving durability is small, and furthermore, C dissolved in the matrix is insufficient, and sufficient base hardness cannot be obtained even by quenching. At the same time, high alloying becomes difficult. on the other hand,
If the content exceeds 2.0%, carbides become coarse and the amount of crystallization becomes excessive, so that the uniformity required for a work roll for cold rolling cannot be maintained, and particularly, scratches such as uneven grinding or small scratches during grinding. Therefore, the upper limit was set to 2.0%.
【0007】Si,Mnはともに脱酸効果を有し、同時
に溶湯の流動性の点から有効な元素であり、各々2.0
%以下の一般の高速度鋼に含まれている量を含有させ
る。しかし、0.2%以上あればその効果を奏するため
下限とする。Niは焼入れ性を向上させる効果を有す
る。特に直径の大きいロール等で大きい硬化深度が要求
される場合には、その要求に応じて添加するとよい。し
かし、5.0%を超えると残留オーステナイトが過剰と
なり、かえって高硬度が得られなくなるため、その上限
を5.0%とした。0.1%以上であれば、その効果を
奏するため下限とする。Si and Mn both have a deoxidizing effect and are effective elements at the same time in view of the fluidity of the molten metal.
% Or less contained in general high-speed steel. However, if the content is 0.2% or more, the effect is exhibited, so the lower limit is set. Ni has an effect of improving hardenability. In particular, when a large curing depth is required for a roll having a large diameter or the like, it may be added according to the requirement. However, if the content exceeds 5.0%, the retained austenite becomes excessive and high hardness cannot be obtained, so the upper limit is set to 5.0%. If it is 0.1% or more, the lower limit is set for achieving the effect.
【0008】CrはCと結合しM7 C3 型の硬い炭化物
を結晶粒界に晶出生成し、耐摩耗性を向上させると共に
圧延時に塑性流動しにくい強固な鋳造組織を生成する。
しかしながら、添加量が少ないとその効果が十分確保で
きず、一方、多過ぎると炭化物が粗大化し網目状に発達
し、組織の均質性、研削性が阻害されるとともに靱性が
低下する。そこで適正な範囲として4.0%以上10.
0%以下とした。MoはCrと同様に硬質のM2 C型も
しくはM6 C型炭化物が得られ、また高温で焼戻しを行
う場合、その二次硬化に強く寄与する元素である。1.
0%未満の場合、炭化物としての析出が不十分である。
しかし、6.0%を超えると網目状の粗大な炭化物とな
るため、その適正な範囲を1.0%以上6.0%以下と
した。[0008] Cr combines with C to form a hard carbide of M 7 C 3 type at crystal grain boundaries, thereby improving wear resistance and forming a strong cast structure which is less likely to plastically flow during rolling.
However, if the added amount is small, the effect cannot be sufficiently secured, while if too large, the carbides are coarsened and develop into a network, and the homogeneity and grindability of the structure are impaired and the toughness is reduced. Therefore, an appropriate range is 4.0% or more.
0% or less. Mo is a hard M 2 C-type or M 6 C-type carbide similar to Cr, and is an element that strongly contributes to the secondary hardening when tempering is performed at a high temperature. 1.
If it is less than 0%, precipitation as carbides is insufficient.
However, if the content exceeds 6.0%, coarse carbides having a network shape are formed. Therefore, the appropriate range is set to 1.0% or more and 6.0% or less.
【0009】Vは極めて硬く粒状のMC系炭化物を形成
するため耐摩耗性を向上させるために有用な元素であ
る。しかし、0.5%未満であるとその効果は小さく、
3.0%を超えるとMC系炭化物がスクラッチ傷の発生
原因となり研削性が阻害されるためその範囲を0.5%
以上3.0%以下とした。Ti,B,Mgの添加は晶出
炭化物、特にMC炭化物の晶出の生成核となり、これを
結晶粒内に分散させ、さらにM7 C3 型、M2 C型、も
しくはM6 C型炭化物により囲まれた結晶粒を、後述す
る連続鋳掛け法にて鋳造する作用と相乗化し、安定して
微細化する作用を有する。このように、Ti,B,Mg
を添加・含有させることは、本発明の最大の特徴であ
る。その添加量は、0.02%未満では十分な効果が得
られず、一方、これらの元素は、酸化傾向が強いため、
0.50%を超えると、かえって酸化系介在物の発生を
助長するために望ましくない。V is an element useful for forming extremely hard and granular MC-based carbides and improving wear resistance. However, if it is less than 0.5%, the effect is small,
If the content exceeds 3.0%, MC-based carbides cause scratches and impair the grindability.
It was set to not less than 3.0%. The addition of Ti, B, and Mg serves as nuclei for crystallization of crystallized carbides, particularly MC carbides, and disperses them in crystal grains, and further forms M 7 C 3 type, M 2 C type, or M 6 C type carbides. Has a synergistic effect with the action of casting the crystal grains surrounded by the above-described continuous casting method, which will be described later, and has an action of stably reducing the size. Thus, Ti, B, Mg
Is the greatest feature of the present invention. If the addition amount is less than 0.02%, a sufficient effect cannot be obtained. On the other hand, since these elements have a strong tendency to oxidize,
If it exceeds 0.50%, it is undesirable to promote the generation of oxidized inclusions.
【0010】Cbalの値は炭化物が存在する材質にお
いて炭化物と基地組織をバランスさせ、特に基地中の固
溶Cを制御する上で重要である。本発明材では前述の硬
質炭化物を適量晶出させ、さらに焼入れにより基地硬度
を確保する上でその値を0.1〜1.0とした。0.1
未満ではCの基地組織への固溶が少なく硬さが得られな
い。一方、1.0を超えると炭化物が多くなり研削性を
損なう。WはCrやMoと同様に硬い炭化物を生成する
ため、これらの元素と複合または置換して添加すること
も3.0%以下の範囲で有効である。0.5%以上添加
するとその効果を奏する。[0010] The value of Cbal is important for balancing the carbide and the matrix structure in the material in which the carbide exists, and particularly for controlling the solid solution C in the matrix. In the material of the present invention, an appropriate amount of the above-mentioned hard carbide is crystallized, and the value is set to 0.1 to 1.0 in order to secure the base hardness by quenching. 0.1
If it is less than 3, the solid solution of C in the base structure is so small that hardness cannot be obtained. On the other hand, if it exceeds 1.0, carbides increase and grindability is impaired. Since W produces hard carbides like Cr and Mo, it is effective to add or replace with these elements in a range of 3.0% or less. The effect is exerted when 0.5% or more is added.
【0011】本発明は耐摩耗性を向上させるため前記の
通り、硬質の晶出炭化物を利用することを最大の特徴の
一つとし、さらに基地組織の硬さをビッカース硬度で7
50以上とした。炭化物はVによるMC型あるいはCr
・Mo・WによるM7 C3 型、M2 C型、もしくはM6
C型を主として利用した。詳しくは、従来ロールの場
合、高い残留応力をも利用してショア硬度を管理指標と
していたが、耐摩耗性、粗度保持性、耐凹性についての
耐久性を確保し向上させる上では押し込み型の代表硬度
の一つであるビッカース硬度を管理指標として採用し7
50以上、望ましくは800以上とすることで耐久性の
向上を達成した。As described above, the present invention is characterized in that the use of hard crystallized carbide is one of the most important features in order to improve the wear resistance.
50 or more. Carbide is MC type by V or Cr
・ M 7 C 3 type, M 2 C type or M 6 by Mo ・ W
Type C was mainly used. In detail, in the case of conventional rolls, Shore hardness was used as a control index using high residual stress, but in order to secure and improve the durability of abrasion resistance, roughness retention, and dent resistance, push-in type Vickers hardness, one of the representative hardnesses of
The durability was improved by setting it to 50 or more, preferably 800 or more.
【0012】特に耐事故性を向上させるため高温で焼戻
しを実施し、外層表面で700MPa以下の低い圧縮残
留応力とした。その結果、従来一般的に管理指標として
採用されていた材料自身の性質に加え残留応力等が影響
する反発型の硬度であるショア硬度は従来ロールのよう
に95以上といった高い硬度とする必要はなく、例えば
90以下でもビッカース硬度を前記値以上にすれば十分
な耐久性の向上が図られ、さらに耐事故性も兼備され
た。また、圧延途中のロール表面の粗度を所定の範囲に
保持出来れば圧延操業が安定し、かつ長時間にわたり連
続して圧延作業ができ操業性が向上させることができ
る。Particularly, in order to improve accident resistance, tempering was performed at a high temperature, and a low compressive residual stress of 700 MPa or less was obtained on the outer layer surface. As a result, the Shore hardness, which is a rebound type hardness affected by residual stress and the like in addition to the properties of the material itself, which has conventionally been generally used as a management index, does not need to be as high as 95 or more as in the conventional roll. For example, if the Vickers hardness is 90 or less, if the Vickers hardness is not less than the above value, the durability is sufficiently improved, and the accident resistance is also provided. Further, if the roughness of the roll surface during rolling can be maintained within a predetermined range, the rolling operation is stable, and the rolling operation can be continuously performed for a long time, so that the operability can be improved.
【0013】そこで、本発明ロール材を外層表層材とし
て連続鋳掛け法にて鋳造し、圧延中のロール表面の粗度
保持性を格段に向上させた。これは、表面粗度と強い関
係がある鋳造組織を連続鋳掛け法の有する大きな凝固速
度により緻密なものに制御することにより達成される。
すなわち、本発明での連続鋳掛け法での鋳造と前記T
i,B,Mgの添加による作用の相乗化により共晶炭化
物で囲まれた結晶粒径は小さく緻密な鋳造組織を安定的
に達成でき、圧延作業が安定すると共に、圧延時のロー
ル表面粗度を小さく保つ美麗な圧延材表面を得ることが
できる。Therefore, the roll material of the present invention was cast as a surface material of the outer layer by a continuous casting method, and the roll surface roughness retention during rolling was remarkably improved. This is achieved by controlling the cast structure, which has a strong relationship with the surface roughness, to be dense by the high solidification rate of the continuous casting method.
That is, the casting by the continuous casting method of the present invention and the T
The synergistic effect of the addition of i, B, and Mg makes it possible to stably achieve a dense casting structure with a small crystal grain size surrounded by the eutectic carbide, thereby stabilizing the rolling operation and the roll surface roughness during rolling. And a beautiful rolled material surface can be obtained.
【0014】[0014]
【実施例】以下、本発明の実施例を従来材および比較材
と共に説明する。 (実施例1)本発明の実施例として表1に示す本発明材
No.1〜10、従来材No.11〜13、比較材N
o.14〜17について、ミクロ組織を調査比較した。
まず、試験片は、高周波誘導炉にて溶解した後、該溶湯
を、実際のロールと同等の凝固速度となるよう直径10
0mm、高さ300mmの砂型に注入し、その後、10
00℃からの焼入れ処理と、さらに500〜550℃の
焼戻し処理を施し、上記ミクロ組織調査用各種の試験片
を製作した。前記製作した各試験片から、画像解析装置
を使用して晶出炭化物量、結晶粒径、結晶粒内の炭化物
の分布、さらには硬度を測定した。その結果を表1に示
す。EXAMPLES Examples of the present invention will be described below together with conventional materials and comparative materials. (Example 1) As an example of the present invention, the material No. 1 of the present invention shown in Table 1 was used. No. 1 to 10, conventional material No. 11-13, comparative material N
o. Microstructures of 14 to 17 were investigated and compared.
First, the test piece was melted in a high-frequency induction furnace, and then the molten metal was cooled to a diameter of 10 so that the solidification rate was equivalent to that of an actual roll.
0mm, 300mm height sand mold, then 10
A quenching treatment from 00 ° C. and a tempering treatment at 500 to 550 ° C. were performed to produce various test pieces for microstructure examination. The amount of crystallized carbide, the crystal grain size, the distribution of carbide in the crystal grains, and the hardness were measured from each of the manufactured test pieces using an image analyzer. Table 1 shows the results.
【0015】[0015]
【表1】 [Table 1]
【0016】まず、本発明の耐摩耗性、圧延中のロール
表面の耐粗度保持性および研削性に大きく作用する結晶
粒径については、従来材の結晶粒径が約50μmである
のに比べ、Ti,B,Mgの1種以上を0.02〜0.
50%含有する本発明材の結晶粒径は全て40μm以下
で20〜30%小さくなり、緻密な組織が得られている
ことが明確である。また、炭化物の結晶粒内への分散も
十分であった。一方、比較材として示したTi,B,M
gの含有量は、本発明材と同じ範囲であるがCの量が本
発明材より少ない低C材では十分な炭化物量が得られ
ず、逆にCの量が多い高C材では炭化物量が増し本発明
の特徴の一つである炭化物の結晶粒内への分散も不十分
であった。以上のラボ試験の結果、本発明材の作用、効
果を十分に確認できたため、次に実際の圧延用ロールを
製作した。以下に説明する。First, the grain size of the present invention, which greatly affects the wear resistance, the retention of roughness of the roll surface during rolling, and the grindability, is smaller than that of the conventional material having a grain size of about 50 μm. , Ti, B, Mg at least one of 0.02 to 0.2.
It is clear that the crystal grain size of the material of the present invention containing 50% is reduced by 20 to 30% when the crystal grain size is 40 μm or less, and a dense structure is obtained. In addition, the dispersion of the carbide in the crystal grains was also sufficient. On the other hand, Ti, B, M shown as comparative materials
The content of g is in the same range as the material of the present invention, but a sufficient amount of carbide cannot be obtained with a low C material in which the amount of C is smaller than that of the material of the present invention. In addition, the dispersion of the carbide in the crystal grains, which is one of the features of the present invention, was insufficient. As a result of the above lab test, the operation and effect of the material of the present invention were sufficiently confirmed. Next, an actual rolling roll was manufactured. This will be described below.
【0017】(実施例2)本発明の実施例として、表2
に示す化学成分を外層材とし、鋼系芯材との組み合わせ
により連続鋳掛け法にて、胴径φ550mm、胴長15
00mm、全長3500mmの冷延用複合ワークロール
を鋳造した。鋳造後、軟化焼鈍を施し、粗加工実施後、
炭化物の分断を目的として調質処理を行った。その後、
焼入れは表面温度950〜1100℃にて漸進誘導加熱
・水焼入れにより行った。さらに、焼き戻しは450〜
600℃で実施した。前記の圧延用ロールの一部より試
験片を採取し、前記のラボ試験と同様に、画像解析装置
を使用して晶出炭化物量、結晶粒径、結晶粒内の炭化物
の分布、さらには硬度を測定した。その結果を表3に示
す。表から明らかなように、本実機ロールでの結果、つ
まり、晶出炭化物量、結晶粒径、結晶粒内の炭化物の分
布、さらには硬度等は、いずれも前記の本発明のラボテ
ストの結果と同様な良好な結果を示しており、本発明材
の作用、効果を実機ロールにおいて確証することができ
た。(Embodiment 2) As an embodiment of the present invention, Table 2
The outer layer is made of the chemical components shown in the above, and the body diameter φ550 mm, the body length 15
A composite work roll for cold rolling of 00 mm and a total length of 3500 mm was cast. After casting, subjected to soft annealing, after rough processing,
A tempering treatment was performed for the purpose of separating carbides. afterwards,
Quenching was performed by progressive induction heating and water quenching at a surface temperature of 950 to 1100 ° C. Furthermore, tempering is 450 ~
Performed at 600 ° C. A test piece was taken from a part of the rolling roll, and the amount of crystallized carbide, the crystal grain size, the distribution of carbide in the crystal grain, and the hardness were also measured using an image analyzer in the same manner as in the lab test. Was measured. Table 3 shows the results. As is clear from the table, the results with the actual machine roll, that is, the amount of crystallized carbides, the crystal grain size, the distribution of carbides in the crystal grains, and further the hardness, etc. are all the same as the results of the lab test of the present invention described above. The same good result was shown, and the operation and effect of the material of the present invention could be confirmed on the actual roll.
【0018】[0018]
【表2】 [Table 2]
【0019】[0019]
【表3】 [Table 3]
【0020】また、表3には、実機ロールを実際の冷間
圧延に供した結果を示す。表3に示す結果から明らかな
ように、該ロールの使用前の研削作業は必要な表面粗度
が比較的大きな前段圧延機用から、順次小さな中段圧延
機用、後段圧延機用としてのそれぞれの条件で有害なス
クラッチ傷を生じることなく可能であった。さらに、実
際の冷延に供した場合、従来の鍛造ロールが約500ト
ンの製品を圧延後に必要な表面粗度が確保できずに圧延
作業を中断してロールを取り替えていたのに対し、該ロ
ールは連続して3000トン以上を粗度が低下すること
なく圧延が可能であった。Table 3 shows the results of actual rolls subjected to actual cold rolling. As is evident from the results shown in Table 3, the grinding work before use of the rolls was performed for the first-stage rolling mill having a relatively large required surface roughness, for the successively smaller middle-stage rolling mill, and for the second-stage rolling mill. This was possible without harmful scratches under the conditions. Furthermore, in the case of actual cold rolling, the conventional forging roll was unable to secure the required surface roughness after rolling a product of about 500 tons, and the rolling operation was interrupted and the roll was replaced. The roll could be continuously rolled to 3000 tons or more without lowering the roughness.
【0021】また、前記従来例として示した特開平11
−302777号公報に記載のロールについては、特に
厳格な品質の製品を圧延する際に、例えば後段圧延機用
等としては十分満足できるものではなかったが、該ロー
ルはミルの制約なく安定して使用が可能となり、圧延作
業での生産性が著しく向上した。なお、圧延時の事故に
遭遇した際の亀裂の発生もなく、ロールの性能として代
表的な耐摩耗性は従来の鍛造ロールの6倍以上に向上し
た。Further, Japanese Patent Application Laid-Open No.
With regard to the roll described in JP-A-302777, particularly when rolling a product of strict quality, it was not sufficiently satisfactory, for example, for a subsequent rolling mill, etc. It became possible to use it, and productivity in the rolling operation was remarkably improved. In addition, there was no generation of cracks when encountering an accident during rolling, and the typical wear resistance of the roll was improved to at least six times that of a conventional forged roll.
【0022】[0022]
【発明の効果】以上述べたように、本発明の圧延ロール
は、適度な晶出炭化物量を有し、結晶粒径は小さく、ま
た結晶粒内に炭化物が分散して分布されており、要求さ
れる表面品質の高い材料を圧延する場合や圧延条件が一
段と過酷である圧延機で使用しても優れた耐摩耗性、圧
延中のロール表面の耐粗度保持性および研削性を兼備す
ることが可能となり冷間圧延の生産性の向上に大きく貢
献するものである。As described above, the rolling roll of the present invention has an appropriate amount of crystallized carbide, a small crystal grain size, and carbides dispersed and distributed in the crystal grains. When used for rolling materials with high surface quality or used in rolling mills where rolling conditions are more severe, it must have both excellent wear resistance, roughness retention of the roll surface during rolling, and grindability. This greatly contributes to improving the productivity of cold rolling.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 FI テーマコート゛(参考) C22C 38/58 C22C 38/58 Fターム(参考) 4E016 CA04 CA09 EA03 EA22 EA23 FA01 ──────────────────────────────────────────────────の Continued on the front page (51) Int.Cl. 7 Identification FI theme coat ゛ (reference) C22C 38/58 C22C 38/58 F term (reference) 4E016 CA04 CA09 EA03 EA22 EA23 FA01
Claims (3)
連続鋳掛肉盛法にて外層を形成してなり、前記外層材の
化学成分が重量%で、 C:0.8〜2.0%、 Si:0.2〜2.0%、 Mn:0.2〜2.0%、 Cr:4.0〜10.0%、 Mo:1.0〜6.0%、 V:0.5〜3.0%、 W:0.5〜3.0% からなり、残部がFeおよび不可避的成分であり、かつ
下記式のCbalを0.1〜1.0からなる冷間圧延用
ワークロールにおいて、前記外層に、さらにTi,B,
Mgの1種以上を0.02〜0.50%含有したことを
特徴とする冷間圧延用ワークロール。 Cbal=C−(0.060Cr+0.063Mo+
0.033W+0.235V)1. Around a core material made of cast steel or forged steel,
An outer layer is formed by a continuous casting overlaying method, and the chemical composition of the outer layer material is% by weight: C: 0.8 to 2.0%, Si: 0.2 to 2.0%, Mn: 0 0.2 to 2.0%, Cr: 4.0 to 10.0%, Mo: 1.0 to 6.0%, V: 0.5 to 3.0%, W: 0.5 to 3.0% %, The balance being Fe and an unavoidable component, and Cbal of the following formula being 0.1 to 1.0 in a cold-rolling work roll, wherein Ti, B,
A work roll for cold rolling, comprising 0.02 to 0.50% of at least one kind of Mg. Cbal = C- (0.060Cr + 0.063Mo +
0.033W + 0.235V)
で、Ni:0.1〜5.0%を含有したことを特徴とす
る請求項1記載の冷間圧延用ワークロール。2. The chemical composition of the outer layer further comprises:
The work roll for cold rolling according to claim 1, wherein the content of Ni is 0.1 to 5.0%.
と、700MPa以下の圧縮残留応力を有することを特
徴とする請求項1または2記載の冷間圧延用ワークロー
ル。3. The work roll for cold rolling according to claim 1, wherein the outer layer surface has a Vickers hardness of 750 or more and a compressive residual stress of 700 MPa or less.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2001077363A JP2002273506A (en) | 2001-03-19 | 2001-03-19 | Work roll for cold rolling |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2001077363A JP2002273506A (en) | 2001-03-19 | 2001-03-19 | Work roll for cold rolling |
Publications (1)
Publication Number | Publication Date |
---|---|
JP2002273506A true JP2002273506A (en) | 2002-09-25 |
Family
ID=18934128
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP2001077363A Withdrawn JP2002273506A (en) | 2001-03-19 | 2001-03-19 | Work roll for cold rolling |
Country Status (1)
Country | Link |
---|---|
JP (1) | JP2002273506A (en) |
-
2001
- 2001-03-19 JP JP2001077363A patent/JP2002273506A/en not_active Withdrawn
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