JP2002220635A - Single-layer sleeve roll for hot rolling made with centrifugal casting - Google Patents
Single-layer sleeve roll for hot rolling made with centrifugal castingInfo
- Publication number
- JP2002220635A JP2002220635A JP2001015029A JP2001015029A JP2002220635A JP 2002220635 A JP2002220635 A JP 2002220635A JP 2001015029 A JP2001015029 A JP 2001015029A JP 2001015029 A JP2001015029 A JP 2001015029A JP 2002220635 A JP2002220635 A JP 2002220635A
- Authority
- JP
- Japan
- Prior art keywords
- roll
- sleeve roll
- resistance
- hot rolling
- hardness
- 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.)
- Granted
Links
Landscapes
- 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、例えば鉄鋼の熱間
圧延に用いられ、特に耐摩耗性、耐肌荒れ性および耐割
損性に優れた熱間圧延用スリーブ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 sleeve roll for hot rolling, which is used, for example, for hot rolling of steel, and is particularly excellent in wear resistance, surface roughening resistance and breakage resistance.
【０００２】[0002]
【従来の技術】近年、鉄鋼の熱間圧延分野においては、
特にＨ形鋼等の形鋼圧延において、スリーブロールが多
用されており、外層材には高Ｃ％アダマイト材、内層材
としては、球状黒鉛鋳鉄、黒鉛鋼、アダマイト材が使用
されてきた。また、圧延製品の品質向上の要求が高く、
圧延用スリーブロールに対しても、高い耐摩耗性、耐肌
荒れ性および耐クラック性等が求められてきている。こ
れらの要求に対して、形鋼圧延用スリーブロールとして
は、特公平５−１４０２３号公報や特許第２６０１７４
６号に開示されている。2. Description of the Related Art In recent years, in the field of hot rolling of steel,
In particular, sleeve rolls are frequently used in rolling section steel such as H-section steel, and a high C% adamite material has been used as an outer layer material, and spheroidal graphite cast iron, graphite steel, and adamite material have been used as an inner layer material. In addition, there is a high demand for quality improvement of rolled products,
Rolling sleeve rolls are also required to have high wear resistance, rough surface resistance, crack resistance, and the like. To meet these requirements, sleeve rolls for rolling section steel are disclosed in Japanese Patent Publication No. 5-14023 and Japanese Patent No. 260174.
No. 6 discloses.
【０００３】特公平５−１４０２３号公報の技術内容
は、外層材には従来から知られている高炭素アダマイト
系の材料を、内層材には、焼ばめ芯力や圧延時の発生応
力に耐え得るだけの強靱性を満足させるために、特殊鋳
鋼材質を採用し、両者を溶着させた複合スリーブロール
である。しかしながら、この技術では、内層材の方が低
Ｃ材質となっているため、外層材より内層材の方が凝固
点が高いことに起因する鋳造欠陥が、外内層境界部付近
に発生する危険性が極めて高く、また、異種材料を組み
合わせた複合構造となっているため、過大な残留応力が
発生しやすい。従って、これらが原因で、圧延時にクラ
ックが発生し、スリーブロールの割損に至るという問題
がある。[0003] The technical content of Japanese Patent Publication No. 5-14023 is that a conventionally known high-carbon adamite-based material is used for an outer layer material, and a shrink-fit core force and a stress generated during rolling are used for an inner layer material. This is a composite sleeve roll that uses special cast steel material and welds both to satisfy the toughness that can withstand. However, in this technique, since the inner layer material has a lower C material, there is a risk that a casting defect due to a higher solidification point of the inner layer material than the outer layer material may occur near the outer inner layer boundary. Since it is extremely high and has a composite structure combining different materials, excessive residual stress is likely to occur. Accordingly, there is a problem that cracks occur during rolling due to these factors, leading to breakage of the sleeve roll.
【０００４】また、特許第２６０１７４６号の技術内容
は、耐摩耗性を重視して、外層材にはＶを３．０％以上
含有させた高合金系の鋳鋼、鋳鉄を、内層材には強靱性
に富む黒鉛鋼を適用した複合スリーブロールである。し
かしながら、この特許第２６０１７４６号に開示されて
いる複合スリーブロールは、外層材が耐摩耗性を重視し
てＶを３．０％以上含有した高合金系の鋳鋼、鋳鉄材料
であるため、強靱性が確保できず、特公平５−１４０２
３号公報の技術と同様に内層材に異種材料を組み合わせ
た複合構造となっている。さらに、外層材が高合金系の
材料であるため、熱処理時の変態膨張量が大きく、極め
て大きな残留応力が発生する。従って、鋼材の熱間圧延
に使用すると、過大な残留応力と焼きばめ応力に圧延時
に発生する熱応力と圧延応力が重畳した応力の合計がス
リーブロールの材力を超過して、スリーブロールが割損
に至る危険性が極めて高く、実際に、この技術は熱間圧
延用スリーブロールとして、適用が殆ど進んでいない状
況にある。The technical content of Japanese Patent No. 2601746 is based on the importance of wear resistance. The outer layer material is made of a high alloy cast steel or cast iron containing 3.0% or more of V, and the inner layer material is made of tough material. This is a composite sleeve roll to which graphite steel with high properties is applied. However, the composite sleeve roll disclosed in Japanese Patent No. 2601746 is a high alloy cast steel or cast iron material in which the outer layer material contains V at 3.0% or more with emphasis on abrasion resistance. Could not be secured,
As in the technique disclosed in Japanese Patent Application Laid-Open No. 3-3, a composite structure is provided in which different materials are combined with the inner layer material. Furthermore, since the outer layer material is a high alloy material, the amount of transformation expansion during heat treatment is large, and an extremely large residual stress is generated. Therefore, when used for hot rolling of steel materials, the sum of the stress obtained by superimposing the thermal stress and rolling stress generated during rolling on excessive residual stress and shrink fit stress exceeds the material strength of the sleeve roll, and the sleeve roll becomes The risk of breakage is extremely high, and in fact, this technology is in a situation where its application as a sleeve roll for hot rolling has hardly progressed.
【０００５】[0005]
【発明が解決しようとする課題】以上のように、複合ス
リーブロールの場合、その構造は、外内層境界近傍にお
ける鋳造欠陥と過大な残留応力が避け難い状況にあっ
た。また、耐摩耗性を向上させるために外層材の高合金
化を図ると、さらに残留応力が過大となる。従って、複
合スリーブロールという構造では、外層材の高合金化に
よる耐摩耗性、耐肌荒れ性の向上と耐割損性の両立には
限界があった。As described above, in the case of the composite sleeve roll, the structure is such that casting defects and excessive residual stress near the boundary between the outer and inner layers are inevitable. Further, if the outer layer material is made to be highly alloyed in order to improve the wear resistance, the residual stress is further increased. Therefore, in the structure of the composite sleeve roll, there is a limit in improving wear resistance and skin roughening resistance by combining the outer layer material with a high alloy, and attaining crack resistance.
【０００６】本発明は、このような従来のスリーブロー
ルが有する課題に鑑みてなされたものであり、Ｃｕおよ
びＢ，Ａｌの微量複合添加とＶ，Ｎｂを粒状ＭＣ共晶炭
化物晶出範囲で適量添加することで、耐摩耗性、耐肌荒
れ性および、従来の複合スリーブロールの内層材と同等
の強靱性を兼備した材質を提供することにより、外内層
を同一材質とした単層構造のスリーブロールの製造を可
能とさせ、外内層境界に発生していた鋳造欠陥の完全な
防止と、スリーブロールの径方向の硬度差をショア硬度
換算で、１０度以内とすることで、残留応力の大幅な低
減を図り、耐割損性の大幅な向上と耐摩耗性、耐肌荒れ
性の向上を両立させた熱間圧延用スリーブロールを提供
することを目的とする。The present invention has been made in view of the above-mentioned problems of the conventional sleeve roll, and has a small amount of complex addition of Cu, B, and Al, and an appropriate amount of V, Nb in the range of crystallization of particulate MC eutectic carbide. A single-layered sleeve roll with the same outer and inner layers by providing a material that has the same abrasion resistance, rough surface resistance, and toughness as the inner layer material of conventional composite sleeve rolls. By completely preventing casting defects that occurred at the boundary between the outer and inner layers, and by setting the radial hardness difference of the sleeve roll within 10 degrees in Shore hardness conversion, the residual stress can be significantly reduced. It is an object of the present invention to provide a sleeve roll for hot rolling that achieves both reduction in breakage resistance and significant improvement in wear resistance and surface roughness resistance.
【０００７】[0007]
【課題を解決するための手段】本発明は上述した問題を
解消したもので、その発明の要旨とするところは、 （１）化学成分が質量％で、Ｃ：１．０〜２．５％、Ｓ
ｉ：０．２〜２．５％、Ｍｎ：０．２〜２．０％、Ｎ
ｉ：０．２〜３．０％、Ｃｒ：０．５〜１５．０％、Ｍ
ｏ：０．１〜８．０％、Ｂ：０．００１〜０．５０％、
Ａｌ：０．００１〜０．５０％、Ｃｕ；０．００１〜
０．５０％を含有し、さらに、Ｖ：０．２〜１．９％、
Ｎｂ：０．２〜３．０％の１種または２種、残部Ｆｅ及
び不可避的不純物からなる単一材質のスリーブロールで
あって、焼入れ後のスリーブロールの径方向の硬度差を
ショア硬度で１０度以内としたことを特徴とする遠心鋳
造製熱間圧延用単層スリーブロール。 （２）化学成分としてさらに、質量％で、Ｗ：０．１〜
１０．０％、Ｔｉ：０．００１〜０．５０％、Ｃｏ：
０．１〜５．０％の１種または２種以上含有する請求項
１記載の遠心鋳造製熱間圧延用単層スリーブロールにあ
る。Means for Solving the Problems The present invention has solved the above-mentioned problems. The gist of the present invention is as follows: (1) The chemical component is mass% and C: 1.0 to 2.5% , S
i: 0.2 to 2.5%, Mn: 0.2 to 2.0%, N
i: 0.2 to 3.0%, Cr: 0.5 to 15.0%, M
o: 0.1 to 8.0%, B: 0.001 to 0.50%,
Al: 0.001 to 0.50%, Cu; 0.001 to
0.50%, V: 0.2-1.9%,
Nb: One or two kinds of 0.2 to 3.0%, the balance being Fe and inevitable impurities, a single material sleeve roll, and the hardness difference in the radial direction of the quenched sleeve roll is represented by Shore hardness. A single-layer sleeve roll for hot rolling made by centrifugal casting, wherein the temperature is within 10 degrees. (2) Further, as a chemical component, in mass%, W: 0.1 to
10.0%, Ti: 0.001 to 0.50%, Co:
The single-layer sleeve roll for hot rolling by centrifugal casting according to claim 1, which contains one or more of 0.1 to 5.0%.
【０００８】以下、本発明について詳細に説明する。従
来技術による熱間圧延用スリーブロールの外層材に適用
されている高炭素アダマイト材のミクロ組織は、一般的
に適度な熱処理を施してベイナイトもしくはパーライト
となったマトリックス組織と、Ｍ3 ＣあるいはＭ7 Ｃ3
型共晶炭化物で構成されている。本発明では、強度劣化
の主因となっているＭ3 ＣあるいはＭ7Ｃ3 型共晶炭化
物の均一・微細分散化を図るために、Ｂ，Ａｌを微量に
複合添加することが有効であることを見出した。Hereinafter, the present invention will be described in detail. The microstructure of a high-carbon adamite material applied to the outer layer material of a sleeve roll for hot rolling according to the prior art generally includes a matrix structure that has been subjected to an appropriate heat treatment to be bainite or pearlite, and M 3 C or M 3 7 C 3
It is composed of a type eutectic carbide. In the present invention, it is effective to add a small amount of B and Al in combination in order to uniformly and finely disperse the M 3 C or M 7 C 3 type eutectic carbide which is the main cause of the strength deterioration. Was found.
【０００９】また、Ｖ，Ｎｂの適量（各０．２〜３．０
％）添加により、ネット状に晶出したＭ3 ＣあるいはＭ
7 Ｃ3 型共晶炭化物の一部を、粒状のＭＣ型共晶炭化物
に置換させることで、耐摩耗性、耐肌荒れ性および強靱
性を大きく向上させることが可能であることを見出し
た。さらに、Ｃｕを微量に含有させることで、マトリッ
クス組織の強化も図ることで、熱間圧延用スリーブロー
ル材として、優れた耐摩耗性、耐肌荒れ性および強靱性
を兼備させるものである。この材質のみで形成された単
層の熱間圧延用スリーブロールは、耐摩耗性、耐肌荒れ
性と耐割損性を兼備している。Further, an appropriate amount of V and Nb (0.2 to 3.0 each)
%), M 3 C or M
Some of the 7 C 3 type eutectic carbides, by replacing the MC-type eutectic carbides granular, abrasion resistance, and found that it is possible to greatly improve the surface roughening resistance and toughness. Further, by containing a trace amount of Cu, the matrix structure is strengthened, and as a sleeve roll material for hot rolling, excellent wear resistance, rough surface resistance and toughness are achieved. A single-layer sleeve roll for hot rolling made of only this material has both abrasion resistance, surface roughness resistance and splitting resistance.
【００１０】[0010]
【発明の実施の形態】以下に、本発明に係る各化学成分
の限定理由について述べる。 Ｃ：１．０〜２．５％ Ｃは、主として黒鉛およびＦｅ，Ｃｒ，Ｍｏ，Ｎｂ，
Ｖ，Ｗ等と結合して種々の炭化物を形成する。また、マ
トリックス中に固溶されベイナイトやマルテンサイト相
を生成する。多量に含有させるほど、耐摩耗性の向上に
有効であるが、２．５％を超えると本発明の特徴であ
る、Ｂ，Ａｌを微量に含有させても共晶炭化物が粗大に
晶出し、均一・微細分散化が図れないことより、その上
限を２．５％とした。また、１．０％未満になると、炭
化物が少なく、耐摩耗性の劣化が起こるため下限をこの
値にした。BEST MODE FOR CARRYING OUT THE INVENTION The reasons for limiting each chemical component according to the present invention will be described below. C: 1.0 to 2.5% C is mainly graphite and Fe, Cr, Mo, Nb,
Combines with V, W, etc. to form various carbides. Further, they are dissolved in the matrix to form a bainite or martensite phase. The larger the content, the more effective in improving the abrasion resistance. However, if it exceeds 2.5%, the eutectic carbides are coarsely crystallized even when a small amount of B or Al is contained, which is a feature of the present invention. Since uniform and fine dispersion cannot be achieved, the upper limit is set to 2.5%. When the content is less than 1.0%, the amount of carbides is small, and the wear resistance is deteriorated. Therefore, the lower limit is set to this value.
【００１１】Ｓｉ：０．２〜２．５％ Ｓｉは、脱酸作用を目的として添加する。しかし、０．
２％未満であるとその効果が不十分であり、逆に、２．
５％を超える添加は靱性を低下させるため、その範囲を
０．２〜２．５％とする。 Ｍｎ：０．２〜２．０％ Ｍｎは、脱酸、脱硫作用を目的として添加する。しか
し、０．２％未満であるとその効果が不十分であり、ま
た、２．０％を超えると靱性を低下させるため、その範
囲を０．２〜２．０％とする。Si: 0.2-2.5% Si is added for the purpose of deoxidizing. However, 0.
If the content is less than 2%, the effect is insufficient.
Since the addition exceeding 5% lowers the toughness, the range is set to 0.2 to 2.5%. Mn: 0.2 to 2.0% Mn is added for the purpose of deoxidation and desulfurization. However, if it is less than 0.2%, the effect is insufficient, and if it exceeds 2.0%, the toughness is reduced, so the range is made 0.2 to 2.0%.
【００１２】Ｎｉ：０．２〜３．０％ Ｎｉは、焼入性の向上と靱性の確保のために添加する。
しかし、０．２％未満では、それらの効果が弱く、一
方、３．０％を超えると焼入性および靱性の効果が飽和
するので、この範囲を０．２〜３．０％とする。 Ｃｒ：０．５〜１５．０％ Ｃｒは、焼入性の増加、硬度の増加、焼き戻し軟化抵抗
の増加、炭化物硬度の安定化等のために添加する。しか
し、１５．０％を超えると共晶炭化物量が、増え過ぎ靱
性が低下するため、その上限を１５．０％とした。一
方、０．５％未満だと前記添加する効果が得られない。
従って、その範囲を０．５〜１５．０％とする。Ni: 0.2-3.0% Ni is added for improving hardenability and ensuring toughness.
However, if it is less than 0.2%, their effects are weak, while if it exceeds 3.0%, the effects of hardenability and toughness are saturated, so this range is made 0.2-3.0%. Cr: 0.5 to 15.0% Cr is added for increasing hardenability, increasing hardness, increasing tempering softening resistance, stabilizing carbide hardness, and the like. However, if the content exceeds 15.0%, the eutectic carbide content increases too much and the toughness is reduced. Therefore, the upper limit is set to 15.0%. On the other hand, if it is less than 0.5%, the effect of the addition cannot be obtained.
Therefore, the range is set to 0.5 to 15.0%.
【００１３】Ｍｏ：０．１〜８．０％ Ｍｏは、マトリックス中に固溶されて焼入性、硬度、焼
き戻し軟化抵抗等を増加させるとともに、Ｃと結合して
Ｍ2 ＣやＭ6 Ｃ等の共晶炭化物を形成し耐摩耗性を向上
させるために添加する。しかし、８．０％を超えると共
晶炭化物が増え過ぎて靱性が低下するため、その上限を
８．０％とした。一方、０．１％未満では前記添加する
効果が得られない。 Ｂ：０．００１〜０．５０％ Ｂは、０．００１％以上で、焼入れ性が高まり、また、
靱性の低下を防ぐとともに、晶出する炭化物を均一微細
分散化させる効果がある。しかし、過剰になると、靱性
が低下するため、０．５０％以下に抑える必要がある。
従って、その範囲を０．００１〜０．５０％とする。Mo: 0.1-8.0% Mo is solid-dissolved in a matrix to increase hardenability, hardness, temper softening resistance, etc., and combine with C to form M 2 C or M 6. C is added to form a eutectic carbide such as C to improve wear resistance. However, if the content exceeds 8.0%, the eutectic carbides increase too much and the toughness is reduced. Therefore, the upper limit is set to 8.0%. On the other hand, if it is less than 0.1%, the effect of the addition cannot be obtained. B: 0.001 to 0.50% B is 0.001% or more, the hardenability increases, and
This has the effect of preventing a decrease in toughness and uniformly and finely dispersing the crystallized carbide. However, if it is excessive, the toughness is reduced, so it is necessary to suppress the content to 0.50% or less.
Therefore, the range is set to 0.001 to 0.50%.
【００１４】Ａｌ：０．００１〜０．５０％ Ａｌは、溶湯中で酸化物を生成して、溶湯中の酸素含有
量を低下させ、製品の健全性を向上させる共に、生成し
た酸化物が結晶核として作用するために凝固組織の均一
・微細化に効果がある。０．００１％でその効果がある
が、余り多く含有させると、介在物となって製品中に残
存することになるため、その上限は０．５０％となるよ
うにする。 Ｃｕ：０．００１〜０．５０％ Ｃｕは、基地組織を強化し高温硬度を向上させるため、
前述したＢ，Ａｌ等と共に本発明の主要な化学成分であ
る。０．００１％以下では、その効果がなく、一方、
０．５０％を超えると、耐摩耗性、耐クラック性が低下
すると共にロールの表面性状が劣化するため、その上限
を０．５０％とする。Al: 0.001 to 0.50% Al forms an oxide in the molten metal, lowers the oxygen content in the molten metal, improves the soundness of the product, and improves the soundness of the product. Since it acts as a crystal nucleus, it is effective in making the solidification structure uniform and fine. The effect is 0.001%, but if contained too much, it will become an inclusion and remain in the product, so the upper limit is made 0.50%. Cu: 0.001 to 0.50% Cu strengthens the base structure and improves the high-temperature hardness.
It is a main chemical component of the present invention together with B, Al and the like described above. If it is less than 0.001%, there is no effect.
If it exceeds 0.50%, the abrasion resistance and crack resistance are reduced and the surface properties of the roll are deteriorated. Therefore, the upper limit is set to 0.50%.
【００１５】Ｖ：０．２〜１．９％ Ｖは、Ｃと結合して高硬度のＭＣ型炭化物を形成する重
要な元素である。しかし、１．９％未満の場合、晶出す
るＭＣ型炭化物の形状が粒状となるため、ネット状に晶
出したＭ3 ＣあるいはＭ7 Ｃ3 型共晶炭化物の一部を、
この粒状ＭＣ型共晶炭化物に置換させることで、耐摩耗
性、耐肌荒れ性および強靱性を大きく向上させることが
できる。また、マトリックスにも固溶して基地を強化す
る。基地強化のためには、最低０．２％以上の含有量が
必要である。一方、１．９％を超えると、晶出するＭＣ
炭化物の形状が粗大なデンドライト状になるため、強靱
性が劣化する。従って、その範囲を０．２〜１．９％と
する。V: 0.2-1.9% V is an important element that combines with C to form MC-type carbide with high hardness. However, if it is less than 1.9%, the MC-type carbide to be crystallized becomes granular, so that a part of the net-shaped M 3 C or M 7 C 3 -type eutectic carbide is
By substituting the particulate MC type eutectic carbide, abrasion resistance, surface roughening resistance and toughness can be greatly improved. It also forms a solid solution in the matrix to strengthen the matrix. To strengthen the base, a content of at least 0.2% or more is required. On the other hand, when it exceeds 1.9%, MC
Since the carbide has a coarse dendrite shape, the toughness deteriorates. Therefore, the range is set to 0.2 to 1.9%.
【００１６】Ｎｂ：０．２〜３．０％ Ｎｂは、マトリックス中に殆ど固溶されず、その殆どが
高硬度で粒状のＭＣ型炭化物を形成して、耐摩耗性と強
靱性を向上させる。しかし、０．２％未満ではその効果
は不十分であり、３．０％を超えて含有させた場合、Ｍ
Ｃ型炭化物が初晶として粗大なデントライト状に晶出す
るため、強靱性が劣化する。従って、その範囲を０．２
〜３．０％とする。Nb: 0.2 to 3.0% Nb hardly forms a solid solution in the matrix, and most of the Nb forms high hardness and granular MC-type carbides to improve wear resistance and toughness. . However, if the content is less than 0.2%, the effect is insufficient. If the content exceeds 3.0%, M
Since the C-type carbide is crystallized as a primary crystal in a coarse dendritic state, the toughness is deteriorated. Therefore, the range is 0.2
To 3.0%.
【００１７】また、焼入れ後のスリーブロールの径方向
の硬度差をショア硬度で１０度以内に限定することは、
下記の理由による。本発明の熱間圧延用単層スリーブロ
ールの用途としては、例えば、形鋼、熱延鋼板等の熱間
圧延に使用される。その場合スリーブロールに要求され
る具備特性の一つとして、前記の通り耐摩耗性（耐肌荒
れ性）があり、そのため鋳造後のロールは、焼入れを実
施し、主として硬度の確保を図る。この場合、単層材質
のスリーブロールであっても、径方向の硬度差がショア
硬度で、１０以上になると従来の複合スリーブロールの
如き、ロールの内部で、引張りの残留応力が過大し、圧
延使用時にロールが、割損することになる。従って、そ
の上限は１０とする。なお、本発明の焼入れ後のスリー
ブロールの径方向の硬度差は、その後の軸との嵌合のた
めの内側の機械加工等を容易にするため１０の範囲内
で、ロールの内側の方を外側より低くすると良い。その
焼き入れの方法としては、例えば、公知のミスト焼き入
れ、ブロワー焼入れとすればよい。Further, limiting the difference in hardness in the radial direction of the sleeve roll after quenching to 10 degrees or less in Shore hardness is as follows.
For the following reasons. The single-layer sleeve roll for hot rolling of the present invention is used, for example, for hot rolling of shaped steel, hot-rolled steel sheet and the like. In this case, one of the required characteristics of the sleeve roll is abrasion resistance (skin roughness resistance) as described above. Therefore, the roll after casting is subjected to quenching to mainly secure the hardness. In this case, even if the sleeve roll is made of a single layer material, if the hardness difference in the radial direction becomes 10 or more in Shore hardness, the residual tensile stress becomes excessive inside the roll as in the case of the conventional composite sleeve roll, and the roll is rolled. The roll will break during use. Therefore, the upper limit is set to 10. Incidentally, the hardness difference in the radial direction of the sleeve roll after quenching according to the present invention is within a range of 10 in order to facilitate the subsequent machining or the like for fitting with the shaft. It should be lower than the outside. As a quenching method, for example, a known mist quenching or a blower quenching may be used.
【００１８】本発明材の基本成分は、上記の通りである
が、適用を対象とするロールのサイズ、要求されるロー
ルの使用特性等により、その他の化学成分として、上記
した本発明の化学成分に加えて、さらに、以下に記載す
る化学成分を適宜選択し含有してもよい。 Ｗ：０．１〜１０．０％ Ｗは、Ｍｏと同様にマトリックス中に固溶されて基地を
強化すると共に、Ｃと結合してＭ2 ＣやＭ6 Ｃ等の共晶
炭化物を形成し耐摩耗性を向上させるために添加する。
基地強化のためには、最低０．１％以上の含有が必要で
あるが、１０．０％を超えると粗大炭化物が形成され靱
性が低下する。Ｗの添加有無の選択については、例えば
適用を対象とするロールサイズ、要求されるロールの使
用特性等を考慮し、適宜判断するとよい。The basic components of the material of the present invention are as described above. However, depending on the size of the roll to which the material is to be applied, the required characteristics of use of the roll, etc., the above-mentioned chemical components of the present invention may be used as other chemical components. In addition to the above, the chemical components described below may be appropriately selected and contained. W: 0.1-10.0% W is dissolved in a matrix as in the case of Mo to strengthen the matrix, and combines with C to form eutectic carbides such as M 2 C and M 6 C. It is added to improve abrasion resistance.
In order to strengthen the matrix, the content must be at least 0.1% or more, but if it exceeds 10.0%, coarse carbides are formed and the toughness is reduced. The selection of the addition or non-addition of W may be appropriately determined in consideration of, for example, a roll size to be applied, required roll use characteristics, and the like.
【００１９】Ｔｉ：０．００１〜０．５０％ Ｔｉは、Ｃと結合して高硬度のＭＣ炭化物を形成し、耐
摩耗性を向上させるとともに、マトリックス中に固溶さ
れて基地を強化する。基地強化のためには、最低０．０
０１％以上の含有が必要であるが、０．５０％を超える
と、共晶のＭＣ炭化物が粗大化しすぎて靱性の低下に繋
がるとともに、溶湯の粘性が高まり鋳造性を阻害する。
Ｔｉの添加有無の選択については、例えば適用を対象と
するロールサイズ、要求されるロールの使用特性等によ
り、適宜判断するとよい。Ti: 0.001 to 0.50% Ti combines with C to form a high-hardness MC carbide, improves abrasion resistance, and forms a solid solution in the matrix to strengthen the matrix. At least 0.0 to strengthen the base
A content of not less than 01% is necessary, but if it exceeds 0.50%, the eutectic MC carbide becomes too coarse, leading to a decrease in toughness, and also increases the viscosity of the molten metal and impairs castability.
The selection of the presence or absence of addition of Ti may be appropriately determined depending on, for example, the size of the roll to be applied and the required roll use characteristics.
【００２０】Ｃｏ：０．２〜５．０％ Ｃｏは、その殆どがマトリックス中に固溶され基地を強
化する。そのため、高温での硬度および強度を向上させ
る作用を有している。しかし、０．２％未満ではその効
果は不十分であり、５．０％を超えてはその効果が飽和
するため、経済性の観点からも５．０％以下が望まし
い。Ｃｏ添加の選択有無については、例えば、使用特性
上の高温硬度や摩擦係数低減等を考慮し、その添加の要
否を適宜判断するとよい。Co: 0.2-5.0% Co is mostly dissolved in the matrix and strengthens the matrix. Therefore, it has the effect of improving the hardness and strength at high temperatures. However, if the content is less than 0.2%, the effect is insufficient, and if the content is more than 5.0%, the effect is saturated. Therefore, from the viewpoint of economy, the content is preferably 5.0% or less. Regarding the presence or absence of the addition of Co, for example, the necessity of the addition may be appropriately determined in consideration of the high-temperature hardness and the reduction of the friction coefficient in the use characteristics.
【００２１】[0021]
【実施例】以下、本発明の実施例を従来材と共に説明す
る。 （実施例１）表１に示す化学成分の鋼を高周波誘導炉に
て１５５０℃に溶解した後、該溶湯を、直径１００ｍ
ｍ、高さ１００ｍｍの砂型に１４５０℃で鋳造した。そ
の後、１０００℃からの焼入れ処理とさらに５００〜５
５０℃の焼戻し処理を施し熱間摩耗試験片を作成した。
なお、前記試験材の製造において、表１に示す本発明例
であるＡ〜Ｎ材、及び比較材であるＯ〜Ｒ材について、
熱間摩耗試験および表面粗度試験を実施した。EXAMPLES Examples of the present invention will be described below together with conventional materials. (Example 1) Steel having the chemical composition shown in Table 1 was melted in a high-frequency induction furnace at 1550 ° C, and the molten metal was melted to a diameter of 100 m.
m and a sand mold having a height of 100 mm were cast at 1450 ° C. After that, quenching treatment from 1000 ° C and further 500 ~ 5
A hot abrasion test piece was prepared by performing a tempering treatment at 50 ° C.
In the production of the test materials, the A to N materials of the present invention examples shown in Table 1 and the O to R materials of the comparative materials are shown in Table 1.
A hot abrasion test and a surface roughness test were performed.
【００２２】[0022]
【表１】 [Table 1]
【００２３】次に、図１に示す熱間回転摩耗試験機を用
いて、比較試験を行った。なお、熱間回転摩耗試験機と
しては、図１に示すような加熱片１および試験片２を接
触状態で回転させる転動装置３と、加熱片１および試験
片２を囲み、これらを加熱する高周波誘導加熱コイル４
と冷却装置５と、放射温度計６とを備えたディスク対デ
ィスクタイプの試験機を使用した。その時の試験条件
は、両ディスク間の最大接触応力は約２５０Ｎ／ｍｍ2
で、試験片２の周速度（回転数）は、７２０ｒｐｍと
し、両ディスク間のすべり率は、４．５％で行った。ま
た、熱間圧延材に相当する加熱片の温度は９６０℃と
し、試験片の温度は６５０℃として５００回転動させ、
試験片の摩耗量を測定した。その後、該摩耗試験後の試
験片の表面粗度を各々測定した。Next, a comparative test was performed using a hot rolling wear tester shown in FIG. As a hot rotary wear tester, a rolling device 3 for rotating a heating piece 1 and a test piece 2 in a contact state as shown in FIG. 1 and a heating piece 1 and a test piece 2 are surrounded and heated. High frequency induction heating coil 4
A disk-to-disk type tester equipped with a cooling device 5 and a radiation thermometer 6 was used. The test conditions at that time were that the maximum contact stress between both disks was about 250 N / mm 2
The peripheral speed (number of rotations) of the test piece 2 was set to 720 rpm, and the slip ratio between both disks was set to 4.5%. Further, the temperature of the heating piece corresponding to the hot-rolled material was 960 ° C., the temperature of the test piece was 650 ° C., and 500 rotations were performed.
The wear amount of the test piece was measured. Thereafter, the surface roughness of the test piece after the wear test was measured.
【００２４】図２は本発明材Ａ〜Ｎ材および比較材Ｏ〜
Ｒ材の熱間回転摩耗試験による摩耗減量の測定結果を示
す図である。また、図３は、本発明材、および比較材の
熱間回転摩耗試験後の試験片の表面粗度の測定結果を示
す図である。この図２及び図３から明らかなように、本
発明材のＡ〜Ｎ材は比較材Ｏ〜Ｒに比較し、いずれもそ
の摩耗減量が少なく、また、耐肌荒れ性の評価の指標と
なる表面粗度も小さくなっている。以上の各種の試験結
果により、本発明材は、実際の圧延ロールに適用した場
合、その目的とする耐摩耗性と耐肌荒れ性の作用・効果
を十分に奏することが明らかとなり、続いて、実際の圧
延ロールに適用した結果について説明する。FIG. 2 shows materials A to N of the present invention and comparative materials O to
It is a figure which shows the measurement result of abrasion loss by the hot rotational abrasion test of R material. FIG. 3 is a view showing the measurement results of the surface roughness of the test piece after the hot rotational wear test of the material of the present invention and the comparative material. As is clear from FIGS. 2 and 3, the A to N materials of the present invention have less wear loss than the comparative materials O to R, and have a surface as an index for evaluating the resistance to rough skin. The roughness is also small. From the above various test results, it is clarified that the material of the present invention, when applied to an actual rolling roll, sufficiently exerts its intended wear resistance and surface roughness resistance action and effect. The result applied to the rolling roll of Example 1 will be described.
【００２５】（実施例２）低周波誘導炉を用いて溶解し
た表２に示す本発明ロール３本、従来例としての比較材
ロール２本の化学組成の溶湯を、水平式の遠心鋳造機に
組み込んだ内径１２５０ｍｍ、長さ１０００ｍｍの回転
鋳型内に鋳造して、スリーブロール用素材を作製した。
次に、粗削加工を行い、１０００℃の焼入れと５００〜
５５０℃で数回の焼き戻し処理を実施した後、機械加工
により、寸法が外径１２００ｍｍ、内径５６０ｍｍ、幅
５００ｍｍのスリーブロール本体を作製した。このスリ
ーブロール本体の品質確性のために、超音波探傷によ
る内部性状検査、ロールの径方向における硬度分布を
１０ｍｍピッチで測定、Ｘ線によりスリーブロール内
面における残留応力の測定、さらに、スリーブロール
本体の機械的性質を調査するために、素材の余長部を利
用して機械試験を実施した。以下にその結果について説
明する。(Example 2) A molten metal having the chemical composition of three rolls of the present invention shown in Table 2 and two comparative rolls as a conventional example melted using a low frequency induction furnace was placed in a horizontal centrifugal casting machine. It was cast in a rotating mold having a built-in inner diameter of 1250 mm and a length of 1000 mm to prepare a sleeve roll material.
Next, roughing is performed, quenching at 1000 ° C. and 500 to
After performing the tempering treatment several times at 550 ° C., a sleeve roll body having dimensions of an outer diameter of 1200 mm, an inner diameter of 560 mm, and a width of 500 mm was produced by machining. In order to confirm the quality of the sleeve roll main body, the internal property inspection by ultrasonic inspection, the hardness distribution in the radial direction of the roll is measured at a pitch of 10 mm, the residual stress on the inner surface of the sleeve roll is measured by X-rays, In order to investigate the mechanical properties, a mechanical test was performed using the extra length of the material. The results will be described below.
【００２６】超音波探傷による内部性状検査の結果、
５本のスリーブロールは、何れも欠陥のない健全なもの
であることを確認した。ロールの径方向における硬度
分布の測定結果を図４に示す。この図から明らかなよう
に、比較ロール１および２の径方向におけるショア硬度
での硬度差は、２５、３０と大きく、一方、本発明ロー
ル１、２、３では、その硬度差は、３、５、８と何れも
１０以下の小さなものとなっている。Ｘ線によりスリ
ーブロール内面における残留応力の測定結果を表２に示
す。前記の硬度差の説明および表２より、ロールの径方
向における硬度差がショア硬度で１０度以内とした本発
明ロール１、２、３では、何れもスリーブロール内面に
おける残留応力は、周方向、軸方向ともに従来のスリー
ブロール１、２と比較して、約８０％低減されており、
単層のスリーブロールを採用した効果が極めて大きいこ
とが確認できた。As a result of the internal property inspection by ultrasonic testing,
It was confirmed that all of the five sleeve rolls were sound without defects. FIG. 4 shows the measurement results of the hardness distribution in the radial direction of the roll. As is clear from this figure, the hardness difference in the Shore hardness in the radial direction between the comparative rolls 1 and 2 is as large as 25 and 30, whereas the hardness difference between the rolls 1, 2 and 3 of the present invention is 3 and Both 5 and 8 are as small as 10 or less. Table 2 shows the measurement results of the residual stress on the inner surface of the sleeve roll by X-rays. From the description of the hardness difference and Table 2, in the rolls 1, 2, and 3 of the present invention in which the hardness difference in the radial direction of the roll is within 10 degrees in Shore hardness, the residual stress on the inner surface of the sleeve roll is in the circumferential direction. In both the axial direction, it is reduced by about 80% compared to the conventional sleeve rolls 1, 2.
It was confirmed that the effect of employing the single-layer sleeve roll was extremely large.
【００２７】これは、従来の複合スリーブロールの場
合、異種材料を金属結合させているため、焼入れ時に発
生する変態膨張量が外内層で異なるため、その差が残留
応力に加算され、結果的に大きな残留応力となっていた
が、本発明の単層スリーブロールの場合、単一材質で形
成されていることを特徴とするため、変態膨張量差が極
めて少ないことに起因する効果である。 スリーブ内面における機械的性質は、表２に示すよう
に、引張強度、伸びともに、従来の複合スリーブロール
の内層材並みに確保できており、本発明材は従来の複合
スリーブロール内層材と同等以上の機械的性質を有する
ことも確認できた。This is because, in the case of the conventional composite sleeve roll, since different materials are metal-bonded, the amount of transformation expansion that occurs during quenching differs between the outer and inner layers, and the difference is added to the residual stress. Although the residual stress was large, the single-layer sleeve roll of the present invention is characterized by being formed of a single material, which is an effect caused by a very small difference in transformation expansion. As shown in Table 2, the mechanical properties of the inner surface of the sleeve can be secured to the same level as the inner layer material of the conventional composite sleeve roll in both tensile strength and elongation. It was also confirmed that it had the following mechanical properties.
【００２８】[0028]
【表２】 [Table 2]
【００２９】その後、別途作製した、例えば鋼製のロー
ル軸に、本発明のスリーブロールを焼きばめ方式により
取付け、一体型の圧延用ロールとして組み立てた後、実
際の形鋼圧延に供した。その結果、従来のアマダイト複
合スリーブロールに比べて、耐摩耗性および耐肌荒れ性
の向上によりロールの原単位が、約３倍に向上するとと
もに、割損等のトラブルもなく、本発明材の効果が多大
であることを確認した。なお、本発明スリーブロール
は、形鋼圧延に限らず、例えばホットストリップミルの
粗圧延用ロールやエッジャーロール等、鉄鋼の熱間圧延
全般に適用してもよい。Thereafter, the sleeve roll of the present invention was attached to a separately manufactured roll shaft made of, for example, steel by a shrink fit method, assembled as an integrated rolling roll, and then subjected to actual shaped steel rolling. As a result, the basic unit of the roll is improved by about three times due to the improvement of abrasion resistance and surface roughening resistance as compared with the conventional Amadite composite sleeve roll, and there is no trouble such as breakage and the effect of the material of the present invention. Was confirmed to be enormous. The sleeve roll of the present invention is not limited to the shape steel rolling, but may be applied to general hot rolling of steel such as a rough rolling roll or an edger roll of a hot strip mill.
【００３０】[0030]
【発明の効果】以上述べたように、本発明のスリーブロ
ール用材質は、マトリックス組織を強化するために、Ｃ
ｕを微量に含有させるとともに、Ｍ3 ＣあるいはＭ7 Ｃ
3 型共晶炭化物の均一・微細分散化を図るために、Ｂ，
Ａｌを微量に複合添加させ、さらに、Ｖ，Ｎｂを粒状の
ＭＣ型共晶炭化物が晶出する範囲内で、適量添加するこ
とにより、ネット状に晶出したＭ3 ＣあるいはＭ7 Ｃ3
型共晶炭化物の一部を、粒状のＭＣ型共晶炭化物に置換
させることで、耐摩耗性、耐肌荒れ性および強靱性を大
きく向上させたものである。As described above, the material for the sleeve roll according to the present invention is used to enhance the matrix structure.
u in a small amount, and M 3 C or M 7 C
To achieve uniform and fine dispersion of type 3 eutectic carbide, B,
A small amount of Al is added in a complex manner, and V and Nb are added in an appropriate amount within a range in which granular MC-type eutectic carbide is crystallized, whereby M 3 C or M 7 C 3 crystallized in a net shape.
Abrasion resistance, surface roughening resistance and toughness are greatly improved by substituting a part of the type eutectic carbide for the MC type eutectic carbide.
【００３１】つまり、本発明のスリーブロール用材質
は、優れた耐摩耗性、耐肌荒れ性とともに、従来の熱間
圧延用複合スリーブロールの内層材と同等の強靱性を同
時に確保させたものである。従って、本発明の材質を熱
間圧延用スリーブロールに適用することにより、耐摩耗
性および耐肌荒れ性の向上と同時に、スリーブロールの
構造を従来の異種材質を組合せた複合構造から、本発明
材のみで形成された単層構造とすることが可能となるた
め、外内層境界部に発生する鋳造欠陥の防止と残留応力
の大幅な低減により、耐割損性を飛躍的に向上させるこ
とが可能となった。この結果、圧延ロールの長寿命化に
よるロール原単位の大幅な向上が達成できる。また、ロ
ール性能の向上による圧延製品の品質改善にも、大幅に
寄与する効果がある。That is, the material for the sleeve roll of the present invention has excellent abrasion resistance and surface roughening resistance, and at the same time, the same toughness as the inner layer material of the conventional composite sleeve roll for hot rolling. . Therefore, by applying the material of the present invention to a sleeve roll for hot rolling, it is possible to improve the abrasion resistance and the surface roughening resistance, and at the same time, change the structure of the sleeve roll from the conventional composite structure combining different materials to the material of the present invention. It is possible to achieve a single-layer structure formed only with a single layer, which can dramatically improve the breakage resistance by preventing casting defects occurring at the boundary between the outer and inner layers and greatly reducing residual stress. It became. As a result, it is possible to achieve a significant improvement in the unit consumption of rolls by extending the life of the rolls. In addition, there is an effect of greatly contributing to quality improvement of a rolled product by improving roll performance.
【図１】熱間回転摩耗試験機の概要構成を示す説明図で
ある。FIG. 1 is an explanatory diagram showing a schematic configuration of a hot rotary wear tester.
【図２】本発明材及び比較材の回転摩耗試験による摩耗
減量を示す図である。FIG. 2 is a view showing a wear loss of a material of the present invention and a comparative material by a rotational wear test.
【図３】本発明材及び比較材の回転摩耗試験後の表面粗
度を示す図である。FIG. 3 is a diagram showing the surface roughness of a material of the present invention and a comparative material after a rotational wear test.
【図４】スリーブロールの径方向における硬度分布の測
定結果を示す図である。FIG. 4 is a diagram showing a measurement result of a hardness distribution in a radial direction of a sleeve roll.
１ 加熱片 ２ 試験片 ３ 転動装置 ４ 高周波誘導加熱コイル ５ 冷却装置 ６ 放射温度計 DESCRIPTION OF SYMBOLS 1 Heating piece 2 Test piece 3 Rolling device 4 High frequency induction heating coil 5 Cooling device 6 Radiation thermometer
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 38/46 Ｃ２２Ｃ 38/46 38/52 38/52 (72)発明者 滝川 浩 福岡県北九州市戸畑区大字中原46−59 新 日本製鐵株式会社エンジニアリング事業本 部内 Ｆターム(参考） 4E016 AA03 AA07 DA04 EA03 EA22 FA07 Continued on the front page (51) Int.Cl. 7 Identification code FI Theme coat II (Reference) C22C 38/46 C22C 38/46 38/52 38/52 (72) Inventor Hiroshi Takigawa 46 Oaza Nakahara, Tobata-ku, Kitakyushu-shi, Fukuoka Prefecture −59 Nippon Steel Corporation Engineering Business Unit F-term (reference) 4E016 AA03 AA07 DA04 EA03 EA22 FA07
Claims (2)
る単一材質のスリーブロールであって、焼入れ後のスリ
ーブロールの径方向の硬度差をショア硬度で１０度以内
としたことを特徴とする遠心鋳造製熱間圧延用単層スリ
ーブロール。1. A chemical component in mass%, C: 1.0 to 2.5%, Si: 0.2 to 2.5%, Mn: 0.2 to 2.0%, Ni: 0.2 To 3.0%, Cr: 0.5 to 15.0%, Mo: 0.1 to 8.0%, B: 0.001 to 0.50%, Al: 0.001 to 0.50%, Cu; 0.001 to 0.50%, and V: 0.2 to 1.9%, Nb: 0.2 to 3.0%, one or two of the following, the balance being Fe and inevitable Single-layer sleeve roll for hot rolling made by centrifugal casting, characterized in that the difference in hardness in the radial direction of the sleeve roll after quenching is within 10 degrees in Shore hardness. .
製熱間圧延用単層スリーブロール。2. As a chemical component, one or more of W: 0.1 to 10.0%, Ti: 0.001 to 0.50%, and Co: 0.1 to 5.0% by mass% or The single-layer sleeve roll for centrifugal casting hot rolling according to claim 1, which contains two or more kinds.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001015029A JP4372364B2 (en) | 2001-01-23 | 2001-01-23 | Single layer sleeve roll for hot rolling made by centrifugal casting |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001015029A JP4372364B2 (en) | 2001-01-23 | 2001-01-23 | Single layer sleeve roll for hot rolling made by centrifugal casting |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2002220635A true JP2002220635A (en) | 2002-08-09 |
| JP4372364B2 JP4372364B2 (en) | 2009-11-25 |
Family
ID=18881645
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2001015029A Expired - Fee Related JP4372364B2 (en) | 2001-01-23 | 2001-01-23 | Single layer sleeve roll for hot rolling made by centrifugal casting |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP4372364B2 (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2012521489A (en) * | 2009-03-26 | 2012-09-13 | フェデラル−モーグル ブルシェイド ゲーエムベーハー | Nitritable steel piston ring, steel cylinder liner and casting method for manufacturing the same |
| EP2745944A1 (en) * | 2011-09-21 | 2014-06-25 | Hitachi Metals, Ltd. | Centrifugal casted composite roller for hot rolling and method for producing same |
| CN104593691A (en) * | 2014-12-26 | 2015-05-06 | 中钢集团邢台机械轧辊有限公司 | Roller sleeve for large forged alloy steel carrying roller and manufacturing method thereof |
| CN106191697A (en) * | 2016-08-16 | 2016-12-07 | 安徽瑞泰新材料科技有限公司 | A kind of impact-resistant abrasion-proof steel ball and preparation method thereof |
| CN106191703A (en) * | 2016-08-16 | 2016-12-07 | 安徽瑞泰新材料科技有限公司 | A kind of high-chromium wear-resistant steel ball and preparation method thereof |
| EP3119918A1 (en) * | 2014-03-18 | 2017-01-25 | Innomaq 21, Sociedad Limitada | Extremely high conductivity low cost steel |
| CN107119221A (en) * | 2017-04-26 | 2017-09-01 | 含山县朝霞铸造有限公司 | A kind of micro alloyed high strength grey cast iron part and its method of smelting |
| CN108118247A (en) * | 2018-01-04 | 2018-06-05 | 湖州中杭轧辊有限公司 | A kind of alloy half steel roll for being exclusively used in rolling bearings steel ball and its production technology |
| CN108144965A (en) * | 2018-01-04 | 2018-06-12 | 湖州中杭轧辊有限公司 | A kind of roll and production technology suitable for cross-wedge-rolling shaft part |
| CN108690940A (en) * | 2018-06-18 | 2018-10-23 | 滁州华海中谊工业炉有限公司 | A kind of high-intensity vacuum flue |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5318420A (en) * | 1976-08-04 | 1978-02-20 | Hitachi Metals Ltd | Graphite steel for hot working tools and structures |
| JPS5858254A (en) * | 1981-09-30 | 1983-04-06 | Daido Steel Co Ltd | Alloy steel |
| JPH03162551A (en) * | 1989-11-17 | 1991-07-12 | Hitachi Ltd | Corrosion-resistant alloy for nonferrous hot dip metal and roll for the above hot dip metal coating |
| JPH05311334A (en) * | 1992-05-12 | 1993-11-22 | Hitachi Ltd | Hardened roll for rolling and its manufacture |
-
2001
- 2001-01-23 JP JP2001015029A patent/JP4372364B2/en not_active Expired - Fee Related
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5318420A (en) * | 1976-08-04 | 1978-02-20 | Hitachi Metals Ltd | Graphite steel for hot working tools and structures |
| JPS5858254A (en) * | 1981-09-30 | 1983-04-06 | Daido Steel Co Ltd | Alloy steel |
| JPH03162551A (en) * | 1989-11-17 | 1991-07-12 | Hitachi Ltd | Corrosion-resistant alloy for nonferrous hot dip metal and roll for the above hot dip metal coating |
| JPH05311334A (en) * | 1992-05-12 | 1993-11-22 | Hitachi Ltd | Hardened roll for rolling and its manufacture |
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2012521489A (en) * | 2009-03-26 | 2012-09-13 | フェデラル−モーグル ブルシェイド ゲーエムベーハー | Nitritable steel piston ring, steel cylinder liner and casting method for manufacturing the same |
| EP2745944A1 (en) * | 2011-09-21 | 2014-06-25 | Hitachi Metals, Ltd. | Centrifugal casted composite roller for hot rolling and method for producing same |
| EP2745944A4 (en) * | 2011-09-21 | 2015-04-22 | Hitachi Metals Ltd | Centrifugal casted composite roller for hot rolling and method for producing same |
| US9757779B2 (en) | 2011-09-21 | 2017-09-12 | Hitachi Metals, Ltd. | Centrifugally cast composite roll for hot rolling and its production method |
| EP3119918A1 (en) * | 2014-03-18 | 2017-01-25 | Innomaq 21, Sociedad Limitada | Extremely high conductivity low cost steel |
| EP3119918B1 (en) * | 2014-03-18 | 2023-02-15 | Innomaq 21, Sociedad Limitada | Extremely high conductivity low cost steel |
| CN104593691B (en) * | 2014-12-26 | 2017-03-22 | 中钢集团邢台机械轧辊有限公司 | Roller sleeve for large forged alloy steel carrying roller and manufacturing method thereof |
| CN104593691A (en) * | 2014-12-26 | 2015-05-06 | 中钢集团邢台机械轧辊有限公司 | Roller sleeve for large forged alloy steel carrying roller and manufacturing method thereof |
| CN106191703A (en) * | 2016-08-16 | 2016-12-07 | 安徽瑞泰新材料科技有限公司 | A kind of high-chromium wear-resistant steel ball and preparation method thereof |
| CN106191697A (en) * | 2016-08-16 | 2016-12-07 | 安徽瑞泰新材料科技有限公司 | A kind of impact-resistant abrasion-proof steel ball and preparation method thereof |
| CN107119221A (en) * | 2017-04-26 | 2017-09-01 | 含山县朝霞铸造有限公司 | A kind of micro alloyed high strength grey cast iron part and its method of smelting |
| CN108118247A (en) * | 2018-01-04 | 2018-06-05 | 湖州中杭轧辊有限公司 | A kind of alloy half steel roll for being exclusively used in rolling bearings steel ball and its production technology |
| CN108144965A (en) * | 2018-01-04 | 2018-06-12 | 湖州中杭轧辊有限公司 | A kind of roll and production technology suitable for cross-wedge-rolling shaft part |
| CN108690940A (en) * | 2018-06-18 | 2018-10-23 | 滁州华海中谊工业炉有限公司 | A kind of high-intensity vacuum flue |
Also Published As
| Publication number | Publication date |
|---|---|
| JP4372364B2 (en) | 2009-11-25 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| WO2013057914A1 (en) | Roll surface-layer material for hot rolling with excellent fatigue resistance produced by centrifugal casting, and composite roll for hot rolling produced through centrifugal casting | |
| JP4366475B2 (en) | High-alloy glen cast iron material for hot rolling rolls made by centrifugal casting | |
| JP2000160277A (en) | Composite roll | |
| JP4372364B2 (en) | Single layer sleeve roll for hot rolling made by centrifugal casting | |
| JPH06179947A (en) | Composite roll made by centrifugal casting | |
| JP2002161332A (en) | Composite roll for hot rolling made with continuous hardfacing by casting | |
| KR20180084108A (en) | Rolls for hot rolling processes and methods for their manufacture | |
| JP2006281301A (en) | Composite rolling roll | |
| CN109641250B (en) | Outer layer material for hot rolling roll and composite roll for hot rolling | |
| JP5516545B2 (en) | Centrifugal cast roll outer layer material for hot rolling with excellent fatigue resistance and composite roll made of centrifugal cast for hot rolling | |
| JP3859958B2 (en) | Outer layer material of composite roll for centrifugal casting | |
| JP2618309B2 (en) | Centrifugal casting sleeve roll and its manufacturing method | |
| JPH05311334A (en) | Hardened roll for rolling and its manufacture | |
| JPH0649914B2 (en) | Quenching roll for rolling and rolling mill | |
| JP6669109B2 (en) | Roll outer layer material for hot rolling and composite roll for hot rolling | |
| JP3919092B2 (en) | Composite roll for hot rolling | |
| JP2002161334A (en) | Adamite roll for hot rolling | |
| JPH08209299A (en) | High seizing resistant roll material for hot rolling and its production | |
| JP5867143B2 (en) | Centrifugal cast roll outer layer material for hot rolling excellent in fatigue resistance, centrifugal cast composite roll for hot rolling, and production method thereof | |
| JP5327342B2 (en) | Centrifugal cast roll outer layer material for hot rolling with excellent fatigue resistance and composite roll made of centrifugal cast for hot rolling | |
| JPH05295479A (en) | Composite roll made by centrifugal casting | |
| JP4260670B2 (en) | Adamite roll for hot rolling | |
| JP2003183766A (en) | Tool material for hot working | |
| JP5867144B2 (en) | Centrifugal cast roll outer layer material for hot rolling excellent in fatigue resistance, centrifugal cast composite roll for hot rolling, and production method thereof | |
| JPH06182408A (en) | Centrifugal casting combined roll |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A711 | Notification of change in applicant |
Free format text: JAPANESE INTERMEDIATE CODE: A711 Effective date: 20051024 |
|
| A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A821 Effective date: 20051025 |
|
| A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20051219 |
|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20070731 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20090820 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20090901 |
|
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20090902 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20120911 Year of fee payment: 3 |
|
| R150 | Certificate of patent or registration of utility model |
Ref document number: 4372364 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130911 Year of fee payment: 4 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| S533 | Written request for registration of change of name |
Free format text: JAPANESE INTERMEDIATE CODE: R313533 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| LAPS | Cancellation because of no payment of annual fees |