JPH06179947A - Composite roll made by centrifugal casting - Google Patents

Composite roll made by centrifugal casting

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Publication number
JPH06179947A
JPH06179947A JP35375592A JP35375592A JPH06179947A JP H06179947 A JPH06179947 A JP H06179947A JP 35375592 A JP35375592 A JP 35375592A JP 35375592 A JP35375592 A JP 35375592A JP H06179947 A JPH06179947 A JP H06179947A
Authority
JP
Japan
Prior art keywords
layer
less
composite roll
cast iron
roll
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Withdrawn
Application number
JP35375592A
Other languages
Japanese (ja)
Inventor
Yoshihiro Kataoka
義弘 片岡
Original Assignee
Kawasaki Steel Corp
川崎製鉄株式会社
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 Kawasaki Steel Corp, 川崎製鉄株式会社 filed Critical Kawasaki Steel Corp
Priority to JP35375592A priority Critical patent/JPH06179947A/en
Publication of JPH06179947A publication Critical patent/JPH06179947A/en
Withdrawn legal-status Critical Current

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Abstract

PURPOSE:To obtain a composite roll made by centrifugal casting in which wear resistance and crack resistance are combined by integrating an external layer material having a specified compsn. constituted of C, Si, Mn, Cr, Mo, W, V, Nb and Fe and a shaft material made of cast iron by fusing. CONSTITUTION:By a centrifugal casting method by which excellent productivity and cost effectiveness are obtainable an external layer material and a shaft material of common cast iron or ductile cast iron good in toughness are integrated by fusing to obtain a composite roll. At this time, the componental compsn. of the external layer material is constituted of a one contg. 1.5 to 3.5% C, <=1.5% Si, <=1.2% Mn, 5.5 to 12.0% Cr, 1.0 to 8.0% Mo, >1.0 to 4.0% W, 3.0 to 10.0% V and 0.6 to 7.0% Nb, furthermore contg., at need, one or more kinds among <=2.0% Cu, <=5.5% Ni, <=10.0% Co, <=2.0% Ti, <=2.0% Zr and <=0.1% B and satisfying V+1.8Nb<=7.5C-6.0%, Mo+3.0W<=14.0 and 0.2<=Nb/V<=0.8, and the balance Fe with inevitable impurities.

Description

【発明の詳細な説明】Detailed Description of the Invention
【0001】[0001]
【産業上の利用分野】本発明は、耐摩耗性と耐クラック
性を兼備した遠心鋳造製複合ロールに関する。
BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a centrifugally cast composite roll having both wear resistance and crack resistance.
【0002】[0002]
【従来の技術】従来、耐摩耗性が要求される熱間圧延用
ロールは、外層と内層からなる複合ロールとされ、外層
材をセメンタイト系の炭化物が晶出した高Cr鋳鉄、又
はNiグレン鋳鉄、内層材を靱性の良いねずみ鋳鉄、又
はダクタイル鋳鉄として、遠心力鋳造法によって製造さ
れている。
2. Description of the Related Art Conventionally, a hot rolling roll required to have wear resistance is a composite roll consisting of an outer layer and an inner layer, and a high Cr cast iron or Ni grain cast iron in which cementite type carbide is crystallized as an outer layer material. The inner layer material is manufactured by a centrifugal casting method using gray cast iron or ductile cast iron having good toughness.
【0003】然るに、圧延条件の苛酷化及び圧延におけ
る生産性向上の要求等から、より一層の耐摩耗性と耐ク
ラック性を備えた圧延用ロールの提供が要求されてい
る。
However, due to severer rolling conditions and demand for improved productivity in rolling, it is required to provide rolling rolls having further wear resistance and crack resistance.
【0004】このような状況から、例えば特開昭60-124
407 号、特開昭61-177355 号には、従来の遠心力鋳造ロ
ールの外層材として高V鋳鉄を用いることが提案されて
いる。
Under such circumstances, for example, Japanese Patent Laid-Open No. 60-124
No. 407 and Japanese Patent Application Laid-Open No. 61-177355 propose to use high V cast iron as the outer layer material of a conventional centrifugal casting roll.
【0005】[0005]
【発明が解決しようとする課題】然しながら、遠心力鋳
造ロールの外層材として高V鋳鉄を用いる圧延用ロール
では、比重の小さいV炭化物が遠心分離により偏析し、
ロール外層内の特性が肉厚方向で不均一になる。この傾
向は大型ロールで外層肉厚が大なるほど著しく、実用ロ
ールとしての使用に耐えることができないという問題点
がある。
However, in the rolling roll using high V cast iron as the outer layer material of the centrifugal casting roll, V carbide having a small specific gravity is segregated by centrifugal separation,
The characteristics in the outer layer of the roll become uneven in the thickness direction. This tendency is remarkable as the outer layer thickness of the large roll increases, and there is a problem that it cannot withstand use as a practical roll.
【0006】尚、特開昭58-87249号、特開平1-96355 号
公報には、高速度鋼なみに高合金化した鋳鋼、鋳鉄を適
用したロール材が提案されている。然しながら、特開昭
58-87249号公報には焼嵌め又は組立ロールを対象とした
ものであり、圧延中に生ずる外層と軸材間の滑りが問題
となる。また、特開平1-96355 号公報は特殊な鋳かけ肉
盛法等、遠心力鋳造法以外の特殊な製造手法しか適用で
きず、生産性、経済性の面で問題がある。
Incidentally, Japanese Unexamined Patent Publication (Kokai) No. 58-87249 and Japanese Unexamined Patent Publication (Kokai) No. 1-96355 propose roll materials to which cast steel, which is highly alloyed like high speed steel, and cast iron are applied. However,
Japanese Patent Laid-Open No. 58-87249 is intended for shrink-fitting or assembling rolls, and slippage between the outer layer and the shaft material that occurs during rolling poses a problem. Further, Japanese Patent Application Laid-Open No. 1-96355 can only be applied to a special manufacturing method other than the centrifugal force casting method, such as a special overlay welding method, which is problematic in terms of productivity and economy.
【0007】即ち、圧延用ロールの製造に際し、ロール
外層にVを多量に含有させることにより、耐摩耗性を著
しく向上させることは可能であるが、複合ロール製造時
に生産性、経済性が最も優れているとして一般に実施さ
れている遠心力鋳造法を採用した場合には、遠心分離に
よる炭化物の偏析を生じ所定の特性を均一に得られない
という問題点がある。
That is, when a rolling roll is manufactured, it is possible to remarkably improve the wear resistance by adding a large amount of V to the outer layer of the rolling roll, but the productivity and the economical efficiency are most excellent at the time of manufacturing the composite roll. However, when the centrifugal casting method which is generally carried out is adopted, there is a problem that the segregation of carbides occurs due to the centrifugal separation and the predetermined characteristics cannot be obtained uniformly.
【0008】本発明は、外層を形成する合金成分を適正
化し、炭化物組成を限定することにより、生産性、経済
性の優れた遠心力鋳造法を適用しても、偏析等の生じな
い耐摩耗性と耐クラック性の均一な遠心鋳造製複合ロー
ルを提供することを目的とする。
According to the present invention, by optimizing the alloy components forming the outer layer and limiting the carbide composition, even if a centrifugal casting method having excellent productivity and economical efficiency is applied, segregation does not occur. An object of the present invention is to provide a centrifugally cast composite roll having uniform cracking resistance and crack resistance.
【0009】[0009]
【課題を解決するための手段】請求項1に記載の本発明
は、外層材と、該外層材と溶着一体化した普通鋳鉄又は
ダクタイル鋳鉄の軸材とからなる遠心鋳造製複合ロール
であって、該外層材が、C:1.5 〜 3.5%,Si:1.5
%以下,Mn:1.2 %以下,Cr:5.5 〜12.0%,M
o:1.0 〜8.0 %,W:1.0 超〜4.0 %,V:3.0 〜1
0.0%,Nb:0.6 〜7.0 %を含有し、かつ下記(1)
式、(2) 式、(3) 式を満足し、 V+ 1.8Nb ≦ 7.5 C−6.0(%) …(1) Mo+ 3.0W ≦ 14.0 …(2) 0.2 ≦ Nb/V ≦ 0.8 …(3) 残部Fe及び不可避的不純物よりなるようにしたもので
ある。
The present invention according to claim 1 is a centrifugally cast composite roll comprising an outer layer material and a shaft material of ordinary cast iron or ductile cast iron fused and integrated with the outer layer material. , The outer layer material is C: 1.5 to 3.5%, Si: 1.5
% Or less, Mn: 1.2% or less, Cr: 5.5 to 12.0%, M
o: 1.0 to 8.0%, W: over 1.0 to 4.0%, V: 3.0 to 1
0.0%, Nb: 0.6 to 7.0%, and the following (1)
Expressions (2), (3) are satisfied, and V + 1.8Nb ≤ 7.5 C-6.0 (%) (1) Mo + 3.0W ≤ 14.0 (2) 0.2 ≤ Nb / V ≤ 0.8 (3) The balance is Fe and inevitable impurities.
【0010】請求項2に記載の本発明は、外層材と、該
外層材と溶着一体化した普通鋳鉄又はダクタイル鋳鉄の
軸材とからなる遠心鋳造製複合ロールであって、該外層
材が、C:1.5 〜 3.5%,Si:1.5 %以下,Mn:1.
2 %以下,Cr:5.5 〜12.0%,Mo:1.0 〜8.0 %,
W:1.0 超〜4.0 %,V:3.0 〜10.0%,Nb:0.6 〜
7.0 %,更に、Cu:2.0 %以下,Ni:5.5 %以下,
Co:10.0%以下,Ti:2.0 %以下,Zr:2.0 %以
下,B:0.1 %以下のうちから選ばれた1種又は2種以
上を含有し、かつ下記(1) 式、(2) 式、(3) 式を満足
し、 V+ 1.8Nb ≦ 7.5 C−6.0(%) …(1) Mo+ 3.0W ≦ 14.0 …(2) 0.2 ≦ Nb/V ≦ 0.8 …(3) 残部Fe及び不可避的不純物よりなるようにしたもので
ある。
The present invention according to claim 2 is a centrifugally cast composite roll comprising an outer layer material and a shaft material of ordinary cast iron or ductile cast iron fused and integrated with the outer layer material, the outer layer material comprising: C: 1.5 to 3.5%, Si: 1.5% or less, Mn: 1.
2% or less, Cr: 5.5 to 12.0%, Mo: 1.0 to 8.0%,
W: over 1.0 ~ 4.0%, V: 3.0 ~ 10.0%, Nb: 0.6 ~
7.0%, Cu: 2.0% or less, Ni: 5.5% or less,
Co: 10.0% or less, Ti: 2.0% or less, Zr: 2.0% or less, B: 0.1% or less, and at least one selected from the following formulas (1) and (2) , V + 1.8Nb ≤ 7.5 C-6.0 (%) (1) Mo + 3.0W ≤ 14.0 (2) 0.2 ≤ Nb / V ≤ 0.8 (3) Residual Fe and inevitable impurities It is made up of:
【0011】請求項3に記載の本発明は、請求項1又は
2に記載の本発明において更に、前記外層材と軸材の間
に中間層を有し、該中間層を介して外層材と軸材とを溶
着一体化してなるようにしたものである。
According to a third aspect of the present invention, in the present invention according to the first or second aspect, an intermediate layer is further provided between the outer layer material and the shaft material, and an outer layer material is provided through the intermediate layer. The shaft material and the shaft material are integrally welded.
【0012】[0012]
【作用】本発明複合ロールの外層材における合金元素の
含有量の限定理由及びV,Nb,C量の限定式について
説明する。
The reason for limiting the content of alloying elements in the outer layer material of the composite roll of the present invention and the limiting formula for the amounts of V, Nb, and C will be described.
【0013】C:1.5 〜3.5 % Cはロール外層材の耐摩耗性を向上する硬い炭化物を形
成するための必須元素で1.5 %以上必要であるが、3.5
%を超えると耐クラック性が著しく低下するため上限を
3.5 %とする。
C: 1.5 to 3.5% C is an essential element for forming a hard carbide which improves the wear resistance of the outer layer material of the roll, and is required to be 1.5% or more.
%, The crack resistance will drop significantly, so the upper limit is
3.5%
【0014】Si:1.5 %以下 Siは脱酸剤及び鋳造性の確保に必要な元素で添加する
が、1.5 %を超えると耐クラック性を低下するため上限
を1.5 %とする。
Si: 1.5% or less Si is added as a deoxidizing agent and an element necessary for ensuring castability, but if it exceeds 1.5%, the crack resistance decreases, so the upper limit is made 1.5%.
【0015】Mn:1.2 %以下 Mnも上記Siと同様の目的のために必要であるが、1.
2 %を超えると耐クラック性が低下するため好ましくな
く上限を1.2 %とする。
Mn: 1.2% or less Mn is necessary for the same purpose as the above Si, but 1.
If it exceeds 2%, the crack resistance is deteriorated, so that it is not preferable and the upper limit is made 1.2%.
【0016】Cr:5.5 〜12.0% Crは炭化物を形成し、耐摩耗性を向上するために必要
な元素で5.5 %以上添加するが、12.0%を超えると本発
明が対象とするV,Nbを添加した場合には耐摩耗性が
劣化するため上限を12.0%とする。
Cr: 5.5 to 12.0% Cr forms carbides and is an element necessary for improving wear resistance, and is added in an amount of 5.5% or more. If it exceeds 12.0%, V and Nb targeted by the present invention are added. If added, wear resistance deteriorates, so the upper limit is made 12.0%.
【0017】Mo:1.0 〜8.0 %、W:1.0 超〜4.0 % MoはCrと同様に炭化物を形成して耐摩耗性の向上に
有効であるとともに、基地の焼入性、焼もどし軟化抵抗
を向上し、基地組織の強化に有効であるため1.0 %以上
必要であるが、8.0 %を超えると耐クラック性が低下す
るため、上限を8.0 %をする。
Mo: 1.0 to 8.0%, W: more than 1.0 to 4.0% Mo forms a carbide similarly to Cr and is effective in improving wear resistance, as well as hardenability and temper softening resistance of the matrix. It is required to be 1.0% or more because it improves and is effective in strengthening the base structure, but if it exceeds 8.0%, the crack resistance decreases, so the upper limit is made 8.0%.
【0018】WはCrと同様に炭化物を形成して耐摩耗
性の向上に有効であるとともに、基地の焼入性、焼もど
し軟化抵抗を向上し、基地組織の強化に有効であるため
1.0%超にて添加する必要があるが、4.0 %を超えると
耐クラック性が低下するため、上限を4.0 %をする。
Like W, W forms carbides and is effective in improving wear resistance, and is also effective in improving the hardenability and temper softening resistance of the matrix and is effective in strengthening the matrix structure.
It is necessary to add more than 1.0%, but if it exceeds 4.0%, the crack resistance deteriorates, so the upper limit is made 4.0%.
【0019】更に、MoとWとの複合添加に際し、(M
o+3.0 W)が14.0%を超えると共晶炭化物の形状が針
状又は棒状となり、耐クラック性が著しく低下するため Mo+3.0 W≦14.0% とする。
Further, when adding Mo and W in combination, (M
When o + 3.0 W) exceeds 14.0%, the shape of the eutectic carbide becomes needle-like or rod-like and the crack resistance remarkably decreases, so Mo + 3.0 W ≦ 14.0%.
【0020】Ni:5.5 %以下、Co:10.0%以下 Niは焼入れ性を向上し、基地組織を強化するために添
加するが、5.5 %を超えると残留γの存在など不安定な
組織を形成するため好ましくなく、上限を 5.5%とす
る。
Ni: 5.5% or less, Co: 10.0% or less Ni is added to improve the hardenability and strengthen the matrix structure, but if it exceeds 5.5%, an unstable structure such as the presence of residual γ is formed. Therefore, it is not preferable and the upper limit is set to 5.5%.
【0021】Coは高温における組織を安定化させるた
めに添加するが、10.0%を超えるとその耐熱性向上効果
が飽和するため経済性の点から上限を10.0%とする。
Co is added to stabilize the structure at high temperatures, but if it exceeds 10.0%, its heat resistance improving effect is saturated, so the upper limit is made 10.0% from the economical point of view.
【0022】Cu:2.0 %以下 Cuは基地組織を強化し、高温硬さを向上するため添加
するが、Cuは 2.0%を超えるとロールの表面性状を劣
化するとともに耐摩耗性、耐クラック性を低下するため
上限を 2.0%とする。
Cu: 2.0% or less Cu is added to strengthen the matrix structure and improve the high temperature hardness, but if Cu exceeds 2.0%, the surface properties of the roll are deteriorated and the wear resistance and crack resistance are improved. The upper limit is set to 2.0% because it will decrease.
【0023】Ti: 2.0%以下、Zr:2.0 %以下、
B:0.1 %以下 Ti、Zr、Bはともに粗大な共晶炭化物の形成を抑制
し、耐摩耗性、耐クラック性を向上するため添加する
が、TiとZrは 2.0%を超えるとV,Nb複合炭化物
の形状を劣化し逆に耐摩耗性を低下するため上限を 2.0
%とし、Bは0.1%を超えると粒界に偏析して耐クラッ
ク性を低下するので上限を 0.1%とする。
Ti: 2.0% or less, Zr: 2.0% or less,
B: 0.1% or less Ti, Zr, and B are added to suppress the formation of coarse eutectic carbides and improve wear resistance and crack resistance. However, when Ti and Zr exceed 2.0%, V, Nb The upper limit is 2.0 because it deteriorates the shape of the composite carbide and conversely reduces wear resistance.
%, And if B exceeds 0.1%, it segregates at the grain boundaries to reduce crack resistance, so the upper limit is made 0.1%.
【0024】V:3.0 〜10.0%、Nb:0.6 〜7.0 % V、Nbは本発明における最も重要な必須元素であり、
これらの複合添加と含有量制限条件が本発明の最大の特
徴である。
V: 3.0-10.0%, Nb: 0.6-7.0% V, Nb is the most important essential element in the present invention,
These combined additions and content limiting conditions are the greatest features of the present invention.
【0025】Vは耐摩耗性の向上に最も有効な硬いMC
又はM43 炭化物を形成するための必須元素で、その
効果を発揮するためには3.0 %以上必要であるが、10.0
%を超えると耐クラック性の低下、製造上の問題を生じ
るため上限を10.0%とする。
V is a hard MC that is most effective in improving wear resistance
Or, it is an essential element for forming M 4 C 3 carbide, and 3.0% or more is necessary to exert its effect.
%, The crack resistance decreases and manufacturing problems occur, so the upper limit is made 10.0%.
【0026】NbもVと同様耐摩耗性に有効な硬いMC
型炭化物を形成するが、単独添加では粗大な塊状炭化物
となりその効果が得られないだけでなく耐クラック性が
問題となる。
Nb, like V, is a hard MC effective for wear resistance.
Formed carbides are formed, but if added alone, they become coarse lumpy carbides and their effect cannot be obtained, and crack resistance becomes a problem.
【0027】そこで、VとNbを複合添加した場合の母
材硬さに及ぼすC量との関係、及び遠心力鋳造したリン
グ材の炭化物分布に起因する外層、内層間の熱間摩耗
比、熱衝撃試験におけるクラックの最大深さとNb,V
の含有量比Nb/Vとの関係を調べた結果をそれぞれ図
1、図2に示す。
Therefore, the relationship between the amount of C and the hardness of the base material when V and Nb are added in combination, the hot wear ratio between the outer layer and the inner layer due to the carbide distribution of the centrifugally cast ring material, and the heat Maximum crack depth and Nb, V in impact test
The results of examining the relationship with the content ratio Nb / V of are shown in FIGS. 1 and 2, respectively.
【0028】図1から耐摩耗熱間圧延用ロールとして必
要な硬さHs 75以上を得るためには V+1.8 Nb≦7.5 C−6.0 (%) を満足する必要があることが明らかとなった。
From FIG. 1, it is clear that V + 1.8 Nb≤7.5 C-6.0 (%) must be satisfied in order to obtain the hardness Hs 75 or more required for the wear-resistant hot rolling roll. .
【0029】尚、図1の実験は、Si:0.3 %,Mn:
0.4 %, Cr:6.2 %,Mo:3.2%,W:1.5 %を含
有し、C,V,Nbを変化させた溶湯を鋳造した25mmY
−ブロックについて1050℃焼入れ処理、550 ℃焼もどし
処理を施した試料を用いた。
In the experiment of FIG. 1, Si: 0.3%, Mn:
25mmY which was cast a molten metal containing 0.4%, Cr: 6.2%, Mo: 3.2%, W: 1.5% and varying C, V, Nb.
-For the blocks, samples that had been subjected to 1050 ° C quenching treatment and 550 ° C tempering treatment were used.
【0030】また、図2から遠心力鋳造法で製造した場
合にも均一な外層材を得ることができ、かつ耐クラック
性を損なわないためには 0.2 ≦ Nb/V ≦ 0.8 を満足する必要があることが明らかとなった。
Further, it is necessary to satisfy 0.2 ≤ Nb / V ≤ 0.8 in order to obtain a uniform outer layer material even when manufactured by the centrifugal casting method from Fig. 2 and not to impair crack resistance. It became clear that there is.
【0031】尚、図2において、「摩耗比(内層/外
層)」は、リング材の内層側から採取した試験片の摩耗
量(Iw)と外層側から採取した試験片の摩耗量(O
w)との比(Iw/Ow)であり、「熱衝撃クラック最
大深さ」は、熱衝撃試験で発生したクラックの最大深さ
である。
In FIG. 2, "wear ratio (inner layer / outer layer)" means the wear amount (Iw) of the test piece taken from the inner layer side of the ring material and the wear amount (O of the test piece taken from the outer layer side).
w) and the ratio (Iw / Ow), and the “maximum depth of thermal shock cracks” is the maximum depth of cracks generated in the thermal shock test.
【0032】また、図2の実験は、C:2.3 %,Si:
0.3 %,Mn:0.5 %,Cr:6.5%,Mo:2.6 %,
W: 1.3%,V:5.2 %,Nb:0 〜7.0 %を含有する
溶湯を遠心力鋳造(140 G)して得た肉厚100mm のリン
グサンプルについて1050℃焼入れ処理、550 ℃焼もどし
処理を施した試料を用いた。
In the experiment of FIG. 2, C: 2.3%, Si:
0.3%, Mn: 0.5%, Cr: 6.5%, Mo: 2.6%,
A ring sample with a wall thickness of 100 mm obtained by centrifugal force casting (140 G) containing a melt containing W: 1.3%, V: 5.2% and Nb: 0 to 7.0% was quenched at 1050 ° C and tempered at 550 ° C. The applied sample was used.
【0033】そして、摩耗試験は、φ190 ×15の相手材
とφ50×10の試験材の2円盤のすべり摩耗方式で相手材
を800 ℃に加熱し、荷重100kgfで圧接した状態で試験材
を800rpmで回転させ、すべり率3.9 %として120 分後の
摩耗減量を測定して行なった。
The wear test was conducted by heating the mating material to 800 ° C. by the sliding wear method of a two-disc of a mating material of φ190 × 15 and a test material of φ50 × 10, and pressing the test material under a load of 100 kgf to 800 rpm. Rotation was carried out at a slip rate of 3.9% to measure the wear loss after 120 minutes.
【0034】また、熱衝撃試験は、1200rpm で回転して
いるローラーに55×40×15の板状試験片を圧接する方式
で、荷重150kgf、接触時間15sの条件で行ない、試験片
に発生したクラック長さを測定した。
The thermal shock test was conducted by pressing a 55 × 40 × 15 plate-shaped test piece against a roller rotating at 1200 rpm under the conditions of a load of 150 kgf and a contact time of 15 s, and the test piece was generated. The crack length was measured.
【0035】[0035]
【実施例】【Example】
(実施例1)表1に示す化学組成の溶湯(本発明材:B
〜E、比較材:A、F〜Q)を遠心力鋳造により鋳造
し、肉厚100mm のリングサンプルを試作し、ショアー硬
さ、熱間摩耗及び熱衝撃試験を行なった。
(Example 1) Molten metal having the chemical composition shown in Table 1 (material of the present invention: B
.About.E, comparative materials: A, F to Q) were cast by centrifugal force casting, a ring sample having a wall thickness of 100 mm was prototyped, and Shore hardness, hot wear and thermal shock tests were conducted.
【0036】[0036]
【表1】 [Table 1]
【0037】尚、摩耗試験は、リング材の内層側と外層
側からそれぞれφ50×10の試験片を採取し、前記条件と
同一の方法で行なった。
The wear test was carried out by the same method as the above conditions by taking test pieces of φ50 × 10 from the inner layer side and the outer layer side of the ring material.
【0038】また、熱衝撃試験は、リング材の外層側よ
り前記した板状試験片を採取し、同一の条件で行なっ
た。
The thermal shock test was carried out under the same conditions by collecting the above-mentioned plate-shaped test piece from the outer layer side of the ring material.
【0039】それら摩耗試験と熱衝撃試験の結果を表2
に示す。表2によれば、本発明材は従来のNi−グレン
材(A材)と比べ、硬さは同程度であるが、耐摩耗性、
耐クラック性ともに著しく向上していることが認められ
る。
The results of the wear test and the thermal shock test are shown in Table 2.
Shown in. According to Table 2, the material of the present invention has the same hardness as the conventional Ni-Glen material (A material), but the wear resistance,
It is recognized that the crack resistance is significantly improved.
【0040】[0040]
【表2】 [Table 2]
【0041】また、比較材F〜P材は本発明の限定をは
ずれているため、F材はC量が低いため硬さが不足して
いるとともに炭化物の偏析で外層の耐摩耗性が低下し、
G材については炭化物の偏析で外層の耐摩耗性が低下
し、H材については耐クラック性が低下し、I材につい
ては硬さが不足している。また、J材はC量が過多であ
るため耐クラック性が低下し、K材はSi量が過多であ
るため耐クラック性が低下し、L材はMn量が過多であ
るため耐クラック性が低下し、M材はCr量が過多であ
るため耐摩耗性、耐クラック性が低下し、N材はMo量
が過多であるため耐クラック性が低下し、O材はV量が
不足しているため耐摩耗性、耐クラック性が低下し、P
材はV量が過多であるため耐クラック性が低下し、Q材
はW量が過多であるため耐クラック性が低下している。
Further, since the comparative materials F to P are out of the limitation of the present invention, the hardness of the F material is low due to the low C content, and the segregation of carbide reduces the wear resistance of the outer layer. ,
With respect to the G material, segregation of carbide reduces the wear resistance of the outer layer, the H material has a reduced crack resistance, and the I material has insufficient hardness. In addition, the J material has an excessive amount of C and thus has low crack resistance, the K material has an excessive amount of Si, which has poor crack resistance, and the L material has an excessive amount of Mn and therefore has an excellent crack resistance. Wear resistance and crack resistance of the M material decrease due to excessive Cr content, and crack resistance decreases of the N material due to excessive Mo content, and V content of the O material is insufficient. Wear resistance and crack resistance are reduced due to
Since the V content of the material is excessive, the crack resistance is lowered, and the Q material of the material is excessive, and the crack resistance is degraded.
【0042】表3に示す組成の外層及び内層を有し、胴
径670mm 、胴長1450mmの複合ロールを以下に示す手順で
製造した。低周波溶解炉にて外層材の溶湯を溶解し、こ
の外層材溶湯を遠心力 140Gで回転する遠心鋳造用鋳型
内に1490℃で厚さ75mmになるように鋳込んだ。外層材の
鋳込み後20分後に鋳型の回転を停止し、鋳型を直立さ
せ、外層鋳込み後35分後に内層材溶湯を鋳込んだ。室温
まで冷却後、鋳型を解体し、粗加工を行なった後、1050
℃から焼入れし、その後550 ℃にて焼き戻しを行なう熱
処理を行なった。熱処理後超音波探傷等の検査を行なっ
たが、欠陥のない健全なロールであり、仕上げ加工後の
外層厚は45mmであり、表面硬さはショアー硬さで78〜82
であった。
A composite roll having an outer layer and an inner layer having the compositions shown in Table 3 and having a cylinder diameter of 670 mm and a cylinder length of 1450 mm was manufactured by the following procedure. The molten metal for the outer layer material was melted in a low frequency melting furnace, and the molten metal for the outer layer material was cast into a centrifugal casting mold rotating at a centrifugal force of 140 G to a thickness of 75 mm at 1490 ° C. Twenty minutes after the casting of the outer layer material, the rotation of the mold was stopped to erect the mold, and 35 minutes after the casting of the outer layer, the molten metal for the inner layer material was cast. After cooling to room temperature, dismantling the mold and performing rough processing, 1050
A heat treatment was carried out by quenching from ℃, and then tempering at 550 ℃. After heat treatment, inspections such as ultrasonic flaw detection were performed, but it was a sound roll with no defects, the outer layer thickness after finishing was 45 mm, and the surface hardness was 78-82 Shore hardness.
Met.
【0043】[0043]
【表3】 [Table 3]
【0044】上記複合ロールを、実際のホットストリッ
プミル仕上げスタンドに使用した結果、図4に示すよう
に、従来のニッケルグレン鋳鉄ロールの使用成績を大き
く上回るものであった。また、ロール表面の肌荒れ等も
問題なく、良好な結果が得られた。
As a result of using the above composite roll for an actual hot strip mill finishing stand, as shown in FIG. 4, the use result of the conventional nickel-glen cast iron roll was greatly exceeded. In addition, the surface of the roll was not roughened, and good results were obtained.
【0045】尚、本発明の実施において、表1に示した
本発明材を外層材とする複合ロールを構成するに際し、
外層と内層の間に後述実施例2における如くの中間層を
設けるものであっても良い。
In the practice of the present invention, when forming a composite roll using the material of the present invention shown in Table 1 as an outer layer material,
An intermediate layer as in Example 2 described later may be provided between the outer layer and the inner layer.
【0046】(実施例2)表4に示す化学組成の溶湯
(本発明材:B〜H、比較材A、I〜L)を遠心力鋳造
により鋳造し、肉厚100mm のリングサンプルを試作し、
ショアー硬さ、熱間摩耗及び熱衝撃試験を行なった。
(Example 2) A molten metal having the chemical composition shown in Table 4 (materials of the present invention: B to H, comparative materials A and IL) was cast by centrifugal force casting to produce a ring sample having a wall thickness of 100 mm as a prototype. ,
Shore hardness, hot wear and thermal shock tests were performed.
【0047】[0047]
【表4】 [Table 4]
【0048】尚、摩耗試験は、リング材の内層側と外層
側からそれぞれφ50×10の試験片を採取し、前記条件と
同一の方法で行なった。
The wear test was carried out by the same method as the above conditions by taking test pieces of φ50 × 10 from the inner layer side and the outer layer side of the ring material.
【0049】また、熱衝撃試験は、リング材の外層側よ
り前記した板状試験片を採取し、同一の条件で行なっ
た。
The thermal shock test was conducted under the same conditions by collecting the above-mentioned plate-shaped test piece from the outer layer side of the ring material.
【0050】それらの摩耗試験と熱衝撃試験の結果を表
5に示す。表5によれば、本発明材は従来のNi−グレ
ン材(A材)と比べ、硬さは同程度であるが、耐摩耗
性、耐クラック性ともに著しく向上していることが認め
られる。
The results of the wear test and the thermal shock test are shown in Table 5. According to Table 5, the material of the present invention has a hardness comparable to that of the conventional Ni-Glen material (material A), but it is recognized that both wear resistance and crack resistance are remarkably improved.
【0051】[0051]
【表5】 [Table 5]
【0052】また、比較材I〜L材は本発明の限定を外
れているため、I材はCu量が過多であるため耐摩耗
性、耐クラック性が低下し、J材はW量が過多であるた
め炭化物の偏析で外層側の耐摩耗性が低下し、K材はT
i とB量が過多であるため耐摩耗性、耐クラック性が低
下し、L材はZr 量が過多であるため耐摩耗性が低下し
ている。
Further, since the comparative materials I to L are out of the limitation of the present invention, the material I has an excessive Cu content, so that the wear resistance and crack resistance are deteriorated, and the material J has an excessive W content. Therefore, segregation of carbide reduces wear resistance on the outer layer side, and K material has T
Since the amounts of i and B are excessive, the wear resistance and crack resistance are deteriorated, and the wear resistance of the L material is deteriorated because the amount of Zr is excessive.
【0053】表6に示す組成の外層、中間層、及び内層
を有し、図3に示す胴径670mm 、胴長1450mmの複合ロー
ルを以下に示す手順で製造した。低周波溶解炉にて外層
材の溶湯を溶解し、この外層材溶湯を遠心力 140Gで回
転する遠心鋳造用鋳型内に1490℃で厚さ75mmになるよう
に鋳込んだ。外層材が凝固した直後に中間層の溶湯を15
40℃で厚さ40mmになるように鋳込んだ。この中間層が完
全凝固した後に鋳型の回転を停止し、鋳型を直立させ、
外層材鋳込み後40分後に内層材溶湯を1450℃で鋳込ん
だ。室温まで冷却後、鋳型を解体し、粗加工を行なった
後、1050℃から焼入れし、その後550 ℃にて焼き戻しを
行なう熱処理を行なった。熱処理後超音波探傷等の検査
を行なったが、外層と中間層の境界及び中間層と内層と
の境界ともに欠陥は発生せず、内部性状も健全なロール
であり、仕上げ加工後の外層厚は45mmであり、表面硬さ
はショアー硬さで78〜82であった。
A composite roll having an outer layer, an intermediate layer, and an inner layer having the compositions shown in Table 6 and having a cylinder diameter of 670 mm and a cylinder length of 1450 mm shown in FIG. 3 was manufactured by the following procedure. The molten metal for the outer layer material was melted in a low frequency melting furnace, and the molten metal for the outer layer material was cast into a centrifugal casting mold rotating at a centrifugal force of 140 G to a thickness of 75 mm at 1490 ° C. Immediately after solidification of the outer layer material,
It was cast at 40 ° C to a thickness of 40 mm. After this intermediate layer is completely solidified, the rotation of the mold is stopped, the mold is erected,
40 minutes after the casting of the outer layer material, the molten metal of the inner layer material was cast at 1450 ° C. After cooling to room temperature, the mold was disassembled, rough processing was performed, quenching was performed from 1050 ° C., and then tempering was performed at 550 ° C. for tempering. After heat treatment, inspections such as ultrasonic flaw detection were performed, but no defects occurred at the boundary between the outer layer and the intermediate layer and at the boundary between the intermediate layer and the inner layer, and the internal properties were sound, and the outer layer thickness after finishing was It was 45 mm, and the surface hardness was 78 to 82 in Shore hardness.
【0054】[0054]
【表6】 [Table 6]
【0055】上記複合ロールを、実際のホットストリッ
プミル仕上げスタンドに使用した結果、従来のニッケル
グレン鋳鉄ロールの使用成績を大きく上回るものであっ
た。また、ロール表面の肌荒れ等も問題なく、良好な結
果が得られた。
As a result of using the above-mentioned composite roll in an actual hot strip mill finishing stand, the use result of the conventional nickel-grain cast iron roll was greatly exceeded. In addition, the surface of the roll was not roughened, and good results were obtained.
【0056】尚、本発明の実施において、表4に示した
本発明材を外層材とする複合ロールを構成するに際し、
外層と内層の間に中間層を設けないものであっても良
い。
In the practice of the present invention, when forming a composite roll using the material of the present invention shown in Table 4 as the outer layer material,
The intermediate layer may not be provided between the outer layer and the inner layer.
【0057】[0057]
【発明の効果】以上のように本発明によれば、生産性、
経済性の優れた遠心力鋳造法を適用しても、偏析等の生
じない耐摩耗性と耐クラック性に優れた遠心鋳造製複合
ロールを得ることができる。
As described above, according to the present invention, productivity,
Even if the centrifugal casting method with excellent economical efficiency is applied, it is possible to obtain a centrifugally cast composite roll excellent in wear resistance and crack resistance without segregation and the like.
【図面の簡単な説明】[Brief description of drawings]
【図1】図1はVとNbの複合添加量とC量とが母材硬
さに及ぼす影響を示す線図である。
FIG. 1 is a diagram showing the influence of the combined addition amount of V and Nb and the C amount on the hardness of a base material.
【図2】図2は遠心力鋳造したリング材の炭化物分布に
起因する外層と内層間の熱間摩耗比と、熱衝撃試験にお
けるクラック最大深さに及ぼすNbとVの含有量比Nb
/Vの影響を示す線図である。
FIG. 2 is a hot wear ratio between an outer layer and an inner layer due to a carbide distribution of a centrifugally cast ring material, and a Nb and V content ratio Nb which affects the maximum crack depth in a thermal shock test.
It is a diagram which shows the influence of / V.
【図3】図3は実施例2に関わる複合ロールの縦断面図
である。
FIG. 3 is a vertical sectional view of a composite roll according to a second embodiment.
【図4】図4は実施例1と2で製造した複合ロールの実
機ミルでの圧延成績を従来ロールのそれと比較して示す
線図である。
FIG. 4 is a diagram showing rolling results of the composite rolls manufactured in Examples 1 and 2 in an actual mill in comparison with those of conventional rolls.

Claims (3)

    【特許請求の範囲】[Claims]
  1. 【請求項1】 外層材と、該外層材と溶着一体化した普
    通鋳鉄又はダクタイル鋳鉄の軸材とからなる遠心鋳造製
    複合ロールであって、該外層材が、 C:1.5 〜 3.5%,Si:1.5 %以下,Mn:1.2 %以
    下,Cr:5.5 〜12.0%,Mo:1.0 〜8.0 %,W:1.
    0 超〜4.0 %,V:3.0 〜10.0%,Nb:0.6 〜7.0 %
    を含有し、 かつ下記(1) 式、(2) 式、(3) 式を満足し、 V+ 1.8Nb ≦ 7.5 C−6.0(%) …(1) Mo+ 3.0W ≦ 14.0 …(2) 0.2 ≦ Nb/V ≦ 0.8 …(3) 残部Fe及び不可避的不純物よりなることを特徴とする
    遠心鋳造製複合ロール。
    1. A centrifugally cast composite roll comprising an outer layer material and a shaft material of ordinary cast iron or ductile cast iron fused and integrated with the outer layer material, wherein the outer layer material is C: 1.5 to 3.5%, Si : 1.5% or less, Mn: 1.2% or less, Cr: 5.5 to 12.0%, Mo: 1.0 to 8.0%, W: 1.
    Over 0 ~ 4.0%, V: 3.0 ~ 10.0%, Nb: 0.6 ~ 7.0%
    And satisfy the following formulas (1), (2), and (3), and V + 1.8Nb ≤7.5 C-6.0 (%) (1) Mo + 3.0W ≤14.0 (2) 0.2 ≤ Nb / V ≦ 0.8 (3) A centrifugally cast composite roll characterized by comprising the balance Fe and inevitable impurities.
  2. 【請求項2】 外層材と、該外層材と溶着一体化した普
    通鋳鉄又はダクタイル鋳鉄の軸材とからなる遠心鋳造製
    複合ロールであって、該外層材が、 C:1.5 〜 3.5%,Si:1.5 %以下,Mn:1.2 %以
    下,Cr:5.5 〜12.0%,Mo:1.0 〜8.0 %,W:1.
    0 超〜4.0 %,V:3.0 〜10.0%,Nb:0.6 〜7.0
    %,更に、Cu:2.0 %以下,Ni:5.5 %以下,C
    o:10.0%以下,Ti:2.0 %以下,Zr:2.0 %以
    下,B:0.1 %以下のうちから選ばれた1種又は2種以
    上を含有し、 かつ下記(1) 式、(2) 式、(3) 式を満足し、 V+ 1.8Nb ≦ 7.5 C−6.0(%) …(1) Mo+ 3.0W ≦ 14.0 …(2) 0.2 ≦ Nb/V ≦ 0.8 …(3) 残部Fe及び不可避的不純物よりなることを特徴とする
    遠心鋳造製複合ロール。
    2. A centrifugally cast composite roll comprising an outer layer material and a shaft material of ordinary cast iron or ductile cast iron fused and integrated with the outer layer material, wherein the outer layer material is C: 1.5 to 3.5%, Si : 1.5% or less, Mn: 1.2% or less, Cr: 5.5 to 12.0%, Mo: 1.0 to 8.0%, W: 1.
    0 over ~ 4.0%, V: 3.0 ~ 10.0%, Nb: 0.6 ~ 7.0
    %, Cu: 2.0% or less, Ni: 5.5% or less, C
    o: 10.0% or less, Ti: 2.0% or less, Zr: 2.0% or less, B: 0.1% or less, and one or more selected from, and the following formulas (1) and (2): , V + 1.8Nb ≤ 7.5 C-6.0 (%) (1) Mo + 3.0W ≤ 14.0 (2) 0.2 ≤ Nb / V ≤ 0.8 (3) Residual Fe and inevitable impurities A composite roll made by centrifugal casting characterized by comprising
  3. 【請求項3】 前記外層材と軸材の間に中間層を有し、
    該中間層を介して外層材と軸材とを溶着一体化してなる
    請求項1又は2に記載の遠心鋳造製複合ロール。
    3. An intermediate layer is provided between the outer layer material and the shaft material,
    The centrifugally cast composite roll according to claim 1 or 2, wherein the outer layer material and the shaft material are welded and integrated via the intermediate layer.
JP35375592A 1992-12-15 1992-12-15 Composite roll made by centrifugal casting Withdrawn JPH06179947A (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP35375592A JPH06179947A (en) 1992-12-15 1992-12-15 Composite roll made by centrifugal casting

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
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Publications (1)

Publication Number Publication Date
JPH06179947A true JPH06179947A (en) 1994-06-28

Family

ID=18433001

Family Applications (1)

Application Number Title Priority Date Filing Date
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Country Link
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Publication number Priority date Publication date Assignee Title
KR100256369B1 (en) * 1995-12-12 2000-05-15 이구택 The wear resistant alloy for built-up welding
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WO2020032144A1 (en) 2018-08-08 2020-02-13 日立金属株式会社 Centrifugal cast composite roll for rolling and manufacturing method therefor

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