JPH01162745A - Roll for rolling - Google Patents
Roll for rollingInfo
- Publication number
- JPH01162745A JPH01162745A JP32193987A JP32193987A JPH01162745A JP H01162745 A JPH01162745 A JP H01162745A JP 32193987 A JP32193987 A JP 32193987A JP 32193987 A JP32193987 A JP 32193987A JP H01162745 A JPH01162745 A JP H01162745A
- Authority
- JP
- Japan
- Prior art keywords
- cast iron
- roll
- rolling
- wear resistance
- ratio
- 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.)
- Pending
Links
- 238000005096 rolling process Methods 0.000 title claims abstract description 19
- 239000000463 material Substances 0.000 claims abstract description 44
- 229910001018 Cast iron Inorganic materials 0.000 claims abstract description 42
- 239000002131 composite material Substances 0.000 claims abstract description 20
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 12
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 7
- 229910001141 Ductile iron Inorganic materials 0.000 claims abstract description 6
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 229910001208 Crucible steel Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 3
- 239000000203 mixture Substances 0.000 abstract description 8
- 229910052748 manganese Inorganic materials 0.000 abstract description 5
- 239000011159 matrix material Substances 0.000 abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 5
- 229910052759 nickel Inorganic materials 0.000 abstract description 5
- 238000000034 method Methods 0.000 abstract description 3
- 229910052758 niobium Inorganic materials 0.000 abstract description 3
- 229910052710 silicon Inorganic materials 0.000 abstract description 3
- 229910052721 tungsten Inorganic materials 0.000 abstract description 2
- 230000005496 eutectics Effects 0.000 abstract 1
- 230000002401 inhibitory effect Effects 0.000 abstract 1
- 230000001105 regulatory effect Effects 0.000 abstract 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 8
- 229910002804 graphite Inorganic materials 0.000 description 8
- 239000010439 graphite Substances 0.000 description 8
- 150000001247 metal acetylides Chemical class 0.000 description 7
- 229910001220 stainless steel Inorganic materials 0.000 description 6
- 239000010935 stainless steel Substances 0.000 description 6
- 239000000126 substance Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 238000002425 crystallisation Methods 0.000 description 4
- 230000008025 crystallization Effects 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 230000000717 retained effect Effects 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 238000009750 centrifugal casting Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000010587 phase diagram Methods 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 230000003746 surface roughness Effects 0.000 description 2
- 241000316887 Saissetia oleae Species 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 238000007639 printing Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 239000002002 slurry Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 230000002747 voluntary effect Effects 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B27/00—Rolls, roll alloys or roll fabrication; Lubricating, cooling or heating rolls while in use
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Reduction Rolling/Reduction Stand/Operation Of Reduction Machine (AREA)
Abstract
Description
本発明は、圧延用複合高、特にホットストリップ仕上ミ
ルのワークロールに関するもので、その特徴は、外層材
として、改良された高Cr鋳鉄材を採用した圧延用複合
ロールに存するものである。The present invention relates to a work roll for a rolling composite roll, particularly a hot strip finishing mill, and its feature resides in a composite roll for rolling that employs an improved high Cr cast iron material as the outer layer material.
最近、ホットストリップミルの仕−L前段には複合高C
r鋳鉄ロールがアダマイトロール(1,6〜1.8%G
、0.8〜1.5%Cr)に代わり用いられてきている
。又、仕上中・後段においても複合高Cr鋳鉄ロールが
使用され始めている。
一般に用いられている熱間圧延用複合高C「ロールは、
外層材の化学成分が第1図に示すFc−CrC系状態図
(液相線図)の領域Aの範囲(2,3〜3.1%C11
3〜23%Cr、Cr/C比−5,5〜7.5)にあり
、20〜35而積%のCr共共成炭化物M t c 3
型)が微細に分散した組織となっており、耐摩耗性に優
れているのが特長である。
しかしながら、最近の圧延製品の表面品質の高級化指向
に伴い、耐摩耗性のみならず耐肌荒性に対する要求が一
層強くなっている。特に、低温高圧下圧延時やステンレ
ス圧延時などにおいては、ロールと圧延材間の保護皮膜
となる、ロール表面にイ・1着するスケール(黒皮)の
生成が少なく、従来の高Cr鋳鉄材では熱疲労と塑性流
動による肌荒れが大となり、圧延製品表面状況を著しく
損なう場合がある。例えば、第7図は、ステンレス圧延
時に従来の複合歯Cr鋳鉄ロール(2,7’5%C1I
8%Cr)を仕り曲設に使用した後のロール組を示す表
面写真であるが、塑性流動による肌荒れが大で、一部に
は焼付きも発生していることが判る。
この対策として、ステンレス圧延時においては、1’J
+G 鋳鉄ロールを使用したり、−;πく、黒鉛晶出型
の高Crが適用されたりしている。
これらの N1−G鋳鉄ロール及び黒鉛晶出型の高Cr
ロールは、いずれも組織中に品析出している黒鉛の自己
潤滑作用により肌荒れを防止するものとされているが、
その反面、黒鉛粒はロール組織の脱落、はく離の起点と
なるので、従来の複合歯Cr鋳鉄ロールに比べて著しく
耐摩耗性に劣るという欠点を有している。Recently, the front stage of the hot strip mill has a compound height of C.
rThe cast iron roll is an adamite roll (1.6~1.8%G
, 0.8-1.5% Cr). Additionally, composite high Cr cast iron rolls are beginning to be used in the middle and later stages of finishing. Commonly used composite height C rolls for hot rolling are
The chemical composition of the outer layer material is in the range A of the Fc-CrC system phase diagram (liquidus diagram) shown in Figure 1 (2.3 to 3.1% C11
3 to 23% Cr, Cr/C ratio -5.5 to 7.5), and 20 to 35 volume% Cr co-synthetic carbide M t c 3
It has a finely dispersed structure, and is characterized by excellent wear resistance. However, with the recent trend toward higher surface quality of rolled products, the demand for not only wear resistance but also roughness resistance is becoming stronger. In particular, during low-temperature, high-reduction rolling or stainless steel rolling, there is less scale (black scale) that forms on the roll surface, which forms a protective film between the roll and the rolled material. In this case, roughness due to thermal fatigue and plastic flow becomes severe, and the surface condition of the rolled product may be significantly impaired. For example, Fig. 7 shows a conventional composite tooth Cr cast iron roll (2,7'5% C1I roll) during stainless steel rolling.
This is a surface photograph showing a roll set after using 8% Cr) for finishing and bending, and it can be seen that the surface roughness due to plastic flow is severe and seizure has also occurred in some parts. As a countermeasure for this, when rolling stainless steel, 1'J
+G cast iron rolls are used, -;π and graphite crystallized high Cr rolls are used. These N1-G cast iron rolls and graphite crystallized high Cr
All rolls are said to prevent rough skin due to the self-lubricating effect of graphite precipitated in the structure.
On the other hand, since the graphite grains become a starting point for shedding and flaking of the roll structure, it has the disadvantage of being significantly inferior in wear resistance compared to conventional composite tooth Cr cast iron rolls.
【発明の解決すべき課題】
本発明は、Cr共共成炭化物よる高Cr鋳鉄材本来の耐
摩耗性を全く阻害せずに、基地組織の特性を改りして、
ロールと圧延材間の摩擦係数μを軽減することにより、
耐摩耗性及び耐肌荒性に優れた複合歯Cr鋳鉄ロールを
提供しようとするものである。Problems to be Solved by the Invention The present invention aims to improve the characteristics of the matrix structure without impairing the inherent wear resistance of high Cr cast iron material due to Cr co-synthetic carbides.
By reducing the friction coefficient μ between the roll and the rolled material,
The object of the present invention is to provide a composite tooth Cr cast iron roll with excellent wear resistance and surface roughness resistance.
本発明者は、先ずホットストリップミルの各スタンドに
おける高Cr鋳鉄ロールとN1−G鋳鉄ロールの摩耗量
及びロールと圧延材間の全摩擦仕事W「との関係を調べ
、これを第2図a、bに示した。
全摩擦仕事W「は、圧延負荷条件により次式を用いて求
めたものである。
Wf= μ Pm Vr Tr
ここで、pH1は平均圧延圧力
Vrはロールと圧延材の相対速度の絶
対値の平均値
Trはロールと圧延材の接触時間
μ は一般的な値として0.3を用いた。
第2図に示されているように、ロールの摩耗量がWrに
略々比例していること、又W「の大きいスタンドの肌荒
れが大であることから、本発明者は、ロール材の固有の
特性であるμを軽減した[l−ル材が前記本発明の[1
的達成に打効であると考え、これを基礎として総合的な
最適条件設定について研究を進めた。その結果、複合ロ
ールの外層材として、Cr共共成炭化物20〜37而積
%含有させることにより耐摩耗性を維持せしめるととも
に、Cr/C比を従来の高Cr鋳鉄材とは異なる範囲で
ある3〜5とすることによりμの軽減を図り、耐摩耗性
及び耐肌荒性を共に改善することに成功したものである
。
即し、本発明は、C2,5〜3.5%、Si 2.0%
以下、Mn 2.0%以下、Ni 5.0%以F1Cr
9.0〜16.0%、MoもしくはWl、0〜4.0
%、■ もしくはNb1.0%以下を含み、残部がFe
及び不可避的不純物であり、且つCr及びCの比(Cr
/C)が3〜5の範囲にある高Cr鋳鉄材を外層材とし
、高級鋳鉄、球状黒鉛鋳鉄もしくは鋳鋼を内層材とした
、耐摩耗性及び耐肌荒性に優れた圧延用複合歯Cr鋳鉄
ロールを要旨とするものである。The present inventor first investigated the relationship between the wear amount of the high Cr cast iron roll and the N1-G cast iron roll in each stand of a hot strip mill and the total frictional work W' between the roll and the rolled material, and calculated this as shown in Figure 2a. , b. The total frictional work W' is calculated using the following formula according to the rolling load conditions. Wf = μ Pm Vr Tr Here, pH 1 is the average rolling pressure Vr is the relative The average value Tr of the absolute value of the speed and the contact time μ between the roll and the rolled material were set to 0.3 as a general value.As shown in Figure 2, the wear amount of the roll is approximately equal to Wr. Since the roughness of the surface of stands with a large W' is large, the present inventors have reduced μ, which is an inherent characteristic of roll materials.
Based on this, we conducted research on setting comprehensive optimal conditions. As a result, the outer layer material of the composite roll maintains wear resistance by containing 20 to 37% by volume of Cr co-synthetic carbide, and has a Cr/C ratio in a range different from that of conventional high Cr cast iron materials. By setting the value to 3 to 5, we succeeded in reducing μ and improving both wear resistance and roughness resistance. That is, in the present invention, C2.5 to 3.5%, Si 2.0%
Below, Mn 2.0% or less, Ni 5.0% or more F1Cr
9.0-16.0%, Mo or Wl, 0-4.0
%,■ or containing 1.0% or less of Nb, with the balance being Fe
and unavoidable impurities, and the ratio of Cr and C (Cr
/C) is a high Cr cast iron material in the range of 3 to 5 as the outer layer material, and the inner layer material is high-grade cast iron, spheroidal graphite cast iron, or cast steel.Composite Cr tooth for rolling with excellent wear resistance and roughness resistance. The gist is cast iron rolls.
従来の高Cr鋳鉄ロール材のC及びCrが、第1図中の
領域への範囲に限定されてきたのは、耐摩耗性の向上が
要求される中で、実機ミルにおける試行錯誤を経て設定
されたものではあるが、主として次の理由によるものと
考えられる。
まず、従来の高Cr鋳鉄ロール材におけるCr/C比が
5.5〜7.5の範囲にあるのは、第3図に示すように
Cr/C比が6近傍で最高の焼入れ硬さが得られるため
に、耐摩耗性を重点指向する場合にはこの範囲のCr/
C比にするのが効果的であったためである。
又、Cr共品炭化物量%Kが20〜35面積%の範囲に
限定されてきた理由は、第4図に示すように、%Kが2
0面積%以下では耐摩耗性が低下しはじめること、%K
が35面積%以」二では、第1図中のa−1)線(γ−
M 7 G−共晶線)を超えて粗大な初晶炭化物を晶出
して耐摩耗性及び強靭性が著しく劣化することによる。
尚、第4図の試験はアl、スラー型高温摩耗試験機によ
るもので、相手材温度が800℃、線圧20 kg/
mm、すべり率2%、又摩耗量の測定はlXl0’回転
接触後に測定した。
このような従来の高Cr鋳鉄ロール材は、基地組織が6
0〜80%も占めるので、基地組織の性状を変えること
により耐摩耗性及び耐肌荒性の改みを図る試みも一部な
されている。しかしながらごれらの試みは熱処理により
基地組織中の残留オーステナイト!+1を減少させるよ
うなことにとどまり、抜本的に基地組織、ひいてはロー
ル材の特性を変化させるものではない。
そこで本発明者は、鋭意研究を進めた結果、従来の高C
r鋳鉄材よりもCr/C比を小さくすることにより、基
地組織即ち高Cr鋳鉄材の特性が粁しく改善されること
を見出した。
即ち第5図は、高Cr鋳鉄の基地中のC量とCr1C比
との関係を示すものであるが、G rl C比が小さい
程基地中のC,8を即ち圧延材との親和性の小さい析出
炭化物量が増し、摩擦係数μが小さくなる可能性がある
ことを示している。
第6図は、Crl C比と摩耗量及びμの関係を示ずも
のであるが、この図から明らかなように、Cr/C比が
3〜5の範囲でμが最小となり、耐摩耗性も向上してい
ることがわかる。なお、CrlC比が3未満で耐摩耗性
が劣化しているのは、Fc共共成炭化物 M G C型
)が混在してきて炭化物が粗大、軟質化するためと黒鉛
が晶析用するためである。第6図の試験は第4図と同様
の試験機を用いた。The reason why C and Cr in conventional high Cr cast iron roll materials have been limited to the range shown in Figure 1 is because they were set through trial and error in actual mills as improvements in wear resistance were required. This is thought to be mainly due to the following reasons. First of all, the reason why the Cr/C ratio in conventional high Cr cast iron roll materials is in the range of 5.5 to 7.5 is that, as shown in Figure 3, the highest quenching hardness is achieved when the Cr/C ratio is around 6. Therefore, when aiming at wear resistance, Cr/
This is because setting the ratio to C was effective. Also, the reason why the Cr-component carbide amount %K has been limited to the range of 20 to 35 area % is because %K is 2 as shown in Figure 4.
Wear resistance begins to decrease below 0 area%, %K
35 area% or more"2, line a-1) (γ-
This is because coarse primary carbides are crystallized beyond the M 7 G-eutectic line, resulting in significant deterioration of wear resistance and toughness. The test shown in Fig. 4 was conducted using an aluminum slurry type high-temperature wear tester, and the temperature of the mating material was 800°C and the linear pressure was 20 kg/
mm, slip rate of 2%, and wear amount were measured after lXl0' rotational contact. Such conventional high Cr cast iron roll material has a base structure of 6
Since it accounts for as much as 0 to 80%, some attempts have been made to improve the wear resistance and roughness resistance by changing the properties of the matrix structure. However, Goret et al.'s attempt was to remove retained austenite in the base structure through heat treatment. It only decreases the +1 and does not fundamentally change the base structure or the properties of the roll material. Therefore, as a result of intensive research, the present inventor discovered that the conventional high-C
It has been found that by making the Cr/C ratio smaller than that of the r-cast iron material, the matrix structure, that is, the properties of the high-Cr cast iron material, can be significantly improved. In other words, Fig. 5 shows the relationship between the amount of C in the base of high Cr cast iron and the Cr1C ratio. This indicates that the amount of small precipitated carbides increases and the friction coefficient μ may become smaller. Although Figure 6 does not show the relationship between the CrlC ratio, the amount of wear, and μ, it is clear from this figure that μ is minimum when the Cr/C ratio is in the range of 3 to 5, and the wear resistance is It can be seen that the results have also improved. In addition, the reason why the wear resistance deteriorates when the CrlC ratio is less than 3 is because the carbide becomes coarse and soft due to the mixture of Fc co-conjugated carbide (MG C type) and because graphite is used for crystallization. be. The test shown in FIG. 6 used a testing machine similar to that shown in FIG. 4.
次に本発明における外層材の各成分の限定理由について
述べる。
C及びCrの関係
」二足の理由により、基本的考え方として、%Kが20
〜37而積%の範囲で、かつCr/C比が3〜5の範囲
になるようにC及びCrの量を限定したものである。
C; 2.5〜3.5%
必要な耐摩耗性を維持しうる2、5%(20%K)を下
限とし、粗大な初晶炭化物の晶出しない3.5%(37
%K)を−L限とする。
Cr ; 9.0〜1 6.0%
Crの含有量は9.0%以上とし、かつCr/C比の下
限を3とすることにより、耐摩耗性を阻害する黒鉛を晶
析用することなしに、微細なCr共共成炭化物分散した
組織が得られる。又、Crのrll及びCr1C比の1
−限をそれぞれ16.0%及び5とすることにより、[
」的とする/7の小さい高Cr鋳鉄材かえられる。
第1図中の領域Bは、以−ヒに述べたC及びCrの範囲
を示したものである。
Si ; 2.0%以下
Siは、脱酸調整及び焼入性改善の補助のために必要で
あるが、2.0%を超えると黒鉛の晶出があり耐摩耗性
を著しく劣化させるので2.0%を」二限とする。
Mn及びNi ; 2.0%以下及び5.0%以上Mn
及びNiは焼入性改丹に有効であるが、Mnは2.0%
以−1−で靭性の劣化が激し7くなるので2.0%をL
限とする。Niは5,0%を超えるとMs点が低くなり
すぎて製造時に割れが生じ易くなり、又、残留オーステ
ナイトも安定化し耐肌荒性を阻害させるので5.0%以
下とする。
Mo及びW;1.0〜4.0%
Moは、Mn及びNiのように残留オーステナイトを安
定化さ什ずに焼入性を改善し、焼もどし抵抗を大にする
とともに炭化物を硬質化するのにイf効であるので積極
的に含有させる。 1.0%以」二のMoの添加でFT
効であるが、4.0%を超える添加は過剰でありコスト
高にもなるのでその範囲は1.0〜4.0%とする。
WはMoと同様の効果を有するので、Moの一部もしく
は全部に代えて両者の合計rt’Lが4.0%まで添加
することができる。
N b及びV;1.0%以下
Nb及び■は共に炭化物の微細化、高硬度化に効果があ
るので夫々単独又は併用で1.0%以下添加する。1.
0%を超えて含有させても効果は増大せずコスト高にな
る。
本発明の複合[J−ルにおける内層材としては、この種
の内層材として通常用いられる材質即ち、高級鋳鉄、球
状黒鉛鋳鉄もしくは鋳鋼が採用され又、複合ロールの製
造法としては公知の遠心鋳造法等が用いられる。
本発明における外層材の表面硬度は用途によって異なる
が、概ねl1s70〜80の範囲で適宜選択される。
本発明の複合歯Cr鋳鉄ロールは、主として熱間圧延用
複合高、特にホットストリップミルのワークロールとし
て有用であるが、これらに限定されるものではなく、例
えば実施例2に示す如く、冷間圧延用複合高としてもそ
の効果を発揮するものである。Next, the reason for limiting each component of the outer layer material in the present invention will be described. The basic idea is that %K is 20 due to two reasons:
The amounts of C and Cr are limited so that the Cr/C ratio is in the range of 3 to 5. C; 2.5 to 3.5% The lower limit is 2.5% (20% K) that can maintain the necessary wear resistance, and 3.5% (37% K) that does not crystallize coarse primary carbides.
%K) is the −L limit. Cr; 9.0 to 1 6.0% By setting the Cr content to 9.0% or more and setting the lower limit of the Cr/C ratio to 3, graphite that inhibits wear resistance can be used for crystallization. A structure in which fine Cr co-formed carbides are dispersed can be obtained without the use of Cr. Moreover, rll of Cr and 1 of Cr1C ratio
- By setting the limits to 16.0% and 5, respectively, [
” /7 small high Cr cast iron materials can be changed. Region B in FIG. 1 shows the range of C and Cr described below. Si: 2.0% or less Si is necessary for adjusting deoxidation and assisting in improving hardenability, but if it exceeds 2.0%, graphite crystallization occurs and wear resistance is significantly deteriorated. The second limit is 0%. Mn and Ni; 2.0% or less and 5.0% or more Mn
and Ni are effective in improving hardenability, but Mn is 2.0%
In -1-, the toughness deteriorates severely and becomes 7, so 2.0% is added to L.
limited. If Ni exceeds 5.0%, the Ms point becomes too low and cracks are likely to occur during manufacturing, and retained austenite also stabilizes and impedes roughness resistance, so the content should be 5.0% or less. Mo and W; 1.0 to 4.0% Mo improves hardenability without stabilizing retained austenite like Mn and Ni, increases tempering resistance, and hardens carbides. Since it is effective, it is actively included. FT with the addition of Mo of 1.0% or more
However, adding more than 4.0% is excessive and increases costs, so the range is set to 1.0 to 4.0%. Since W has the same effect as Mo, it can be added in place of part or all of Mo up to a total rt'L of 4.0%. Nb and V: 1.0% or less Nb and V are both effective in refining carbides and increasing hardness, so they are added individually or in combination in an amount of 1.0% or less. 1.
Even if the content exceeds 0%, the effect will not increase and the cost will increase. As the inner layer material in the composite roll of the present invention, materials commonly used for this type of inner layer material, such as high-grade cast iron, spheroidal graphite cast iron, or cast steel, are used, and the method for manufacturing the composite roll is known centrifugal casting. Law etc. are used. The surface hardness of the outer layer material in the present invention varies depending on the use, but is approximately selected as appropriate within the range of l1s 70 to 80. The composite tooth Cr cast iron roll of the present invention is useful mainly as a work roll for hot rolling, especially for hot strip mills, but is not limited thereto. It also exhibits its effect as a composite height for rolling.
実施例1
0−ル胴径φ768、胴長1780(2,全長3824
12の熱間圧延仕上用ワークロールを2本、F記のよう
にして製造した。
(a)外層材として、表1に示す化学成分の高Cr鋳鉄
材溶湯と、内層材として球状黒鉛鋳鉄溶湯を用いて、通
常の遠心鋳造法により複合ロールを製造した。
(b)鋳放し後、所定の熱処理及び機械加工を行って最
終製品複合ロールを得た。尚、ロール1及び2の表面硬
さは夫々l−1s72.3及び75.0であり、目的と
する硬さが得られている。
このようにして製造されたロールを熱間圧延仕上前段で
ステンレス圧延時に使用したところ、第8図に示すよう
に、塑性流動及び焼付きなどによる肌荒れの全く認めら
れない美麗なロール肌が得られた。又、表2に示すよう
に、昔通調圧延時においても、耐摩耗性も従来の高Cr
鋳鉄ロール及び黒鉛晶出空高Crロールに比べて優れて
いることが確認された。
(以下 余白)
表1 実施例!の外層材の化学成分およびCr/C比、
%に表2 本発明ロールと他ロールとの耐摩耗性の比較
実施例2
0−ル胴経φ480、胴長260り、全長900Qの製
管用冷間圧延ロールを2本、外層材として表3に示す成
分の高Cr鋳鉄材、内層材として球状黒鉛鋳鉄を用いて
、実施例1と同様にして製造した。
得られたロールを萌記目的に使用したところ、耐摩耗性
の大幅な向」ユとともに、板端部との接触位置の焼付き
疵の解消がみられた。
(以下 余白)
表3 実施例2の外層材の化学成分およびCr/C比、
%にExample 1 0-le body diameter φ768, body length 1780 (2, total length 3824
Two No. 12 hot rolling finishing work rolls were manufactured as described in F. (a) A composite roll was manufactured by a normal centrifugal casting method using a high Cr cast iron molten metal having the chemical composition shown in Table 1 as an outer layer material and a spheroidal graphite cast iron molten metal as an inner layer material. (b) After being cast, predetermined heat treatment and machining were performed to obtain a final product composite roll. The surface hardness of rolls 1 and 2 was l-1s 72.3 and 75.0, respectively, and the desired hardness was obtained. When the roll manufactured in this manner was used during stainless steel rolling in the pre-hot rolling finishing stage, as shown in Figure 8, a beautiful roll surface was obtained with no roughness due to plastic flow or seizure. Ta. In addition, as shown in Table 2, even during regular rolling, the wear resistance was lower than that of conventional high Cr.
It was confirmed that the roll was superior to cast iron rolls and graphite crystallization height Cr rolls. (See margin below) Table 1 Examples! The chemical composition and Cr/C ratio of the outer layer material,
Table 2 Comparative Example 2 of abrasion resistance between rolls of the present invention and other rolls Two cold rolling rolls for pipe making with a diameter of 480 mm, a length of 260 mm, and a total length of 900 Q were used as outer layer materials in Table 3 It was manufactured in the same manner as in Example 1 using a high Cr cast iron material having the components shown in and spheroidal graphite cast iron as the inner layer material. When the obtained roll was used for printing purposes, it was found that the wear resistance was significantly improved and the seizure flaws at the contact position with the plate edge were eliminated. (The following is a blank space) Table 3 Chemical composition and Cr/C ratio of the outer layer material of Example 2,
to %
第1図は、Fe−Cr−C系状態図(液相線図)におい
て、従来の高Cr鋳鉄材の化学成分の領域A及び本発明
の高Cr鋳鉄材の化学成分の領域Bを示すグラフ、
第2図a及びbは、ホットストリップミルの各スタンド
におけるロールの摩耗量及び全摩擦仕事を示すグラフ、
第3図は、高Cr鋳鉄材におけるCr/C比と焼入れ硬
さの関係を示すグラフ、
第4図は、高Cr鋳鉄材のCr共品炭化物%にと摩擦量
の関係を示すグラフ、
第5図は、高Cr鋳鉄材におけるCr/C比と基地中の
C?+にの関係を示すグラフ、
第6図は、高Cr鋳鉄材のCr/C比と摩耗特性の関係
を示すグラフ、
第7図は、従来の複合高Cr鋳鉄ロールのステンレス圧
延時における肌荒れ状況を示す表面写真、第8図は、本
発明ロールのステンレス圧延時における表面写真である
。
第1図
z
第 2図
〜
スタンド
第3図
第4図
10K
第5図
第6図゛
crlc比
図面の浄書
第8図
手続補正書(自発)
昭和63年IJ12γ日
1、事件の表示
昭和62年特許願第321939号
2、発明の名称
圧延用複合高
3、補正をする者
4、代理人
住所 東京都千代田区丸の内二丁目4番1号第1図
θ ノ02.θ 30 4.
0 5.DC′/ζFIG. 1 is a graph showing the chemical composition region A of the conventional high Cr cast iron material and the chemical composition region B of the high Cr cast iron material of the present invention in the Fe-Cr-C system phase diagram (liquidus diagram). , Figure 2 a and b are graphs showing the amount of roll wear and total frictional work in each stand of a hot strip mill, Figure 3 shows the relationship between Cr/C ratio and quenching hardness in high Cr cast iron material. Figure 4 is a graph showing the relationship between Cr co-product carbide % of high Cr cast iron material and amount of friction. Figure 5 is a graph showing the relationship between the Cr/C ratio in high Cr cast iron material and C in the matrix. Figure 6 is a graph showing the relationship between Cr/C ratio and wear characteristics of high Cr cast iron materials. Figure 7 is a graph showing the rough surface of a conventional composite high Cr cast iron roll during stainless steel rolling. FIG. 8 is a surface photograph of the roll of the present invention during stainless steel rolling. Figure 1 z Figure 2 ~ Stand Figure 3 Figure 4 Figure 10K Figure 5 Figure 6 Engraving of CRLC drawings Figure 8 Procedural amendment (voluntary) IJ12γ Day 1, 1985, Indication of incident 1988 Patent Application No. 321939 2, Name of the invention: Composite height for rolling 3, Person making the amendment 4, Agent address: 2-4-1 Marunouchi, Chiyoda-ku, Tokyo, Figure 1 θ No. 02. θ 30 4.
0 5. DC′/ζ
Claims (1)
以下、Ni5.0%以下、Cr9.0〜16.0%、M
oもしくはW1.0〜4.0%、VもしくはNb1.0
%以下を含み、残部がFe及び不可避的不純物であり、
かつCr及びC量の比(Cr/C)が3〜5の範囲にあ
る高Cr鋳鉄材を外層材とし、高級鋳鉄、球状黒鉛鋳鉄
もしくは鋳鋼を内層材とした、耐摩耗性及び耐肌荒性に
優れた圧延用複合高Cr鋳鉄ロール。C2.5-3.5%, Si2.0% or less, Mn2.0%
Below, Ni5.0% or less, Cr9.0-16.0%, M
o or W1.0-4.0%, V or Nb1.0
% or less, the remainder being Fe and unavoidable impurities,
The outer layer material is a high Cr cast iron material with a ratio of Cr and C content (Cr/C) in the range of 3 to 5, and the inner layer material is high-grade cast iron, spheroidal graphite cast iron, or cast steel, which has wear resistance and roughness resistance. Composite high Cr cast iron roll for rolling with excellent properties.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP32193987A JPH01162745A (en) | 1987-12-19 | 1987-12-19 | Roll for rolling |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP32193987A JPH01162745A (en) | 1987-12-19 | 1987-12-19 | Roll for rolling |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH01162745A true JPH01162745A (en) | 1989-06-27 |
Family
ID=18138106
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP32193987A Pending JPH01162745A (en) | 1987-12-19 | 1987-12-19 | Roll for rolling |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH01162745A (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0364443A (en) * | 1989-08-02 | 1991-03-19 | Hitachi Ltd | Composite roll for rolling and its manufacture |
BE1006356A3 (en) * | 1991-12-19 | 1994-08-02 | Fond Marichal Ketin & Cie Sa D | Bimetal working cylinder for hot rolling of steel strips |
WO2019109138A1 (en) * | 2017-12-04 | 2019-06-13 | Weir Minerals Australia Limited | Tough and corrosion resistant white cast irons |
-
1987
- 1987-12-19 JP JP32193987A patent/JPH01162745A/en active Pending
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0364443A (en) * | 1989-08-02 | 1991-03-19 | Hitachi Ltd | Composite roll for rolling and its manufacture |
BE1006356A3 (en) * | 1991-12-19 | 1994-08-02 | Fond Marichal Ketin & Cie Sa D | Bimetal working cylinder for hot rolling of steel strips |
WO2019109138A1 (en) * | 2017-12-04 | 2019-06-13 | Weir Minerals Australia Limited | Tough and corrosion resistant white cast irons |
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