JPH0534413B2 - - Google Patents
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- Publication number
- JPH0534413B2 JPH0534413B2 JP63241249A JP24124988A JPH0534413B2 JP H0534413 B2 JPH0534413 B2 JP H0534413B2 JP 63241249 A JP63241249 A JP 63241249A JP 24124988 A JP24124988 A JP 24124988A JP H0534413 B2 JPH0534413 B2 JP H0534413B2
- Authority
- JP
- Japan
- Prior art keywords
- roll
- hardness
- content
- amount
- graph showing
- 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.)
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- 239000000463 material Substances 0.000 claims description 46
- 229910052804 chromium Inorganic materials 0.000 claims description 8
- 238000005098 hot rolling Methods 0.000 claims description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims description 7
- 229910052710 silicon Inorganic materials 0.000 claims description 5
- 229910052721 tungsten Inorganic materials 0.000 claims description 5
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- 239000011651 chromium Substances 0.000 description 13
- 239000011162 core material Substances 0.000 description 11
- 230000000694 effects Effects 0.000 description 9
- 239000011159 matrix material Substances 0.000 description 9
- 229910001018 Cast iron Inorganic materials 0.000 description 8
- 238000010438 heat treatment Methods 0.000 description 8
- 229910052751 metal Inorganic materials 0.000 description 8
- 239000002184 metal Substances 0.000 description 8
- 238000004519 manufacturing process Methods 0.000 description 7
- 150000001247 metal acetylides Chemical class 0.000 description 6
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 5
- 238000005336 cracking Methods 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 239000011733 molybdenum Substances 0.000 description 4
- 239000010955 niobium Substances 0.000 description 4
- -1 C 3 carbides Chemical class 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 239000002131 composite material Substances 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 239000011572 manganese Substances 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 230000003746 surface roughness Effects 0.000 description 3
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 3
- 239000010937 tungsten Substances 0.000 description 3
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 3
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 239000010941 cobalt Substances 0.000 description 2
- 229910017052 cobalt Inorganic materials 0.000 description 2
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000013011 mating Effects 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 206010013786 Dry skin Diseases 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000007373 indentation Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000007788 roughening Methods 0.000 description 1
- 238000004439 roughness measurement Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 238000004227 thermal cracking Methods 0.000 description 1
- 230000004584 weight gain Effects 0.000 description 1
- 235000019786 weight gain Nutrition 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)
Description
〔産業上の利用分野〕
本発明は耐摩耗性の高い熱間圧延用の鋳鉄ロー
ル材に関する。
〔従来の技術〕
熱間圧延用ロール材としては、高温度における
耐摩耗性、耐熱亀裂性が特に要求される。従来こ
の用途のロールの材質としては、例えばＣ：3.3
％、Si：0.75％、Mn：0.6％、Ni0.5％、Cr：1.6
％、Mo：0.4％、残余はFeおよび通常の不純物か
らなる合金であり、その硬さはせいぜいHs85が
限度である。しかし現下の圧延における生産性の
向上を目的とするために、さらに高硬度の耐摩耗
性のあるロールが要求されてきている。
〔発明が解決しようとする課題〕
ところで、硬さHs85以上のロールを製造する
とすれば、主として製造時の残留応力の点から、
複合構造による製法は困難となり、組立ロール構
造を採用する必要がある。このような組立ロール
構造の場合は、例えば焼ばめの場合は、円周方向
にロールリングを張割する焼ばめ応力が作用す
る。又圧延荷重の作用で、ロールリング内面に前
記焼ばめ応力と同方向に応力が発生する。この応
力は、従来の一体ロールには見られなかつた応力
であり、この応力の発生により、組立ロールでは
耐摩耗性のみならず、これらの応力に耐えるため
に引張り強さや靭性等も高い値が要求される。
例えば、チルド鋳物で採用している方法である
が、鋳鉄の硬さを増すためには、構成中のＣを炭
化物、主としてFe3Cにする方法がある。この炭
化物は基地に比し非常に硬いため、この炭化物を
増加させると硬さの増加とともに耐摩耗性は向上
するが材料の強度、靭性を著しく低下させ、また
高温域での耐熱亀裂性についても問題があり、高
温域で使用されるロールの寿命が短かくなるとい
う問題点があつた。
本発明は高温での耐摩耗性、耐熱亀裂性に優
れ、かつ耐酸化性を向上させた熱間圧延用ロール
材を提供する。
〔課題を解決するための手段〕
本発明は、Ｃ：1.0〜2.4％、Si：0.3〜2.0％、
Mn：0.3〜1.5％、Cr：4.0〜1.0％、Mo：3.0〜10
％、Ｗ：3.0〜10％、Ｖ：2.5〜10％、Co：5.0〜
10％、Ni：≦1.0％、Nb：≦3.0％、残部はFeお
よび不可避不純物からなる熱間圧延用ロール材で
ある。
〔作用〕
以下本発明の鋳鉄ロールについて詳細に説明す
る。先ず本発明において、上記のような成分に限
定した理由について説明する。
Ｃの含有量を1.0〜2.4％としたものは、炭素は
焼入れ性を上げる重要な元素で、マトリツクス硬
さを上昇させる。またニオブ、バナジウム、クロ
ム、モリブデン、タングステンと化合し、硬度の
高いMC系炭化物、M3C、M7C3系の炭化物を晶
出、析出させ、耐摩耗性を向上させる。下限１％
は、それ以下では炭化物の量が少なく、マトリツ
クスも焼きが入り難く、硬度が低くなる。上限の
2.4％は、これ以上の添加では炭化物量が多くな
り過ぎ、強度、靭性が落ち、ロール品質も悪くな
る。またロール製造技術上難しくなる。
Siの含有量を0.3〜2.0％としたのは、ケイ素は
鋳造性に影響し、少な過ぎると湯流れ性が悪くな
る。また、溶湯中の酸素と化合し脱酸効果もある
ため、0.3〜２％添加する。
Mnの含有量を0.3〜2.0％としたのは、マンガ
ンはケイ素と同様溶湯の酸素と化合し、ガス欠陥
を防止する。またMnSで溶湯中のＳを固定する
ため、0.3〜1.5％添加する。
Crの含有量を4.0〜10％としたのは、クロムは
炭素と同様マトリツクスの焼入れ性を向上させ、
硬度を上げる。またＣと炭化物をつくり、全体硬
度を上げる。Crは４％以上加えないとその効果
はなく、10％以上になると炭化物が粗大化し、熱
疲労特性が悪くなり、圧延使用中肌あれ等が発生
し、耐摩耗性が悪くなる。
Moの含有量を3.0〜10％としたのは、モリブデ
ンはマトリツクスの焼入れ硬度を上昇させる効果
的な元素である。またモリブデンは焼戻し抵抗性
の優れた元素であり、クロム、タングステンとと
もに高硬度の複合炭化物をつくり、高温硬度を上
げ耐摩耗性を向上させる。上限の10％以上になる
とその効果はほとんど変わらなくなる。
Ｗの含有量を3.0〜10％としたのは、タングス
テンはモリブデン同様マトリツクスの焼入れ性を
上げ、硬い炭化物をつくるが、その効果はMoよ
り低い。また10％以上になると粗大な樹枝状の炭
化物ができ、品質上悪影響を与える。
Ｖの含有量を2.5〜10％としたのは、バナジウ
ムは炭素と結合し、MC系の硬い微細な炭化物を
析出し、耐摩耗性を著しく改善させる。その量は
最低2.5％以上加えないと効果はない。10％以上
では炭化物量が増え過ぎ、マトリツクスの固溶Ｃ
量が減少するためマトリツクスを軟化させる。
また鋳造作業性においても、Ｖが10％以上にな
ると溶湯の湯流性を著しく悪くするため鋳造でき
なくなる。
Coの含有量を5.0〜10％としたのは、コバルト
はニツケルと同じ効果を有し、焼入れ性を向上さ
せ、マトリツクス組織を緻密にし、マトリツクス
硬度を上げ高温硬度を上げる効果がある。またバ
ナジウムを多量に含む材料にコバルトを入れると
熱処理中のスケール発生防止に効果がある。
Niの含有量を≦1.0％としたのは、ニツケルは
出来るだけ少ない方が好ましいが、1.0％以下で
あればあまり悪影響がないため１％以下とする。
Nbの含有量を≦3.0％としたのは、ニオブは
MC系炭化物を形成し、安定な炭化物を形成さ
せ、耐摩耗性を向上させる。
〔実施例〕
次に本発明の実施例として、第１表に示す成分
のHC（高クロム）材、従来材、本発明材の鋳鉄
ロールについて、各種試験をおこなつた結果を図
示する。
[Industrial Application Field] The present invention relates to a cast iron roll material for hot rolling that has high wear resistance. [Prior Art] Roll materials for hot rolling are particularly required to have wear resistance and heat cracking resistance at high temperatures. Conventionally, the material of the roll for this purpose is, for example, C: 3.3.
%, Si: 0.75%, Mn: 0.6%, Ni 0.5%, Cr: 1.6
%, Mo: 0.4%, the remainder is an alloy consisting of Fe and normal impurities, and its hardness is at most Hs85. However, in order to improve productivity in current rolling, rolls with even higher hardness and wear resistance are required. [Problem to be solved by the invention] By the way, if a roll with a hardness of Hs85 or higher is manufactured, mainly from the viewpoint of residual stress during manufacturing,
Manufacturing methods using composite structures are difficult, and it is necessary to adopt an assembled roll structure. In the case of such an assembled roll structure, for example, in the case of shrink fit, a shrink fit stress that stretches the roll ring in the circumferential direction acts. Further, due to the action of the rolling load, stress is generated on the inner surface of the roll ring in the same direction as the shrink fit stress. This stress is not seen in conventional integral rolls, and due to the occurrence of this stress, assembled rolls must not only have high wear resistance but also high tensile strength and toughness in order to withstand these stresses. required. For example, in order to increase the hardness of cast iron, a method used in chilled castings is to replace C in the composition with carbide, mainly Fe 3 C. This carbide is extremely hard compared to the base material, so increasing the amount of this carbide increases the hardness and improves the wear resistance, but it also significantly reduces the strength and toughness of the material, and also reduces the thermal cracking resistance at high temperatures. There was a problem in that the lifespan of rolls used in high temperature ranges was shortened. The present invention provides a roll material for hot rolling that has excellent wear resistance and heat cracking resistance at high temperatures and improved oxidation resistance. [Means for solving the problem] The present invention provides C: 1.0 to 2.4%, Si: 0.3 to 2.0%,
Mn: 0.3~1.5%, Cr: 4.0~1.0%, Mo: 3.0~10
%, W: 3.0~10%, V: 2.5~10%, Co: 5.0~
10%, Ni: ≦1.0%, Nb: ≦3.0%, and the remainder is Fe and unavoidable impurities. [Function] The cast iron roll of the present invention will be explained in detail below. First, the reason why the present invention is limited to the above components will be explained. When the C content is 1.0 to 2.4%, carbon is an important element that increases hardenability and increases matrix hardness. It also combines with niobium, vanadium, chromium, molybdenum, and tungsten to crystallize and precipitate highly hard MC carbides, M 3 C, and M 7 C 3 carbides, improving wear resistance. Lower limit 1%
If the amount is less than that, the amount of carbide will be small, the matrix will be difficult to burn, and the hardness will be low. upper limit
If 2.4% is added, the amount of carbide becomes too large, strength and toughness decrease, and roll quality also deteriorates. Moreover, it becomes difficult in terms of roll manufacturing technology. The reason why the Si content is set to 0.3 to 2.0% is because silicon affects castability, and if it is too small, the flowability will deteriorate. Additionally, since it combines with oxygen in the molten metal and has a deoxidizing effect, it is added in an amount of 0.3 to 2%. The reason for setting the Mn content to 0.3 to 2.0% is that manganese, like silicon, combines with oxygen in the molten metal to prevent gas defects. Also, in order to fix S in the molten metal with MnS, 0.3 to 1.5% is added. The reason for setting the Cr content to 4.0 to 10% is that chromium, like carbon, improves the hardenability of the matrix.
Increase hardness. It also forms carbides with C, increasing the overall hardness. Cr has no effect unless it is added in an amount of 4% or more, and if it exceeds 10%, carbides become coarse, thermal fatigue properties deteriorate, roughness occurs during rolling, and wear resistance deteriorates. The Mo content is set at 3.0 to 10% because molybdenum is an effective element that increases the hardness of the matrix. In addition, molybdenum is an element with excellent tempering resistance, and together with chromium and tungsten, it forms a highly hard composite carbide, increasing high-temperature hardness and improving wear resistance. If it exceeds the upper limit of 10%, the effect will hardly change. The W content is set to 3.0 to 10% because, like molybdenum, tungsten improves the hardenability of the matrix and creates hard carbides, but its effect is lower than that of Mo. Moreover, if it exceeds 10%, coarse dendritic carbides are formed, which has an adverse effect on quality. The reason why the V content is set to 2.5 to 10% is that vanadium combines with carbon to precipitate MC-based hard fine carbides, which significantly improves wear resistance. It will not be effective unless the amount is added at least 2.5%. If it exceeds 10%, the amount of carbide will increase too much and the solid solution C of the matrix will increase.
softens the matrix as the volume decreases. Also, in terms of casting workability, if V exceeds 10%, the flowability of the molten metal will be significantly impaired, making it impossible to cast. The reason for setting the Co content to 5.0 to 10% is that cobalt has the same effects as nickel, and has the effect of improving hardenability, making the matrix structure denser, increasing matrix hardness, and increasing high-temperature hardness. Additionally, adding cobalt to materials containing a large amount of vanadium is effective in preventing scale formation during heat treatment. The reason why the Ni content is set to ≦1.0% is that although it is preferable to have as little Ni as possible, if it is 1.0% or less, there is not much of a negative effect, so it is set to 1% or less. The reason for setting the Nb content to ≦3.0% is that niobium is
Forms MC-based carbide, forming stable carbide and improving wear resistance. [Example] Next, as an example of the present invention, the results of various tests conducted on cast iron rolls made of HC (high chromium) material, conventional material, and material of the present invention having the components shown in Table 1 are illustrated.
【表】
第１図はHC材３、従来材２、本発明材１につ
いて、温度に対する摩耗減量の比較を示すグラ
フ、第２図は加熱温度に対するクラツク深さの比
較を示すグラフ、第３図は温度にたいする硬度の
比較を示すグラフである。以上のグラフから判る
ように、本発明材１はHC材３、従来材２に比較
して何れも優れているいることが判る。
第４図は上記成分において、Coの含有量（％）
の変化に対するロールの各種特性を示すグラフで
あり、本図からは、Co量の増加とともに摩耗減
量１１酸化増量１２は小さくなるが、同時に硬度
１３、耐熱亀裂性１４も小さくなり、従つてCo
量は５〜10％の範囲が最適であることが判る。
第５図は上記成分において、Crの含有量（％）
の変化に対するロールの各種特性を示すグラフで
あり、本図からは、Cr量の増加とともに硬度１
３は増加するが炭化物サイズ15が粗大化し、また
耐熱亀裂性14が悪くなり、従つてCr量は４〜10
％の範囲が最適であることが判る。
第６図〜第８図は、HC鋳鉄３、従来材２、本
発明材１にて製作した第９図に示すロール試験材
２１について、摩耗量、肌荒れ、ロール表面の粗
度プロフイールを測定した結果をまとめたグラフ
および図面であり、この試験は、第９図に示すロ
ール配置にて、相手ロール２２としては軟鋼材
（SS−41）を使用し、次の条件にて試験をおこな
つた。
＜試験条件＞
相手ロール温度900℃、荷重300Kg
試験片温度500℃〜600℃
すべり率−10％
試験片回転速度100rpm
総回転数50000回
第６図は摩耗量を比較したグラフであり、本発
明材はHC鋳鉄およびい従来材と比較して摩耗量
は1/3〜1/2以下と、非常に少なくなる。また第７
図に示す肌荒れの比較においては、本発明材はそ
の荒れ具合（くぼみ）は1/4〜1/3以下となる。
第８図はロール表面の粗度プロフイールを示す
図面であり、本発明材１のロールにおいては他の
二者２，３に比較して表面は非常に滑らかであ
り、第６図および第７図に示すグラフの結果と併
せ考えても耐肌荒れ性は非常に良好なことが判
る。
以下本発明の熱間圧延用ロール材の製造法につ
いて説明する。
第１０図は本発明の熱間圧延用ロール材の製造
方法の一例を示す側断面図である。先ず内層にな
る鋼系材料の芯材３１を架台の上に垂直にセツト
し、芯材３１の外周部に外層材３２になる厚みだ
けの一定の〓間をあけて水冷モールド２５を配設
する。水冷モールド３５の上に耐火枠３９をセツ
トし、水冷モールド３５と耐火枠３９の間に〓間
がない様に固定する。加熱コイル３６はこの耐火
枠３９の外周に、また予熱コイル３６ａは耐火枠
３９の上部で芯材３１の周囲にセツトする。
外層材３２の鋳造に際して、まず芯材３１を上
昇させてスタートタブ３１ａのある芯材胴部下端
を水冷モールド３５内にセツトし、加熱コイル３
６と予熱コイル３６ａに通電し、芯材３１の表面
が所定の温度に達するまで加熱し、目標の温度に
達した時にロール外層材３２になる溶湯を、予め
溶解保持していた溶解炉から耐火枠３９内に注入
する。溶湯は芯材３１と水冷モールド３５の間〓
に流れこみ、水冷モールド３５の抜熱により黒鉛
リング３８を介して凝固する。
なお、外層溶湯と芯材３１の境界で溶着不良等
の欠陥がない健全な境界層を確保するため、予熱
コイル３６ａに所定の電流を流し、芯材３１を所
定の温度まで加熱し、耐火枠３９内容湯を加熱コ
イル３６で通電加熱しながら溶湯を撹拌、昇温し
て境界の溶着を円滑にし、一定の速度で芯材３１
を下降させ、連続的に複合ロールを製造する。
なお図中３１ｂはエンドタブ、４３は芯押し装
置である。
第２表には、上記製造方法における施工条件の
諸元の概要を示す。[Table] Figure 1 is a graph showing a comparison of wear loss with respect to temperature for HC material 3, conventional material 2, and inventive material 1. Figure 2 is a graph showing a comparison of crack depth with respect to heating temperature. Figure 3 is a graph showing a comparison of crack depth with respect to heating temperature. is a graph showing a comparison of hardness versus temperature. As can be seen from the graphs above, it can be seen that the material 1 of the present invention is superior to the HC material 3 and the conventional material 2. Figure 4 shows the Co content (%) in the above components.
It is a graph showing various characteristics of the roll with respect to changes in Co. From this figure, it can be seen that as the amount of Co increases, wear loss 11 and oxidation weight gain 12 become smaller, but at the same time, hardness 13 and heat cracking resistance 14 also become smaller.
It has been found that the optimum amount is in the range of 5 to 10%. Figure 5 shows the content (%) of Cr in the above components.
This is a graph showing various characteristics of rolls with respect to changes in Cr content.
3 increases, but the carbide size 15 becomes coarser and the heat cracking resistance 14 worsens, so the Cr content increases from 4 to 10.
% range is found to be optimal. Figures 6 to 8 show the amount of wear, surface roughness, and roll surface roughness profile measured for the roll test material 21 shown in Figure 9, which was manufactured using HC cast iron 3, conventional material 2, and inventive material 1. These are graphs and drawings summarizing the results, and this test was conducted with the roll arrangement shown in Figure 9, using mild steel material (SS-41) as the mating roll 22, and under the following conditions. . <Test conditions> Mating roll temperature 900°C, load 300Kg Test piece temperature 500°C to 600°C Slip rate -10% Test piece rotation speed 100 rpm Total number of rotations 50000 times Figure 6 is a graph comparing the amount of wear, and the present invention Compared to HC cast iron and conventional materials, the amount of wear is extremely low, 1/3 to 1/2 or less. Also the 7th
In the comparison of rough skin shown in the figure, the degree of roughness (indentation) of the material of the present invention is 1/4 to 1/3 or less. FIG. 8 is a drawing showing the roughness profile of the roll surface, and the surface of the roll of the invention material 1 is much smoother than that of the other two materials 2 and 3. When considered in conjunction with the results shown in the graph below, it can be seen that the skin roughness resistance is very good. The method for manufacturing the hot rolling roll material of the present invention will be explained below. FIG. 10 is a side sectional view showing an example of the method for manufacturing a roll material for hot rolling according to the present invention. First, a core material 31 made of steel material that will become the inner layer is set vertically on a frame, and a water-cooled mold 25 is placed around the outer periphery of the core material 31 with a certain distance equal to the thickness of the outer layer material 32. . A refractory frame 39 is set on the water-cooled mold 35 and fixed so that there is no gap between the water-cooled mold 35 and the refractory frame 39. The heating coil 36 is set on the outer periphery of this refractory frame 39, and the preheating coil 36a is set around the core material 31 at the upper part of the refractory frame 39. When casting the outer layer material 32, first the core material 31 is raised and the lower end of the core material body where the start tab 31a is located is set in the water cooling mold 35, and the heating coil 3
6 and the preheating coil 36a to heat the surface of the core material 31 until it reaches a predetermined temperature, and when the target temperature is reached, the molten metal that will become the roll outer layer material 32 is transferred from the melting furnace where it was previously melted and held. Inject into the frame 39. The molten metal is between the core material 31 and the water-cooled mold 35
It flows into the water-cooled mold 35 and solidifies through the graphite ring 38 due to heat removal from the water-cooled mold 35. In order to ensure a healthy boundary layer free of defects such as poor welding at the boundary between the outer molten metal and the core material 31, a predetermined current is passed through the preheating coil 36a to heat the core material 31 to a predetermined temperature, and the refractory frame is heated to a predetermined temperature. The molten metal 39 is stirred and heated while being electrically heated by the heating coil 36 to smooth the welding of the boundary, and the core material 31 is heated at a constant speed.
is lowered to continuously produce composite rolls. In addition, in the figure, 31b is an end tab, and 43 is a tailstock device. Table 2 summarizes the specifications of the construction conditions in the above manufacturing method.
以上説明したごとくに本発明による鋳鉄ロール
材によれば、従来のロール材に比し、耐摩耗性、
耐熱亀裂性、耐酸化性に優れるとともに耐肌荒れ
性もよくなり、従つて熱間圧延におけるワークロ
ールの寿命を向上させ、また良質の圧延材を得る
ことができる。
As explained above, the cast iron roll material according to the present invention has better wear resistance and better wear resistance than conventional roll materials.
It has excellent heat cracking resistance and oxidation resistance, and also has good surface roughening resistance, thus improving the life of work rolls in hot rolling and making it possible to obtain high-quality rolled materials.
第１図は各種ロール材の温度に対する摩耗減量
をあらわすグラフ、第２図は各種ロール材の加熱
温度におけるクラツク深さを示すグラフ、第３図
は各種ロール材のそれぞれの温度における硬度を
示すグラフ、第４図はCo含有量の変化に対する
ロールの各種特性を示すグラフ、第５図はCr含
有量の変化に対するロールの各種特性を示すグラ
フ、第６図はロール試験材による摩耗量測定結果
を示すグラフ、第７図はロール試験材による肌荒
れ測定結果を示すグラフ、第８図はロール試験材
のロール表面粗度の測定結果を示す図面、第９図
はロールの試験要領を示す側面図、第１０図は耐
摩耗鋳鉄ロールの製造方法の一例を示す側断面図
である。
１……本発明材、２……従来材、３……高クロ
ム鋳造材、２１……ロール試験材、２２……相手
材、３１……芯材、３２……外層材、３５……水
冷モールド、３６……加熱コイル、３６ａ……予
熱コイル、３９……耐火枠。
Figure 1 is a graph showing the wear loss of various roll materials with respect to temperature, Figure 2 is a graph showing the crack depth at various heating temperatures of roll materials, and Figure 3 is a graph showing the hardness of various roll materials at each temperature. , Fig. 4 is a graph showing various characteristics of the roll as a function of changes in Co content, Fig. 5 is a graph showing various characteristics of a roll as a function of change in Cr content, and Fig. 6 shows the results of measurement of wear amount using roll test materials. 7 is a graph showing the roughness measurement results of the roll test material, FIG. 8 is a drawing showing the measurement results of the roll surface roughness of the roll test material, and FIG. 9 is a side view showing the roll test procedure. FIG. 10 is a side sectional view showing an example of a method for manufacturing a wear-resistant cast iron roll. 1... Inventive material, 2... Conventional material, 3... High chromium cast material, 21... Roll test material, 22... Compatible material, 31... Core material, 32... Outer layer material, 35... Water cooling Mold, 36... Heating coil, 36a... Preheating coil, 39... Fireproof frame.
Claims (1)
1.5％、Cr：4.0〜1.0％、Mo：3.0〜10％、Ｗ：3.0
〜10％、Ｖ：2.5〜10％、Co：5.0〜10％、Ni：≦
1.0％、Nb：≦3.0％、残部はFeおよび不可避不
純物からなる熱間圧延用ロール材。1 C: 1.0~2.4%, Si: 0.3~2.0%, Mn: 0.3~
1.5%, Cr: 4.0~1.0%, Mo: 3.0~10%, W: 3.0
~10%, V:2.5~10%, Co:5.0~10%, Ni:≦
Hot rolling roll material consisting of 1.0%, Nb: ≦3.0%, and the remainder Fe and unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24124988A JPH0288745A (en) | 1988-09-27 | 1988-09-27 | Wear-resistant cast iron roll material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24124988A JPH0288745A (en) | 1988-09-27 | 1988-09-27 | Wear-resistant cast iron roll material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0288745A JPH0288745A (en) | 1990-03-28 |
| JPH0534413B2 true JPH0534413B2 (en) | 1993-05-24 |
Family
ID=17071426
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP24124988A Granted JPH0288745A (en) | 1988-09-27 | 1988-09-27 | Wear-resistant cast iron roll material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0288745A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110484809A (en) * | 2019-09-09 | 2019-11-22 | 广东省材料与加工研究所 | Composite hammer head, preparation method and composite hammer head cast model |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20090050196A1 (en) | 2005-03-18 | 2009-02-26 | Mitsui Chemicals, Inc. | Resin Composition for Solar Cell Package |
| JP4548263B2 (en) * | 2005-07-29 | 2010-09-22 | Ｊｆｅスチール株式会社 | Manufacturing method of cast iron products with excellent wear resistance |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5340623A (en) * | 1976-08-03 | 1978-04-13 | Acos Villares Sa | Hard alloy and producing method of it |
| JPS5858254A (en) * | 1981-09-30 | 1983-04-06 | Daido Steel Co Ltd | Alloy steel |
| JPS5886974A (en) * | 1981-11-20 | 1983-05-24 | Nittetsu Hard Kk | Abrasion resistant roll |
| JPS58113356A (en) * | 1981-12-26 | 1983-07-06 | Hitachi Metals Ltd | High-speed tool steel |
| JPS6328843A (en) * | 1986-07-23 | 1988-02-06 | Hitachi Metals Ltd | Alloyed cast iron material for screw for compacting machine |
| JPS63199092A (en) * | 1987-02-12 | 1988-08-17 | Kubota Ltd | Welded overlay roll for hot rolling |
| JPS63309393A (en) * | 1987-06-10 | 1988-12-16 | Kubota Ltd | Roll cladded by welding for hot rolling |
-
1988
- 1988-09-27 JP JP24124988A patent/JPH0288745A/en active Granted
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5340623A (en) * | 1976-08-03 | 1978-04-13 | Acos Villares Sa | Hard alloy and producing method of it |
| JPS5858254A (en) * | 1981-09-30 | 1983-04-06 | Daido Steel Co Ltd | Alloy steel |
| JPS5886974A (en) * | 1981-11-20 | 1983-05-24 | Nittetsu Hard Kk | Abrasion resistant roll |
| JPS58113356A (en) * | 1981-12-26 | 1983-07-06 | Hitachi Metals Ltd | High-speed tool steel |
| JPS6328843A (en) * | 1986-07-23 | 1988-02-06 | Hitachi Metals Ltd | Alloyed cast iron material for screw for compacting machine |
| JPS63199092A (en) * | 1987-02-12 | 1988-08-17 | Kubota Ltd | Welded overlay roll for hot rolling |
| JPS63309393A (en) * | 1987-06-10 | 1988-12-16 | Kubota Ltd | Roll cladded by welding for hot rolling |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110484809A (en) * | 2019-09-09 | 2019-11-22 | 广东省材料与加工研究所 | Composite hammer head, preparation method and composite hammer head cast model |
| CN110484809B (en) * | 2019-09-09 | 2020-07-07 | 广东省材料与加工研究所 | Composite hammer head, preparation method thereof and composite hammer head casting model |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0288745A (en) | 1990-03-28 |
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