JPH04198455A - Corrosion resisting alloy, hot roll and its production, and hot rolling mill - Google Patents
Corrosion resisting alloy, hot roll and its production, and hot rolling millInfo
- Publication number
- JPH04198455A JPH04198455A JP33217590A JP33217590A JPH04198455A JP H04198455 A JPH04198455 A JP H04198455A JP 33217590 A JP33217590 A JP 33217590A JP 33217590 A JP33217590 A JP 33217590A JP H04198455 A JPH04198455 A JP H04198455A
- Authority
- JP
- Japan
- Prior art keywords
- roll
- less
- amount
- retained austenite
- unavoidable impurities
- 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
- 238000005098 hot rolling Methods 0.000 title claims description 35
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- 239000001997 corrosion-resisting alloy Substances 0.000 title 1
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 45
- 230000007797 corrosion Effects 0.000 claims abstract description 31
- 238000005260 corrosion Methods 0.000 claims abstract description 31
- 230000000717 retained effect Effects 0.000 claims abstract description 26
- 239000012535 impurity Substances 0.000 claims abstract description 22
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 20
- 229910000851 Alloy steel Inorganic materials 0.000 claims abstract description 18
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 18
- 239000010959 steel Substances 0.000 claims abstract description 18
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 16
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 15
- 238000005242 forging Methods 0.000 claims abstract description 4
- 230000003014 reinforcing effect Effects 0.000 claims description 28
- 239000000463 material Substances 0.000 claims description 20
- 238000005096 rolling process Methods 0.000 claims description 17
- 238000005496 tempering Methods 0.000 claims description 13
- 238000000034 method Methods 0.000 claims description 12
- 238000010791 quenching Methods 0.000 claims description 11
- 230000000171 quenching effect Effects 0.000 claims description 10
- 229910045601 alloy Inorganic materials 0.000 claims description 8
- 239000000956 alloy Substances 0.000 claims description 8
- 238000000137 annealing Methods 0.000 claims description 7
- 229910052742 iron Inorganic materials 0.000 claims description 7
- 238000003466 welding Methods 0.000 claims description 6
- 229910000734 martensite Inorganic materials 0.000 claims description 5
- 239000002184 metal Substances 0.000 claims description 4
- 229910052751 metal Inorganic materials 0.000 claims description 4
- 229910001563 bainite Inorganic materials 0.000 claims description 3
- 238000010276 construction Methods 0.000 claims description 3
- 238000009792 diffusion process Methods 0.000 claims description 3
- 229910052757 nitrogen Inorganic materials 0.000 claims description 3
- 238000005507 spraying Methods 0.000 claims description 2
- 239000000203 mixture Substances 0.000 abstract description 12
- 229910052804 chromium Inorganic materials 0.000 abstract description 9
- 229910052748 manganese Inorganic materials 0.000 abstract description 9
- 229910052799 carbon Inorganic materials 0.000 abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 7
- 229910052759 nickel Inorganic materials 0.000 abstract description 6
- 229910052710 silicon Inorganic materials 0.000 abstract description 6
- 229910052720 vanadium Inorganic materials 0.000 abstract description 5
- 229910052726 zirconium Inorganic materials 0.000 abstract description 5
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 238000010438 heat treatment Methods 0.000 description 11
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 11
- 230000000694 effects Effects 0.000 description 8
- 238000001816 cooling Methods 0.000 description 7
- 239000002131 composite material Substances 0.000 description 6
- 230000006698 induction Effects 0.000 description 6
- 239000011159 matrix material Substances 0.000 description 6
- 238000010586 diagram Methods 0.000 description 5
- 238000012360 testing method Methods 0.000 description 5
- 238000005299 abrasion Methods 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 239000010949 copper Substances 0.000 description 4
- 238000003825 pressing Methods 0.000 description 4
- 238000005266 casting Methods 0.000 description 3
- 210000000078 claw Anatomy 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 239000011162 core material Substances 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 230000003746 surface roughness Effects 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000006378 damage Effects 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000005470 impregnation Methods 0.000 description 2
- JKQOBWVOAYFWKG-UHFFFAOYSA-N molybdenum trioxide Chemical compound O=[Mo](=O)=O JKQOBWVOAYFWKG-UHFFFAOYSA-N 0.000 description 2
- 238000004901 spalling Methods 0.000 description 2
- 239000002436 steel type Substances 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- ZAMOUSCENKQFHK-UHFFFAOYSA-N Chlorine atom Chemical compound [Cl] ZAMOUSCENKQFHK-UHFFFAOYSA-N 0.000 description 1
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- 229910052801 chlorine Inorganic materials 0.000 description 1
- 239000000460 chlorine Substances 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 210000001787 dendrite Anatomy 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000004043 dyeing Methods 0.000 description 1
- 229910001651 emery Inorganic materials 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 229910052745 lead Inorganic materials 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 238000007750 plasma spraying Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000007788 roughening Methods 0.000 description 1
- 238000004439 roughness measurement Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 238000007751 thermal spraying Methods 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- 230000009466 transformation 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)
- Coating By Spraying Or Casting (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、耐食合金、熱間圧延用ロール及びその製造方
法、並びに熱間圧延機に関するものである。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention relates to a corrosion-resistant alloy, a hot rolling roll, a manufacturing method thereof, and a hot rolling mill.
熱間圧延用補強ロールに要求される性質としては主に耐
摩耗性及び対スポーリング性があげられる。耐摩耗性の
向上対策としては鋼糸のロール利料で硬さ及び炭化物の
分散が考えられる。多量の炭化物の分散による耐摩耗性
の向上にはＣ量を多くすればよいが、ロール製造問題を
生じ靭性の低下にもつながり採用は難しい。Properties required of reinforcing rolls for hot rolling include wear resistance and spalling resistance. As a measure to improve abrasion resistance, hardness and carbide dispersion can be considered by rolling the steel thread. In order to improve the wear resistance by dispersing a large amount of carbide, it is possible to increase the amount of C, but this causes problems in roll manufacturing and reduces toughness, making it difficult to employ.
次に、補強ロールは作業ロールと接触するため、スリッ
プが生じ、転勤疲労による肌荒れが激しくなって、ロー
ル寿命を低下させる。また、ロール表面が腐食により肌
荒れを起し凹凸が激しくなり問題となっている。Next, since the reinforcing roll comes into contact with the work roll, slippage occurs, and roughness due to transfer fatigue becomes severe, reducing the life of the roll. In addition, the roll surface becomes rough due to corrosion and becomes extremely uneven, which is a problem.
従来、熱間圧延機の補強ロール材には粗圧延の２重圧延
機用の作業ロールとして複合鋳鋼（熱間金型用）、粗圧
延、前段、後段仕−にげ用の補強口−ルには熱間ダイス
鋼系５ＫＩ）−６１相当（Ｃｏ。Conventionally, reinforcing roll materials for hot rolling mills include composite cast steel (for hot molds) as work rolls for double rolling mills for rough rolling, reinforcing holes for rough rolling, front stage, and rear finishing. Hot die steel type 5KI)-61 equivalent (Co.
３〜０．６％、Ｓｉ０．４〜０．９％、Ｍｎ１％以下、
ＮｉＯ〜０．５％、Ｃｒ２〜５％、ＭｏＯ３〜０．９％
，Ｖ０，３％以下）が使用されている。3 to 0.6%, Si 0.4 to 0.9%, Mn 1% or less,
NiO~0.5%, Cr2~5%, MoO3~0.9%
, V0, 3% or less) is used.
第２図は熱間圧延機のロール配置を示す構成図である。FIG. 2 is a configuration diagram showing the roll arrangement of a hot rolling mill.
４重圧延粗スタンドロールは作業ロール１〜４および補
強ロール１７〜２０で構成されている。粗圧延スタンド
を通過した銅相３４は次の仕」二前段および仕上後段の
圧延スタンド工程に入る。仕上スタンド圧延機のロール
は作業ロール５〜１６、補強ロール２１〜３２で構成さ
れている。The quadruple rolling rough stand roll is composed of work rolls 1 to 4 and reinforcing rolls 17 to 20. The copper phase 34 that has passed through the rough rolling stand enters the next rolling stand process, which is the first stage of finishing and the second stage of finishing. The rolls of the finishing stand rolling mill are comprised of work rolls 5-16 and reinforcing rolls 21-32.
なお、圧延された銅相はコイル３３としてまきとられる
。Note that the rolled copper phase is wound as a coil 33.
〔発明が解決しようとする課題］
最近、製鉄所では省エネ及び圧延利の精度に一層高度な
ものが要求されてきた。しかも、従来、熱間圧延機用補
強ロールに要求される性質は靭性と耐スポーリング性及
び耐摩耗性であったが、最近は腐食により肌荒れを起し
、摩耗が激しくなり、ロールの寿命を著しく損なうので
問題となっている。こうした点について満足し得る熱間
圧延用補強ロールの開発が要望されている。[Problems to be Solved by the Invention] In recent years, steel mills have been required to achieve higher levels of energy saving and accuracy of rolling yield. Moreover, the properties traditionally required of reinforcing rolls for hot rolling mills were toughness, spalling resistance, and abrasion resistance, but recently corrosion has caused rough skin and increased wear, shortening the lifespan of the rolls. This is a problem because it causes significant damage. There is a demand for the development of a reinforcing roll for hot rolling that satisfies these points.
本発明は、」二連の従来技術の問題点を解決するため、
オーステナイト量を６０％以上残留させて、高硬度と耐
摩耗性、特に、耐食性にすぐれた熱間圧延用補強ロール
とその製造法を提供することを主なる目的とするもので
ある。The present invention solves two problems of the prior art:
The main object of the present invention is to provide a reinforcing roll for hot rolling that retains 60% or more of austenite and has high hardness and excellent wear resistance, particularly corrosion resistance, and a method for manufacturing the same.
上述の課題を解決するためにとられた本発明の構成は次
の如くである。The structure of the present invention adopted to solve the above-mentioned problems is as follows.
熱間圧延用ロールは、
（］）重臣比で、ＣＣｒ５〜１．２％、Ｓ１０゜７〜３
％、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１
０％、Ｍｏ１〜５％と、残部がＦ ｅ及び不可避的な不
純物とからなり、残留オーステナイト量が６０％以］二
である合金鋼からなることを特徴とし、
（２）重量比で、Ｃ０．５〜１．２％、Ｓｉ０゜７〜３
％、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ ３〜
１０％、Ｍｏ１〜５％と、Ｗ、Ｖ２％以下、Ｔ ｌ ＋
Ｎｌ）、 Ｚ ｒ １％の少なくとも１種以上を含み
、残部がＦ ｅ及び不可避的な不純物とからなり、胴部
の残留オーステナイト量が６０％以上である合金鋼で、
硬さがＩＴ ｓ ５０以１−で軸材の引張り強さが８０
ｋｇ ／ ｍｍ２以上であることを特徴とし、
（３）重量比で、Ｃ０．５〜１．２％、８１０゜７〜３
％、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１
０％、Ｍｏ１〜５％と、Ｗ、Ｖ２％以下、Ｔｉ、Ｎｂ、
Ｚｒ１％以下の少なくとも１押爪」二を含み、残部がＦ
ｅ及び不可避的な不純物とからなり、残留オーステナイ
ト量が６０％以上である合金鋼からなることを特徴とし
、
（４）重量比で、Ｃ０．５〜１．２％、Ｓｉ０゜７〜３
％、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１
０％、Ｍｏ１〜−５％と、Ｗ、Ｖ２％以下、Ｔｉ、Ｎｂ
、Ｚｒ１％の少なくとも１種以上を含み、残部がＦｅ及
び不可避的な不純物とからなり、残留オーステナイト量
が６０％以上である合金からなる熱間圧延用ロールで、
一体型又はスリーブ組立式補強ロールからなることを特
徴とし、（５）重量比で、ＣＣｒ５〜１．２％、Ｓｉ０
゜７〜３％、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃ
ｒ２〜５％％、Ｍｏ１〜５％と、Ｗ、Ｖ２％以下、Ｔｉ
、Ｎｂ、Ｚｒ １％の少なくとも１押爪−１−を含み、
残部がＦｅ及び不可避的な不純物とからなり、残留オー
ステナイト量が６０％以上である合金鋼からなり基地中
の組織がマルテンサイト及びベイナイトと炭化物の１種
が１５％以下であることを特徴とし、
（６）重量比で、Ｃ０．５〜１．２％、８１０゜７〜３
％、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１
０％、Ｍｏ１〜５％と、Ｗ、Ｖ２％以下、Ｔｉ、Ｎｂ、
Ｚｒ１％の少なくとも１押爪」−を含み、残部がＦｅ及
び不可避的な不純物とからなる熱間圧延用ロールにおい
て、胴部のスリーブがエレクトロスラグ再溶解法、金属
溶射法、又は、溶接法で形成されており、スリーブ組立
式であることを特徴とし、
耐食合金は、
（７）重量比テ、Ｃ０，５〜１．２％、Ｓｉｎ。The hot rolling roll is (]) CCr5~1.2%, S10°7~3
%, Mn0.6-5%, Ni0.6-5%, Cr3-1
0%, Mo 1 to 5%, the balance consisting of Fe and unavoidable impurities, and the amount of retained austenite is 60% or more. (2) In terms of weight ratio, C0 .5~1.2%, Si0°7~3
%, Mn 0.6-5%, Ni 0.6-5%, Cr 3-5%
10%, Mo1-5%, W, V2% or less, T l +
An alloy steel containing at least one of the following: (Nl), Zr (1%), the balance consisting of Fe and unavoidable impurities, and the amount of retained austenite in the body is 60% or more,
The hardness is IT s 50 or more and the tensile strength of the shaft material is 80.
kg/mm2 or more, (3) Weight ratio: C0.5-1.2%, 810°7-3
%, Mn0.6-5%, Ni0.6-5%, Cr3-1
0%, Mo1-5%, W, V2% or less, Ti, Nb,
Contains at least one pressing claw with Zr of 1% or less, and the remainder is F.
(4) By weight, C0.5-1.2%, Si0.7-3.
%, Mn0.6-5%, Ni0.6-5%, Cr3-1
0%, Mo1 to -5%, W, V2% or less, Ti, Nb
A hot rolling roll made of an alloy containing at least one kind of Zr, 1% or more, the balance consisting of Fe and unavoidable impurities, and the amount of retained austenite is 60% or more,
It is characterized by consisting of an integrated type or sleeve assembly type reinforcing roll, (5) weight ratio: CCr5~1.2%, Si0
゜7~3%, Mn0.6~5%, Ni0.6~5%, C
r2~5%%, Mo1~5%, W, V2% or less, Ti
, Nb, containing at least one pressing claw -1- of 1% of Zr,
It is characterized by being made of an alloy steel in which the balance consists of Fe and unavoidable impurities, and the amount of retained austenite is 60% or more, and the structure in the matrix is characterized in that martensite, bainite, and one type of carbide account for 15% or less, (6) Weight ratio: C0.5-1.2%, 810°7-3
%, Mn0.6-5%, Ni0.6-5%, Cr3-1
0%, Mo1-5%, W, V2% or less, Ti, Nb,
In a hot rolling roll containing at least one pressing pawl of 1% Zr, the remainder being Fe and unavoidable impurities, the sleeve of the body is formed by electroslag remelting, metal spraying, or welding. (7) Weight ratio: C0.5 to 1.2%, Sin.
７〜３％、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ
３〜１０％、Ｍｏ１〜５％と、ｗ、７２％以下、Ｔｉ、
Ｎｂ、Ｚｒ１％の少なくとも１種以上を含み、残部がＦ
ｅ及び不可避的な不純物とがらなり、残留オーステナイ
ト量が６０％以上である合金鋼からなることを特徴とし
、
（９）重量比で、Ｃ０．５〜１．２％、５ｉＯ７〜３％
、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１０
％、Ｍｏ１〜５％と、Ｗ、７２％以下、Ｔｉ、Ｎｂ、Ｚ
ｒ１％の少なくとも１種以上を含み、残部がＦｅ及び不
可避的な不純物とからなり、残留オーステナイト量が６
０％以上である合金鋼よりなり、衝撃摩耗をうける建設
機械用部利に用いることを特徴とし、
熱間圧延機は、
（８）粗圧延及び仕上げ前段、後段圧延用の作業ロール
及び補強ロールを有する圧延機において、粗ロール、仕
上げ前段、後段ロールに少なくとも一体および組立式補
強ロールが、重量比で、ｃｏ。7-3%, Mn0.6-5%, Ni0.6-5%, Cr
3-10%, Mo1-5%, w, 72% or less, Ti,
Contains at least one of Nb and 1% of Zr, and the remainder is F.
(9) By weight, C0.5-1.2%, 5iO7-3%
, Mn0.6-5%, Ni0.6-5%, Cr3-10
%, Mo1 to 5%, W, 72% or less, Ti, Nb, Z
Contains at least one type of r1%, the remainder consists of Fe and unavoidable impurities, and the amount of retained austenite is 6
The hot rolling mill is made of alloy steel of 0% or more and is used for parts of construction machinery that are subject to impact wear. In a rolling mill having a roughening roll, a pre-finishing roll, a post-finishing roll, and at least an integral reinforcing roll and an assembled reinforcing roll, the weight ratio is co.
５〜１．２％、Ｓｉ０．７〜３％、Ｍｎ０．６〜５％、
Ｎｉ０．６〜５％、Ｃｒ３〜１０％、Ｍｏ１〜５％と、
Ｗ、Ｖ２％以下、Ｔｉ、Ｎｂ、Ｚｒ１％の少なくとも１
種以上を含み、残部がＦｅ及び不可避的な不純物とがら
なり、残留オーステナイト量が６０％以上である合金鋼
からなることを特徴とし、
熱間圧延用ロールの製造方法は、
（１０）重量比で、Ｃ０９５〜１．２％、Ｓ１０゜７〜
３％、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜
１０％、Ｍｏ１〜５％と、Ｗ、Ｖ２％以下、Ｔｉ、Ｎｂ
、Ｚｒ１％の少なくとも１押爪−１−を含み、残部がＦ
ｅ及び不可避的な不純物とからなり、残留オーステナイ
１〜量６０％以上の合金鋼からなる熱間圧延用ロールの
製造方法であって、鋼塊を製造する工程、７５０〜９０
０℃で焼鈍する工程、１１００〜１２５０’Ｃで拡散焼
鈍後１０５０〜１２００℃で熱間拘束鍛造を行なう工程
、１０００〜１２００℃で焼入後、１００〜６５０℃の
焼戻しを行なう工程を順次行うことを特徴とする。5-1.2%, Si0.7-3%, Mn0.6-5%,
Ni0.6-5%, Cr3-10%, Mo1-5%,
At least 1 of W, V2% or less, Ti, Nb, Zr 1%
(10) A method for manufacturing a hot rolling roll is characterized in that the alloy steel is made of an alloy steel containing at least 60% of iron, the remainder being Fe and unavoidable impurities, and the amount of retained austenite being 60% or more. , C095~1.2%, S10°7~
3%, Mn0.6-5%, Ni0.6-5%, Cr3-
10%, Mo1-5%, W, V2% or less, Ti, Nb
, containing at least one pressing claw -1- of 1% Zr, the remainder being F
A method for producing a hot rolling roll made of an alloy steel containing e and unavoidable impurities and having a retained austenie content of 1 to 60% or more, the step of producing a steel ingot, 750-90
The steps of annealing at 0°C, diffusion annealing at 1100-1250'C and hot restraint forging at 1050-1200°C, and quenching at 1000-1200°C followed by tempering at 100-650°C are performed in sequence. It is characterized by
ものである。It is something.
すなわち、熱間圧延用補強ロールによる耐食性について
検討した結果、金属組織中にオーステナイトの特定量残
留させても、硬さと耐食性の向上がはかれる点に着目し
てなされたもので、要約すると下記の通りである。In other words, as a result of studying the corrosion resistance of reinforcing rolls for hot rolling, it was found that even if a certain amount of austenite remains in the metal structure, hardness and corrosion resistance can be improved.The following is a summary: It is.
本発明は、重量比で、Ｃ０８５〜１．２％、８１０．７
〜３％、Ｍ］１０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ
３〜１０％、Ｍｏ１〜５％残部がＦｅ及び不可避的な不
純物からなり、残留オーステナイト量が６０％以上であ
る合金鋼からなるか、または、重量で比で、Ｃ０．５〜
１．２％、８１０．７〜３％、Ｍｎ０．６〜５％、Ｎ１
０，６〜５％、Ｃｒ３〜１０％、Ｍｏ１〜５％とＷ、Ｖ
２％以下、ｌ″ｉ、Ｎｂ、Ｚｒ １％の少なくとも１種
以上を含み、残部がＦｅ及び不可避的な不純物からなり
、残留オーステナイト量が６０％以上である合金鋼から
なる熱間丁延用ロールおよびその製造法である。The present invention has a weight ratio of C085 to 1.2%, 810.7
~3%, M]10.6~5%, Ni0.6~5%, Cr
3 to 10%, Mo 1 to 5%, the balance consists of Fe and unavoidable impurities, and the amount of retained austenite is 60% or more, or it is made of alloy steel with a weight ratio of C0.5 to
1.2%, 810.7-3%, Mn0.6-5%, N1
0.6~5%, Cr3~10%, Mo1~5% and W, V
2% or less, l″i, Nb, and Zr 1% or more, the balance consists of Fe and unavoidable impurities, and the amount of retained austenite is 60% or more for hot rolling. A roll and its manufacturing method.
熱間圧延機用補強ロールの耐食性は、Ｃ，Ｓｉ、Ｍｎ、
Ｎｉの組合せにより、基地組織中のオーステナイト量を
６０％以上残留させることにより得られる。The corrosion resistance of reinforcing rolls for hot rolling mills is based on C, Si, Mn,
This can be obtained by allowing 60% or more of austenite to remain in the matrix structure by combining Ni.
特に、オーステナイトを安定化させる、好ましい組成は
Ｃ１，０％、Ｓｉ２．４％、Ｍｎ２．３％、Ｎｉ２．９
％、Ｍｏ２．９％で熱間圧延用補強ロールの耐食性を向
上することができる。さらに、」１記の組成の合金を一
体とした鍛鋼または防造利からなるものの他、芯拐（例
えば合金鋼）の外側に溶着一体化して複合ロールとする
ことができる。溶着後は溶着のまま及び溶着後鍛造する
ことができる。In particular, the preferred composition for stabilizing austenite is C1.0%, Si2.4%, Mn2.3%, Ni2.9
%, Mo2.9% can improve the corrosion resistance of the reinforcing roll for hot rolling. Furthermore, in addition to those made of forged steel or forged steel in which the alloy having the composition described in 1 is integrated, a composite roll can be made by integrally welding it to the outside of a core (for example, alloy steel). After welding, it can be forged as is or after welding.
上記ロールを製造するには、鋼芯材の外側に本発明の組
成からなる消耗電極を配置し、エレクトロスラグ再溶解
法により、芯材の外周部と上記消耗電極を溶融しながら
、順次凝固させて外層部を形成させる方法により、境界
部に不溶着部やミクロギャビティ等の欠陥のない健全な
接合部を有す−１４＝
る複合ロールが得られる。To manufacture the above roll, a consumable electrode made of the composition of the present invention is placed on the outside of a steel core material, and the outer periphery of the core material and the above consumable electrode are melted and solidified one after another by an electroslag remelting method. By the method of forming the outer layer part by using the method of forming the outer layer part, it is possible to obtain a composite roll having a -14= sound joint part without defects such as unwelded parts and microgavites at the boundary part.
また、本発明では上記複合ロールに熱処理を施すことが
できる。１０００〜１２００℃で焼入後、１００〜６５
０の焼戻しによって、オーステナイトの分解と炭化物の
析出により、Ｈｓ５０（ＨＶ３６０）以上の硬さをもつ
ロールが得られ、耐摩耗性、耐肌荒れ性、特に、耐食性
のすぐれたものが得られる。更に、また、プラズマ溶射
法及び溶接法で溶射複合化し熱処理を施ずことによって
上記と同様にすぐれたロールを得ることができる。Further, in the present invention, the composite roll can be subjected to heat treatment. After quenching at 1000-1200℃, 100-65
0 tempering results in the decomposition of austenite and the precipitation of carbides, resulting in a roll having a hardness of Hs50 (HV360) or higher, with excellent wear resistance, roughness resistance, and especially corrosion resistance. Furthermore, an excellent roll can be obtained in the same manner as above by thermal spraying composite using plasma spraying method and welding method without heat treatment.
本発明のロールは熱間圧延機の粗圧延ロール及び補強ロ
ール並びに前段、後段仕」二げロールの補強ロールとし
て組入れ用いられる。The roll of the present invention is incorporated and used as a rough rolling roll and a reinforcing roll of a hot rolling mill, as well as a reinforcing roll of a front-stage and a rear-stage finishing roll.
本発明における組織はオーステナイト相の他、マルテン
サイト相とベイナイト相と炭化物量は４〜１０％で残部
がオーステナイ１へ相とマルテンサイト相である。The structure in the present invention includes an austenite phase, a martensite phase, a bainite phase, and a carbide content of 4 to 10%, with the remainder being an austenite phase and a martensite phase.
本発明において、Ｃは焼入状態で一部基地に溶解し、他
はＭｏ，Ｗ、Ｃｒ、Ｖなどと結合して複合炭化物を作る
。Ｃが少ないと二次硬化が少なく、反面、Ｃが高すぎる
と溶融点が下がり、焼入温度を下げないと共晶組織を生
じ脆（なる。本発明者らの検討では０．５％未満では炭
化物を作るためのＣ量としては少なく、１．２％を超え
ると炭化物量が増へ靭性及び耐食性が低下する。In the present invention, C is partially dissolved in the matrix in the quenched state, and the rest is combined with Mo, W, Cr, V, etc. to form a composite carbide. If the C content is low, secondary hardening will be small; on the other hand, if the C content is too high, the melting point will drop, and if the quenching temperature is not lowered, a eutectic structure will occur and become brittle (becoming less than 0.5%). Therefore, the amount of C for forming carbides is small, and if it exceeds 1.2%, the amount of carbides increases and toughness and corrosion resistance decrease.
Ｓｌは鋼中にある程度不可避的に含まれている成分であ
り、通常は脱酸を目的として添加されるがその量は０．
４％以下である。しかし、耐食性、耐孔食性の改善には
０．７〜３％がよい。Sl is a component that is unavoidably included in steel, and is usually added for the purpose of deoxidizing, but the amount is 0.
It is less than 4%. However, 0.7 to 3% is preferable for improving corrosion resistance and pitting corrosion resistance.
Ｍｒも必らず含んでいる元素であるが、通常の含有量は
０．４％以下である。本発明はＭｎ量を０．６〜５％と
した。Ｍｎは焼入性の向上に寄与する元素で０．６％未
満では効果は少なく、５％を超えると残留オーステナイ
ト量が増加し、安定化してロール仕様硬さに達しない。Mr is also an element that is necessarily included, but its usual content is 0.4% or less. In the present invention, the Mn amount is set to 0.6 to 5%. Mn is an element that contributes to improving hardenability, and if it is less than 0.6%, the effect is small, and if it exceeds 5%, the amount of retained austenite increases, becomes stable, and does not reach the roll specification hardness.
また、鋳物に毛割れが生じ易くなる。Moreover, hair cracking is likely to occur in the casting.
Ｎｉは金属組織を微細にしオーステナイトおよびフェラ
イトに固溶して基地を強化する。また、Ｃｒ、Ｍｏと共
存して焼入性を増し、耐摩耗性と靭性を向」ニさせる。Ni makes the metal structure fine and dissolves in austenite and ferrite to strengthen the base. It also coexists with Cr and Mo to increase hardenability and improve wear resistance and toughness.
その含有量は０．６〜５％の範囲でオーステナイト量が
６０％以上残留するので耐食性を改善する。０．６％未
満では」１記の靭性が十分発揮されず、５％を超えると
オーステナイトの安定化により、ロール仕様硬さに達し
ない。When the content is in the range of 0.6 to 5%, 60% or more of austenite remains, improving corrosion resistance. If it is less than 0.6%, the toughness described in item 1 will not be sufficiently exhibited, and if it exceeds 5%, the roll specification hardness will not be achieved due to stabilization of austenite.
ＣｒはＣと結合してＣｒ炭化物を晶出し耐摩耗性及び耐
食性向」二に寄与する。その含有量は３〜１０％特に、
４．８％がよい。Cr combines with C to crystallize Cr carbide, contributing to wear resistance and corrosion resistance. Its content is 3-10%, especially
4.8% is good.
本発明において、Ｍｏは一部Ｃと結合してＭ。In the present invention, Mo is partially combined with C to form M.
Ｃ炭化物を形成し、残部は基地に固溶して二次硬化現象
（焼戻し二次硬化）により硬さを増加させる。その含有
量は１〜５％がよい。１％未満では硬さ、耐摩耗性が向
」ニせず、５％を超えると網状に晶出して靭性を低下さ
せる恐れがある。C carbide is formed, and the remainder is solidly dissolved in the matrix to increase hardness by a secondary hardening phenomenon (tempering secondary hardening). Its content is preferably 1 to 5%. If it is less than 1%, the hardness and abrasion resistance will not be improved, and if it exceeds 5%, it may crystallize in a network shape and reduce toughness.
ＷはＭｏと同様に一部Ｃと結合してＭｏＣ炭化物を形成
し二次硬化現象により硬さと耐摩耗性を向上させ、残部
は基地に固溶して基地を緻密なマルテンサイト組織とす
る。その含有量は１％以下が好ましい。なお、ＷはＭｏ
と同様な効果があり、Ｍｏの１／２程度でよく、二次硬
化以後の焼戻し軟化抵抗がある。Similar to Mo, a portion of W combines with C to form MoC carbide and improves hardness and wear resistance through a secondary hardening phenomenon, and the remaining portion is solidly dissolved in the matrix to form a dense martensitic structure. Its content is preferably 1% or less. In addition, W is Mo
It has the same effect as Mo, only requires about 1/2 of Mo, and has resistance to temper softening after secondary hardening.
ＶはＣと結合して極めて硬いＭＣ炭化物を作り、耐摩耗
性の向」二に寄与する。しかし，Ｖ炭化物は固溶しに＜
＜、結晶粒の成長を妨げる。また、Ｃとの結びつきが強
いので焼入加熱の際基地に固溶するＣ量に強（影響する
。適当な焼入、焼もどし硬さを得るにはＣとＶは一定量
的関係が必要とされる。更にまた、粒界腐食を防止し、
耐孔食性を改善する効果がある。■は２％以上では研削
性及び溶解作業性に影響を及ぼすので２％以下がよい。V combines with C to form extremely hard MC carbide, which contributes to improved wear resistance. However, V carbide does not form a solid solution.
<, hinders the growth of crystal grains. In addition, since it has a strong bond with C, it has a strong influence on the amount of C dissolved in the matrix during quenching heating.C and V must have a certain quantitative relationship to obtain appropriate quenching and tempering hardness. Furthermore, it also prevents intergranular corrosion,
It has the effect of improving pitting corrosion resistance. (2) If it exceeds 2%, it will affect the grindability and melting workability, so it is preferably 2% or less.
Ｚｒは炭化物及びフェライトの生成元素であり、強力な
清浄作用や結晶粒の微細化をもたらし、安定なＺｒ炭化
物を形成する。但し、該炭化物は角状となり、機械的性
質を低下させるので１９％以下がよい。Zr is a carbide and ferrite forming element, has a strong cleaning effect and refines crystal grains, and forms stable Zr carbide. However, since the carbide becomes angular and deteriorates mechanical properties, it is preferably 19% or less.
Ｔｉは一部炭素と結合してＴｉＣを形成し、Ｖ、Ｃｒと
併用して用いると耐摩耗性及び靭性がさらに向上する。Ti partially combines with carbon to form TiC, and when used in combination with V and Cr, wear resistance and toughness are further improved.
１％以上ではＴｉＣは角状となり、靭性が低下する。If it exceeds 1%, TiC becomes angular and its toughness decreases.
ＮｂはＭＣ型の炭化物を形成し、耐摩耗性を著しく向上
させる元素である。また、結晶粒の微細化に寄与する元
素でもあり、１％以上の添加はＴＩＣと同様に角状とな
って靭性を低下する。Nb is an element that forms MC type carbide and significantly improves wear resistance. It is also an element that contributes to the refinement of crystal grains, and when added in an amount of 1% or more, they become angular and reduce toughness, similar to TIC.
その他、不可避的に含有されっＰ、Ｓ、Ｃｕ、Ｐｂ、Ｎ
等の不純物について説明する。Other unavoidably contained P, S, Cu, Pb, N
We will explain impurities such as:
Ｐは微量でも偏析する元素であり、焼割れ、歪みなどの
原因となる。また、脆性が著しく増加するので、０．１
％以下ならば特に問題はない。P is an element that segregates even in minute amounts, causing quench cracking, distortion, etc. Also, since brittleness increases significantly, 0.1
% or less, there is no particular problem.
ＳはＰと同様に有害元素であるがＭｕＳなど比較的無害
のものにできるので、０．１％以下であれば問題ない。Although S is a harmful element like P, it can be made into a relatively harmless element such as MuS, so there is no problem if it is 0.1% or less.
Ｃｕは組織の微細化に寄与するが、鋳造の際に割れの原
因ともなる。０．１％以下であれば特に害はない。Although Cu contributes to refinement of the structure, it also causes cracks during casting. There is no particular harm if it is 0.1% or less.
１） ｂはＭ ｎ Ｓやその池の介在物とともに凝集し
、樹枝状間に集まる傾向がある。添加量が多くなると熱
間作業性を悪くするが、０．１％以下であれば問題はな
い。1) b tends to aggregate with M n S and its pond inclusions and collect between dendrites. If the amount added is too large, hot workability will deteriorate, but if it is 0.1% or less, there will be no problem.
Ｎはオーステナイト組織を安定化するなどＣと類似して
いるが、０．１％以下とするのが好ましい。N is similar to C in that it stabilizes the austenite structure, but it is preferably 0.1% or less.
さらに、本発明はオーステナイト量を６０％以上残留す
るため、過酷な衝撃摩耗をうける建設機械用部月にも使
用することが可能である。Furthermore, since the present invention retains 60% or more of austenite, it can also be used in construction machinery parts that are subject to severe impact wear.
Ｃｒ量を極力抑えた組成にＣ，Ｓｌ、ＭＩ）及びＮｉ量
を増加させた。そのために、残留オーステナイトは安定
化するにもかかわらず高硬度が得られるとともに、なお
かつ、耐食性を改善することができた。The content of C, Sl, MI) and Ni was increased while keeping the Cr content as low as possible. Therefore, although the retained austenite is stabilized, high hardness can be obtained, and corrosion resistance can also be improved.
また、変態点温度が低いので高温度に」二げやすくなり
、オーステナイト量を多量に残留することが可能である
。In addition, since the transformation point temperature is low, it is easy to heat up to high temperatures, and it is possible to retain a large amount of austenite.
その」二、高硬度と耐摩耗性、特に、耐食性の改善によ
り、ロール表面の肌荒れ性が向」ニした。Second, due to high hardness and improved abrasion resistance, especially corrosion resistance, the roughness of the roll surface has been improved.
さらに、スリーブ組立式ロールはアーバ嵌めして製造す
る。アーμはＣｒ−Ｍｏ鋼およびＮｉ −Ｃｒ−Ｍｏ鋼
が用いられる。第１図はスリーブ組立式ロールの概略図
である。スリーブ外層３５．３５のなかにアーμ３６を
焼ばめして作製し、高周波焼入装置３７．３７′を用い
回転しながら焼入を行ない、その後、低温および高温の
焼もどしの熱処理を行なってロールを製造する。これら
は熱間圧延機に組入れられて長時間使用されても、補強
ロール用合金として極めて好ましい作用と効果がある。Furthermore, sleeve assembly type rolls are manufactured by arbor fitting. Cr-Mo steel and Ni-Cr-Mo steel are used for the arc. FIG. 1 is a schematic diagram of a sleeve assembly type roll. The sleeve outer layer 35, 35 is made by shrink-fitting the arm 36, hardened while rotating using an induction hardening device 37, 37', and then subjected to low temperature and high temperature tempering heat treatment to form a roll. Manufacture. Even when these alloys are incorporated into hot rolling mills and used for long periods of time, they have extremely favorable functions and effects as alloys for reinforcing rolls.
以下、本発明を実施例により具体的に説明する。 Hereinafter, the present invention will be specifically explained with reference to Examples.
〔実施例 １〕 熱間圧延用補強ロール利の組成を第１表に示す。[Example 1] Table 1 shows the composition of the reinforcing roll for hot rolling.
第１表において、１］は従来の熱間ダイス鋼系の５ＫＤ
６］に相当する鋼である。本発明の組成に比べてＣＶＳ
ｉ 、Ｍｎ、Ｍｏ量が低く、Ｎｉ及びＷは添加されて
いない。なお、Ｃｒは同等の組成となっている。In Table 1, 1] is the conventional hot die steel type 5KD
6]. CVS compared to the composition of the present invention.
i, Mn, and Mo amounts are low, and Ni and W are not added. Note that Cr has the same composition.
また、８．９および１ｏは比較利であり、８はＳｉ、Ｎ
ｉが低い組成、９はＣが低く、Ｗは８．９とも添加され
ていない。１０はＭｎ、Ｎ１およびＷが低い組成である
。Also, 8.9 and 1o are comparative profits, and 8 is Si, N
The composition with low i, 9, has low C, and no W is added in 8.9. No. 10 has a composition with low Mn, N1 and W.
第１表
本発明材１〜７の組成はＣ，Ｓ ｉ 、Ｍｎ、Ｃｒ、Ｍ
ｏ１■およびＷを含有した試料であるが、Ｗは１．５．
６．７には含まれていない。５にはＴｉ、６にはＮｂ、
７にはＺｒを添加した。１〜７のＭｎ及びＮｉは０．６
〜５％添加させた組成である。Table 1 The compositions of the invention materials 1 to 7 are C, Si, Mn, Cr, M
This is a sample containing o1■ and W, but W is 1.5.
6.7 is not included. 5 is Ti, 6 is Nb,
In No. 7, Zr was added. Mn and Ni of 1 to 7 are 0.6
This is a composition in which ~5% is added.
試料は高層゛波溶解炉で溶解し、金をに鋳込み鋼塊を製
造した。鋳込み後の鋼塊は８８０℃ＸＩＯ時間→７００
℃×５時間→炉冷の焼なましを行なった。The sample was melted in a high-wave melting furnace, and gold was cast into a steel ingot. The steel ingot after casting is heated at 880℃XIO time → 700
Annealing was performed at ℃×5 hours→furnace cooling.
第２表は残留オーステナイト量、熱処理硬さの測定結果
を示す。熱処理硬さは１５ｍｍ角の試験片を用いてロッ
クウェル硬度ｉ’ｌｌ （ｒｌＲｃ）で４ｔｌｌ定した
。熱処理は従来イイ７は９８０℃から焼入後、５００℃
で焼もどした。比較月８〜１０、本発明材１〜７の焼入
温度は１１２５℃に１時間保持後空冷を行なった。焼も
どしは５００℃Ｘｌｈ→空冷１回とした。Table 2 shows the measurement results of residual austenite amount and heat treatment hardness. The heat treatment hardness was determined by Rockwell hardness i'll (rlRc) of 4tll using a 15 mm square test piece. Conventional heat treatment for Good 7 ranges from 980℃ to 500℃ after quenching.
It was tempered. Comparative months 8 to 10, the quenching temperature of inventive materials 1 to 7 was held at 1125° C. for 1 hour and then air cooled. Tempering was performed at 500°C Xlh → air cooling once.
本発明材１〜７はＭ ｎおよびＮｉが添加され、オース
テナイト量が多いにもかかわらずＨＲＣ５１，５〜６２
、８ （１−１ｓ ６９〜８７）の高い値が得られた
。Inventive materials 1 to 7 have HRC51.5 to 62 despite the addition of Mn and Ni and a large amount of austenite.
, 8 (1-1s 69-87).
残留オーステナイ！・量は直径５ ｍｍ Ｘ長さ７０ｍ
ｍの試験片を熱処理したのち、弾導検流計による磁気分
析法で測定した。熱処理は従来材、比較月、本発明材と
もに１１２５℃に１時間保持後、５００°Ｃに保持して
空冷した。Remaining Austenai!・Amount is 5 mm in diameter x 70 m in length
After heat-treating a test piece of m, it was measured by magnetic analysis using a ballistic galvanometer. For heat treatment, the conventional material, comparative material, and inventive material were held at 1125° C. for 1 hour, then held at 500° C., and cooled in air.
従来材７は焼入、焼もどしによりほとんど残留オーステ
ナイトが分解している。比較月８〜］０は焼入、焼もど
しで１５〜５５％に分解し、硬さもＩ−■ＲＣ５２、１
〜５６ 、 ２ （Ｈｓ ７０〜７９ ）が得られる。In conventional material 7, almost all residual austenite has been decomposed by quenching and tempering. Comparison Month 8 ~] 0 is decomposed into 15-55% by quenching and tempering, and the hardness is I-■RC52, 1
~56,2 (Hs70-79) is obtained.
一方、本発明材１〜７は焼もどし後の残留オーステナイ
ト量に６８〜９７．９％オーステナイトが残留するにも
かかわらずＨＲＣ５１゜５〜６２．８（Ｈｓ６９〜８７
）の高硬度が得られた。On the other hand, inventive materials 1 to 7 had an HRC of 51°5 to 62.8 (Hs69 to 87%) despite having 68 to 97.9% austenite remaining after tempering.
) high hardness was obtained.
第３図は残留オーステナイｌ−量と腐食量との関係を示
すグラフである。FIG. 3 is a graph showing the relationship between the amount of residual austenite and the amount of corrosion.
浸漬実験用の試験片は１０ｍｍ角Ｘ２５＋ｎｍｇに機械
加を行なった。表面粗らさを一定にするため＃５００の
エメリーペーパで研磨した。試験片の熱処理は従来材１
１は９８０℃から焼入したのち５００℃で焼もどしを行
なった。また、比較月８〜１０は１１２５℃→空冷後、
５００℃の焼もどしを行なった。The test piece for the immersion experiment was machined to a size of 10 mm square x 25+ nm. It was polished with #500 emery paper to make the surface roughness constant. Heat treatment of test piece was conventional material 1
No. 1 was quenched at 980°C and then tempered at 500°C. In addition, comparison month 8 to 10 is 1125℃ → after air cooling,
Tempering was performed at 500°C.
第２表
次に、本発明材１〜７は１１２５℃から焼入し、５００
℃→空冷の焼戻しを行なった。Table 2 Next, materials 1 to 7 of the present invention were quenched at 1125°C and heated to 500°C.
Tempering was performed by cooling from °C to air.
含浸実験は１５ＯＮＸ８０で×３０での容量に試料を挿
入し、１ｏｐｐｍの塩素イオンを含む水溶液中に３週間
含浸した。含浸後は３％塩酸水溶液でサビを除去し腐食
量を測定した。In the impregnation experiment, a sample was inserted into a volume of 15ON x 80 x 30 and immersed in an aqueous solution containing 1 oppm of chloride ions for 3 weeks. After impregnation, rust was removed with a 3% aqueous hydrochloric acid solution and the amount of corrosion was measured.
第３図から明らかなように、残留オーステナイト量が６
０％以下の従来材１１および比較月８〜１０は腐食量が
増加する傾向を示している。一方、本発明材１〜７はオ
ーステナイト量が６０％以上残留する場合で腐食量が非
常に僅少となることが明白となった。As is clear from Figure 3, the amount of retained austenite is 6
Conventional materials 11 and Comparisons 8 to 10 with a corrosion rate of 0% or less show a tendency for the amount of corrosion to increase. On the other hand, it became clear that in the materials 1 to 7 of the present invention, the amount of corrosion was extremely small when 60% or more of austenite remained.
第４図は残留オーステナイ１〜量と粗らさとの関係を示
すグラフである。表面粗らさの測定は小板式５Ｅ−３Ｃ
型を用いて行なった。図から明らかなように、従来材１
１および比較月８〜１０に比べて本発明材１〜７は非常
に滑らかな面を持つことが明らかである。FIG. 4 is a graph showing the relationship between the amount of retained austenite and roughness. Surface roughness measurement is by small plate type 5E-3C
This was done using a mold. As is clear from the figure, conventional material 1
It is clear that inventive materials 1 to 7 have very smooth surfaces compared to Comparative Materials 1 to 10.
〔実施例 ２〕
第１表に示す、本発明材３の即成４４料を用いて、熱間
連続圧延機の仕」こげ前段に組入れる一体式補強ロール
を作製した。熱間連続圧延機のロール構成は第２図に示
す如くであり、士、下、一対の作業ロール２〜１７は補
強ロール１８〜３３にＪ−って支持されている６２〜５
および１８〜２１は粗圧延スタンド用ロール、６〜１１
および２２〜２７は仕」二げ前段ロール、１２〜１７お
よび２８〜３３は仕」二げ後段用ロールである。[Example 2] An integral reinforcing roll to be installed in the pre-rolling stage of a continuous hot rolling mill was manufactured using ready-made 44 materials of the present invention material 3 shown in Table 1. The roll configuration of the continuous hot rolling mill is as shown in FIG.
and 18-21 are rolls for rough rolling stands, 6-11
22 to 27 are rolls for the first stage of finishing, and 12 to 17 and 28 to 33 are rolls for the second stage of finishing.
鍛鋼製一体補強ロールは塩素性電気炉で溶製して、調度
は８８０℃→７２５℃→炉冷の二段焼なましを行なった
。拡散焼鈍は１１５０で行ない、１０５０〜１１５０℃
で鍛造を行ない、１５００φｘ１８００℃の鍛鋼製一体
補強ロールを作製した。機械加工後は磁気探傷及び染色
試験により、検査を行なったが無欠陥であった。The forged steel integrally reinforced roll was melted in a chlorine electric furnace and subjected to two-stage annealing at temperatures of 880°C → 725°C → furnace cooling. Diffusion annealing is performed at 1150℃, 1050-1150℃
Forging was carried out to produce a 1500φ x 1800°C forged steel integrally reinforced roll. After machining, magnetic flaw detection and dyeing tests were performed and no defects were found.
鍛鋼製一体補強ロールの熱処理は、第５図に示すように
、高周波焼入装置により、誘導加熱によりロール表面を
空冷加熱しながら噴霧冷却により空冷焼入を行なった。As shown in FIG. 5, the heat treatment of the forged steel integral reinforcing roll was carried out by using an induction hardening device to air-cool harden the roll surface by induction heating while air-cooling the roll surface by spray cooling.
その後、高温焼戻しを行ない、ロール表面の硬さがＨＰ
Ｏ３５，３（Ｈｓ ６０）を示し、ロール仕様硬さが得
られた。After that, high-temperature tempering is performed to reach the hardness of the roll surface.
It showed O35,3 (Hs 60) and the roll specification hardness was obtained.
鍛鋼製一体補強ロールは熱間連続圧延機に紹入られて使
用した結果、従来ロール１１は耐摩耗性および腐食によ
る肌荒れに劣ったが、不発明月３の組成月料は非常によ
い成績を示し、ロール寿命を大幅に延長することができ
た。The forged steel integrally reinforced roll was introduced and used in a hot continuous rolling mill, and as a result, the conventional roll 11 had poor wear resistance and roughness due to corrosion, but the composition of the non-invention month 3 showed very good results. It was possible to significantly extend the roll life.
オーステナイト量を６０％以上残留させた本発明の熱間
圧延用補強ロールは従来利のロールに比べて高硬度で耐
食性による肌荒れ性にもすぐれ、ロール寿命を２倍程度
に向」ニすることがで、産業上の効果の大なるものであ
る。The reinforcing roll for hot rolling of the present invention, which retains 60% or more of austenite, has higher hardness and corrosion resistance than conventional rolls, and is superior in surface roughness due to its corrosion resistance, and can approximately double the life of the roll. This has great industrial effects.
第１図は本発明の熱間圧延補強ロールの一実施例のスリ
ーブ組立式ロールと高周波焼入装置との関係を示す説明
図、第２図は熱間圧延機のロール配置を示す構成図、第
３図は残留オーステナイト量を腐食量との関係を示すグ
ラフ、第４図は残留オーステナイト量と粗らさとの関係
を示すグラフ、第５図は本発明の熱間圧延補強ロールの
一実施例の鍛鋼製一体補強ロールと高周波焼入装置との
関係を示す説明図である。
３５・・スリーブ外層、３６・・アーμ、３７・高周波
焼入れ装置。FIG. 1 is an explanatory diagram showing the relationship between the sleeve assembly type roll of one embodiment of the hot rolling reinforcing roll of the present invention and an induction hardening device, and FIG. 2 is a configuration diagram showing the roll arrangement of the hot rolling mill. FIG. 3 is a graph showing the relationship between the amount of retained austenite and the amount of corrosion, FIG. 4 is a graph showing the relationship between the amount of retained austenite and roughness, and FIG. 5 is an example of the hot rolling reinforcing roll of the present invention. FIG. 3 is an explanatory diagram showing the relationship between the forged steel integral reinforcing roll and the induction hardening device. 35. Sleeve outer layer, 36. AR μ, 37. Induction hardening device.
Claims (1)
、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１０
％、Ｍｏ１〜５％と、残部がＦｅ及び不可避的な不純物
とからなり、残留オーステナイト量が６０％以上である
合金鋼からなることを特徴とする熱間圧延用ロール。 ２）重量比で、Ｃ０．５〜１．２％、Ｓｉ０．７〜３％
、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１０
％、Ｍｏ１〜５％と、Ｗ、Ｖ２％以下、Ｔｉ，Ｎｂ，Ｚ
ｒ１％の少なくとも１種以上を含み、残部がＦｅ及び不
可避的な不純物とからなり、胴部の残留オーステナイト
量が６０％以上である合金鋼で、硬さがＨｓ５０以上で
軸材の引張り強さが８０ｋｇ／ｍｍ＾２以上であること
を特徴とする熱間圧延用ロール。 ３）重量比で、Ｃ０．５〜１．２％、Ｓｉ０．７〜３％
、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１０
％、Ｍｏ１〜５％と、Ｗ、Ｖ２％以下、Ｔｉ，Ｎｂ，Ｚ
ｒ１％以下の少なくとも１種以上を含み、残部がＦｅ及
び不可避的な不純物とからなり、残留オーステナイト量
が６０％以上である合金鋼からなることを特徴とする熱
間圧延用ロール。 ４）重量比で、Ｃ０．５〜１．２％、Ｓｉ０．７〜３％
、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１０
％、Ｍｏ１〜５％と、Ｗ、Ｖ２％以下、Ｔｉ，Ｎｂ，Ｚ
ｒ１％の少なくとも１種以上を含み、残部がＦｅ及び不
可避的な不純物とからなり、残留オーステナイト量が６
０％以上である合金からなる熱間圧延用ロールで、一体
型又はスリーブ組立式補強ロールからなることを特徴と
する熱間圧延用ロール。 ５）重量比で、Ｃ０．５〜１．２％、Ｓｉ０．７〜３％
、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１０
％、Ｍｏ１〜５％と、Ｗ，Ｖ２％以下、Ｔｉ，Ｎｂ，Ｚ
ｒ１％の少なくとも１種以上を含み、残部がＦｅ及び不
可避的な不純物とからなり、残留オーステナイト量が６
０％以上である合金鋼からなり、基地中の組織がマルテ
ンサイト及びベイナイトと炭化物の１種が１５％以下で
あることを特徴とする熱間圧延用ロール。 ６）重量比で、Ｃ０．５〜１．２％、Ｓｉ０．７〜３％
、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１０
％、Ｍｏ１〜５％と、Ｗ，Ｖ２％以下、Ｔｉ，Ｎｂ，Ｚ
ｒ１％の少なくとも１種以上を含み、残部がＦｅ及び不
可避的な不純物とからなる熱間圧延用ロールにおいて、
胴部のスリーブがエレクトロスラグ再溶解法、金属溶射
法、又は、溶接法で形成されており、スリーブ組立式で
あることを特徴とする熱間圧延用ロール。 ７）重量比で、Ｃ０．５〜１．２％、Ｓｉ０．７〜３％
、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１０
％、Ｍｏ１〜５％と、Ｗ、Ｖ２％以下、Ｔｉ，Ｎｂ，Ｚ
ｒ１％の少なくとも１種以上を含み、残部がＦｅ及び不
可避的な不純物とからなり、残留オーステナイト量が６
０％以上である合金鋼からなることを特徴とする耐食合
金。 ８）粗圧延及び仕上げ前段、後段圧延用の作業ロール及
び補強ロールを有する圧延機において、粗ロール、仕上
げ前段、後段ロールに少なくとも一体および組立式補強
ロールが、重量比で、Ｃ０．５〜１．２％、Ｓｉ０．７
〜３％、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３
〜１０％、Ｍｏ１〜５％と、Ｗ、Ｖ２％以下、Ｔｉ，Ｎ
ｂ，Ｚｒ１％の少なくとも１種以上を含み、残部がＦｅ
及び不可避的な不純物とからなり、残留オーステナイト
量が６０％以上である合金鋼からなることを特徴とする
熱間圧延機。 ９）重量比で、Ｃ０．５〜１．２％、Ｓｉ０．７〜３％
、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１０
％、Ｍｏ１〜５％と、Ｗ、Ｖ２％以下、Ｔｉ，Ｎｂ，Ｚ
ｒ１％の少なくとも１種以上を含み、残部がＦｅ及び不
可避的な不純物とからなり、残留オーステナイト量が６
０％以上である合金鋼よりなり、衝撃摩耗をうける建設
機械用部材に用いることを特徴とする耐食合金。 １０）重量比で、Ｃ０．５〜１．２％、Ｓｉ０．７〜３
％、Ｍｎ０．６〜５％、Ｎｉ０．６〜５％、Ｃｒ３〜１
０％、Ｍｏ１〜５％と、Ｗ、Ｖ２％以下、Ｔｉ，Ｎｂ，
Ｚｒ１％の少なくとも１種以上を含み、残部がＦｅ及び
不可避的な不純物とからなり、残留オーステナイト量６
０％以上の合金鋼からなる熱間圧延用ロールの製造方法
であつて、鋼塊を製造する工程、７５０〜９００℃で焼
鈍する工程、１１００〜１２５０℃で拡散焼鈍後１０５
０〜１２００℃で熱間拘束鍛造を行なう工程、１０００
〜１２００℃で焼入後、１００〜６５０℃の焼戻しを行
なう工程を順次行うことを特徴とする熱間圧延用ロール
の製造方法。[Claims] 1) By weight: C0.5-1.2%, Si0.7-3%
, Mn0.6-5%, Ni0.6-5%, Cr3-10
%, Mo1 to 5%, the balance being Fe and unavoidable impurities, and the amount of retained austenite being 60% or more. 2) Weight ratio: C0.5-1.2%, Si0.7-3%
, Mn0.6-5%, Ni0.6-5%, Cr3-10
%, Mo1-5%, W, V2% or less, Ti, Nb, Z
Alloy steel containing at least one type of r1%, the balance consisting of Fe and unavoidable impurities, and the amount of retained austenite in the body is 60% or more, the hardness is Hs50 or more, and the tensile strength of the shaft material is 80 kg/mm^2 or more. 3) Weight ratio: C0.5-1.2%, Si0.7-3%
, Mn0.6-5%, Ni0.6-5%, Cr3-10
%, Mo1-5%, W, V2% or less, Ti, Nb, Z
A roll for hot rolling, characterized in that it is made of an alloy steel containing at least one kind of r1% or less, the remainder consisting of Fe and unavoidable impurities, and having a retained austenite amount of 60% or more. 4) Weight ratio: C0.5-1.2%, Si0.7-3%
, Mn0.6-5%, Ni0.6-5%, Cr3-10
%, Mo1-5%, W, V2% or less, Ti, Nb, Z
Contains at least one type of r1%, the remainder consists of Fe and unavoidable impurities, and the amount of retained austenite is 6
1. A hot rolling roll made of an alloy of 0% or more, characterized in that it is made of an integral type or sleeve assembly type reinforcing roll. 5) Weight ratio: C0.5-1.2%, Si0.7-3%
, Mn0.6-5%, Ni0.6-5%, Cr3-10
%, Mo1-5%, W, V2% or less, Ti, Nb, Z
Contains at least one type of r1%, the remainder consists of Fe and unavoidable impurities, and the amount of retained austenite is 6
1. A roll for hot rolling, characterized in that the base structure is made of alloy steel containing 0% or more of martensite, bainite, and 15% or less of one type of carbide. 6) Weight ratio: C0.5-1.2%, Si0.7-3%
, Mn0.6-5%, Ni0.6-5%, Cr3-10
%, Mo1-5%, W, V2% or less, Ti, Nb, Z
In a hot rolling roll containing at least one or more of r1% and the remainder consisting of Fe and unavoidable impurities,
1. A hot rolling roll characterized in that the sleeve of the body is formed by an electroslag remelting method, a metal spraying method, or a welding method, and is of a sleeve assembly type. 7) Weight ratio: C0.5-1.2%, Si0.7-3%
, Mn0.6-5%, Ni0.6-5%, Cr3-10
%, Mo1-5%, W, V2% or less, Ti, Nb, Z
Contains at least one type of r1%, the remainder consists of Fe and unavoidable impurities, and the amount of retained austenite is 6
A corrosion-resistant alloy characterized by being made of alloy steel having a content of 0% or more. 8) In a rolling mill having work rolls and reinforcing rolls for rough rolling and finishing front stage and rear stage rolling, at least integral and assembled reinforcing rolls in the roughing roll, finishing stage front stage and rear stage roll have a weight ratio of C0.5 to 1. .2%, Si0.7
~3%, Mn0.6~5%, Ni0.6~5%, Cr3
~10%, Mo1~5%, W, V2% or less, Ti, N
b, contains at least one or more of Zr 1%, and the balance is Fe.
and unavoidable impurities, and the amount of retained austenite is 60% or more. 9) Weight ratio: C0.5-1.2%, Si0.7-3%
, Mn0.6-5%, Ni0.6-5%, Cr3-10
%, Mo1-5%, W, V2% or less, Ti, Nb, Z
Contains at least one type of r1%, the remainder consists of Fe and unavoidable impurities, and the amount of retained austenite is 6
1. A corrosion-resistant alloy made of alloy steel with a content of 0% or more, characterized in that it is used for construction machinery parts that are subject to impact wear. 10) Weight ratio: C0.5-1.2%, Si0.7-3
%, Mn0.6-5%, Ni0.6-5%, Cr3-1
0%, Mo1-5%, W, V2% or less, Ti, Nb,
Contains at least one type of Zr 1%, the balance consists of Fe and unavoidable impurities, and the amount of retained austenite is 6
A method for producing a hot rolling roll made of 0% or more alloy steel, comprising a step of producing a steel ingot, annealing at 750 to 900°C, and 105% after diffusion annealing at 1100 to 1250°C.
Process of hot restraint forging at 0 to 1200°C, 1000
A method for manufacturing a hot rolling roll, comprising sequentially performing steps of quenching at ~1200°C and then tempering at 100~650°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2332175A JP2617029B2 (en) | 1990-11-29 | 1990-11-29 | Corrosion resistant alloy, hot rolling roll, method for producing the same, and hot rolling mill |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2332175A JP2617029B2 (en) | 1990-11-29 | 1990-11-29 | Corrosion resistant alloy, hot rolling roll, method for producing the same, and hot rolling mill |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04198455A true JPH04198455A (en) | 1992-07-17 |
| JP2617029B2 JP2617029B2 (en) | 1997-06-04 |
Family
ID=18252002
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2332175A Expired - Lifetime JP2617029B2 (en) | 1990-11-29 | 1990-11-29 | Corrosion resistant alloy, hot rolling roll, method for producing the same, and hot rolling mill |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2617029B2 (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1300445C (en) * | 2003-12-26 | 2007-02-14 | 东方汽轮机厂 | Turbine high temperature blade and its heat treatment process |
| DE102009010726B3 (en) * | 2009-02-26 | 2010-12-09 | Federal-Mogul Burscheid Gmbh | Piston rings and cylinder liners |
| 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 |
| JP2016068115A (en) * | 2014-09-30 | 2016-05-09 | 日立金属株式会社 | Composite sleeve roll made of hard metal |
| CN105821336A (en) * | 2016-04-28 | 2016-08-03 | 宁国市开源电力耐磨材料有限公司 | Multi-element alloy abrasion-resistant liner plate and casting method thereof |
| CN106222580A (en) * | 2016-08-22 | 2016-12-14 | 合肥东方节能科技股份有限公司 | A kind of high finishing mill slitting wheel alloy material and preparation method thereof |
| CN110218954A (en) * | 2019-04-18 | 2019-09-10 | 江油市长祥特殊钢制造有限公司 | A kind of preparation method of 4Cr13V plastic die steel |
| CN110373527A (en) * | 2019-08-29 | 2019-10-25 | 哈尔滨汽轮机厂有限责任公司 | A kind of heat treatment method improving supercritical turbine heat resisting cast steel material creep rupture strength |
| CN115161544A (en) * | 2022-04-07 | 2022-10-11 | 燕山大学 | Secondary hardening nano bainite hot work die steel and preparation method thereof |
| CN115255807A (en) * | 2022-07-20 | 2022-11-01 | 北京晟鼎新材料科技有限公司 | Long-life surfacing repair and composite manufacturing method for axial roller and main roller of ring forging mill |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2662462A1 (en) * | 2012-05-07 | 2013-11-13 | Valls Besitz GmbH | Low temperature hardenable steels with excellent machinability |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60110841A (en) * | 1983-11-18 | 1985-06-17 | Toyota Motor Corp | High si spheroidal graphite bainite cast iron |
| JPH02153045A (en) * | 1988-12-02 | 1990-06-12 | Hitachi Ltd | Hardened roll for rolling and rolling mill |
| JPH02205656A (en) * | 1989-02-01 | 1990-08-15 | Hitachi Ltd | Quenched roll for rolling |
| 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 |
-
1990
- 1990-11-29 JP JP2332175A patent/JP2617029B2/en not_active Expired - Lifetime
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60110841A (en) * | 1983-11-18 | 1985-06-17 | Toyota Motor Corp | High si spheroidal graphite bainite cast iron |
| JPH02153045A (en) * | 1988-12-02 | 1990-06-12 | Hitachi Ltd | Hardened roll for rolling and rolling mill |
| JPH02205656A (en) * | 1989-02-01 | 1990-08-15 | Hitachi Ltd | Quenched roll for rolling |
| 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 |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1300445C (en) * | 2003-12-26 | 2007-02-14 | 东方汽轮机厂 | Turbine high temperature blade and its heat treatment process |
| DE102009010726B3 (en) * | 2009-02-26 | 2010-12-09 | Federal-Mogul Burscheid Gmbh | Piston rings and cylinder liners |
| 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 |
| JP2016068115A (en) * | 2014-09-30 | 2016-05-09 | 日立金属株式会社 | Composite sleeve roll made of hard metal |
| CN105821336A (en) * | 2016-04-28 | 2016-08-03 | 宁国市开源电力耐磨材料有限公司 | Multi-element alloy abrasion-resistant liner plate and casting method thereof |
| CN106222580A (en) * | 2016-08-22 | 2016-12-14 | 合肥东方节能科技股份有限公司 | A kind of high finishing mill slitting wheel alloy material and preparation method thereof |
| CN110218954A (en) * | 2019-04-18 | 2019-09-10 | 江油市长祥特殊钢制造有限公司 | A kind of preparation method of 4Cr13V plastic die steel |
| CN110373527A (en) * | 2019-08-29 | 2019-10-25 | 哈尔滨汽轮机厂有限责任公司 | A kind of heat treatment method improving supercritical turbine heat resisting cast steel material creep rupture strength |
| CN115161544A (en) * | 2022-04-07 | 2022-10-11 | 燕山大学 | Secondary hardening nano bainite hot work die steel and preparation method thereof |
| CN115255807A (en) * | 2022-07-20 | 2022-11-01 | 北京晟鼎新材料科技有限公司 | Long-life surfacing repair and composite manufacturing method for axial roller and main roller of ring forging mill |
| CN115255807B (en) * | 2022-07-20 | 2024-04-09 | 北京晟鼎新材料科技有限公司 | Long-life surfacing repair and composite manufacturing method for axial roller and main roller of ring rolling mill |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2617029B2 (en) | 1997-06-04 |
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