JPH01225751A - Work roll for heavy-load cold rolling excellent in spalling resistance and its production - Google Patents
Work roll for heavy-load cold rolling excellent in spalling resistance and its productionInfo
- Publication number
- JPH01225751A JPH01225751A JP4862488A JP4862488A JPH01225751A JP H01225751 A JPH01225751 A JP H01225751A JP 4862488 A JP4862488 A JP 4862488A JP 4862488 A JP4862488 A JP 4862488A JP H01225751 A JPH01225751 A JP H01225751A
- Authority
- JP
- Japan
- Prior art keywords
- roll
- less
- hardness
- cold rolling
- subjected
- 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
- 238000005097 cold rolling Methods 0.000 title claims abstract description 13
- 238000004901 spalling Methods 0.000 title claims abstract description 10
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 8
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 24
- 238000010438 heat treatment Methods 0.000 claims abstract description 13
- 238000011282 treatment Methods 0.000 claims abstract description 11
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 10
- 239000010959 steel Substances 0.000 claims abstract description 10
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 239000002344 surface layer Substances 0.000 claims abstract description 8
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 7
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 7
- 238000000034 method Methods 0.000 claims abstract description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 6
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 6
- 238000005242 forging Methods 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 230000006698 induction Effects 0.000 claims abstract description 5
- 230000000717 retained effect Effects 0.000 claims description 17
- 238000010791 quenching Methods 0.000 claims description 9
- 230000000171 quenching effect Effects 0.000 claims description 9
- 238000005496 tempering Methods 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 7
- 239000000203 mixture Substances 0.000 abstract description 6
- 229910052742 iron Inorganic materials 0.000 abstract 1
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 12
- 238000012546 transfer Methods 0.000 description 10
- 238000005096 rolling process Methods 0.000 description 7
- 239000011159 matrix material Substances 0.000 description 4
- 230000007423 decrease Effects 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 101150018425 Cr1l gene Proteins 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 238000009661 fatigue test Methods 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000010606 normalization Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000000979 retarding effect Effects 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 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)
- Heat Treatment Of Articles (AREA)
Abstract
Description
【発明の詳細な説明】
〈産業上の利用分野〉
本発明はビッカース硬さ(Hv)が800以上の表面硬
さを有する冷間圧延用ワークロールおよびその製造方法
に関し、とくにスポーリング破損などの事故に対する耐
久性を高めようとするものである。Detailed Description of the Invention <Industrial Application Field> The present invention relates to a work roll for cold rolling having a surface hardness with a Vickers hardness (Hv) of 800 or more and a method for manufacturing the same, and particularly relates to a work roll for cold rolling having a surface hardness of 800 or more in Vickers hardness (Hv), and a method for manufacturing the same. The aim is to increase durability against accidents.
〈従来の技術〉
冷間圧延においては、近年変形抵抗の高い材料や、より
肉厚の薄いものを圧延することへの要望が強いため、ワ
ークロールへの負荷はますます増大する傾向にある。そ
のため、ロールの摩耗が著しくなり、ロールの交替頻度
が増し圧延能率などの低下を生じており、硬さを増加し
たり、あるいは炭化物量を増加したりして、耐摩耗性を
向上させる方法が利用されている。一方、ワークロール
にかかる負荷の増大は、ロールの損傷確率も上昇する傾
向にあり、ロールの耐事故性の向上も必要である。とこ
ろが硬さの増加、炭化物量の増加は、耐事故性を低下さ
せる傾向であり、耐事故性の向上が一層要望されていた
。<Prior Art> In cold rolling, there has been a strong demand in recent years for materials with high deformation resistance and for rolling thinner materials, so the load on work rolls has tended to increase more and more. As a result, the wear of the rolls has become significant, the frequency of roll replacement has increased, and rolling efficiency has been reduced.Therefore, there is no way to improve wear resistance by increasing the hardness or the amount of carbide. It's being used. On the other hand, an increase in the load applied to the work rolls tends to increase the probability of damage to the rolls, and it is also necessary to improve the accident resistance of the rolls. However, an increase in hardness and an increase in the amount of carbide tend to reduce accident resistance, and there has been a demand for further improvement in accident resistance.
特公昭61−21300号公報には2〜4%(重量%以
下同じ) Crを含有し、かつCを1〜2%、■を1〜
2%含有し、含有炭化物量を増加させることにより耐摩
耗性を増加させ、同時に耐クラツク性。Japanese Patent Publication No. 61-21300 contains 2 to 4% (same weight %) Cr, 1 to 2% C, and 1 to 1% ■.
Contains 2% and increases wear resistance by increasing the amount of carbide contained, as well as crack resistance.
耐折損性を改善した大径のワークロールが開示されてい
る。また特開昭57−47849号公報には、0.4〜
3.0%Mo、 0.2〜2%Vを含む高Cr系冷延用
ワークロールが提案されている。これは硬さをHv80
0以下と制限し、合金炭化物量の増大により耐摩耗性を
向上させたものだが、硬さを低く抑えているため、圧延
時のロールのへこみの問題が懸念され、しかもC、Cr
、 Mo+ Vが高いため、鍛造性が悪く、製造コス
トも高かった。A large diameter work roll with improved breakage resistance is disclosed. Furthermore, in Japanese Patent Application Laid-open No. 57-47849, 0.4~
A high Cr cold rolling work roll containing 3.0% Mo and 0.2 to 2% V has been proposed. This has a hardness of Hv80
0 or less, and the wear resistance is improved by increasing the amount of alloy carbide, but since the hardness is kept low, there is a concern about the problem of roll dents during rolling.
, Mo+V was high, so the forgeability was poor and the manufacturing cost was high.
〈発明が解決しようとする課題〉
これら従来の技術では、鍛造性が劣り、しかも高価な合
金元素を多量に含有しており、またV。<Problems to be Solved by the Invention> These conventional techniques have poor forgeability, contain large amounts of expensive alloying elements, and contain V.
Mo、 Cr等の含有量を富め硬さを増加しているので
、靭性が劣り、ロール寿命が短く、特に耐スポーリング
性に問題を残していた。Since the content of Mo, Cr, etc. is increased and the hardness is increased, the toughness is poor, the roll life is short, and there remains a problem particularly in spalling resistance.
本発明は高負荷圧延において、スポーリングなどの事故
発生の少ない、しかも耐摩耗性のすぐれたロールおよび
その製造方法を提供するものである。The present invention provides a roll that is less likely to cause accidents such as spalling during high-load rolling, and has excellent wear resistance, and a method for manufacturing the roll.
く課題を解決するための手段〉
本発明は(11重量%で、C: 0.80〜1.00%
、Si:0.10〜0.65%、 Mn : 0.20
〜1.60%+ Cr: 4.O〜6.5%、 Ni
: 0.10〜0.70%、 Mo : 0.30%
以下、■:O,XO%以下、P:0.25%以下、
S : 0.010%以下、残部Feおよび不可避的
不純物からなり、表層部の硬度がビッカース硬度でll
v 800を超え、かつ残留オーステナイト量が、体積
率で5%以上有することを特徴とする耐スポーリング性
に優れた高負荷冷間圧延用ワークロールおよび(2)重
量%で、C: 0.80〜1.00%、 Si : 0
.10〜0.65%、 Mn : 0.20〜1.60
%、 Cr : 4.0〜6.5%、 Ni : 0.
10〜0.10%。Means for Solving the Problems> The present invention provides (11% by weight, C: 0.80-1.00%
, Si: 0.10-0.65%, Mn: 0.20
~1.60%+Cr: 4. O~6.5%, Ni
: 0.10~0.70%, Mo: 0.30%
Below, ■: O, XO% or less, P: 0.25% or less,
S: 0.010% or less, the balance consists of Fe and unavoidable impurities, and the hardness of the surface layer is 11 on Vickers hardness.
A work roll for high-load cold rolling with excellent spalling resistance characterized by having a residual austenite content of more than 800 and a volume fraction of 5% or more, and (2) a C: 0. 80-1.00%, Si: 0
.. 10~0.65%, Mn: 0.20~1.60
%, Cr: 4.0-6.5%, Ni: 0.
10-0.10%.
Mo : 0.30%以下、V:o、to%以下、Pl
、25%以下、 s : o、oto%以下、残部
Feおよび不可避的不純物からなる鋼を所定の形状に鍛
造後、焼入焼戻処理をし、次いで誘導加熱により表層部
を930〜1000℃の温度範囲に昇温しオーステナイ
ト化し、焼入れ処理後O〜−50℃の温度範囲で゛サブ
ゼロ処理を施し、引続き110〜150’Cの温度範囲
で焼戻しすることを特徴とする耐スポーリング性に優れ
た高負荷冷間圧延用ワークロールの製造方法である。Mo: 0.30% or less, V: o, to% or less, Pl
, 25% or less, s: o, oto% or less, the remainder being Fe and unavoidable impurities. After forging the steel into a predetermined shape, it is quenched and tempered, and then the surface layer is heated to 930 to 1000°C by induction heating. It has excellent spalling resistance, characterized by being heated to a temperature range to austenitize, then quenched, then subjected to sub-zero treatment in a temperature range of 0 to -50 degrees Celsius, and then tempered in a temperature range of 110 to 150 degrees Celsius. This is a method for manufacturing work rolls for high-load cold rolling.
く作 用〉
冷間圧延用ワークロールの耐事故性の指標として、転勤
疲労により導入されたクラックが起点となり大きなスポ
ーリングが生じることから、転勤疲労寿命が挙げられる
。転勤疲労寿命が長いことはロールの耐事故性を高める
ことになる。そこで、転勤疲労寿命をとくに高い面正に
おいて各種の要因をかえて検討した結果、残留オーステ
ナイト量と化学成分の適正な組合せにより転勤疲労寿命
が大きく変化することを発見した。Effects〉 As an indicator of the accident resistance of work rolls for cold rolling, transfer fatigue life is cited because large spalling occurs with cracks introduced due to transfer fatigue as a starting point. A long transfer fatigue life increases the accident resistance of the roll. Therefore, as a result of examining various factors to determine the transfer fatigue life, especially at high surface roughness, it was discovered that the transfer fatigue life greatly changes depending on the appropriate combination of retained austenite amount and chemical components.
第1図には本発明の組成範囲の鋼およびCrが低い鋼の
転勤疲労試験結果と残留オーステナイト量の関係につい
て示したもので、本発明の範囲の鋼であれば、残留オー
ステナイトが5%以上(体積率)で転勤疲労寿命が著し
く長時間側となり、スポーリング発生まで長時間の負荷
に耐えうることが分かる。このように残留オーステナイ
トがロールの耐事故性に重要な要因であるが、とくに転
勤疲労寿命に及ぼす残留オーステナイトの効果は、化学
組成−により大きく変化し第1図かられかるように、C
rfiの低い場合には、残留オーステナイトの効果が顕
著でない。Figure 1 shows the relationship between the transfer fatigue test results and the amount of retained austenite for steels in the composition range of the present invention and steels with low Cr content. It can be seen that the transfer fatigue life is significantly longer at (volume ratio), and that it can withstand long-term loads until spalling occurs. As described above, retained austenite is an important factor in the accident resistance of rolls, but the effect of retained austenite on rolling fatigue life in particular varies greatly depending on the chemical composition.
When rfi is low, the effect of retained austenite is not significant.
硬さの高いロールでは、クランクが発生すると、直ちに
大きく損傷し、事故につながるので転勤疲労寿命を高め
ることが重要である。そのためには、安定な残留オース
テナイト量の確保が必要となるが、従来は硬さを確保す
るために残留オーステナイト量の減少をもっばらはかる
考え方であったが、本発明はこのように別の思想に基づ
くものである。If a roll with high hardness is cranked, it will immediately be severely damaged and lead to an accident, so it is important to increase the rolling fatigue life. To achieve this, it is necessary to secure a stable amount of retained austenite, and conventionally the idea was to reduce the amount of retained austenite to ensure hardness, but the present invention adopts a different idea as described above. It is based on
本発明のロールは表面硬さがビッカース硬度でHv’
800以上に限定されるが、これは高負荷冷間圧延用ワ
ークロールとしての耐摩耗性の点およびへこみ発生の防
止の点から必要な硬度である。The roll of the present invention has a surface hardness of Hv' in terms of Vickers hardness.
The hardness is limited to 800 or more, which is necessary from the viewpoint of wear resistance as a work roll for high-load cold rolling and prevention of occurrence of dents.
つぎに、本発明の成分限定理由について述べる。Next, the reason for limiting the ingredients of the present invention will be described.
c : o、so〜1.00%
本成分系で、Cは一部基地中に固溶し、焼入性を向上さ
せる元素であり、Cr、 Mo+ vと炭化物を形成
し、耐摩耗性を向上させる。しかし、0.80%未満で
は焼入性に対してその効果が少なく 、1.00%を超
えると巨大な共晶炭化物を晶出し、加工性を害するため
、Cは0.80〜1.00%の範囲に制限される。c: o, so~1.00% In this component system, C is an element that partially dissolves in the matrix and improves hardenability, and forms carbides with Cr and Mo+v, improving wear resistance. Improve. However, if it is less than 0.80%, it has little effect on hardenability, and if it exceeds 1.00%, huge eutectic carbides will crystallize, impairing workability. % range.
Si : 0.10〜0.65%
Siは、焼入性と焼戻軟化抵抗を高める効果や、マルテ
ンサイトの分解を遅滞する効果があるが、0.1%未満
ではその効果が少なく 、0.65%を超えると脆化を
助長するため、0.10〜0.65%の範囲に制限され
る。Si: 0.10-0.65% Si has the effect of increasing hardenability and temper softening resistance, and the effect of retarding the decomposition of martensite, but if it is less than 0.1%, the effect is small and 0. If it exceeds .65%, it promotes embrittlement, so it is limited to a range of 0.10 to 0.65%.
Mn : 0.20〜1.60%
Mnは焼入性を増加させかつオーステナイトを安定化さ
せる元素であるが、0.2%未満ではその効果が小さく
、1’、60%を超えると脆化を生ずるため、0.2
0〜1.60%の範囲とした。Mn: 0.20-1.60% Mn is an element that increases hardenability and stabilizes austenite, but if it is less than 0.2%, the effect is small, and if it exceeds 1', 60%, it becomes brittle. 0.2
The range was 0 to 1.60%.
(:r: 4.0〜6.5%
Crは炭化物形成元素であり、炭化物はマトリックス中
に分散し耐摩耗性を向上させるとともに、一部は固溶し
てオーステナイトを安定化し、焼入性を増加させる。C
r量の増加により、Cr炭化物量の増加をもたらし耐摩
耗性を向上させることが従来から知られている。本発明
ではさらに、4.0%以上添加し、Ni添加量との組合
せで熱処理を適正化することにより、安定な残留オース
テナイト量が増加し、転勤疲労特性が向上することを見
いだした。しかしCr1lが6.5%を越えると炭化物
量の増加によりマトリックス中に固溶するC量が減少す
るため焼入性が阻害される。したがって、Cr量は4.
0〜6.5%の範囲とした。(:r: 4.0-6.5% Cr is a carbide-forming element. Carbide is dispersed in the matrix and improves wear resistance, and some of it is dissolved in solid solution to stabilize austenite and improve hardenability. Increase C.
It has been conventionally known that an increase in the amount of r brings about an increase in the amount of Cr carbide and improves wear resistance. In the present invention, we have further discovered that by adding 4.0% or more and optimizing the heat treatment in combination with the amount of Ni added, the amount of stable retained austenite increases and the transfer fatigue properties are improved. However, when Cr1l exceeds 6.5%, the amount of C dissolved in the matrix decreases due to the increase in the amount of carbides, which impairs hardenability. Therefore, the amount of Cr is 4.
The range was 0 to 6.5%.
旧1.10〜0.70%
Niは焼入性を増加させ、さらに残留オーステナイトを
安定に増加させる元素であり高負荷圧延ロールに必要な
元素である。0.1%未満では、その効果が少なく、0
.7%を越えると硬さ確保の効果は飽和し、経済的でな
いので0.10〜0,70%の範囲とした。Old 1.10 to 0.70% Ni is an element that increases hardenability and stably increases retained austenite, and is an element necessary for high-load rolling rolls. If it is less than 0.1%, the effect is small and 0.
.. If it exceeds 7%, the effect of ensuring hardness is saturated and is not economical, so it is set in the range of 0.10 to 0.70%.
台o : 0.30%以下
Moは焼入性1耐摩耗性を増加させる元素であるが、多
量の添加は熱間加工性を害することおよび経済性の観点
から0.30%以下に制限される。Mo: 0.30% or less Mo is an element that increases hardenability 1 wear resistance, but addition of a large amount is limited to 0.30% or less because it impairs hot workability and from the economic point of view. Ru.
V:0.10%以下
■は炭化物形成元素であり、Crと同様に、マトリック
ス中に分散して耐摩耗性を向上させるが、0.10%を
越えると研削性が劣化するため、0.10%以下とした
。V: 0.10% or less ■ is a carbide-forming element, and like Cr, it is dispersed in the matrix and improves wear resistance, but if it exceeds 0.10%, grindability deteriorates, so 0. It was set to 10% or less.
S : 0.010%以下
Sは介在物量を増し疲労寿命を低下させるので、o、o
io%以下に制限される。S: 0.010% or less S increases the amount of inclusions and reduces fatigue life, so o, o
io% or less.
P : 0.025%以下
PはSと同様、有害元素で脆化を助長するため、その量
を減少させる必要があり、0.025%以下に制限され
る。P: 0.025% or less Like S, P is a harmful element and promotes embrittlement, so its amount must be reduced and is limited to 0.025% or less.
上記の化学成分の組成になる鋼塊は、鍛造後、−通常の
次の熱処理が施される。After forging, the steel ingot having the above chemical composition is subjected to the following usual heat treatment.
まず、焼ならし、球状化焼ならし処理を行い、内質の均
一性を得る。さらに焼入れ焼戻し処理によりロール内部
の靭性を確保する。First, normalization and spheroidization are performed to obtain uniformity of internal quality. Furthermore, the toughness inside the roll is ensured by quenching and tempering.
その後、硬化に必要な表層領域のみ930〜1000℃
の温度範囲に昇温しで表面焼入れを実施する。After that, only the surface layer area necessary for curing is heated to 930-1000℃.
Surface hardening is performed by raising the temperature to a temperature range of .
この表面焼入れには誘導加熱を用いる。硬化領域すなわ
ち、ロール使用領域においては、硬くかつ耐事故性が良
好でなくてはならない。加熱温度が930℃未満では硬
さが低(、加熱温度が1000℃を越えると残留オース
テナイトが多量に残存し、サブゼロ処理を施しても硬さ
が低い。Induction heating is used for this surface hardening. The hardened area, ie, the area where rolls are used, must be hard and have good accident resistance. If the heating temperature is less than 930°C, the hardness will be low (and if the heating temperature exceeds 1000°C, a large amount of retained austenite will remain, and the hardness will be low even if sub-zero treatment is performed.
次のサブゼロ処理により不安定なオーステナイトを変態
させ、硬さの上界をはかる。一方安定な残留オーステナ
イト量を5%以上得ることが、耐事故性の向上に必要で
ある。The next sub-zero treatment transforms the unstable austenite and establishes the upper limit of hardness. On the other hand, it is necessary to obtain a stable amount of retained austenite of 5% or more in order to improve accident resistance.
C: 0.95%、 Si : 0.60%、 Mn
: 0.40%+Ni:0.15%、 Cr: 5.
0%、 Mo : 0.30%、V:0.07%。C: 0.95%, Si: 0.60%, Mn
: 0.40%+Ni: 0.15%, Cr: 5.
0%, Mo: 0.30%, V: 0.07%.
P : 0.012%、 S : 0.003%
の鋼について、その加熱温度と一30″Cサブゼロ処理
、120”C焼戻しにより得られたロールの表面硬さと
の関係を第2図に示す。P: 0.012%, S: 0.003%
Figure 2 shows the relationship between the heating temperature and the surface hardness of the roll obtained by -30''C sub-zero treatment and 120''C tempering for the steel.
焼入温度が930℃未満の温度では必要十分な硬さが得
られない、一方、1000℃を超えると、残留オーステ
ナイト量の増加を招き、硬さの著しい低下を招くととも
に、オーステナイト粒径が粗大化となり、靭性が低下し
逆効果となる。そこで、焼入温度は925〜1000℃
の範囲に制限される。また、サブゼロ処理温度の上限は
、Hv 800を超える硬さを確保するため0℃とし、
第3図に示すように5%以上の残留オーステナイトを得
るためには一50℃を下限とした。If the quenching temperature is less than 930°C, the necessary and sufficient hardness cannot be obtained. On the other hand, if the quenching temperature exceeds 1000°C, the amount of retained austenite will increase, resulting in a significant decrease in hardness, and the austenite grain size will become coarse. , and the toughness decreases, which has the opposite effect. Therefore, the quenching temperature is 925-1000℃.
limited to the range of In addition, the upper limit of the sub-zero treatment temperature is 0°C to ensure hardness exceeding Hv 800.
As shown in FIG. 3, in order to obtain 5% or more retained austenite, the lower limit was set at -50°C.
〈実施例〉
第1表に示す組成の鋼を電気炉ついで取鍋精錬炉で溶製
し造塊した。これらの鋼塊は鍛造により直径600 r
taのロール形状に成形された。次に1000℃に加熱
焼入れし700’Cで焼戻し処理した、各ロールに第2
表に示す熱処理を施し、熱処理後の製品について残留オ
ーステナイト、硬さ、転勤寿命比をそれぞれ調べた。そ
の結果を第2表に併せて示す、なお熱処理は誘導加熱に
より表層下25mm程度まで焼入れ温度に加熱し、焼入
れは水中に焼入れた。<Example> Steel having the composition shown in Table 1 was melted and made into ingots in an electric furnace and then in a ladle refining furnace. These steel ingots are forged to a diameter of 600 r.
It was formed into a ta roll shape. Next, a second
The heat treatments shown in the table were performed, and the retained austenite, hardness, and transfer life ratio of the heat-treated products were examined. The results are also shown in Table 2.The heat treatment was carried out by induction heating to the quenching temperature up to about 25 mm below the surface layer, and the quenching was performed by quenching in water.
〈発明の効果〉
本発明によれば、比較的少ない合金添加により高負荷冷
間圧延時におけるロールの寿命の大幅な延長が期待でき
ロール原単位の向上が可能となる。<Effects of the Invention> According to the present invention, by adding a relatively small amount of alloy, the life of the roll can be expected to be significantly extended during high-load cold rolling, and the roll unit consumption can be improved.
第1図は転勤疲労寿命に及ぼす残留オーステナイ13の
影響を示す測定図、第2図は焼入温度と硬さの関係を示
す測定図、第3図はサブゼロ処理温度と残留オーステナ
イl−ff1との関係を示すグラフである。
特許出願人 川崎製鉄株式会社
第1図
り(冒rR(%〕
第2図
九心渡(℃)
第3図
サブゼロ処理温度(℃)Figure 1 is a measurement diagram showing the influence of retained austenite 13 on transfer fatigue life, Figure 2 is a measurement diagram showing the relationship between quenching temperature and hardness, and Figure 3 is a measurement diagram showing the relationship between sub-zero treatment temperature and retained austenite l-ff1. It is a graph showing the relationship between. Patent Applicant: Kawasaki Steel Co., Ltd. 1st chart (R (%)) Figure 2 Kushinwa (℃) Figure 3 Sub-zero treatment temperature (℃)
Claims (2)
.10〜0.65%、Mn:0.20〜1.60%、C
r:4.0〜6.5%、Ni:0.10〜0.70%、
Mo:0.30%以下、V:0.10%以下、P:0.
25%以下、S:0.010%以下、残部Feおよび不
可避的不純物からなり、表層部の硬度がビッカース硬度
でHv800を超え、かつ残留オーステナイト量が、体
積率で5%以上有することを特徴とする耐スポーリング
性に優れた高負荷冷間圧延用ワークロール。(1) In weight%, C: 0.80-1.00%, Si: 0
.. 10-0.65%, Mn: 0.20-1.60%, C
r: 4.0-6.5%, Ni: 0.10-0.70%,
Mo: 0.30% or less, V: 0.10% or less, P: 0.
25% or less, S: 0.010% or less, the balance is Fe and unavoidable impurities, the hardness of the surface layer exceeds Hv800 in Vickers hardness, and the amount of retained austenite is 5% or more in volume percentage. A work roll for high-load cold rolling with excellent spalling resistance.
.10〜0.65%、Mn:0.20〜1.60%、C
r:4.0〜6.5%、Ni:0.10〜0.70%、
Mo:0.30%以下、V:0.10%以下、P:0.
25%以下、S:0.010%以下、残部Feおよび不
可避的不純物からなる鋼を所定の形状に鍛造後、焼入焼
戻処理をし、次いで誘導加熱により表層部を930〜1
000℃の温度範囲に昇温しオーステナイト化し、焼入
れ処理後0〜−50℃の温度範囲でサブゼロ処理を施し
、引続き110〜150℃の温度範囲で焼戻しすること
を特徴とする耐スポーリング性に優れた高負荷冷間圧延
用ワークロールの製造方法。(2) In weight%, C: 0.80-1.00%, Si: 0
.. 10-0.65%, Mn: 0.20-1.60%, C
r: 4.0-6.5%, Ni: 0.10-0.70%,
Mo: 0.30% or less, V: 0.10% or less, P: 0.
25% or less, S: 0.010% or less, the balance being Fe and unavoidable impurities. After forging the steel into a predetermined shape, it is quenched and tempered, and then the surface layer is heated to 930~1 by induction heating.
Spalling resistance characterized by raising the temperature to a temperature range of 000℃ to austenite, performing sub-zero treatment in a temperature range of 0 to -50℃ after quenching, and subsequently tempering in a temperature range of 110 to 150℃. A method for manufacturing excellent work rolls for high-load cold rolling.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP4862488A JPH01225751A (en) | 1988-03-03 | 1988-03-03 | Work roll for heavy-load cold rolling excellent in spalling resistance and its production |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP4862488A JPH01225751A (en) | 1988-03-03 | 1988-03-03 | Work roll for heavy-load cold rolling excellent in spalling resistance and its production |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH01225751A true JPH01225751A (en) | 1989-09-08 |
Family
ID=12808557
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP4862488A Pending JPH01225751A (en) | 1988-03-03 | 1988-03-03 | Work roll for heavy-load cold rolling excellent in spalling resistance and its production |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH01225751A (en) |
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
BE1004247A5 (en) * | 1989-06-26 | 1992-10-20 | Hitachi Ltd | Working cylinder rolling metal and manufacturing method thereof. |
KR100719397B1 (en) * | 2000-11-17 | 2007-05-17 | 두산중공업 주식회사 | Deep hardened work roll for cold strip mills |
KR100852089B1 (en) * | 2006-07-26 | 2008-08-13 | 두산중공업 주식회사 | Anti-Thermal Shock Forged Work Roll for Cold Rolling and The Manufacturing Method of The Work Roll |
JP2010242166A (en) * | 2009-04-06 | 2010-10-28 | Kobe Steel Ltd | Cold rolling roll made from forged steel excellent in toughness |
CN102002644A (en) * | 2010-09-26 | 2011-04-06 | 中钢集团邢台机械轧辊有限公司 | Working roll for automobile sheet cold rolling and manufacturing method thereof |
CN106282510A (en) * | 2016-08-25 | 2017-01-04 | 瑞安市劲力机械制造有限公司 | The forging of Cr12 steel mold and Technology for Heating Processing |
-
1988
- 1988-03-03 JP JP4862488A patent/JPH01225751A/en active Pending
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
BE1004247A5 (en) * | 1989-06-26 | 1992-10-20 | Hitachi Ltd | Working cylinder rolling metal and manufacturing method thereof. |
KR100719397B1 (en) * | 2000-11-17 | 2007-05-17 | 두산중공업 주식회사 | Deep hardened work roll for cold strip mills |
KR100852089B1 (en) * | 2006-07-26 | 2008-08-13 | 두산중공업 주식회사 | Anti-Thermal Shock Forged Work Roll for Cold Rolling and The Manufacturing Method of The Work Roll |
JP2010242166A (en) * | 2009-04-06 | 2010-10-28 | Kobe Steel Ltd | Cold rolling roll made from forged steel excellent in toughness |
CN102002644A (en) * | 2010-09-26 | 2011-04-06 | 中钢集团邢台机械轧辊有限公司 | Working roll for automobile sheet cold rolling and manufacturing method thereof |
CN106282510A (en) * | 2016-08-25 | 2017-01-04 | 瑞安市劲力机械制造有限公司 | The forging of Cr12 steel mold and Technology for Heating Processing |
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