JP4392376B2 - Method for producing composite roll for hot rolling - Google Patents
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Description
本発明は、熱間圧延用複合ロールにおいて、外層厚みが大きく外層/芯材の断面面積比率が1.0以上、外層長さが外径の1.5倍以上で、外層硬度を80Hs以上確保する熱間圧延用複合ロールの製造方法に関するものである。 The present invention is a composite roll for hot rolling, in which the outer layer thickness is large and the outer layer / core cross-sectional area ratio is 1.0 or more, the outer layer length is 1.5 times or more of the outer diameter, and the outer layer hardness is 80 Hs or more. those related to the hot production method of a rolling composite roll.
熱間圧延用ロールとして、図3(a)に示すように、鋳鋼または鍛鋼製の芯材2の周囲に、ハイス系材料からなる外層1を連続鋳掛け肉盛りにより金属的に接合してなる熱間圧延用複合ロールが知られている。なお、3は外層と芯材との境界である。かかる複合ロールの製造において、連続鋳掛け肉盛りにより複合ロールを形成後、当該ロールの外層に、主として更に耐摩耗性を具備させる目的として、焼入れ、焼戻しなどの熱処理を施し該外層の硬度を例えば80Hs程度に付与させている。
As a roll for hot rolling, as shown in FIG. 3 (a), heat formed by metallicly joining the
かかる複合ロールに対する熱処理の方法が、例えば、特許文献1に開示されている。この技術の概要は、芯材の周囲に、ハイス系材料からなる外層を連続鋳掛け肉盛りにより金属的に接合して複合ロールを形成後、焼入れ冷却時にオーステナイト化温度900〜1100℃で3時間以上加熱した後、400℃まで1〜10時間で冷却させる途中、300〜450℃の温度で3時間以上保定することにより、芯材の膨張変態時に外層と芯材との温度差が小さくなり、該芯材の膨張変態時における外層に作用する引張応力を小さくして外層が割損することを防止するものである。
一般に前記熱間圧延用複合ロールの外層は、前記の如く耐摩耗性を付与させるため高硬度、即ち焼入れ性の良くなる合金元素を多く含んだ成分となっている。それに対して芯材は靭性が必要であるため、合金元素は極力入れない様にしている。従って、焼入れ処理時の冷却時は外層が低温域でマルテンサイト変態或いはベイナイト変態し膨張する。一方、芯材は低温域で膨張変態しないため、低温域での外層膨張変態時に外層と芯材で熱膨張差を生じるため、外層と芯材の境界部に過大な引張応力が働き、この引張応力は外層厚さが大きいほど大きくなる。即ち、外層/芯材の断面積比率が一定以上の値になると、前記熱間圧延用複合ロールにおける径方向の引張応力は境界強度より大きくなり、図3(b)に示すように、境界3から剥離して剥離部4が発生して製品形状を確保出来なくなる。
In general, the outer layer of the composite roll for hot rolling is a component containing a large amount of an alloy element that has high hardness, that is, good hardenability, in order to impart wear resistance as described above. On the other hand, since the core material needs toughness, the alloying elements are kept from entering as much as possible. Accordingly, during cooling during the quenching process, the outer layer expands due to martensitic transformation or bainite transformation in a low temperature region. On the other hand, since the core material does not undergo transformation transformation at a low temperature range, a difference in thermal expansion occurs between the outer layer and the core material at the time of outer layer expansion transformation at a low temperature range. Therefore, an excessive tensile stress acts on the boundary between the outer layer and the core material. The stress increases as the outer layer thickness increases. That is, when the cross-sectional area ratio of the outer layer / core material becomes a certain value or more, the tensile stress in the radial direction in the composite roll for hot rolling becomes larger than the boundary strength, and as shown in FIG. The
前記圧延用複合ロールにおいて、現状外層厚さが大きな実ロールとしては、形鋼、棒鋼及び線材のロールの様に孔型を有する場合、或いは鋼板圧延用ロールで有効径(使用径)が大きいロールについては、外層厚さを大きくする必要がある。その場合、焼入れ冷却時に外層と芯材の境界において境界剥離が生ずる課題を有している。 In the above-mentioned composite roll for rolling, the actual roll having a large outer layer thickness is a roll having a large effective diameter (usable diameter) in the case of having a hole shape, such as a roll of a shape steel, a steel bar and a wire rod. For the above, it is necessary to increase the outer layer thickness. In that case, there is a problem that boundary peeling occurs at the boundary between the outer layer and the core material during quenching cooling.
前記外層厚さが大きい熱間圧延用複合ロールの熱処理に、前記特許文献1に開示されている技術のものを適用してみると、特許文献1に開示されている焼入れの冷却時、300〜450℃で3時間以上保定後、常温まで冷却し、その後、焼戻しをしているため、本発明が対象としている外層厚みが大きなロールにおいては、300℃以下での外層の膨張変態時に外層と芯材で膨張差が大きくなる。特に常温近くの低い温度になると、境界部に境界強度を超えた過大な引張応力が発生するため、実用的な技術でない。
When applying the technique disclosed in
そこで、本発明は、焼入れ処理時の外層.芯材の境界からの剥離トラブルを防止できる熱間圧延用複合ロールの製造方法を提供するものである。 Therefore, the present invention provides an outer layer at the time of quenching treatment. The present invention provides a method for producing a composite roll for hot rolling that can prevent troubles of peeling from the boundary of the core material.
本発明は、低合金鋼又は鋳鋼からなる芯材の周囲に、外層材としてハイス系成分からなる溶湯を連続鋳掛け肉盛り法にて溶着一体化してなる熱間圧延用複合ロールの製造方法において、前記連続鋳掛け法にて、外層と芯材との断面面積比率が1.0以上で外層長さが外径の1.5倍以上の複合ロール素材を形成後、熱処理において、オーステナイト化温度:950〜1150℃にて3時間以上加熱した後、200〜300℃まで1〜3時間で冷却し、引続いて焼戻しを数回行って外層硬度80Hs以上にしたことを特徴とする。 The present invention is a method for producing a composite roll for hot rolling, in which a molten metal composed of a high-speed component as an outer layer material is welded and integrated by a continuous casting overlay method around a core material made of low alloy steel or cast steel. After forming a composite roll material having a cross-sectional area ratio of the outer layer and the core material of 1.0 or more and an outer layer length of 1.5 times or more of the outer diameter by the continuous casting method, in the heat treatment, the austenitizing temperature: 950 After heating at ˜1150 ° C. for 3 hours or more, it is cooled to 200 to 300 ° C. for 1 to 3 hours, followed by tempering several times to obtain an outer layer hardness of 80 Hs or more.
本発明によって、外層厚さの大きいロールでも外層と内層の境界からの剥離トラブルを防止することができ、使用径或いは外層厚さの大きい圧延複合ロールの製造が可能になった。 According to the present invention, it is possible to prevent a peeling trouble from the boundary between the outer layer and the inner layer even in a roll having a large outer layer thickness, and it is possible to produce a rolled composite roll having a large working diameter or a large outer layer thickness.
本発明者らは、前記の課題を解決するために実際に過去、種々の境界剥離を生じた本発明が対象とする熱間圧延用複合ロールと同様な製法、成分、サイズのロールの外層厚さ、熱処理方法を詳細に調査・検討した。その結果、図4に示すように、前記熱間圧延用複合ロールの外層厚さが大きく、詳しくは図2に示す外層断面積S1と芯材断面積S2の比率(S1/S2)が1を超えた場合、且つ、熱処理時、即ち、焼き入れ冷却時に常温まで冷却し、その後に実施する焼戻しの昇温過程でいずれのロールにおいても境界剥離が発生していることが判明した。 In order to solve the above-mentioned problems, the present inventors have actually produced various boundary delaminations in the past, and the outer layer thickness of a roll having the same manufacturing method, composition and size as those of the composite roll for hot rolling targeted by the present invention. The heat treatment method was investigated and examined in detail. As a result, as shown in FIG. 4, the outer layer thickness of the composite roll for hot rolling is large. Specifically, the ratio (S1 / S2) of the outer layer cross-sectional area S1 and the core cross-sectional area S2 shown in FIG. It was found that boundary peeling occurred in any roll during the heat treatment, that is, cooling to quenching at room temperature during quenching and cooling, followed by a temperature raising process of tempering performed thereafter.
なお、ここで、外層と芯材との断面面積比率(S1/S2)が1.0以上であっても、胴長が外径の1.0倍以下の複合ロール、例えば、鋼管圧延用ロール、胴長の短い形鋼ロール等においては、その胴長が短いため、前記焼入れ冷却時に生ずる胴長方向の膨張に対し、芯材も膨張するため、発生応力が軽減されるため境界に発生する外層剥離は生じない。 Here, even if the cross-sectional area ratio (S1 / S2) between the outer layer and the core is 1.0 or more, a composite roll having a body length of 1.0 times or less of the outer diameter, for example, a roll for rolling steel pipes in the cylinder having short section steel roll or the like, therefore barrel length is short with respect to the expansion of the body length direction which occurs during the quenching cooling, since the core expands, occurs at the boundary because the stress generated is reduced No delamination of the outer layer occurs.
即ち、境界に発生する応力は周方向と胴長方向の膨張歪み差により発生する応力であり、 That is, the stress generated at the boundary is the stress generated by the difference in expansion strain between the circumferential direction and the trunk length direction,
また、その後の種々の検討により、前記の境界剥離が発生する原因としては、下記に記す(1)、(2)の相乗作用により、境界剥離に到ったことが判明した。 Further, through various examinations thereafter, it was found that the boundary peeling occurred as a cause of the boundary peeling due to the synergistic action of (1) and (2) described below.
(1)境界部に発生する応力は胴長方向と周方向の外層と芯材の膨張歪み差で発生する応力である。 (1) The stress generated at the boundary is a stress generated due to a difference in expansion strain between the outer layer and the core material in the body length direction and the circumferential direction.
したがって、胴長が外径に対し短い場合は、外層膨張変態時の境界に発生する応力は小さくなる。逆に外径に対し胴長が長い場合には、境界に発生する応力も大きくなる。この発生応力は外層厚さが大きくなると、大きくなる。 Therefore, when the trunk length is shorter than the outer diameter, the stress generated at the boundary during the outer layer expansion transformation is reduced. Conversely, when the body length is long with respect to the outer diameter, the stress generated at the boundary also increases. This generated stress increases as the outer layer thickness increases.
(2)熱処理時、即ち、焼き入れ冷却時に常温まで冷却し、その後に実施する焼戻しにより、外層と芯材の膨張差が最大の時、境界の発生応力が最大になり、更に焼戻し時の昇温時に外層表面から温度上昇するため外層の温度上昇による熱応力も境界部に加わり発生応力が最大となる。 (2) During heat treatment, that is, quenching and cooling to room temperature, the tempering performed thereafter maximizes the stress generated at the boundary when the difference in expansion between the outer layer and the core material is maximum, and further increases during tempering. Since the temperature rises from the surface of the outer layer when it is warm, thermal stress due to the temperature rise of the outer layer is also applied to the boundary portion, and the generated stress becomes maximum.
なお、外層/芯材断面積比率(S1/S2)は以下の方法で計算した。外層の横断面積S1:(π/4)*(D1 2−D2 2)、芯材の横断面積S2:(π/4)*D2 2 The outer layer / core cross-sectional area ratio (S1 / S2) was calculated by the following method. Cross-sectional area S1 of outer layer: (π / 4) * (D 1 2 −D 2 2 ), cross-sectional area S2 of core material: (π / 4) * D 2 2
オーステナイト化温度950〜1150℃に3時間以上加熱とするが、オーステナイト化温度が950℃以下では焼入れ硬度を上げるCの基地への固溶が不十分である。逆に1150℃以上にすると共晶炭化物の一部が溶融するため、950〜1150℃の範囲にした。オーステナイト保定時間は3時間以下では、外層で温度ムラが出るため、均一加熱のため3時間以上とした。 Heating is performed at an austenitizing temperature of 950 to 1150 ° C. for 3 hours or more. However, when the austenitizing temperature is 950 ° C. or less, the solid solution of C that increases the quenching hardness is insufficient. On the other hand, since eutectic carbide partially melts at 1150 ° C. or higher, the temperature range is 950 to 1150 ° C. When the austenite holding time is 3 hours or less, temperature unevenness appears in the outer layer.
300℃まで1〜3時間で冷却した後、続いて焼戻しを数回行う。1時間未満では残留γが多くなる。その後の焼戻しでも残留γが未変態で残る。3時間を越えると、外層内部(内側)で軟らかいパーライトが析出し、80Hs以上の硬度を確保できない。 After cooling to 300 ° C. in 1 to 3 hours, tempering is subsequently performed several times. If it is less than 1 hour, residual γ increases. In the subsequent tempering, residual γ remains untransformed. When it exceeds 3 hours, soft pearlite is precipitated inside (inside) the outer layer, and a hardness of 80 Hs or more cannot be secured.
焼戻しは焼入れ時の残留γのマルテンサイト又はベイナイト変態促進&2次炭化物を析出させ、組織を安定化し、硬度、靭性を向上させる。 Tempering promotes martensite or bainite transformation promotion & secondary carbide of residual γ during quenching, stabilizes the structure, and improves hardness and toughness.
本発明における外層材は、例えば前記特許文献1に開示されているようなハイス系成分であるが、以下にその代表的な成分について、その成分限定理由について説明する。
The outer layer material in the present invention is a high-speed component as disclosed in, for example,
C:1.2〜2.5%
Cは焼入れ性を向上させて基地硬度を高くし、Cr、Mo、W、Vと化合し硬い炭化物をつくり耐摩耗性を向上させる。1.2%未満では炭化物量も少なく、硬度も低くなり耐摩耗性の向上は少ない。また、2.5%を超えると炭化物が粗大或いは炭化物が網目状になり使用中に炭化物或いは炭化物周辺から欠落を生じ、逆に耐摩耗性を悪くする。
C: 1.2 to 2.5%
C improves hardenability and increases the base hardness, and combines with Cr, Mo, W and V to form hard carbides and improve wear resistance. If it is less than 1.2%, the amount of carbide is small, the hardness is low, and the improvement in wear resistance is small. On the other hand, if the content exceeds 2.5%, the carbide is coarse or the carbide becomes a mesh, and the carbide or the periphery of the carbide is lost during use, and the wear resistance is deteriorated.
Si:0.3〜1.5%
Siは鋳造性に影響し、少なすぎると湯流れ性が悪くなり鋳造欠陥等の原因になる。また、溶湯中の酸素とは化合し脱酸効果もありガス巣等の鋳造欠陥の発生を防止するために添加する。0.3%未満ではその効果がなく下限を0.3%とした。1.5%を超えるとその効果が変わらないため、上限を1.5%とした。
Si: 0.3 to 1.5%
Si affects the castability, and if it is too small, the hot-water flow property deteriorates and causes casting defects and the like. Further, it is combined with oxygen in the molten metal to have a deoxidizing effect, and is added to prevent the occurrence of casting defects such as gas nests. If it is less than 0.3%, there is no effect, and the lower limit is set to 0.3%. Since the effect does not change when it exceeds 1.5%, the upper limit was made 1.5%.
Mn:0.3〜1.5%
MnはSiと同様、溶湯の酸素とガス欠陥の発生を防止する。また、MnSを生成し溶湯中のSを固定し、有害な欠陥の発生を防止する。0.3%未満ではその効果がなく、1.5%を超えても効果が変わらないため上限を1.5%とした。
Mn: 0.3 to 1.5%
Mn, like Si, prevents the generation of oxygen and gas defects in the melt. Moreover, MnS is produced | generated, S in molten metal is fixed, and generation | occurrence | production of a harmful defect is prevented. If it is less than 0.3%, there is no effect, and even if it exceeds 1.5%, the effect does not change, so the upper limit was made 1.5%.
Cr:4.0〜10.0%
Crは炭素と同様、基地の焼入れ硬度を上昇させ、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%以上でないとその効果は少なく、10.0%を超えると炭化物が粗大化し熱疲労特性が悪くなり圧延中肌荒れが生じ耐摩耗性が悪くなる。
Cr: 4.0-10.0%
Cr, like carbon, increases the quenching hardness of the base and increases the hardness. Also, C and carbides are made to increase the overall hardness. If Cr is not 4% or more, the effect is small, and if it exceeds 10.0%, the carbides become coarse, the thermal fatigue characteristics deteriorate, the surface becomes rough during rolling, and the wear resistance deteriorates.
Mo:3.0〜10.0%
Moは基地の焼入れ硬度を上昇させる効果的な元素である。また、Moは焼戻し抵抗性の優れた元素でありCr、Wと共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。Moの量は3.0%以上ないと効果がなく3.0%とした。また10.0%を超えると効果は変わらなく、コストも高くなるため10.0%以下とした。
Mo: 3.0 to 10.0%
Mo is an effective element that increases the quenching hardness of the base. Mo is an element excellent in tempering resistance, and forms a high-hardness composite carbide together with Cr and W to increase high-temperature hardness and improve wear resistance. If the amount of Mo is not 3.0% or more, there is no effect and the amount is set to 3.0%. Further, if it exceeds 10.0%, the effect is not changed, and the cost is increased.
W:0.5〜10.0%
WはMo同様、基地の焼入れ性を上げ、且つCr、Moとともに固い複合炭化物をつくり耐摩耗性を向上させる。0.5%以上ないとその効果は少なく、10.0%を超えると粗大な炭化物を生成し、使用中に肌荒れの原因となる。
W: 0.5-10.0%
W, like Mo, improves the hardenability of the base and produces a hard composite carbide together with Cr and Mo to improve wear resistance. If it is not 0.5% or more, the effect is small, and if it exceeds 10.0%, coarse carbides are produced, which causes rough skin during use.
V:2.0〜10.0%
Vは炭素と結合しMC系の硬い微細な炭化物を晶出し、耐摩耗性を向上させる効果的な元素である。その量は最低2.0%以上加えないと効果はない。しかし、10.0%を超えると炭化物が増え過ぎ基地の固溶C量が減少するため基地硬度が低くなる。
V: 2.0 to 10.0%
V is an effective element that combines with carbon to crystallize MC-based hard fine carbides and improve wear resistance. The amount is not effective unless it is added at least 2.0% or more. However, if it exceeds 10.0%, the amount of carbide increases too much and the solid solution C amount of the base decreases, so the base hardness becomes low.
本発明における外層の基本成分は、前記のとおりであるが、適用を対象とするロールのサイズ、要求されるロールの使用特性等により、その他の化学成分として、上記した本発明の化学成分に加えて、さらに以下に記載する化学成分を適宜選択し含有してもよい。 The basic components of the outer layer in the present invention are as described above, but in addition to the above-described chemical components of the present invention as other chemical components, depending on the size of the roll to be applied, required usage characteristics of the roll, and the like. Furthermore, the chemical components described below may be appropriately selected and contained.
Ni:0.1〜3.0%
Niは基地の焼入れ性を向上させ、硬度を高くする効果がある。焼入れ性を向上させるためには0.1%以上必要である。しかし、3.0%を超えると残留オーステナイトが増え硬度低下するため上限を3.0%とした。
Ni: 0.1 to 3.0%
Ni has the effect of improving the hardenability of the base and increasing the hardness. In order to improve hardenability, 0.1% or more is necessary. However, if it exceeds 3.0%, retained austenite increases and hardness decreases, so the upper limit was made 3.0%.
Co:0.1〜10.0%
Coは高温での硬さと強度を向上させる効果がある。高温での耐摩耗性および熱亀裂性が要求されるような圧延条件で使用される場合に効果がある。0.5%以上添加すると効果があるが、経済性の点からその上限を10.0%以下とする。
Co: 0.1-10.0%
Co has the effect of improving the hardness and strength at high temperatures. This is effective when used under rolling conditions that require high temperature wear resistance and thermal cracking. Addition of 0.5% or more is effective, but its upper limit is made 10.0% or less from the viewpoint of economy.
Nb:0.1〜3.0%
NbはVと同様、Cと結合し硬いMC炭化物を生成させ、耐摩耗性を向上させる。NbはVと一緒に添加するため0.1%以上ないとその効果はなく、3.0%を超えて添加するとMC炭化物が増え基地硬度を下げる。
Nb: 0.1-3.0%
Nb, like V, combines with C to form hard MC carbides and improves wear resistance. Since Nb is added together with V, it is not effective unless it is 0.1% or more. If it is added over 3.0%, MC carbide increases and the base hardness is lowered.
次に、本発明について実施例を揚げて詳細に説明する。 Next, the present invention will be described in detail with reference to examples.
表1、表2に本発明と比較例の条件を示す。
図1(a)は本発明の熱処理パターン、(b)は比較例の熱処理パターンである。 FIG. 1A shows a heat treatment pattern of the present invention, and FIG. 1B shows a heat treatment pattern of a comparative example.
本発明1〜6
低合金鋼であるSCM440からなる芯材の周囲に、外層材として表1に示すハイス系化学成分からなる溶湯を連続鋳掛け肉盛り法にて溶着一体化し、同表に示す外層径、境界径、外層と芯材との断面面積比、外層長さが外径の1.5倍以上の複合ロールを形成した。
Inventions 1-6
Around the core material made of SCM440, which is a low alloy steel, a molten metal composed of a high-speed chemical component shown in Table 1 is welded and integrated as an outer layer material by a continuous casting overlay method, and the outer layer diameter, boundary diameter, A composite roll having a cross-sectional area ratio between the outer layer and the core and an outer layer length of 1.5 times or more of the outer diameter was formed.
その後の熱処理は、図1(a)の熱処理パターン、詳しくは、前記表1に示すオーステナイト化温度950〜1150℃々の焼入温度で3時間以上の範囲である5時間で加熱した後、200〜300℃まで1.2〜2.9時間で冷却し、1〜5Hrで保定後又は保定無しで続いて熱処理炉に再度挿入し、500〜550℃の範囲で2回焼戻しした。 Subsequent heat treatment is performed after the heat treatment pattern shown in FIG. 1 (a), more specifically, after heating for 5 hours at a quenching temperature of 950 to 1150 ° C. as shown in Table 1 for 3 hours or more. It cooled to -300 degreeC in 1.2 to 2.9 hours, and it inserted again in the heat processing furnace after hold | maintaining at 1-5Hr, or without hold | maintaining, and tempered twice in the range of 500-550 degreeC.
前記の製造により製造された圧延用複合ロールについて、境界剥離の有無を目視により確認また、外層硬度を測定した。本発明材1〜6においては、いずれも境界剥離は発生してなく、また、外層の硬度はいずれも80Hs以上の値を達成した。
About the composite roll for rolling manufactured by the said manufacture, the presence or absence of boundary peeling was confirmed visually and outer layer hardness was measured. In the
比較例1〜5
比較例1〜5は、前記のとおり過去に外層剥離が生じたロールであり、表1にその製造結果を示す。
Comparative Examples 1-5
Comparative Examples 1-5 are rolls in which outer layer peeling occurred in the past as described above, and Table 1 shows the production results.
低合金鋼であるSCM440からなる芯材の周囲に、外層材として表1に示すハイス系化学成分からなる溶湯を連続鋳掛け肉盛り法にて溶着一体化し、同表に示す外層径、境界径、外層と芯材との断面面積比、外層長さが外径の1.5倍以上、即ち、前記本発明1〜6と同様な複合ロールである。 Around the core material composed of SCM440, which is a low alloy steel, a molten steel composed of a high-speed chemical component shown in Table 1 is welded and integrated as an outer layer material by a continuous casting overlay method, and the outer layer diameter, boundary diameter, The cross-sectional area ratio between the outer layer and the core material and the outer layer length are 1.5 times or more of the outer diameter, that is, the composite roll similar to the first to sixth inventions.
その後の熱処理は、図1(b)の熱処理パターン、詳しくは、前記表1に示すオーステナイト化温度950〜1150℃の焼入温度で5時間で加熱した後、常温(50℃以下)までを1.8〜3時間で冷却した後、続いて熱処理炉に再度挿入し、500〜550℃で焼戻しする予定であったが、焼戻しの昇温過程で何れのロールも外層と芯材との境界から剥離が発生している。 Subsequent heat treatment is performed in the heat treatment pattern of FIG. 1B. Specifically, after heating at a quenching temperature of 950 to 1150 ° C. shown in Table 1 for 5 hours, the heat treatment is performed up to room temperature (50 ° C. or lower). .After cooling in 8 to 3 hours, it was planned to be inserted again into the heat treatment furnace and tempered at 500 to 550 ° C., but any roll was removed from the boundary between the outer layer and the core material in the temperature raising process of tempering. Peeling has occurred.
1.外層
2.芯材
3.外層と芯材との境界
4.剥離部
1.
Claims (1)
前記連続鋳掛け法にて、外層と芯材との断面面積比率が1.0以上で外層長さが外径の1.5倍以上の複合ロール素材を形成後、熱処理において、オーステナイト化温度:950〜1150℃にて3時間以上加熱した後、200〜300℃まで1〜3時間で冷却し、引続いて焼戻しを数回行って外層硬度80Hs以上にしたことを特徴とする熱間圧延用複合ロールの製造方法。 In the manufacturing method of a composite roll for hot rolling, in which a molten metal composed of a high-speed component as an outer layer material is welded and integrated around a core material made of low alloy steel or cast steel by a continuous casting overlay method,
After forming a composite roll material having a cross-sectional area ratio of the outer layer and the core material of 1.0 or more and an outer layer length of 1.5 times or more of the outer diameter by the continuous casting method, in the heat treatment, the austenitizing temperature: 950 After heating at ˜1150 ° C. for 3 hours or more, cooling to 200 to 300 ° C. in 1 to 3 hours, followed by tempering several times to obtain an outer layer hardness of 80 Hs or more, a composite for hot rolling A method for manufacturing a roll.
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