JPH11342403A - Method of manufacturing hot-rolled sheet of high nickel alloy - Google Patents
Method of manufacturing hot-rolled sheet of high nickel alloyInfo
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- JPH11342403A JPH11342403A JP16155198A JP16155198A JPH11342403A JP H11342403 A JPH11342403 A JP H11342403A JP 16155198 A JP16155198 A JP 16155198A JP 16155198 A JP16155198 A JP 16155198A JP H11342403 A JPH11342403 A JP H11342403A
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- hot
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は連続鋳造鋳片から表
面品質の優れた高Ｎｉ合金熱間圧延板を製造する方法に
関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a high Ni alloy hot rolled sheet having excellent surface quality from a continuously cast slab.
【０００２】[0002]
【従来の技術】高Ｎｉ合金は主として電子部品用材料と
して使用されている。例えば、Ｆｅ−４２％Ｎｉ合金は
電気伝導性、耐熱性、曲げ加工性、めっき付着性および
はんだ付着性が優れていることから、ＩＣリードフレー
ムに使用されている。また、熱膨張率の最も小さいＦｅ
−３６％Ｎｉ合金はカラーテレビ受信機のシャドウマス
クなどに使用されている。さらに、ＰＤ材、ＰＢ材、Ｐ
Ｃ材など３０〜８５％Ｎｉ合金は磁気特性が優れている
ことや、蛍光表示管などの封着性の点から磁気シールド
ケースなど磁性材料、電子材料や封着材料として使用さ
れている。これらリードフレームやシャドウマスクおよ
び磁性材料、封着材料用などの圧延板の表面品質に対す
る要求は極めて厳しく、また、歩留向上は製造コスト低
減の最重要項目であり、製造工程での疵防止による歩留
向上が望まれる。2. Description of the Related Art High Ni alloys are mainly used as materials for electronic parts. For example, an Fe-42% Ni alloy is used for IC lead frames because of its excellent electrical conductivity, heat resistance, bending workability, plating adhesion, and solder adhesion. In addition, Fe having the smallest coefficient of thermal expansion
The -36% Ni alloy is used for a shadow mask of a color television receiver. Furthermore, PD material, PB material, P
A 30-85% Ni alloy such as a C material is used as a magnetic material such as a magnetic shield case, an electronic material or a sealing material from the viewpoint of excellent magnetic properties and sealing properties such as a fluorescent display tube. The demands on the surface quality of rolled plates such as those for lead frames, shadow masks, magnetic materials, and sealing materials are extremely strict, and improving yield is the most important item in reducing manufacturing costs. An improvement in yield is desired.
【０００３】上述した厳しい条件下での高Ｎｉ合金熱間
圧延板の製造方法として、通常、鋳造された鋼塊をスラ
ブに鍛造し、その後に、目標の板に熱間圧延されるのが
一般的である。しかし、該鋼塊−鍛造工程では鍛造歩留
が悪く製造コストが高くなることが問題点であった。一
方、製品歩留向上と製造コスト低減のため、連続鋳造鋳
片の圧延法があるが、高Ｎｉ合金は熱間加工性が悪いた
め、連続鋳造鋳片の熱間圧延法では、鋳造組織の結晶粒
界への不純物が偏析しているため、熱間圧延時に粒界割
れを生じ、熱間圧延板に表面割れや板エッジの耳割れに
よる表面疵が多発しやすく、該表面疵の除去のため、熱
延コイルへのグラインダー手入れ負荷が大きくなること
や製品歩留が悪くなる問題があった。[0003] As a method for producing a high-Ni alloy hot-rolled sheet under the above-mentioned severe conditions, usually, a cast steel ingot is forged into a slab and then hot-rolled to a target sheet. It is a target. However, in the steel ingot-forging process, there is a problem that forging yield is low and manufacturing cost is increased. On the other hand, in order to improve product yield and reduce manufacturing costs, there is a method of rolling continuously cast slabs. However, since the hot workability of high Ni alloys is poor, the hot rolled method of continuous cast slabs requires a cast structure. Since impurities to the crystal grain boundaries are segregated, grain boundary cracks occur during hot rolling, and surface cracks due to surface cracks and edge cracks at the plate edge are likely to occur on the hot-rolled sheet, and removal of the surface scratches For this reason, there is a problem that a grinder care load on the hot-rolled coil is increased and a product yield is deteriorated.
【０００４】[0004]
【発明が解決しようとする課題】本発明は、上記のよう
な問題点を解決し、連続鋳造鋳片から表面疵がなく品質
の良好な高Ｎｉ合金熱延板を歩留良く製造することを目
的とするものである。SUMMARY OF THE INVENTION The present invention has been made to solve the above-mentioned problems and to produce a high-quality hot-rolled high-Ni-alloy sheet with good surface quality from a continuous cast slab with good yield. It is the purpose.
【０００５】[0005]
【課題を解決するための手段】本発明者らは、上記問題
を解決するために種々の製造実験を行い、検討を重ねた
結果、連続鋳造された鋳片を加熱し、圧延比（圧延スラ
ブ厚み／鋳片厚み）が３０〜６５％のブレークダウン圧
延を行い、連続鋳造鋳片（以下ＣＣ鋳片と記す）の鋳造
組織を破壊した後に、該ブレークダウンスラブを再加熱
し、再結晶による結晶の微細化と粒界偏析の拡散を行っ
た後に、仕上圧延を行うことによって、表面割れや耳割
れなどの表面欠陥のない高Ｎｉ合金の熱延板が安定して
歩留良く製造することができることを見い出した。ま
た、該ブレークダウン圧延時のＣＣ鋳片の加熱温度は１
１００〜１２５０℃の比較的低温で加熱し、鋳造結晶の
破壊のためのブレークダウンによる圧延効果を大きく
し、仕上圧延前の加熱は１１５０〜１３００℃で加熱
し、粒界偏析の拡散促進と熱延仕上がり温度を高くする
ことによって、より表面割れや耳割れなどの表面欠陥の
ない高Ｎｉ合金の熱延板を安定して歩留良く製造するこ
とができた。Means for Solving the Problems The present inventors have conducted various manufacturing experiments to solve the above-mentioned problems, and as a result of repeated studies, have heated continuously cast slabs to reduce the rolling ratio (rolled slab). Thickness / slab thickness) is subjected to breakdown rolling of 30 to 65% to break the cast structure of the continuous cast slab (hereinafter referred to as CC slab), and then the breakdown slab is reheated and recrystallized. By performing finish rolling after crystal refinement and diffusion of grain boundary segregation, hot rolled sheets of high Ni alloy without surface defects such as surface cracks and edge cracks can be manufactured stably with good yield. I found that I could do it. The heating temperature of the CC slab during the breakdown rolling is 1
Heating is performed at a relatively low temperature of 100 to 1250 ° C. to increase the rolling effect by breakdown for breaking the cast crystal. Heating before finish rolling is performed at 1150 to 1300 ° C. to promote diffusion of grain boundary segregation and heat. By increasing the finishing temperature, a hot rolled sheet of a high Ni alloy free from surface defects such as surface cracks and edge cracks could be manufactured stably with good yield.
【０００６】ＣＣ鋳片をブレークダウン圧延した時に、
鋳片の粒界割れなどによる表面疵が発生した場合は、再
加熱・仕上圧延する前に、該ブレークダウンスラブの表
面手入れによって除去することができる。また、ＣＣ鋳
片は、原則として、鋳片表面の微細結晶かつ成分偏析の
少ないチル晶を残したままの無手入れの状態でブレーク
ダウン圧延することによって、ブレークダウン圧延スラ
ブの表面疵低減と手入軽減または省略が可能となった。
さらに、ＣＣ鋳片やブレークダウンスラブの加熱は、Ｎ
2 またはＨ2 とＮ2 の混合ガスなどの無酸化雰囲気炉で
加熱することによって粒界酸化しやすい高Ｎｉ合金で
も、粒界酸化が防止され表面性状の非常に良好な熱延板
が歩留良く製造することが可能となった。また、ＣＣ鋳
片をブレークダウン圧延と仕上圧延を行う該２ヒート圧
延法は、ＣＣ鋳片から仕上圧延を行う１ヒート圧延法に
比べ、磁気特性などの材質特性も向上することがわかっ
た。When the CC slab is subjected to breakdown rolling,
When a surface flaw occurs due to grain boundary cracking of the slab, it can be removed by surface treatment of the breakdown slab before reheating and finish rolling. In addition, CC slabs are, as a rule, subjected to breakdown rolling in an unmaintained state while leaving fine crystals on the slab surface and chilled crystals with little component segregation, thereby reducing surface flaws of the breakdown rolling slab and reducing hand defects. Reduction or omission is possible.
Furthermore, the heating of CC slabs and breakdown slabs requires N
By heating in a non-oxidizing atmosphere furnace such as 2 or a mixed gas of H 2 and N 2 , even a high Ni alloy that is susceptible to grain boundary oxidation is prevented from grain boundary oxidation and a hot rolled sheet with very good surface properties is obtained. It became possible to manufacture well. Further, it has been found that the two-heat rolling method in which the CC slab is subjected to breakdown rolling and finish rolling has improved material properties such as magnetic properties as compared with the one-heat rolling method in which the CC slab is subjected to finish rolling.
【０００７】すなわち、本発明は、下記手段をとるもの
である。 （１） 重量％でＣ：０．０２％以下、Ｓｉ：０．０３
〜０．３％、Ｍｎ：０．３〜１％、Ｐ：０．０４％以
下、Ｃｒ：０．５％以下、Ｎｉ：３０〜８５％、Ｎ：
０．００５％以下、Ｓ：０．００５％以下、Ｏ：０．０
１５％以下、Ａｌ：０．０５０％以下を含有し、残部は
Ｆｅおよび不可避的不純物成分からなる合金を熱間圧延
板に製造するに際し、連続鋳造された１５０〜３００ｍ
ｍ厚みのＣＣ鋳片を加熱し、圧下比（圧延スラブ厚み／
鋳片厚み）が３０〜６５％のブレークダウン圧延を行っ
た後に、該ブレークダウンスラブを再加熱し、仕上圧延
する高Ｎｉ合金の熱間圧延板を製造する方法。That is, the present invention adopts the following means. (1) C: 0.02% or less by weight%, Si: 0.03
0.3%, Mn: 0.3-1%, P: 0.04% or less, Cr: 0.5% or less, Ni: 30-85%, N:
0.005% or less, S: 0.005% or less, O: 0.0
15% or less, Al: 0.050% or less, with the balance being 150-300 m continuously cast when producing an alloy consisting of Fe and unavoidable impurities into a hot-rolled sheet.
m thickness of CC slab is heated and the reduction ratio (rolled slab thickness /
A method of producing a high-Ni alloy hot-rolled plate to be reheated after performing breakdown rolling with a slab thickness of 30 to 65%, followed by finish rolling.
【０００８】（２） 重量％でＣ：０．０２％以下、Ｓ
ｉ：０．０３〜０．３％、Ｍｎ：０．３〜１％、Ｐ：
０．０４％以下、Ｎｉ：３０〜８５％、Ｎ：０．００５
％以下、Ｓ：０．００５％以下、Ｏ：０．０１５以下、
Ａｌ：０．０５％以下を含有し、さらに、Ｃｒ：３〜１
０％、Ｃｕ：６％以下、Ｍｏ：６％以下、Ｃａ：０．０
２％以下、Ｍｇ：０．０２％以下、Ｂ：０．００５％以
下の１種または２種以上を含有し、残部はＦｅ、および
不可避的不純物成分からなる合金を熱間圧延板に製造す
るに際し、連続鋳造された鋳片厚み１５０〜３００ｍｍ
の連続鋳造鋳片を加熱し、圧下比（圧延スラブ厚み／鋳
片厚み）が３０〜６５％のブレークダウン圧延を行った
後に、該ブレークダウン圧延スラブを再加熱し、仕上圧
延する高Ｎｉ合金の熱間圧延板を製造する方法。(2) C: 0.02% or less by weight%, S
i: 0.03 to 0.3%, Mn: 0.3 to 1%, P:
0.04% or less, Ni: 30 to 85%, N: 0.005
%, S: 0.005% or less, O: 0.015 or less,
Al: 0.05% or less, and Cr: 3-1
0%, Cu: 6% or less, Mo: 6% or less, Ca: 0.0
An alloy containing one or more of 2% or less, Mg: 0.02% or less, and B: 0.005% or less, and the balance being Fe and unavoidable impurity components, is manufactured into a hot-rolled sheet. On the occasion, slab thickness 150-300mm continuously cast
The continuous casting slab is subjected to breakdown rolling with a reduction ratio (rolled slab thickness / slab thickness) of 30 to 65%, and then the breakdown rolled slab is reheated to finish-roll a high Ni alloy. A method for producing a hot-rolled sheet.
【０００９】（３） 連続鋳造鋳片のブレークダウン圧
延の加熱温度が１１００〜１２５０℃で、仕上圧延の加
熱温度が１１５０〜１３００℃である（１）または
（２）記載の高Ｎｉ合金の熱間圧延板を製造する方法。 （４） ブレークダウン圧延後にスラブ表面を手入れす
る（１）ないし（３）のいずれかに記載の高Ｎｉ合金の
熱間圧延板を製造する方法。 （５） 熱間圧延における鋳片加熱およびブレークダウ
ンスラブの加熱は無酸化雰囲気炉で行う（１）ないし
（４）のいずれかに記載の高Ｎｉ合金の熱間圧延板を製
造する方法。 なお、本発明における無酸化雰囲気とはＮ2 、Ａｒ、Ｈ
2 の１種もしくは２種以上の混合気体から成る雰囲気を
いう。(3) The heat of the high Ni alloy according to (1) or (2), wherein the heating temperature for the breakdown rolling of the continuous cast slab is 1100 to 1250 ° C. and the heating temperature for the finish rolling is 1150 to 1300 ° C. A method for producing a cold rolled plate. (4) The method for producing a hot-rolled sheet of a high Ni alloy according to any one of (1) to (3), wherein the slab surface is maintained after the breakdown rolling. (5) The method for producing a hot-rolled sheet of a high Ni alloy according to any one of (1) to (4), wherein the slab heating and the breakdown slab heating in the hot rolling are performed in a non-oxidizing atmosphere furnace. The non-oxidizing atmosphere in the present invention is N 2 , Ar, H
2 refers to an atmosphere composed of one or a mixture of two or more gases.
【００１０】[0010]
【発明の実施の形態】以下、本発明を詳細に説明する。
まず、本発明が含有する合金元素の含有量を限定する理
由を以下に説明する。Ｃは不可避的に混入する不純物で
あり、少ないほど好ましいが、工業的および経済性の観
点から大幅な低減には限界がある。しかし、０．０２％
を超えると鉄炭化物が多量に生成し、エッチング穿孔性
やプレス成形性を低下させ、また、熱間加工性や磁気特
性を劣化させ好ましくないので０．０２％以下とする。
Ｓｉは高Ｎｉ合金の溶製時の脱酸のために添加するが、
０．０３％未満ではその効果がなくなるので、その下限
を０．０３％とする。また、０．３％を超えると、磁性
材料では透磁率が低下するため好ましくなく、またエッ
チング穿孔性を害するので、上限を０．３％とする。DESCRIPTION OF THE PREFERRED EMBODIMENTS The present invention will be described below in detail.
First, the reason why the content of the alloy element contained in the present invention is limited will be described below. C is an impurity that is unavoidably mixed, and the smaller the better, the better. However, there is a limit to a large reduction from the viewpoint of industrial and economic efficiency. However, 0.02%
If it exceeds, a large amount of iron carbide is generated, which deteriorates the etching piercing property and the press formability, and also deteriorates the hot workability and the magnetic properties.
Si is added for deoxidation during melting of a high Ni alloy,
If the content is less than 0.03%, the effect is lost, so the lower limit is made 0.03%. On the other hand, if the content exceeds 0.3%, the magnetic material is not preferable because the magnetic permeability is lowered, and the etching piercing property is impaired. Therefore, the upper limit is set to 0.3%.
【００１１】Ｍｎは脱酸に役立ち、また鋼中Ｓと結びつ
きＭｎＳとして熱間加工性を改善するが、１％を超える
と板の硬さや熱膨張への影響や飽和磁束密度および透磁
率など磁気特性が低下するので０．３〜１％とする。Ｐ
は熱間加工性の点では少ない方が良好で０．０４％以下
とする。Ｓは鋳片での粒界に偏析して熱間加工性、磁気
特性を劣化させ好ましくなく、低い方が良いため０．０
０５％以下とする。Mn is useful for deoxidation and binds with S in steel to improve hot workability as MnS. However, if it exceeds 1%, the effect on the hardness and thermal expansion of the sheet, the saturation magnetic flux density and the magnetic permeability such as the magnetic permeability are increased. Since the characteristics deteriorate, the content is set to 0.3 to 1%. P
The smaller the better, the better in terms of hot workability, and 0.04% or less. S undesirably segregates at the grain boundaries in the slab and degrades hot workability and magnetic properties.
It shall be not more than 05%.
【００１２】Ｃｒはエッチング穿孔性を阻害し、また、
熱膨張率を上げるので、０．５％以下とする。ただし、
磁気特性を向上させるために、磁性材料には必要に応じ
て３〜１０％添加することができる。Ｎｉは熱膨張率、
磁気特性に大きな影響をおよぼす元素である。３０％未
満では熱膨張率が高く、かつ磁気特性も悪く、また８５
％を超えると磁気特性は飽和しコスト的に高価となるた
め、３０〜８５％とする。Ｃｕは透磁率など磁気特性を
改善する作用があり、磁性材料は必要に応じて添加する
が、６％を超えると熱間加工性が低下するとともに磁気
特性が低下するので６％以下とする。ＭｏはＮｉの共存
のもとで透磁率など磁気特性を高める作用があり、磁性
材料は必要に応じて添加するが、６％を超えると磁気特
性が低下するので６％以下とする。[0012] Cr inhibits the etching piercing property,
To increase the coefficient of thermal expansion, the content is set to 0.5% or less. However,
In order to improve the magnetic properties, 3 to 10% can be added to the magnetic material as needed. Ni is the coefficient of thermal expansion,
It is an element that has a significant effect on magnetic properties. If it is less than 30%, the coefficient of thermal expansion is high and the magnetic properties are poor.
%, The magnetic properties are saturated and the cost is high. Cu has an effect of improving magnetic properties such as magnetic permeability, and a magnetic material is added as necessary. However, if it exceeds 6%, hot workability is lowered and magnetic properties are lowered, so Cu is set to 6% or less. Mo has an effect of improving magnetic properties such as magnetic permeability in the coexistence of Ni, and a magnetic material is added as needed. However, if it exceeds 6%, the magnetic properties deteriorate, so the content is set to 6% or less.
【００１３】Ｎは０．００５％を超えると、窒化物が多
量に生成して、板のエッチング穿孔性を阻害し穿孔欠陥
の原因となり、また磁気特性を劣化させるので、０．０
０５％以下とする。Ｏは熱間加工性および介在物性欠陥
防止に対し低い方が良好であり０．０１５％以下とす
る。Ａｌは強力な脱酸元素であるが、冷間圧延製品の表
面疵など介在物性欠陥となる有害なＡｌ2 Ｏ3 やＡｌ2
Ｏ3 ・ＭｇＯスピネル系の介在物生成原因となるため、
０．０５％以下とする。If N exceeds 0.005%, a large amount of nitride is generated, which impairs the etching piercing property of the plate and causes puncturing defects, and also degrades the magnetic properties.
It shall be not more than 05%. The lower the O content, the better the hot workability and the prevention of inclusion defects. Al is a powerful deoxidizing element, but harmful Al 2 O 3 and Al 2 which become inclusion defects such as surface defects of cold rolled products
O 3 · MgO spinel-based inclusions
0.05% or less.
【００１４】Ｃａは熱間加工性改善と連続鋳造のノズル
閉塞防止や介在物欠陥として有害なＡｌ2 Ｏ3 介在物生
成防止のために添加することができるが、０．０２％以
下とした理由は、０．０２％を超えると酸化が激しくＣ
ａＯ系介在物が多く生成され地疵などの介在物性欠陥を
多く発生させるほか、清浄度を悪化させ耐食性も悪く有
害となるためである。Ｍｇは熱間加工性改善のために添
加することができるが、０．０２％を超えるとＭｇＯ系
やＡｌ2 Ｏ3 ・ＭｇＯスピネル系介在物の生成による介
在物原因の表面疵や地疵などの内部欠陥が多発し、製品
歩留低下および品質低下の原因となるので０．０２％以
下とする。Ｂはその適量添加によって熱間加工性の改善
効果があるが、０．００５％を超えるとＢの金属間化合
物が形成され磁気特性を劣化させるため０．００５％を
上限とする。Ca can be added to improve hot workability, prevent nozzle clogging in continuous casting, and prevent Al 2 O 3 inclusions that are harmful as inclusion defects. Exceeds 0.02%, the oxidation is severe and C
This is because many aO-based inclusions are generated and many inclusion defects such as ground flaws are generated, as well as the cleanliness is deteriorated and the corrosion resistance is poor and harmful. Mg can be added to improve hot workability, but if it exceeds 0.02%, surface flaws and ground flaws caused by inclusions due to the formation of MgO-based or Al 2 O 3 .MgO spinel-based inclusions Internal defects frequently occur and cause a reduction in product yield and quality, so the content is set to 0.02% or less. B has an effect of improving hot workability by adding an appropriate amount thereof, but if it exceeds 0.005%, an intermetallic compound of B is formed to deteriorate magnetic properties, so the upper limit is 0.005%.
【００１５】また、ＣＣ鋳片厚みは、１５０ｍｍ未満で
はブレークダウン圧延後に仕上圧延を行う２回加熱圧延
法のため、ブレークダウン後のスラブ厚みが薄くなり、
スラブ加熱炉の長さ制約から仕上圧延製品のコイル単重
（単位幅当たりの熱延コイル重量）が小さくなること
と、ブレークダウンスラブの表面手入保留が悪くなる問
題があり、ＣＣ鋳片厚みが３００ｍｍを超えると連続鋳
造能率および圧延能率が悪くなるため、１５０〜３００
ｍｍとする。When the thickness of the CC slab is less than 150 mm, the slab thickness after the breakdown becomes thin because of the twice heating rolling method in which the finish rolling is performed after the breakdown rolling.
Due to the length limitation of the slab heating furnace, the coil unit weight of the finished rolled product (the weight of the hot-rolled coil per unit width) is reduced, and the maintenance of the surface of the breakdown slab is deteriorated. Exceeds 300 mm, the continuous casting efficiency and the rolling efficiency deteriorate.
mm.
【００１６】ブレークダウン圧延疵（圧延スラブ厚み／
鋳片厚み）は、鋳造組織を壊し粒界偏析の拡散を促進す
るため大きい方が良いが、３０％未満ではその効果はな
く、６５％を超えると仕上圧延前のスラブ厚みが薄くな
りすぎ、仕上圧延製品のコイル単重が小さくなるととも
に、歩留が悪くなるため３０〜６５％とする。ＣＣ鋳片
のブレークダウン圧延前の加熱温度は低い方が鋳造組織
の破壊に対し良好であるが、１１００℃未満では熱間変
形抵抗が高くなるとともに、熱間延性が悪くなるので１
１００〜１２５０℃とする。一方、仕上熱延時のブレー
クダウンスラブの加熱温度は熱間加工性の点から高い方
がよいが、過熱によるバーニング割れ防止と加熱費低減
のため１１５０〜１３００℃とする。上記手段を採るこ
とにより、従来の問題点が解決され、表面品質、内部品
質、材質特性ともに良好な高Ｎｉ合金を安定して歩留良
く製造することが可能となる。Breakdown rolling flaw (rolling slab thickness /
The slab thickness) is preferably large in order to break the casting structure and promote the diffusion of grain boundary segregation, but if it is less than 30%, there is no effect, and if it exceeds 65%, the slab thickness before finish rolling becomes too thin, Since the unit weight of the coil of the finished rolled product is reduced and the yield is deteriorated, the content is set to 30 to 65%. The lower the heating temperature of the CC slab before breakdown rolling is, the better the fracture of the cast structure is. However, if the temperature is lower than 1100 ° C., the hot deformation resistance increases and the hot ductility deteriorates.
100 to 1250 ° C. On the other hand, the heating temperature of the breakdown slab during finishing hot rolling is preferably higher from the viewpoint of hot workability, but is set to 1150 to 1300 ° C. in order to prevent burning cracks due to overheating and reduce heating costs. By adopting the above means, the conventional problems can be solved, and a high Ni alloy having good surface quality, internal quality and material properties can be stably manufactured with a high yield.
【００１７】[0017]
【実施例】次に、本発明の実施例について説明する。表
１は本発明鋼と比較鋼の取鍋下化学成分組成を示すが、
転炉で溶製した後、ＣＣ鋳片（スラブ）に鋳造した。該
スラブは、表２に示した条件でブレークダウン圧延と、
該ブレークダウンスラブの表面をグラインダー手入れ後
に仕上圧延を行い、ホットストリップコイルにした後、
通常通りの酸洗、コイルグラインダーによって熱延コイ
ルの表面手入れと一部の材料はエッジトリミングを行っ
た。その後、通常の冷間圧延によって冷延板とした。Next, an embodiment of the present invention will be described. Table 1 shows the chemical composition under the ladle of the steel of the present invention and the comparative steel.
After being melted in a converter, it was cast into a CC slab (slab). The slab was subjected to breakdown rolling under the conditions shown in Table 2,
After finishing the rolling of the surface of the breakdown slab after grinding with a grinder, to make a hot strip coil,
As usual, the surface of the hot-rolled coil was cleaned with an acid pickling and coil grinder, and some materials were subjected to edge trimming. Thereafter, a cold-rolled sheet was formed by ordinary cold rolling.
【００１８】[0018]
【表１】 [Table 1]
【００１９】[0019]
【表２】 [Table 2]
【００２０】比較例１、２はＣＣ鋳片を手入れした後に
ブレークダウン圧延なしで、熱延コイルに製造したもの
であり、比較例３、４はブレークダウン条件が本発明範
囲外で製造されたものである。実施例は比較例に比べい
ずれも表面疵が少なく、熱延コイルの手入負荷は大幅に
軽減され、手入歩留とコイルエッジのトリミング歩留お
よび製品歩留は良く、品質の良好な熱延コイル製品が製
造できた。Comparative Examples 1 and 2 were made into hot rolled coils without breaking rolling after caring for CC slabs, and Comparative Examples 3 and 4 were made under conditions where the breakdown conditions were outside the scope of the present invention. Things. In each of the examples, the surface flaws were smaller than those of the comparative examples, the maintenance load of the hot-rolled coil was significantly reduced, the maintenance yield, the trimming yield of the coil edge and the product yield were good, and the heat quality was good. Rolled coil products could be manufactured.
【００２１】[0021]
【表３】 [Table 3]
【００２２】表３は該熱延コイルの実施例と比較例につ
いて、板厚と表面疵発生状況、熱延コイル手入歩留およ
び対ＣＣ鋳片の製品歩留を示した。表３から明らかなよ
うに実施例では、従来材の方法で製造された製品と避色
のない良好な材質特性が得られている。Table 3 shows the sheet thickness, the occurrence of surface flaws, the hot rolled coil manual yield, and the product yield of CC slabs for the examples and comparative examples of the hot rolled coil. As is evident from Table 3, in the examples, good material characteristics without color bleeding were obtained with products manufactured by the method of the conventional material.
【００２３】[0023]
【発明の効果】本発明に従って製造された高Ｎｉ合金の
熱間熱燗板は、経済的に表面品質および内部品質ともに
良好な製品が安定して得られるので、産業上に及ぼす効
果は極めて大きい。The hot-plated hot-rolled plate of high Ni alloy produced according to the present invention is economically advantageous in that both the surface quality and the internal quality of the product can be stably obtained.
フロントページの続き (51)Int.Cl.6 識別記号 ＦＩ Ｃ２１Ｄ 9/00 １０１ Ｃ２１Ｄ 9/00 １０１Ａ Ｃ２２Ｃ 19/00 Ｃ２２Ｃ 19/00 Ｑ 38/00 ３０２ 38/00 ３０２Ｚ 38/40 38/40 38/54 38/54 Ｃ２２Ｆ 1/00 ６６１ Ｃ２２Ｆ 1/00 ６６１Ａ ６８４ ６８４Ｃ ６９１ ６９１Ｂ ６９４ ６９４Ａ 1/10 1/10 Ｈ Continued on the front page (51) Int.Cl. 6 Identification code FI C21D 9/00 101 C21D 9/00 101A C22C 19/00 C22C 19/00 Q 38/00 302 38/00 302Z 38/40 38/40 38 / 54 38/54 C22F 1/00 661 C22F 1/00 661A 684 684C 691 691B 694 694A 1/10 1/10 H
Claims (5)
０．０３〜０．３％、Ｍｎ：０．３〜１％、Ｐ：０．０
４％以下、Ｃｒ：０．５％以下、Ｎｉ：３０〜８５％、
Ｎ：０．００５％以下、Ｓ：０．００５％以下、Ｏ：
０．０１５以下、Ａｌ：０．０５％以下を含有し、残部
はＦｅ、および不可避的不純物成分からなる合金を熱間
圧延板に製造するに際し、連続鋳造された鋳片厚み１５
０〜３００ｍｍの連続鋳造鋳片を加熱し、圧下比（圧延
スラブ厚み／鋳片厚み）が３０〜６５％のブレークダウ
ン圧延を行った後に、該ブレークダウン圧延スラブを再
加熱し仕上圧延することを特徴とする高Ｎｉ合金の熱間
圧延板を製造する方法。1. C: 0.02% or less by weight, Si:
0.03 to 0.3%, Mn: 0.3 to 1%, P: 0.0
4% or less, Cr: 0.5% or less, Ni: 30 to 85%,
N: 0.005% or less, S: 0.005% or less, O:
0.015 or less, Al: 0.05% or less, the balance being Fe, and the slab thickness of the continuously cast slab 15 when producing an alloy comprising unavoidable impurity components into a hot-rolled plate.
Heating a continuous cast slab of 0 to 300 mm and performing a breakdown rolling with a reduction ratio (rolled slab thickness / slab thickness) of 30 to 65%, and then reheating the finish-rolled slab and finish rolling. A method for producing a hot-rolled sheet of a high Ni alloy, characterized by the following.
０．０３〜０．３％、Ｍｎ：０．３〜１％、Ｐ：０．０
４％以下、Ｎｉ：３０〜８５％、Ｎ：０．００５％以
下、Ｓ：０．００５％以下、Ｏ：０．０１５以下、Ａ
ｌ：０．０５％以下を含有し、さらに、Ｃｒ：３〜１０
％、Ｃｕ：６％以下、Ｍｏ：６％以下、Ｃａ：０．０２
％以下、Ｍｇ：０．０２％以下、Ｂ：０．００５％以下
の１種または２種以上を含有し、残部はＦｅ、および不
可避的不純物成分からなる合金を熱間圧延板に製造する
に際し、連続鋳造された鋳片厚み１５０〜３００ｍｍの
連続鋳造鋳片を加熱し、圧下比（圧延スラブ厚み／鋳片
厚み）が３０〜６５％のブレークダウン圧延を行った後
に、該ブレークダウン圧延スラブを再加熱し仕上圧延す
ることを特徴とする高Ｎｉ合金の熱間圧延板を製造する
方法。2. C: 0.02% or less by weight%, Si:
0.03 to 0.3%, Mn: 0.3 to 1%, P: 0.0
4% or less, Ni: 30 to 85%, N: 0.005% or less, S: 0.005% or less, O: 0.015 or less, A
l: 0.05% or less, and Cr: 3 to 10
%, Cu: 6% or less, Mo: 6% or less, Ca: 0.02%
% Or less, Mg: 0.02% or less, B: 0.005% or less, when the alloy containing Fe and inevitable impurity components is manufactured into a hot-rolled sheet. A continuously cast slab having a slab thickness of 150 to 300 mm is heated and subjected to breakdown rolling at a reduction ratio (rolled slab thickness / slab slab thickness) of 30 to 65%. A hot rolled sheet of a high Ni alloy characterized by reheating and finish rolling.
熱温度が１１００〜１２５０℃で、仕上圧延の加熱温度
が１１５０〜１３００℃であることを特徴とする請求項
１または請求項２記載の高Ｎｉ合金の熱間圧延板を製造
する方法。3. The method according to claim 1, wherein the heating temperature for the breakdown rolling of the continuous cast slab is 1100 to 1250 ° C., and the heating temperature for the finish rolling is 1150 to 1300 ° C. A method for producing a hot-rolled sheet of a Ni alloy.
入れすることを特徴とする請求項１ないし請求項３のい
ずれかに記載の高Ｎｉ合金の熱間圧延板を製造する方
法。4. The method for producing a hot-rolled high Ni alloy sheet according to claim 1, wherein the surface of the slab is maintained after the breakdown rolling.
クダウンスラブの加熱は無酸化雰囲気炉で行うことを特
徴とする請求項１ないし請求項４のいずれかに記載の高
Ｎｉ合金の熱間圧延板を製造する方法。5. The hot rolling of a high Ni alloy according to claim 1, wherein the heating of the slab and the heating of the breakdown slab in the hot rolling are performed in a non-oxidizing atmosphere furnace. A method of manufacturing boards.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16155198A JP3398050B2 (en) | 1998-05-27 | 1998-05-27 | Method for producing hot rolled sheet of high Ni alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16155198A JP3398050B2 (en) | 1998-05-27 | 1998-05-27 | Method for producing hot rolled sheet of high Ni alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH11342403A true JPH11342403A (en) | 1999-12-14 |
| JP3398050B2 JP3398050B2 (en) | 2003-04-21 |
Family
ID=15737271
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP16155198A Expired - Fee Related JP3398050B2 (en) | 1998-05-27 | 1998-05-27 | Method for producing hot rolled sheet of high Ni alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3398050B2 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2800753A1 (en) * | 1999-11-09 | 2001-05-11 | Nippon Mining Co | LOW THERMAL EXPANSION FE-NI ALLOY FOR SEMI-TENSION MASK, SEMI-TENSION MASK IN THIS ALLOY AND COLOR IMAGE TUBE USING THE MASK |
| FR2849061A1 (en) * | 2002-12-20 | 2004-06-25 | Imphy Ugine Precision | Iron-nickel alloy, used for shadow mask, cryogenic storage and electron canon applications, has low cobalt content and very low coefficient of thermal dilation |
| KR100582802B1 (en) * | 2001-10-19 | 2006-05-23 | 닛폰 긴조쿠 가부시키가이샤 | Method of preparing a magnesium alloy slab for hot-rolling and method of hot-rolling magnesium alloy |
| KR100671196B1 (en) | 2005-04-02 | 2007-01-25 | 주식회사 지알로이테크놀로지 | Manufacturing method of particle-distributed wrought magnesium alloys and wrought magnesium alloys thereby |
| JP2012102375A (en) * | 2010-11-11 | 2012-05-31 | Sumitomo Metal Ind Ltd | Method for producing austenitic alloy large-diameter pipe |
| CN112496037A (en) * | 2020-11-16 | 2021-03-16 | 太原钢铁(集团)有限公司 | Nickel-based alloy plate rolling method |
-
1998
- 1998-05-27 JP JP16155198A patent/JP3398050B2/en not_active Expired - Fee Related
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2800753A1 (en) * | 1999-11-09 | 2001-05-11 | Nippon Mining Co | LOW THERMAL EXPANSION FE-NI ALLOY FOR SEMI-TENSION MASK, SEMI-TENSION MASK IN THIS ALLOY AND COLOR IMAGE TUBE USING THE MASK |
| KR100582802B1 (en) * | 2001-10-19 | 2006-05-23 | 닛폰 긴조쿠 가부시키가이샤 | Method of preparing a magnesium alloy slab for hot-rolling and method of hot-rolling magnesium alloy |
| FR2849061A1 (en) * | 2002-12-20 | 2004-06-25 | Imphy Ugine Precision | Iron-nickel alloy, used for shadow mask, cryogenic storage and electron canon applications, has low cobalt content and very low coefficient of thermal dilation |
| WO2004063411A1 (en) * | 2002-12-20 | 2004-07-29 | Imphy Alloys | Iron-nickel alloy with low coefficient of thermal expansion for making shade masks |
| KR100671196B1 (en) | 2005-04-02 | 2007-01-25 | 주식회사 지알로이테크놀로지 | Manufacturing method of particle-distributed wrought magnesium alloys and wrought magnesium alloys thereby |
| JP2012102375A (en) * | 2010-11-11 | 2012-05-31 | Sumitomo Metal Ind Ltd | Method for producing austenitic alloy large-diameter pipe |
| CN112496037A (en) * | 2020-11-16 | 2021-03-16 | 太原钢铁(集团)有限公司 | Nickel-based alloy plate rolling method |
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| Publication number | Publication date |
|---|---|
| JP3398050B2 (en) | 2003-04-21 |
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