JPH0460741B2 - - Google Patents
Info
- Publication number
- JPH0460741B2 JPH0460741B2 JP3054585A JP3054585A JPH0460741B2 JP H0460741 B2 JPH0460741 B2 JP H0460741B2 JP 3054585 A JP3054585 A JP 3054585A JP 3054585 A JP3054585 A JP 3054585A JP H0460741 B2 JPH0460741 B2 JP H0460741B2
- Authority
- JP
- Japan
- Prior art keywords
- temperature
- water
- slab
- cooled
- cold rolling
- 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.)
- Expired
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- 239000002184 metal Substances 0.000 claims description 23
- 229910052751 metal Inorganic materials 0.000 claims description 23
- 230000009466 transformation Effects 0.000 claims description 15
- 238000010438 heat treatment Methods 0.000 claims description 12
- 238000001816 cooling Methods 0.000 claims description 11
- 238000004519 manufacturing process Methods 0.000 claims description 6
- 238000009749 continuous casting Methods 0.000 claims description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 2
- 238000000034 method Methods 0.000 description 17
- 238000005097 cold rolling Methods 0.000 description 16
- 238000005266 casting Methods 0.000 description 14
- 238000000137 annealing Methods 0.000 description 13
- 229910000831 Steel Inorganic materials 0.000 description 8
- 239000010959 steel Substances 0.000 description 8
- 239000010960 cold rolled steel Substances 0.000 description 5
- 229910001111 Fine metal Inorganic materials 0.000 description 4
- 239000013078 crystal Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 239000011819 refractory material Substances 0.000 description 2
- JZUFKLXOESDKRF-UHFFFAOYSA-N Chlorothiazide Chemical compound C1=C(Cl)C(S(=O)(=O)N)=CC2=C1NCNS2(=O)=O JZUFKLXOESDKRF-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000000498 cooling water Substances 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 238000002347 injection Methods 0.000 description 1
- 239000007924 injection Substances 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、ツインドラム方式による連続鋳造装
置を使用して、金属組織が微細化した金属薄板を
製造する方法に関する。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention relates to a method for producing a thin metal plate with a fine metal structure using a twin-drum continuous casting apparatus.
冷延鋼板を製造する方法として、ツインドラム
方式の連続鋳造機にて薄板鋳片（板厚２mm〜10
mm）を得、その後、鋳片を酸洗（スケールを除去
するため）し、冷間圧延により所定の製品板厚と
し、さらに焼鈍して製品とする方法がある。
As a method of manufacturing cold-rolled steel sheets, a twin-drum continuous casting machine is used to produce thin plate slabs (plate thickness 2 mm to 10 mm).
mm), then pickling the slab (to remove scale), cold rolling it to a predetermined product thickness, and then annealing it to make it into a product.
上記技術の場合最も重要な点は、ドラム方式連
鋳機で得られた薄板鋳片の性状であるが、上記従
来の製造プロセスでは、冷間圧延前（as Cast）
の金属組織が粗く、良質の製品とするためには冷
間圧延率及び焼鈍温度を高くする必要があるとい
つた問題点がある。
In the case of the above technology, the most important point is the properties of the thin plate slab obtained by the drum type continuous caster, but in the above conventional manufacturing process,
The problem is that the metallographic structure of the steel is coarse, and that it is necessary to increase the cold rolling rate and annealing temperature in order to obtain a high-quality product.
本発明は、前記従来のドラム方式連続鋳造機に
よる薄板鋳片の鋳造工程、酸洗工程、冷間圧延工
程及び焼鈍工程よりなるプロセスにおいて、供給
する薄板鋳片の金属組織を微細化することによつ
て、前記問題点を解消する金属薄板の製造方法を
提供するものである。
The present invention aims at refining the metal structure of supplied thin plate slabs in a process consisting of a casting process of thin plate slabs using the conventional drum-type continuous casting machine, a pickling process, a cold rolling process, and an annealing process. Therefore, it is an object of the present invention to provide a method for manufacturing a thin metal plate that solves the above-mentioned problems.
すなわち、本発明は、ドラム方式薄板連続鋳造
装置により得られた薄板鋳片（板厚２〜10mm）を
インラインにて熱処理を施し、金属組織の微細化
を図る方法であつて、この場合の熱処理手段とし
て、次の(1)及び(2)を特徴とするものである。 That is, the present invention is a method of heat-treating a thin plate slab (2 to 10 mm in thickness) obtained by a drum-type continuous thin plate casting apparatus in-line to refine the metal structure, and the heat treatment in this case As a means, it is characterized by the following (1) and (2).
(1) ドラム方式薄板連続鋳造装置により得られた
鋳片をA1変態点以下の温度まで冷却し、再び
インラインにてA3変態点以上の温度に加熱す
る。(1) A slab obtained by a drum-type thin plate continuous casting machine is cooled to a temperature below the A1 transformation point, and then heated in-line again to a temperature above the A3 transformation point.
(2) その後、ガス冷却により所定の温度まで冷却
し、次工程へ送る。(2) After that, it is cooled to a predetermined temperature by gas cooling and sent to the next process.
本発明では、金属組織の微細化を図るものであ
るが、この金属（普通鋼）組織の微細化は、α
（フエライト組織）←→γ（オーステナイト組織）
変態を利用して行なわれる。 The present invention aims to refine the metal structure, but the refinement of the metal (ordinary steel) structure is limited to α
(Ferrite structure) ←→γ (Austenite structure)
It is done using perversion.
普通鋼を常温から徐々に加熱すると、A1点
（723℃）でα←→γ変態を開始し、A3点で全てγ
となる。γの粒径は温度と時間に依存し、温度が
高い程、又時間が長い程大きくなる。ここでは加
熱温度がA3点よりわずかに高いだけであるため、
溶湯から鋳造された状態（as Cast）の鋳片のγ
粒径より小さくなる。 When ordinary steel is gradually heated from room temperature, α←→γ transformation starts at one point A (723℃), and all γ transformation occurs at three points A.
becomes. The particle size of γ depends on temperature and time, and increases as the temperature increases and the time increases. Here the heating temperature is only slightly higher than point A3 , so
γ of slab as cast from molten metal
smaller than the particle size.
次に、これを冷却しA3点以下になると、γの
粒界からαの核が発生して変態が起り、A1点で
終了し、全てαとなる。 Next, when this is cooled down to below A 3 points, α nuclei are generated from the γ grain boundaries and transformation occurs, ending at A 1 point and all becoming α.
したがつて、上記熱処理により鋳片の結晶αは
微細化する（γの粒径が小さい程、粒界が多く、
α核の発生が多い）。 Therefore, the above heat treatment makes the crystal α of the slab finer (the smaller the grain size of γ, the more grain boundaries there are,
α-nuclei are often present).
本発明は、上記手段で金属組織を微細化し、こ
れによつて冷間圧延率の低減化及び焼鈍温度の低
温化を図るものであるが、この理由は、次のとお
りである。すなわち、鋳片は冷間圧延によつてα
は伸長され、かつ、一つの結晶粒内に、別の亜結
晶粒界が生成される。そしてこの冷間圧延材を焼
鈍すると、結晶粒界及び亜結晶粒界にαの核が発
生し、αは再結晶する。αの再結晶温度は、αに
蓄積された歪エネルギーが大きい程（圧延率が高
い程、結晶粒が小さい程）低下する。従つて、あ
らかじめ、熱処理によつて鋳片の組織（α組織）
を微細化することによつて、結晶粒界、亜結晶粒
界を多くし、又冷間圧延時の歪エネルギーを大き
くするため、冷間圧延率を低減させ、又、焼鈍温
度を低くすることができる。 The present invention aims to refine the metal structure by the above-mentioned means and thereby reduce the cold rolling reduction and the annealing temperature, and the reason for this is as follows. In other words, the slab is cold rolled to α
is elongated, and another subgrain boundary is generated within one grain. When this cold-rolled material is annealed, α nuclei are generated at grain boundaries and subgrain boundaries, and α is recrystallized. The recrystallization temperature of α decreases as the strain energy accumulated in α increases (the higher the rolling ratio, the smaller the crystal grains). Therefore, the structure of the slab (α structure) is changed by heat treatment in advance.
By making the steel grain finer, the number of grain boundaries and subgrain boundaries is increased, and in order to increase the strain energy during cold rolling, the cold rolling rate is reduced and the annealing temperature is lowered. I can do it.
以下、第１図に基づいて本発明を詳細に説明す
る。第１図は本発明を実施するためのツインドラ
ム方式金属薄板連続鋳造装置の縦断面図である。
第１図に示す装置は、薄板鋳片３を鋳造する水冷
鋳造ロール１，１′、水冷鋳造ロール１，１′間の
溶湯４の洩れを防止するザイド固定せき２，２′、
溶鋼等の溶湯４を溜めるタンデイツシユ５、鋳片
３を加熱する加熱炉７、冷却装置８などを主要構
成部材としている。本装置を詳細に説明すると、
水冷鋳造ロール１，１′は水平に設置されており、
図示しない駆動装置により回転（矢印方向）駆動
される。この水冷鋳造ロール１，１′は例えば銅
または銅合金あるいは鋼材により形成され、内部
に水冷機構を内蔵するものであり、溶湯４との接
触面積を大きく得るため相当大径のロールとなつ
ている。また、水冷鋳造ロール１，１′の両端部
にはサイドをシールするための耐火材からなる固
定せき２，２′が押し当てられており、２本の鋳
造ロール１，１′と２個の固定せき２，２′で形成
される空間に溶湯４が注湯される。溶湯が鋳造ロ
ール１，１′の表面に接触して冷却され、できた
凝固殻は一体化され、鋳片３となる。 Hereinafter, the present invention will be explained in detail based on FIG. FIG. 1 is a longitudinal cross-sectional view of a twin-drum continuous thin metal plate casting apparatus for carrying out the present invention.
The apparatus shown in FIG. 1 includes water-cooled casting rolls 1, 1' for casting a thin plate slab 3, Zide fixed weirs 2, 2' for preventing leakage of molten metal 4 between the water-cooled casting rolls 1, 1',
The main components include a tundish 5 for storing molten metal 4 such as molten steel, a heating furnace 7 for heating slabs 3, and a cooling device 8. To explain this device in detail:
The water-cooled casting rolls 1, 1' are installed horizontally,
It is rotated (in the direction of the arrow) by a drive device (not shown). The water-cooled casting rolls 1 and 1' are made of copper, copper alloy, or steel, for example, and have a built-in water-cooling mechanism, and have a considerably large diameter in order to have a large contact area with the molten metal 4. . Furthermore, fixed weirs 2, 2' made of refractory material are pressed against both ends of the water-cooled casting rolls 1, 1' to seal the sides, and the two casting rolls 1, 1' and the two Molten metal 4 is poured into the space formed by the fixed weirs 2 and 2'. The molten metal contacts the surfaces of the casting rolls 1, 1' and is cooled, and the solidified shells formed are integrated to form the slab 3.
この鋳片３は、ピンチロール６で引抜かれ、ガ
イドロール９で搬送中にA1変態点以下まで冷却
された後、加熱炉７へ搬送され、A3変態点以上
の温度に加熱される。次いで鋳片３は冷却装置８
（ガス冷却機構を有するもの）により冷却される。 This slab 3 is pulled out by pinch rolls 6, cooled down to below the A1 transformation point while being conveyed by guide rolls 9, and then conveyed to the heating furnace 7 where it is heated to a temperature above the A3 transformation point. Next, the slab 3 is passed through a cooling device 8
(having a gas cooling mechanism).
本発明は、以上詳記したように、鋳造ロール
１，１′により形成された鋳片３を一度A1変態点
以下の温度まで空冷し、次いて加熱炉７により再
度A3変態点以上の温度、好ましくはA3点より20
〜30℃以上の温度に加熱する。その後冷却装置８
により冷却し、次工程に搬送する。この工程によ
り得られた鋳片３は金属組織が非常に微細化され
ており、次工程の冷間圧延を施こすと、この冷間
圧延率の低減化及び焼鈍温度の低温化が図れ、省
エネルギ化につながる。 As described in detail above, in the present invention, the slab 3 formed by the casting rolls 1 and 1' is once air-cooled to a temperature below the A1 transformation point, and then heated again to a temperature above the A3 transformation point in the heating furnace 7. Temperature, preferably 20 from A 3 points
Heat to a temperature of ~30°C or higher. Then the cooling device 8
It is cooled down and transported to the next process. The slab 3 obtained through this process has a very fine metal structure, and when cold rolling is performed in the next process, the cold rolling rate and annealing temperature can be lowered, resulting in savings. Leads to energy generation.
以上本発明を詳細に説明したが、さらに本発明
の具体例をあげて本発明をより詳細に説明する。 Although the present invention has been described in detail above, the present invention will be further explained in more detail by giving specific examples of the present invention.
鋼を鋳造いした場合の構成部材の寸法ならびに
諸条件は以下のとおりである。
The dimensions and various conditions of the structural members when steel is cast are as follows.
(1) 水冷鋳造ロール
鋼製で内部水冷方式のものであり、ロール直
径2000mmφ、ロール幅1200mmのものである。鋳
片寸法は３mmｔ×1200mm幅であり、このときの
ロール回転速度（鋳造速度）は約28ｍ／minで
ある。(1) Water-cooled casting roll The roll is made of steel and has an internal water-cooling system, with a roll diameter of 2000mmφ and a roll width of 1200mm. The dimensions of the slab are 3 mm thick x 1200 mm wide, and the roll rotation speed (casting speed) at this time is about 28 m/min.
(2) 加熱炉
耐火材と電気ヒーターあるいはガスヒーター
等より構成されており、加熱温度は900〜950℃
である。また、設定位置は鋳片が空冷され、
650〜700℃（A1変態点以下）になるところで
あり、加熱時間は１〜２分間である。(2) Heating furnace Consists of refractory material and electric heater or gas heater, etc., heating temperature is 900-950℃
It is. In addition, at the setting position, the slab is air-cooled,
The temperature is 650 to 700°C (below the A1 transformation point), and the heating time is 1 to 2 minutes.
(3) 冷却装置
ガス又は冷却水噴射ノズル（気水混合による
冷却手段でもよい。）複数からなるものである。
配置は上下方向２ケ所であり、鋳片を上下方向
より冷却速度約５℃／秒で冷却する。(3) Cooling device Consists of a plurality of gas or cooling water injection nozzles (cooling means using a mixture of air and water may also be used).
There are two locations in the upper and lower directions, and the slab is cooled from the top and bottom at a cooling rate of about 5°C/sec.
(4) 溶湯
溶湯の成分はＣ：0.03％、Si：0.05％、
Mn：0.22％、残部は不純物およびFeからなり、
タンデイツシユ内溶湯温度は1560℃〜1570℃で
ある。(4) Molten metal The components of the molten metal are C: 0.03%, Si: 0.05%,
Mn: 0.22%, the remainder consists of impurities and Fe,
The temperature of the molten metal in the tundish is 1560°C to 1570°C.
(5) 冷間圧延率 冷間圧延率は、30〜85％である。(5) Cold rolling rate The cold rolling rate is 30-85%.
(6) 焼鈍温度 焼鈍温度は、700℃〜900℃である。(6) Annealing temperature The annealing temperature is 700°C to 900°C.
以上の条件で製造した冷延鋼板と従来プロセス
による冷延鋼板の値（深しぼり性を表わす指数
であり、高い方が深しぼり性が良好である。）と
冷間圧延率の関係を第２図に、また値と焼鈍温
度の関係を第３図に示す。この結果より、本発明
プロセス製造した冷延鋼板は、冷間圧延前の金属
組織が微細であることにより、従来プロセスに比
べ冷間圧延率及び焼鈍温度の低下を図ることがで
きた。 The relationship between the cold-rolled steel sheet manufactured under the above conditions and the cold-rolled steel sheet manufactured by the conventional process (this is an index expressing deep drawing property, the higher the value is, the better the deep drawing property) and the cold rolling rate is shown in the second table. In addition, the relationship between the values and annealing temperature is shown in FIG. From this result, the cold-rolled steel sheet produced by the process of the present invention has a fine metal structure before cold rolling, so that the cold rolling rate and annealing temperature can be lowered compared to the conventional process.
本発明は、以上詳記したように、鋳造された金
属薄板をA1変態点以下に自然冷却した後再度A3
変態点以上に加熱し、次いで冷却するものである
から、金属組織が微細化された薄板鋳片が得るこ
とができ、次工程の冷間圧延工程及び焼鈍工程に
おける冷間圧延率及び焼鈍温度の低下を図ること
ができる効果が生ずるものである。
As described in detail above, the present invention allows a cast metal thin plate to be naturally cooled to below the A1 transformation point and then re-heated to the A3 transformation point.
Since it is heated above the transformation point and then cooled, a thin plate slab with a fine metal structure can be obtained, and the cold rolling rate and annealing temperature in the next cold rolling process and annealing process can be reduced. This has the effect of reducing the amount of water used.
第１図は、本発明の一実施例装置の縦断面図で
ある。第２図及び第３図は本発明プロセス及び従
来プロセスにて製造した冷間圧延鋼板の値と冷
延率（第２図）及び焼鈍温度（第３図）の関係を
示したものである。
FIG. 1 is a longitudinal sectional view of an apparatus according to an embodiment of the present invention. FIGS. 2 and 3 show the relationship between values, cold rolling reduction (FIG. 2), and annealing temperature (FIG. 3) for cold rolled steel sheets manufactured by the process of the present invention and the conventional process.
Claims (1)
て、水平に並設し、互いに回転方向を異にする２
本の水冷ロールを有する連続鋳造装置を使用して
金属薄板を製造する方法において、鋳造した金属
薄板を、一度A1変態点以下の温度に自然冷却し
た後、再度インラインにてA3変態点以上の温度
に加熱・保持し、次いでガス又は水あるいは気水
混合物で冷却することを特徴とする金属薄板製造
方法。1. Installed horizontally with a distance corresponding to the thickness of the thin metal plate to be manufactured, and rotated in different directions 2.
In a method for producing thin metal sheets using a continuous casting device with water-cooled rolls, the cast thin metal sheets are naturally cooled to a temperature below the A1 transformation point, and then in-line again to a temperature above the A3 transformation point. A method for producing a thin metal sheet, which comprises heating and maintaining the metal sheet at a temperature of 1,000,000 yen, and then cooling with gas, water, or a mixture of air and water.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3054585A JPS61189846A (en) | 1985-02-20 | 1985-02-20 | Manufacture of metallic sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3054585A JPS61189846A (en) | 1985-02-20 | 1985-02-20 | Manufacture of metallic sheet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61189846A JPS61189846A (en) | 1986-08-23 |
| JPH0460741B2 true JPH0460741B2 (en) | 1992-09-28 |
Family
ID=12306759
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3054585A Granted JPS61189846A (en) | 1985-02-20 | 1985-02-20 | Manufacture of metallic sheet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS61189846A (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63115654A (en) * | 1986-11-05 | 1988-05-20 | Mitsubishi Heavy Ind Ltd | Method and apparatus for casting metal sheet |
| WO1991009144A1 (en) * | 1989-12-20 | 1991-06-27 | Nippon Steel Corporation | Process for producing thin austenitic stainless steel plate and equipment therefor |
| JP4240590B2 (en) * | 1998-07-27 | 2009-03-18 | 三菱重工業株式会社 | Low carbon steel cold rolled sheet manufacturing method |
| FR2795005B1 (en) | 1999-06-17 | 2001-08-31 | Lorraine Laminage | PROCESS FOR THE MANUFACTURE OF SHEETS SUITABLE FOR DIRECT CASTING STAMPING OF THIN STRIPS, AND SHEETS THUS OBTAINED |
-
1985
- 1985-02-20 JP JP3054585A patent/JPS61189846A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS61189846A (en) | 1986-08-23 |
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| LAPS | Cancellation because of no payment of annual fees |