JPH0344858B2 - - Google Patents
Info
- Publication number
- JPH0344858B2 JPH0344858B2 JP56209731A JP20973181A JPH0344858B2 JP H0344858 B2 JPH0344858 B2 JP H0344858B2 JP 56209731 A JP56209731 A JP 56209731A JP 20973181 A JP20973181 A JP 20973181A JP H0344858 B2 JPH0344858 B2 JP H0344858B2
- Authority
- JP
- Japan
- Prior art keywords
- stirring
- slab
- molten steel
- steel
- unsolidified molten
- 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 - Lifetime
Links
- 238000003756 stirring Methods 0.000 claims description 34
- 229910000831 Steel Inorganic materials 0.000 claims description 29
- 239000010959 steel Substances 0.000 claims description 29
- 238000000034 method Methods 0.000 claims description 19
- 238000005266 casting Methods 0.000 claims description 13
- 239000013078 crystal Substances 0.000 claims description 9
- 238000009749 continuous casting Methods 0.000 claims description 7
- 238000007711 solidification Methods 0.000 description 14
- 230000008023 solidification Effects 0.000 description 14
- 238000005204 segregation Methods 0.000 description 5
- 238000010586 diagram Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 230000000694 effects Effects 0.000 description 2
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/12—Accessories for subsequent treating or working cast stock in situ
- B22D11/122—Accessories for subsequent treating or working cast stock in situ using magnetic fields
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Continuous Casting (AREA)
Description
この発明は、鋼の連続鋳造法に関するものであ
る。
連続鋳造法によりビレツト、ブルーム等の鋳片
を鋳造する場合、低温鋳造法を実施したり、鋳型
内溶鋼を電磁撹拌したり、あるいは鋳片の2次冷
却帯の未凝固溶鋼を電磁撹拌したりすることによ
つて、鋳片の最終凝固部に多量の等軸晶を生成せ
しめ、これによつて中心偏析の防止あるいは中心
組織の密度低下を防止して鋳片中心部の組織改善
を図ることは一般に行われている。
しかし、このような方法によつて等軸晶を鋳片
の最終凝固部に多量に生成しても、鋳片中心部の
組織改善は完全には達成されない。これは、最終
凝固部における等軸晶の流動性が最終凝固部の凝
固完了時の体積収縮に対して十分でなく、このた
めにV偏析や局部的なポロシテイが生じるからで
ある。
上述の問題を解決する方法として、最終凝固部
の未凝固溶鋼を電磁撹拌して、最終凝固部の等軸
晶の流動性を高める方法が提案されている。
本願発明者等は、最終凝固部の未凝固溶鋼の電
磁撹拌方法につき種々研究を重ねた結果、未凝固
溶鋼を旋回型電磁撹拌装置により鋳片の中心軸線
を中心として一方向に連続的に電磁撹拌する従来
方法では鋳片内質の向上は図れないが、第1図に
示されるように一定時間間隔毎に撹拌方向を反転
させる、所謂正逆交番撹拌により未凝固溶鋼を撹
拌すれば、鋳片内質の向上が図れること、およ
び、正逆交番撹拌の半サイクルの時間、すなわち
第1図中Δtが所定の範囲を外れると撹拌の効果
がなくなるといつた知見を得た。
この発明は、上記知見に基きなされたものであ
つて、
鋼を連続鋳造して、円柱または角柱ビレツトを
製造するに際して、多量の等軸晶を鋳片最終凝固
部の未凝固溶鋼に生成し、そして、前記未凝固溶
鋼を電磁撹拌装置によつて前記鋳片の中心軸線を
中心として旋回させて、前記未凝固溶鋼に、鋳片
引抜き方向に直角な平面内での循環流を生じさせ
ることからなる、鋼の連続鋳造法において、
前記撹拌方向を所定時間間隔毎に反転させなが
ら前記未凝固溶鋼を、下式によつて定められる撹
拌時間(ΔT)の間撹拌し、
ΔT=L/V≧0.5(min)
但し、
L:電磁撹拌装置の電磁コイルの長さ(m)、
V:鋳造速度(m/min)。
前記撹拌における半サイクルの撹拌時間ΔT
(sec)を、
5≦Δt≦30(sec)
の範囲とし、前記撹拌のサイクル数nを、
n≧1
としたことに特徴を有する。
次に、この発明における数値の限定理由につい
て説明する。
本願発明者等は、電磁撹拌装置を設置した、短
辺400mm、長辺520mmの鋳型を備えた垂直型連続鋳
造機により、第1表に示される組成を有する鋼を
溶鋼過熱度30℃で鋳造した。この時、鋳型下16m
の最終凝固部に60〜1200KVAの各種の旋回型電
磁撹拌装置を設置し、最終凝固部の未凝固溶鋼を
撹拌した。
The present invention relates to a continuous casting method for steel. When casting slabs such as billets and blooms using the continuous casting method, it is necessary to perform low-temperature casting, electromagnetically stir the molten steel in the mold, or electromagnetically stir the unsolidified molten steel in the secondary cooling zone of the slab. By doing so, a large amount of equiaxed crystals are generated in the final solidified part of the slab, thereby preventing center segregation or a decrease in the density of the central structure, thereby improving the structure at the center of the slab. is commonly practiced. However, even if a large amount of equiaxed crystals are produced in the final solidified part of the slab by such a method, the structure of the central part of the slab cannot be completely improved. This is because the fluidity of the equiaxed crystals in the final solidification zone is not sufficient for the volumetric shrinkage of the final solidification zone upon completion of solidification, resulting in V segregation and local porosity. As a method for solving the above-mentioned problem, a method has been proposed in which the unsolidified molten steel in the final solidification zone is electromagnetically stirred to improve the fluidity of equiaxed crystals in the final solidification zone. As a result of various studies on electromagnetic stirring methods for unsolidified molten steel in the final solidification section, the inventors of the present application have found that unsolidified molten steel is continuously electromagnetically stirred in one direction around the central axis of the slab using a rotating electromagnetic stirring device. Conventional stirring methods cannot improve the internal quality of slabs, but if unsolidified molten steel is stirred by so-called forward-reverse alternating stirring, in which the stirring direction is reversed at regular intervals, as shown in Figure 1, casting can be improved. It was found that the internal quality of the pieces can be improved, and that the effect of stirring is lost when the half-cycle time of forward and reverse alternating stirring, that is, Δt in FIG. 1, is out of a predetermined range. The present invention was made based on the above knowledge, and includes the following steps: When continuously casting steel to produce a cylindrical or prismatic billet, a large amount of equiaxed crystals are generated in the unsolidified molten steel in the final solidified part of the slab; Then, the unsolidified molten steel is swirled about the center axis of the slab by an electromagnetic stirrer to generate a circulation flow in the unsolidified molten steel in a plane perpendicular to the slab drawing direction. In the continuous steel casting method, the unsolidified molten steel is stirred for a stirring time (ΔT) determined by the following formula while reversing the stirring direction at predetermined time intervals, and ΔT=L/V≧ 0.5 (min) However, L: Length of the electromagnetic coil of the electromagnetic stirring device (m), V: Casting speed (m/min). Half cycle stirring time ΔT in the above stirring
(sec) is in the range of 5≦Δt≦30 (sec), and the number of stirring cycles n is in the range of n≧1. Next, the reasons for limiting the numerical values in this invention will be explained. The inventors cast steel having the composition shown in Table 1 at a molten steel superheating degree of 30°C using a vertical continuous casting machine equipped with an electromagnetic stirring device and a mold with a short side of 400 mm and a long side of 520 mm. did. At this time, 16m below the mold
Various types of rotary electromagnetic stirring devices of 60 to 1200 KVA were installed in the final solidification section to stir the unsolidified molten steel in the final solidification section.
【表】
このときの撹拌時間ΔTは、電磁撹拌装置の電
磁コイルの長さをL(m)、鋳造速度をV(m/
min)とすると、
ΔT=L/V(min) ……(1)
で定義した。
この条件で、ΔTおよびΔt(ΔTにおける半サイ
クルの撹拌時間(sec))を種々変更して鋳造を行
ない、鋳造終了後の鋳片の中心部に存在する中心
偏析、ポロシテイを調査した。
この結果、ΔTおよびΔtが第2図に示される斜
線を施した範囲内である場合、すなわち、ΔTお
よびΔtが次式を満足した場合に中心偏析やポロ
シテイのない健全な鋳片が得られることがわかつ
た。
Δ≧=0.5(min) ……(2)
5≦Δt≦30(sec) ……(3)
なお、撹拌サイクル数n(第1図中A〜Bを1
サイクルとする)は1サイクル以上必要であり、
この条件が第1図中直線lで示されている。
以上のことから、この発明では、ΔT,Δtおよ
びnを上記のように限定したのである。
次に、この発明の実施例について説明する。
電磁撹拌装置を設置した短辺400mm、長辺520mm
の角筒状鋳型を備えた垂直型連続鋳造機により、
前記第1表に示される組成を有する鋼を溶鋼過熱
度30℃で第2表に示される条件1〜4にしたがつ
て鋳造速度を0.5m/minとしてそれぞれ鋳造し
た。このとき、鋳型下16mの最終凝固部に1000mm
の長を有する電磁コイルを有する電磁撹拌装置を
設置した。そして、鋳造後の鋳片の中心部のポロ
シテイ発生指数を調べた。この結果を第3図に示
す。
第2表において、条件1は最終凝固部の未凝固
溶鋼を撹拌しなかつた場合であり、条件2および
3は、Δtが本発明範囲外の場合であり、条件4
が本発明法により鋳造した場合である。[Table] The stirring time ΔT at this time is calculated by setting the length of the electromagnetic coil of the electromagnetic stirring device to L (m) and the casting speed to V (m/m).
min), ΔT=L/V(min)... (1) Defined as follows. Under these conditions, casting was carried out with various changes in ΔT and Δt (half-cycle stirring time (sec) at ΔT), and center segregation and porosity present in the center of the slab after casting were investigated. As a result, when ΔT and Δt are within the shaded range shown in Figure 2, that is, when ΔT and Δt satisfy the following formula, a healthy slab without center segregation or porosity can be obtained. I understood. Δ≧=0.5 (min) …(2) 5≦Δt≦30 (sec) …(3) In addition, the number of stirring cycles n (A to B in Figure 1 is 1)
cycle) requires one or more cycles,
This condition is shown by the straight line l in FIG. From the above, in this invention, ΔT, Δt, and n are limited as described above. Next, embodiments of the invention will be described. Short side 400mm, long side 520mm with electromagnetic stirring device installed
A vertical continuous casting machine with a rectangular cylindrical mold allows
Steel having the composition shown in Table 1 above was cast at a molten steel superheating degree of 30 DEG C. under conditions 1 to 4 shown in Table 2 at a casting speed of 0.5 m/min. At this time, 1000mm is added to the final solidification part 16m below the mold.
An electromagnetic stirring device was installed with an electromagnetic coil having a length of . Then, the porosity occurrence index in the center of the cast slab was investigated. The results are shown in FIG. In Table 2, Condition 1 is the case where the unsolidified molten steel in the final solidification zone is not stirred, Conditions 2 and 3 are the cases where Δt is outside the range of the present invention, and Condition 4 is the case where Δt is outside the range of the present invention.
This is the case when cast by the method of the present invention.
【表】
第3図から明らかなように、本発明法により鋳
造した鋳片のポロシテイ指数は、本発明法外の方
法により鋳造した鋳片のポロシテイ指数に比べて
大巾に小さくなつていて、内質に優れた鋳片を鋳
造し得たことがわかる。
次に、別の実施例について説明する。
電磁撹拌装置を設置した210φの筒状鋳型を備
えた、11.5mRのわん曲軌道を有する円弧型連続
鋳造機により、第1表に示される組成を有する鋼
を溶鋼過熱度30℃で、第3表に示される条件5〜
8にしたがつて鋳造速度1.8m/minでそれぞれ
鋳造した。このとき、鋳片中心部の凝固終了点
(クレータエンド)は鋳型内溶鋼湯面から鋳片に
そつて27mの位置であり、鋳片の水平軌道内に達
していた。電磁撹拌装置の電磁コイルは、長さ
1800mmであり、これを最終凝固部に設置した。そ
して、鋳造後の鋳片と中心部のポロシテイ指数を
調べた。この結果を第4図に示す。
第3表において、条件5は最終凝固部の未凝固
溶鋼を撹拌しなかつた場合であり、条件6および
7は、Δtが本発明範囲内の場合であり、条件8
が本発明法によつて鋳造した場合である。[Table] As is clear from Fig. 3, the porosity index of the slab cast by the method of the present invention is significantly smaller than that of the slab cast by a method other than the method of the present invention. It can be seen that a slab with excellent internal quality was cast. Next, another example will be described. Using an arc type continuous casting machine with a 210φ cylindrical mold equipped with an electromagnetic stirring device and a curved orbit of 11.5mR, steel having the composition shown in Table 1 was cast at a molten steel superheating degree of 30°C. Conditions 5~ shown in the table
8 at a casting speed of 1.8 m/min. At this time, the solidification end point (crater end) at the center of the slab was located 27 m along the slab from the molten steel surface in the mold, and reached within the horizontal orbit of the slab. The length of the electromagnetic coil of the electromagnetic stirrer is
It was 1800 mm and was installed in the final solidification section. Then, the porosity index of the cast slab and its center was investigated. The results are shown in FIG. In Table 3, Condition 5 is the case where the unsolidified molten steel in the final solidification zone is not stirred, Conditions 6 and 7 are the case where Δt is within the range of the present invention, and Condition 8 is the case where Δt is within the range of the present invention.
This is the case when cast by the method of the present invention.
【表】
第4図から明らかなように、本発明法により鋳
造した鋳片のポロシテイ指数は、本発明法外の方
法により鋳造した鋳片のポロシテイ指数に比べて
大巾に小さくなつていて、内質の優れた鋳片を鋳
造し得たことがわかる。
なお、上記実施例の場合のように、鋳片の最終
凝固部が水平軌道に達している場合には、等軸晶
が途中で沈降してしまい最終凝固部に十分な量の
等軸晶が生成されないので、この場合には、別の
電磁撹拌装置を途中の円弧軌道に設けて等軸晶の
生成を増大させると良い結果が得らえる。
以上説明したように、この発明によれば、V偏
析やポロシテイ等の欠陥のない優れた内質の鋳片
を得ることができるといつた有用な効果がもたら
される。[Table] As is clear from Fig. 4, the porosity index of the slab cast by the method of the present invention is significantly smaller than that of the slab cast by a method other than the method of the present invention. It can be seen that a slab with excellent internal quality could be cast. In addition, if the final solidified part of the slab reaches the horizontal orbit as in the case of the above example, the equiaxed crystals will settle on the way and a sufficient amount of equiaxed crystals will not be present in the final solidified part. In this case, good results can be obtained by installing another electromagnetic stirring device in the middle of the circular arc orbit to increase the formation of equiaxed crystals. As explained above, according to the present invention, useful effects such as being able to obtain a slab of excellent internal quality free of defects such as V segregation and porosity are brought about.
第1図は、この発明の鋳片最終凝固部の撹拌パ
ターンを示す図、第2図は、ΔTとΔtとの関係を
示す図、第3図および第4図は、ポロシテイ発生
指数を示す図である。
Fig. 1 is a diagram showing the stirring pattern of the final solidification section of the slab according to the present invention, Fig. 2 is a diagram showing the relationship between ΔT and Δt, and Figs. 3 and 4 are diagrams showing the porosity occurrence index. It is.
Claims (1)
を製造するに際して、多量の等軸晶を鋳片最終凝
固部の未凝固溶鋼に生成し、そして、前記未凝固
溶鋼を電磁撹拌装置によつて前記鋳片の中心軸線
を中心として旋回させて、前記未凝固溶鋼に、鋳
片引抜き方向に直角な平面内での循環流を生じさ
せることからなる、鋼の連続鋳造法において、 前記撹拌方向を所定時間間隔毎に反転させなが
ら前記未凝固溶鋼を、下式によつて定められる撹
拌時間(Δt)の間、撹拌し、 Δt=L/V≧0.5(min) 但し、 L:電磁撹拌装置の電磁コイルの長さ(m)、 V:鋳造速度(m/min)。 前記撹拌における半サイクルの撹拌時間Δtを、 5≦Δt≦30(sec) の範囲内とし、前記撹拌のサイクル数nを、 n≧1 としたことを特徴とする、鋼の連続鋳造法。[Scope of Claims] 1. When continuously casting steel to produce a cylindrical or prismatic billet, a large amount of equiaxed crystals are generated in the unsolidified molten steel in the final solidified part of the slab, and the unsolidified molten steel is electromagnetically cast. In a continuous casting method for steel, the method comprises rotating the slab about its central axis by a stirring device to generate a circulation flow in the unsolidified molten steel in a plane perpendicular to the direction of drawing the slab. , While reversing the stirring direction at predetermined time intervals, the unsolidified molten steel is stirred for a stirring time (Δt) determined by the following formula, Δt=L/V≧0.5 (min) provided that L : Length of electromagnetic coil of electromagnetic stirring device (m), V: Casting speed (m/min). A method for continuous casting of steel, characterized in that the half-cycle stirring time Δt in the stirring is within the range of 5≦Δt≦30 (sec), and the number of cycles n of the stirring is n≧1.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP20973181A JPS58112642A (en) | 1981-12-28 | 1981-12-28 | Continuous casting method for steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP20973181A JPS58112642A (en) | 1981-12-28 | 1981-12-28 | Continuous casting method for steel |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS58112642A JPS58112642A (en) | 1983-07-05 |
JPH0344858B2 true JPH0344858B2 (en) | 1991-07-09 |
Family
ID=16577697
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP20973181A Granted JPS58112642A (en) | 1981-12-28 | 1981-12-28 | Continuous casting method for steel |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS58112642A (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2295168A1 (en) | 1997-12-08 | 2011-03-16 | Nippon Steel Corporation | Cast slab and method for casting molten metal, apparatus for the same |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2657946B2 (en) * | 1995-07-17 | 1997-09-30 | 株式会社ソフィア | Gaming machine |
JP5083241B2 (en) * | 2009-02-06 | 2012-11-28 | 住友金属工業株式会社 | Steel continuous casting method and slab manufactured by this method |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5243450A (en) * | 1975-10-01 | 1977-04-05 | Mashiinterumitsukusu Soc Et | Method of determining wear condition of element with a given magnetism |
JPS5244294A (en) * | 1975-09-30 | 1977-04-07 | Phillips Petroleum Co | Production of unicellular protein |
JPS536932A (en) * | 1976-07-08 | 1978-01-21 | Agency Of Ind Science & Technol | Method of underwater flame heating |
-
1981
- 1981-12-28 JP JP20973181A patent/JPS58112642A/en active Granted
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5244294A (en) * | 1975-09-30 | 1977-04-07 | Phillips Petroleum Co | Production of unicellular protein |
JPS5243450A (en) * | 1975-10-01 | 1977-04-05 | Mashiinterumitsukusu Soc Et | Method of determining wear condition of element with a given magnetism |
JPS536932A (en) * | 1976-07-08 | 1978-01-21 | Agency Of Ind Science & Technol | Method of underwater flame heating |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2295168A1 (en) | 1997-12-08 | 2011-03-16 | Nippon Steel Corporation | Cast slab and method for casting molten metal, apparatus for the same |
EP2295169A1 (en) | 1997-12-08 | 2011-03-16 | Nippon Steel Corporation | Cast slab and method for casting molten metal, apparatus for the same |
Also Published As
Publication number | Publication date |
---|---|
JPS58112642A (en) | 1983-07-05 |
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