JPH02205618A - Method for continuously casting cast strip - Google Patents
Method for continuously casting cast stripInfo
- Publication number
- JPH02205618A JPH02205618A JP2641089A JP2641089A JPH02205618A JP H02205618 A JPH02205618 A JP H02205618A JP 2641089 A JP2641089 A JP 2641089A JP 2641089 A JP2641089 A JP 2641089A JP H02205618 A JPH02205618 A JP H02205618A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- alloy
- molten
- cast
- pouring
- 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.)
- Granted
Links
- 238000000034 method Methods 0.000 title claims abstract description 15
- 238000005266 casting Methods 0.000 title description 5
- 239000010935 stainless steel Substances 0.000 claims abstract description 23
- 229910001220 stainless steel Inorganic materials 0.000 claims abstract description 23
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 14
- 239000000956 alloy Substances 0.000 claims abstract description 14
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 14
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 12
- 238000009749 continuous casting Methods 0.000 claims abstract description 12
- 239000001301 oxygen Substances 0.000 claims abstract description 12
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 10
- 239000010959 steel Substances 0.000 claims abstract description 10
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 5
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 4
- 229910004709 CaSi Inorganic materials 0.000 claims abstract description 3
- 238000001816 cooling Methods 0.000 abstract description 14
- 239000000654 additive Substances 0.000 abstract description 5
- 238000001556 precipitation Methods 0.000 abstract description 5
- 230000000996 additive effect Effects 0.000 abstract description 4
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 abstract description 3
- 239000011575 calcium Substances 0.000 description 20
- 229910052751 metal Inorganic materials 0.000 description 9
- 239000002184 metal Substances 0.000 description 9
- 238000005336 cracking Methods 0.000 description 6
- 230000000694 effects Effects 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 239000012535 impurity Substances 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 239000003795 chemical substances by application Substances 0.000 description 2
- 238000004140 cleaning Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 125000004435 hydrogen atom Chemical class [H]* 0.000 description 2
- 238000007654 immersion Methods 0.000 description 2
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- XFWJKVMFIVXPKK-UHFFFAOYSA-N calcium;oxido(oxo)alumane Chemical compound [Ca+2].[O-][Al]=O.[O-][Al]=O XFWJKVMFIVXPKK-UHFFFAOYSA-N 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 230000008602 contraction Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 230000001939 inductive effect Effects 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000005058 metal casting Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 238000005507 spraying Methods 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
Landscapes
- Continuous Casting (AREA)
- Treatment Of Steel In Its Molten State (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、ツインドラム方式の連続鋳造機により割れの
無い薄肉鋳片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 crack-free thin slabs using a twin-drum continuous casting machine.
近年、金属の連続鋳造の分野では、製造コストの切下げ
、新材質の創出等を目的として、最終形状に近い薄肉鋳
片を製造する技術の開発が強く望まれている。この要求
に対して、ツインドラム方式、単ドラム方式、ドラム−
ベルト方式、ｊｌベルト方式、ツインベルト方式等、各
種の方法が提案され、その一部は工業生産のレベルまで
達している。In recent years, in the field of continuous metal casting, there has been a strong desire to develop a technology for producing thin slabs close to the final shape, with the aim of reducing production costs, creating new materials, etc. In response to this demand, twin-drum systems, single-drum systems, drum-
Various methods have been proposed, such as the belt method, JL belt method, and twin belt method, and some of them have reached the level of industrial production.
第２図は、これら連続鋳造方法の一つであるツインドラ
ム方式を説明するための慨略図である。FIG. 2 is a schematic diagram for explaining the twin drum method, which is one of these continuous casting methods.
クンデイフシ５１等の中間容器から浸漬ノズル２を介し
て、一対の冷却ドラム３ａ、 ３ｂの間に形成された湯
溜り部４に溶融金属が供給される。湯溜り１１１ｓ４の
溶融金属は、冷却ドラム３ａ、 ３ｂを介して抜熱され
、冷却ドラム３ａ、 ３ｂの周面に凝固シェルを形成す
る。この凝固シェルは、冷却ドラム３ａ、 ３ｂの回転
に伴ってキッシングポイント５に送られる間に成長する
。そして、両方の冷却ドラム３ａ、 ３ｂ周面に形成さ
れた凝固シェルは、キッシングポイント５で一体化され
、薄肉鋳片６として送り出される。薄肉鋳片６は、ピン
チロール７等を経て次工程に搬送される。Molten metal is supplied from an intermediate container such as a kundeifushi 51 through an immersion nozzle 2 to a sump 4 formed between a pair of cooling drums 3a and 3b. The molten metal in the pool 111s4 is heated through the cooling drums 3a, 3b, and forms a solidified shell on the circumferential surface of the cooling drums 3a, 3b. This solidified shell grows while being sent to the kissing point 5 as the cooling drums 3a, 3b rotate. The solidified shells formed on the circumferential surfaces of both cooling drums 3a and 3b are integrated at a kissing point 5 and sent out as a thin slab 6. The thin slab 6 is conveyed to the next process via pinch rolls 7 and the like.
この薄肉鋳片６鋳造過程で、冷却ドラム３ａ、 ３ｂの
周面を清浄状態に維持することが、凝固シェルの生成・
成長を安定化させる上で必要となる。そこで、クリーニ
ングブラシ８によって、冷却ドラム３ａ、 ３ｂの周面
を磨きながら鋳造する方法が特願昭６２−２９４４６４
号で提案されている。また、ドラムコータ９によってセ
ラミックスを冷却ドラム３ａ。During the casting process of the thin-walled slab 6, maintaining the surrounding surfaces of the cooling drums 3a and 3b in a clean state prevents the formation of a solidified shell.
This is necessary to stabilize growth. Therefore, a method of casting while polishing the circumferential surfaces of the cooling drums 3a and 3b with a cleaning brush 8 is proposed in Japanese Patent Application No. 62-294464.
proposed in No. Further, the ceramics are cooled by the drum coater 9 on the cooling drum 3a.
３ｂの周面に吹き付け、緩冷却条件下で凝固シェルを生
成・成長させる方法も、特願昭６２−３４８４号で提案
されている。Japanese Patent Application No. 3484/1984 also proposes a method in which a solidified shell is generated and grown under slow cooling conditions by spraying on the circumferential surface of 3b.
キッシングポイント５から送り出された薄肉鋳片６は、
従来の連続鋳造に比較して溶融金属を急冷・凝固させて
鋳造したものであり、しかも薄肉であるため、表面に多
数の割れが発生し易い。薄肉鋳片６に割れを発生させる
原因としては、冷却ドラム３ａ、 ３ｂ周面での不均一
凝固、凝固シェル収縮時の局部的な応力集中、冷却ドラ
ム３ａ、 ３ｂ周面に付着した異物等がある。そのため
、これら割れ発生原因を取り除き、品質の優れた薄肉鋳
片６を製造するため、これまでに種々の提案がされてい
る。The thin slab 6 sent out from the kissing point 5 is
Compared to conventional continuous casting, molten metal is cast by rapidly cooling and solidifying it, and since the wall is thinner, many cracks are more likely to occur on the surface. The causes of cracks in the thin slab 6 include uneven solidification on the circumferential surface of the cooling drums 3a and 3b, localized stress concentration during contraction of the solidified shell, and foreign matter adhering to the circumferential surface of the cooling drums 3a and 3b. be. Therefore, various proposals have been made to eliminate these causes of cracking and to manufacture thin slabs 6 of excellent quality.
しかし、薄肉鋳片に割れが発生する原因としては、前述
した鋳造条件の他に、鋳造される溶融金属自体に起因す
るものがあることを本発明者等は見出した。たとえば、
溶鋼に硫化物系の非金属介在物があるとき、この非金属
介在物が割れの起点となって、鋳造された薄肉鋳片に多
数の微少割れを誘発させる。この傾向は、特にステンレ
ス溶鋼の場合に顕著に見られる。However, the inventors of the present invention have discovered that, in addition to the above-mentioned casting conditions, cracks occur in thin slabs due to the molten metal itself being cast. for example,
When molten steel contains sulfide-based nonmetallic inclusions, these nonmetallic inclusions act as starting points for cracks, inducing numerous microcracks in the thin-walled slab that has been cast. This tendency is particularly noticeable in the case of molten stainless steel.
そこで、本発明は、注湯されるステンレス溶鋼に対して
特定された調整を施すことにより、不純物を除去或いは
無害化し、溶融状態から凝固する際に割れ発生の起点と
なる核を減少させ、割れのない薄肉鋳片を製造すること
を目的とする。Therefore, the present invention removes impurities or renders them harmless by making specific adjustments to the molten stainless steel that is poured, thereby reducing the number of nuclei that become the starting point for cracks when solidifying from the molten state, and preventing cracks. The purpose is to manufacture thin-walled cast slabs with no cracks.
本発明の連続鋳造方法は、その目的を達成するため、Ｓ
ｉ及び／又はＭｎで脱酸・溶製したステンレス溶鋼をタ
ンデイツシュに注湯した後、溶存酸素濃度が１５９ｐｐ
ｍ以下になるまでＡｌ、 Ｔｉ、 Ｚｒ□）一種又
は二種以上を添加し、次いでＣａＳｉ合金。In order to achieve the purpose, the continuous casting method of the present invention has S
After pouring the molten stainless steel deoxidized and melted with i and/or Mn into a tandem cup, the dissolved oxygen concentration was 159pp.
One or more of Al, Ti, Zr□) is added until the amount becomes less than m, and then the CaSi alloy is formed.
ＣａＮｉ合金、ＣａＭｇ合金、 Ｃａ−希土類系合金の
一種又は二種以上を添加して溶鋼のＣａ濃度を５〜８０
ｐｐｍ とし、調整されたステンレス溶鋼をツィンドラ
ノ、大連続鋳造機の湯溜り部に注入することを特徴とす
る。Add one or more of CaNi alloy, CaMg alloy, Ca-rare earth alloy to increase the Ca concentration of molten steel from 5 to 80.
ppm, and the adjusted stainless molten steel is injected into the sump of a large continuous casting machine.
旧来の連続鋳造に比較して、溶融金属から薄肉鋳片を直
接製造するツインドラム方式等の連続鋳造方法において
は、溶融金属の降温が急激に行われる。そのため、溶融
金属に含まれている不純物は、溶融金属が冷却ドラムを
介して抜熱される際に、多数の微細粒子として析出する
。たとえば、Ｓ、Ｐ等は、Ｆｅ、 Ｃｒ、 Ｎｉ、
Ｍｎ、 Ｏ等と反応して非金属介在物となる。こ
の非金属介在物は、マトリックスと物性が異なり、凝固
シェルの生成・成長及び冷却・収縮が行われるとき、析
出した非金属介在物の周囲に応力が集中し易くなる。こ
の応力集中が、鋳造された薄肉鋳片に微少な割れを発生
させる原因であると考えられる。Compared to conventional continuous casting, in continuous casting methods such as the twin-drum method in which thin-walled slabs are directly produced from molten metal, the temperature of the molten metal is rapidly lowered. Therefore, impurities contained in the molten metal are precipitated as a large number of fine particles when the molten metal is removed from the heat through the cooling drum. For example, S, P, etc. are Fe, Cr, Ni,
Reacts with Mn, O, etc. to form nonmetallic inclusions. These nonmetallic inclusions have different physical properties from the matrix, and when a solidified shell is generated, grown, cooled, and contracted, stress tends to concentrate around the precipitated nonmetallic inclusions. This stress concentration is considered to be the cause of micro-cracks in the cast thin slab.
この微少割れを解消するためには、非金属介在物の析出
を抑制すること、及び析出した場合にあっても無害な形
態にすることが必要である。この点から、本発明におい
ては、ステンレス溶鋼の調整条件を調査した。In order to eliminate these microcracks, it is necessary to suppress the precipitation of nonmetallic inclusions and to make them harmless even if they are precipitated. From this point of view, in the present invention, conditions for adjusting molten stainless steel were investigated.
通常のステンレス溶鋼は、溶存酸素７００〜１５００ｐ
ｐｍ、 溶存水素３〜１３ｐｐｍ、 ３３０〜１５
０ｐｐｍ、 Ｐ１００〜４００ｐｐｍ程度の不純物元
素を含有している。そこで、前段階として、転炉、取鍋
等においてステンレス溶鋼を脱酸・溶製し、溶存酸素１
５０〜３００ｐｐｍ。Ordinary stainless steel molten steel has dissolved oxygen of 700 to 1500 p.
pm, dissolved hydrogen 3-13 ppm, 330-15
Contains impurity elements of about 0 ppm and P100 to 400 ppm. Therefore, as a preliminary step, molten stainless steel is deoxidized and melted in a converter, ladle, etc., and dissolved oxygen
50-300ppm.
溶存水素３〜１３ｐｐｍ、 ５３０〜１５０ｐｐｍ、
Ｐｌｏｏ 〜４００ｐｐｍ にｉ１１整する。この
ときの脱酸・溶製条件は、後続するタンデイツシュでの
脱酸やカルシウム系合金の添加を考慮して、前述した範
囲に定められる。Dissolved hydrogen 3-13ppm, 530-150ppm,
Adjust the i11 to Ploo ~400ppm. The deoxidizing and melting conditions at this time are determined within the ranges mentioned above, taking into consideration deoxidizing in the subsequent tundish and addition of a calcium-based alloy.
脱酸・溶製されたステンレス溶鋼は、タンデイツシュに
注湯された後、Ａｌ、 Ｔｉ、 Ｚｒ等の添加によ
り溶存酸素濃度１５０ｐｐｍ以下に脱酸される。たとえ
ば、Ａｌを添加したとき、溶存酸素は、Ａｊ２と反応し
、Ａｊ’２０ｓとなって溶鋼から浮上分離する。ところ
で、ステンレス溶鋼においては、溶存酸素が１５０ｐｐ
ｍ超となると、次に添加するＣａ系添加剤中のＣａが酸
素と反応してＣａＯを形成してしまい、ＳやＰとの反応
が促進しなくなるため、Ｃａ系添加剤の添加前には溶存
酸素濃度を１５０ｐｐｍ以下に抑える必要がある。The deoxidized and melted molten stainless steel is poured into a tundish, and then deoxidized to a dissolved oxygen concentration of 150 ppm or less by adding Al, Ti, Zr, etc. For example, when Al is added, dissolved oxygen reacts with Aj2, becomes Aj'20s, and floats away from the molten steel. By the way, dissolved oxygen in molten stainless steel is 150pp.
If it exceeds m, Ca in the Ca-based additive to be added next will react with oxygen to form CaO, and the reaction with S and P will not be promoted, so before adding the Ca-based additive, It is necessary to suppress the dissolved oxygen concentration to 150 ppm or less.
このように、溶存酸素濃度１５０ｐＩｌ１ｍ以下に調整
されたステンレス溶鋼に、Ｃａ Ｓ ｉ、 Ｃａ Ｎ
ｉ、 Ｃａ Ｍｇ。In this way, Ca Si, Ca N
i, Ca Mg.
Ｃａ−希土類等の合金を添加する。このＣａ系添加剤は
、ステンレス溶鋼に依然として残存する酸素をカルシウ
ムアルミネートとして固定する。また、ＳはＣａＳとし
て固定され、ＭｎＳの析出が無くなるために、割れに対
して有害な硫化物であるＭｎＳの影響が無くなる。さら
に、Ｐも僅かではあるがＣａＰとして固定され、有害な
（Ｆｅ、 Ｍｎ） Ｐの生成が抑えられる。Add alloys such as Ca-rare earth. This Ca-based additive fixes oxygen still remaining in the molten stainless steel as calcium aluminate. Further, since S is fixed as CaS and there is no precipitation of MnS, the influence of MnS, which is a harmful sulfide, on cracking is eliminated. Furthermore, P is also fixed as CaP, albeit in a small amount, and the generation of harmful (Fe, Mn) P is suppressed.
このＯ，Ｓ、Ｐ等の悪影響を抑えるためには、Ｃａ系添
加斉りで処理した後のステンレス溶鋼に含まれるＣａを
１０〜３０ｐｐｍにすることが必要である。In order to suppress the adverse effects of O, S, P, etc., it is necessary to control the amount of Ca contained in the molten stainless steel to 10 to 30 ppm after the treatment with Ca-based addition.
ここで、ＣａをｌＯ〜３０ｐｐｍ溶鋼中に残留させる理
由は、ＭｎＳや（Ｆｅ、 Ｍｎ） Ｐの生成温度が、前
者では１４００℃程度、後者では１２００℃程度とステ
ンレス鋼の凝固温度よりも低く、それに比べてＣａＳ
の生成温度は１５００℃以上と溶鋼中ですでに生成し
ているためである。すなわち、ＣａＳ を生成させ浮上
させても、なお平衡的に溶存するＳがあるため、凝固後
に生じる析出物を固定するには溶存Ｃａ が必要である
。なお、Ｐは、一部Ｃａで固定されているが、全てＣａ
で固定されているとは考えにくく、一部の固定でも割
れ防止には効果が出ていると考えられる。Here, the reason why Ca remains in the molten steel at lO~30ppm is that the formation temperature of MnS and (Fe, Mn)P is lower than the solidification temperature of stainless steel, which is about 1400°C for the former and about 1200°C for the latter. Compared to that, CaS
This is because the formation temperature is 1500° C. or higher, which means that it is already formed in the molten steel. That is, even if CaS is generated and floated, there is still S dissolved in equilibrium, so dissolved Ca is required to fix the precipitates that are formed after solidification. Note that P is partially fixed at Ca, but all of P is fixed at Ca.
It is difficult to imagine that it is fixed in place, and it is thought that even some fixation is effective in preventing cracking.
このように、本発明に従って調整されたステンレス溶鋼
は、応力集中が起こり易い核の析出が抑えられる。その
結果、鋳造された薄肉鋳片は、微細割れのない優れた品
質の製品となる。In this way, the molten stainless steel prepared according to the present invention can suppress the precipitation of nuclei that tend to cause stress concentration. As a result, the cast thin slab becomes a product of excellent quality without microcracks.
５ＵＳ３０４組成をもつ温度１４９０℃のステンレス溶
鋼から、第２図に示したツインドラム方式の連続鋳造機
を使用し、板幅８００ｍａ＋、 肉厚２ｍｌ１１の薄
肉鋳片を鋳造速度８０ｍ／分で鋳造した。第１表は、各
段階におけるステンレス溶鋼の清浄度及び鋳造された薄
肉鋳片に発生した微細割れを示す。なお、微細割れは、
鋳片を酸洗した後、１０ｍごとに１ｍの鋳片をサンプリ
ングし目視で観察し、その総長が０．５ｍ／ｍ″以上発
生しているものをＸ、０．１〜０．５ｍ／ｍ’発生して
いるものを△、 ０．０１−０．１ｍ／ｍ″発生してい
るものを○、微細割れが０．０１ ｍ ／ ｍ’以下の
ものを◎で評価した。また、脱酸剤としてはＡＪを使用
したが、Ｔｉ、 Ｚｒ系脱酸剤を使用した場合にも同
様な結果が得られた。From molten stainless steel having a composition of 5US304 at a temperature of 1490°C, a thin slab with a plate width of 800 m+ and a wall thickness of 2 ml11 was cast at a casting speed of 80 m/min using the twin-drum continuous casting machine shown in Fig. 2. Table 1 shows the cleanliness of the molten stainless steel at each stage and the microcracks that occurred in the cast thin slab. In addition, fine cracks are
After pickling the slabs, sample 1m slabs every 10m and visually observe them, and if the total length is 0.5m/m" or more, The results were evaluated as △ if 'microcracks occurred', ○ if microcracks occurred at 0.01-0.1 m/m', and ◎ if microcracks occurred at 0.01 m/m' or less. Furthermore, although AJ was used as the deoxidizing agent, similar results were obtained when Ti and Zr based deoxidizing agents were used.
第１表から明らかなように、本実施例においては、鋳造
された薄肉鋳片に含まれているｏ、ｓが微量で、かつＰ
濃度も低下しており、微細割れが極めて少なくなってい
ることが判る。これに対して、比較的多量のｏ、ｓ、ｐ
を含む鋳片にあっては、大きな非金属介在物が析出し、
その周囲に微細割れが発生していた。As is clear from Table 1, in this example, o and s contained in the cast thin slab were trace amounts, and P
It can be seen that the concentration has also decreased, and the number of microcracks has become extremely small. On the other hand, relatively large amounts of o, s, p
In slabs containing
Microcracks had occurred around it.
また、鋳造された薄肉鋳片に含まれているＣａ含有量と
割れとの関係を調べたところ、第１図に示すような関係
にあることが判った。なお、第１図において、割れ発生
指数は、薄肉鋳片１ ｍｌ当りの割れ長さ（ｍ）で示し
ている。第１図から明らかなように、Ｃａ処理による効
果は、Ｃａ含有量が５ｐｐｍを超えると顕著に現れる。Furthermore, when we investigated the relationship between the Ca content contained in the cast thin slab and cracking, we found that there was a relationship as shown in FIG. 1. In FIG. 1, the crack occurrence index is expressed as the crack length (m) per ml of thin slab. As is clear from FIG. 1, the effect of Ca treatment becomes noticeable when the Ca content exceeds 5 ppm.
しかし、鋳片に多量のＣａを含有させることは、高価な
Ｃａ系添加剤を消費するばかりか、ＣａＯ系のスラグが
鋳片をドラムの間に巻き込み、却って割れ発生を助長さ
せることになる。この点から、Ｃａ処理された後のステ
ンレス溶鋼におけるＣａ含有量を５〜８０ｐｐｍと規定
した。However, containing a large amount of Ca in the slab not only consumes expensive Ca-based additives, but also causes CaO-based slag to cause the slab to get caught between the drums, thereby promoting cracking. From this point of view, the Ca content in the molten stainless steel after Ca treatment was defined as 5 to 80 ppm.
以上に説明したように、本発明においては、湯溜り部に
注湯される前のステンレス溶鋼に対して特定された条件
下で脱酸等の処理を行うことにより、溶鋼から凝固シェ
ルが生成・成長するときに割れ発生の核となる酸化物、
硫化物等の析出を抑えている。これによって、割れの少
ない薄肉鋳片を製造することが可能となる。As explained above, in the present invention, a solidified shell is generated from the molten steel by deoxidizing the molten stainless steel under specified conditions before being poured into the molten metal pool. Oxide, which becomes the nucleus of cracking during growth,
Precipitation of sulfides, etc. is suppressed. This makes it possible to produce thin slabs with fewer cracks.
第１図は薄肉鋳片のＣａ含有量と割れ発生の関係を表し
たグラフ、第２図はツインドラム方式の連続鋳造装置を
示す概略図である。
１：タンデイツシュ ２：浸漬ノズル３ａ、 ３ｂ
：冷却ドラム ４：湯溜り部５：キッシングポイン
ト ６：薄肉鋳片７：ピンチロール ８：クリー
ニングブラシ９ニドラムコータFIG. 1 is a graph showing the relationship between the Ca content of a thin slab and the occurrence of cracks, and FIG. 2 is a schematic diagram showing a twin-drum continuous casting apparatus. 1: Tandite dish 2: Immersion nozzle 3a, 3b
: Cooling drum 4: Pool 5: Kissing point 6: Thin slab 7: Pinch roll 8: Cleaning brush 9 Ni drum coater
Claims (1)
鋼をタンディッシュに注湯した後、溶存酸素濃度が１５
０ｐｐｍ以下になるまでＡｌ、Ｔｉ、Ｚｒの一種又は二
種以上を添加し、次いでＣａＳｉ合金、ＣａＮｉ合金、
ＣａＭｇ合金、Ｃａ−希土類系合金の一種又は二種以上
を添加して溶鋼のＣａ濃度を５〜８０ｐｐｍとし、調整
されたステンレス溶鋼をツインドラム式連続鋳造機の湯
溜り部に注入することを特徴とする薄肉鋳片の連続鋳造
方法。1. After pouring molten stainless steel deoxidized and melted with Si and/or Mn into a tundish, the dissolved oxygen concentration is 15
One or more of Al, Ti, and Zr are added until the concentration becomes 0 ppm or less, and then CaSi alloy, CaNi alloy,
The feature is that one or more of CaMg alloy and Ca-rare earth alloy is added to adjust the Ca concentration of molten steel to 5 to 80 ppm, and the adjusted molten stainless steel is injected into the sump of a twin-drum continuous casting machine. Continuous casting method for thin-walled slabs.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1026410A JP2795871B2 (en) | 1989-02-03 | 1989-02-03 | Continuous casting of thin cast slab |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1026410A JP2795871B2 (en) | 1989-02-03 | 1989-02-03 | Continuous casting of thin cast slab |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02205618A true JPH02205618A (en) | 1990-08-15 |
| JP2795871B2 JP2795871B2 (en) | 1998-09-10 |
Family
ID=12192782
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1026410A Expired - Fee Related JP2795871B2 (en) | 1989-02-03 | 1989-02-03 | Continuous casting of thin cast slab |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2795871B2 (en) |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0647510A (en) * | 1992-08-03 | 1994-02-22 | Sumitomo Metal Ind Ltd | Continuous casting method |
| JPH0655246A (en) * | 1992-08-10 | 1994-03-01 | Nippon Steel Corp | Austenitic stainless steel cast strip |
| WO2003024644A1 (en) * | 2001-09-14 | 2003-03-27 | Nucor Corporation | Casting steel strip |
| US7485196B2 (en) | 2001-09-14 | 2009-02-03 | Nucor Corporation | Steel product with a high austenite grain coarsening temperature |
| EP2059624A1 (en) * | 2006-09-01 | 2009-05-20 | Nucor Corporation | Thin cast strip with controlled manganese and low oxygen levels and method for making same |
| US7588649B2 (en) | 2001-09-14 | 2009-09-15 | Nucor Corporation | Casting steel strip |
| US8016021B2 (en) | 2003-01-24 | 2011-09-13 | Nucor Corporation | Casting steel strip with low surface roughness and low porosity |
| US9149868B2 (en) | 2005-10-20 | 2015-10-06 | Nucor Corporation | Thin cast strip product with microalloy additions, and method for making the same |
| US9999918B2 (en) | 2005-10-20 | 2018-06-19 | Nucor Corporation | Thin cast strip product with microalloy additions, and method for making the same |
| US10071416B2 (en) | 2005-10-20 | 2018-09-11 | Nucor Corporation | High strength thin cast strip product and method for making the same |
| US11193188B2 (en) | 2009-02-20 | 2021-12-07 | Nucor Corporation | Nitriding of niobium steel and product made thereby |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS56156711A (en) * | 1980-05-07 | 1981-12-03 | Nisshin Steel Co Ltd | Reducing method of large impurities in continuous casting of stainless steel |
| JPS6411925A (en) * | 1987-07-04 | 1989-01-17 | Nippon Steel Corp | Method for preventing cracking of austenitic stainless steel or high-alloy steel at the time of rapid solidification |
-
1989
- 1989-02-03 JP JP1026410A patent/JP2795871B2/en not_active Expired - Fee Related
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS56156711A (en) * | 1980-05-07 | 1981-12-03 | Nisshin Steel Co Ltd | Reducing method of large impurities in continuous casting of stainless steel |
| JPS6411925A (en) * | 1987-07-04 | 1989-01-17 | Nippon Steel Corp | Method for preventing cracking of austenitic stainless steel or high-alloy steel at the time of rapid solidification |
Cited By (20)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0647510A (en) * | 1992-08-03 | 1994-02-22 | Sumitomo Metal Ind Ltd | Continuous casting method |
| JPH0655246A (en) * | 1992-08-10 | 1994-03-01 | Nippon Steel Corp | Austenitic stainless steel cast strip |
| AU2008249238B2 (en) * | 2001-09-14 | 2011-03-24 | Nucor Corporation | Casting steel strip |
| HRP20040234B1 (en) * | 2001-09-14 | 2013-02-28 | Nucor Corporation | Casting steel strip |
| EP1439926A4 (en) * | 2001-09-14 | 2004-11-03 | Nucor Corp | Casting steel strip |
| US7485196B2 (en) | 2001-09-14 | 2009-02-03 | Nucor Corporation | Steel product with a high austenite grain coarsening temperature |
| NO342646B1 (en) * | 2001-09-14 | 2018-06-25 | Nucor Corp | Casting of steel strip. |
| EP1439926A1 (en) * | 2001-09-14 | 2004-07-28 | Nucor Corporation | Casting steel strip |
| US7588649B2 (en) | 2001-09-14 | 2009-09-15 | Nucor Corporation | Casting steel strip |
| US7690417B2 (en) | 2001-09-14 | 2010-04-06 | Nucor Corporation | Thin cast strip with controlled manganese and low oxygen levels and method for making same |
| WO2003024644A1 (en) * | 2001-09-14 | 2003-03-27 | Nucor Corporation | Casting steel strip |
| US8002908B2 (en) | 2001-09-14 | 2011-08-23 | Nucor Corporation | Steel product with a high austenite grain coarsening temperature |
| US8016021B2 (en) | 2003-01-24 | 2011-09-13 | Nucor Corporation | Casting steel strip with low surface roughness and low porosity |
| US9149868B2 (en) | 2005-10-20 | 2015-10-06 | Nucor Corporation | Thin cast strip product with microalloy additions, and method for making the same |
| US9999918B2 (en) | 2005-10-20 | 2018-06-19 | Nucor Corporation | Thin cast strip product with microalloy additions, and method for making the same |
| JP2009511749A (en) * | 2005-10-20 | 2009-03-19 | ニューコア・コーポレーション | Steel material with high austenite grain roughening temperature and method for producing the same |
| US10071416B2 (en) | 2005-10-20 | 2018-09-11 | Nucor Corporation | High strength thin cast strip product and method for making the same |
| EP2059624A4 (en) * | 2006-09-01 | 2013-03-06 | Nucor Corp | Thin cast strip with controlled manganese and low oxygen levels and method for making same |
| EP2059624A1 (en) * | 2006-09-01 | 2009-05-20 | Nucor Corporation | Thin cast strip with controlled manganese and low oxygen levels and method for making same |
| US11193188B2 (en) | 2009-02-20 | 2021-12-07 | Nucor Corporation | Nitriding of niobium steel and product made thereby |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2795871B2 (en) | 1998-09-10 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN113649415A (en) | Preparation process of high-strength aluminum alloy welding wire | |
| JPH02205618A (en) | Method for continuously casting cast strip | |
| JP5703919B2 (en) | Mold flux for continuous casting of steel and continuous casting method | |
| EP1323837A1 (en) | Steel product made from carbon steel particularly for galvanisation and process for manufacturing the same | |
| JP2003225744A (en) | Powder for continuous casting and continuous casting method using this powder | |
| JP4010929B2 (en) | Mold additive for continuous casting of steel | |
| JPS63123556A (en) | Production of cr-ni stainless steel being hard to crack at casting and hot rolling process | |
| JP2809464B2 (en) | Continuous casting of thin cast slab | |
| JP3817188B2 (en) | Thin slab manufacturing method using twin drum type continuous casting machine having scum weir and scum weir | |
| JP6084762B2 (en) | Mold powder for continuous casting and continuous casting method | |
| JP3450777B2 (en) | Manufacturing method of stainless steel containing rare earth element | |
| KR100419644B1 (en) | A Method for Manufacturing Continuously Cast Strands from High Ni Containing Steel | |
| JP2001286991A (en) | Method for continuously casting stainless steel thin cast slab excellent in surface characteristic and its apparatus | |
| JPH06339754A (en) | Method for continuously casting thin sheet | |
| JP4081222B2 (en) | A slab having a fine solidification structure and a steel material processed from the slab | |
| JP2779194B2 (en) | Continuous casting of thin cast slab | |
| JPH06122052A (en) | Continuous casting method for steel | |
| JP3474451B2 (en) | Manufacturing method of continuous cast billet of mild steel | |
| JP3843590B2 (en) | Method for producing Ti deoxidized ultra-low carbon steel | |
| JP4081218B2 (en) | Continuous casting method | |
| JP2003071545A (en) | Stainless steel hoop casting piece and manufacturing method therefor | |
| JP2000246402A (en) | Method for casting thin cast slab and additive | |
| JP2002307145A (en) | Thin slab of austenitic stainless steel and twin roll type continuous casting method therefor | |
| JPS63210257A (en) | Heat resisting steel and its production | |
| JPS59141355A (en) | Production of weakly deoxidized steel by continuous casting method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| LAPS | Cancellation because of no payment of annual fees |