JPH04147748A - Method for casting cr and ni-contained iron-base alloy with twin roll type continuous casting - Google Patents
Method for casting cr and ni-contained iron-base alloy with twin roll type continuous castingInfo
- Publication number
- JPH04147748A JPH04147748A JP27058190A JP27058190A JPH04147748A JP H04147748 A JPH04147748 A JP H04147748A JP 27058190 A JP27058190 A JP 27058190A JP 27058190 A JP27058190 A JP 27058190A JP H04147748 A JPH04147748 A JP H04147748A
- Authority
- JP
- Japan
- Prior art keywords
- ribbon
- iron
- casting
- equivalent
- based alloy
- 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
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 21
- 239000000956 alloy Substances 0.000 title claims abstract description 21
- 238000005266 casting Methods 0.000 title claims description 24
- 238000000034 method Methods 0.000 title claims description 7
- 238000009749 continuous casting Methods 0.000 title description 2
- 238000001816 cooling Methods 0.000 claims abstract description 26
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 14
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 12
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 11
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 6
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 35
- 229910000859 α-Fe Inorganic materials 0.000 claims description 23
- 229910052742 iron Inorganic materials 0.000 claims description 17
- 238000004519 manufacturing process Methods 0.000 claims description 5
- 229910052802 copper Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims 2
- 230000008719 thickening Effects 0.000 claims 2
- 239000000203 mixture Substances 0.000 abstract description 14
- 229910000831 Steel Inorganic materials 0.000 abstract description 11
- 239000010959 steel Substances 0.000 abstract description 11
- 239000000463 material Substances 0.000 abstract description 3
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 18
- 230000007547 defect Effects 0.000 description 11
- 230000000694 effects Effects 0.000 description 10
- 238000007711 solidification Methods 0.000 description 7
- 230000008023 solidification Effects 0.000 description 7
- 238000005516 engineering process Methods 0.000 description 6
- 230000007797 corrosion Effects 0.000 description 5
- 238000005260 corrosion Methods 0.000 description 5
- 229920006395 saturated elastomer Polymers 0.000 description 4
- 239000010949 copper Substances 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000003795 chemical substances by application Substances 0.000 description 2
- 239000000498 cooling water Substances 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 210000001787 dendrite Anatomy 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Landscapes
- Continuous Casting (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野］
本発明は、双ロール薄板（帯）連鋳機での鉄基合金の鋳
造に当り、鋳造すべき薄帯の化学組成と、凝固殻の冷却
速度とを制御することにより、鋳造薄帯中の残留フェラ
イト率が所定の値より大きくなるようにして、薄帯の表
面での割れ、細かなひび割れ、不均一な凹凸といった欠
陥の発生を防止するのに有効な鋳造技術、すなわちＣｒ
、 Ｎｉ含有鉄基合金の双ロール式薄帯連鋳機による新
規な鋳造方法に関するものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention is directed to the casting of iron-based alloys using a continuous twin-roll thin plate (strip) caster. By controlling the cooling rate, the residual ferrite percentage in the cast ribbon is made greater than a predetermined value, thereby preventing defects such as cracks, fine cracks, and uneven unevenness on the ribbon surface. Casting technology effective for
, relates to a new method for casting Ni-containing iron-based alloys using a twin-roll continuous ribbon caster.
従来、薄帯（帯）の製造は、例えば第１図に示すような
双ロール式薄帯連鋳機の場合では、水平もしくは傾斜し
て配置した２本の冷却ロール間のロールキス部上に、湯
溜り部を形成させ、その湯溜り部に鋳造金属溶湯を注入
し、同時に前記冷却ロールにより冷却することにより凝
固殻を生成させ、しかもその凝固殻を次第に成長させた
後、ロール間のギャップから肥厚化した鋳片を下方へ引
抜き、金属薄帯を製造している。Conventionally, in the production of ribbon (strip), for example, in the case of a twin-roll continuous ribbon casting machine as shown in FIG. A pool is formed, molten casting metal is poured into the pool, and at the same time it is cooled by the cooling roll to generate a solidified shell, and after the solidified shell has gradually grown, it is poured into the pool from the gap between the rolls. Thickened slabs are pulled downward to produce thin metal strips.
ところが、第１図に示すような双ロール式薄帯連鋳機に
より、Ｃｒ、 Ｎｉを含む鉄基合金を鋳造する場合、鋳
造された薄帯の表面に、割れ、細かいひび割れ、不均一
な凹凸といった表面欠陥が生じることがある。この欠陥
は、薄帯の表面からの深さ０．１〜０．２睡の範囲で発
生しており、薄帯の表面品質を向上する上で重大な問題
となる。However, when iron-based alloys containing Cr and Ni are cast using a twin-roll continuous ribbon casting machine as shown in Figure 1, the surface of the cast ribbon may have cracks, fine cracks, or uneven unevenness. Surface defects may occur. This defect occurs at a depth of 0.1 to 0.2 depth from the surface of the ribbon, and becomes a serious problem in improving the surface quality of the ribbon.
薄帯表面で発生する上述のような欠陥の防止技術として
は、例えば特開平１−２９９７４５号公報では、鋳造薄
帯中の残留フェライト率が所定の値となるように、素材
中に所定の成分を添加してニッケル当量を増加させる技
術を提案している。As a technique for preventing the above-mentioned defects occurring on the surface of the ribbon, for example, Japanese Patent Application Laid-Open No. 1-299745 discloses that a predetermined component is added to the material so that the residual ferrite percentage in the cast ribbon becomes a predetermined value. We are proposing a technology to increase the nickel equivalent by adding nickel.
しかし、この従来技術は、鋳造薄帯の表面に発生する欠
陥を完全に防止するまでには至っていないのが実情であ
る。すなわち、この従来技術では、単に鋳造金属の組成
のみに着目して、凝固時の冷却速度の影響までを考慮し
ていなかったため、残留フェライト量を十分に増大させ
ることができず、そのために表面欠陥の発生を防止する
ことができなかったのである。However, the reality is that this conventional technique has not been able to completely prevent defects occurring on the surface of the cast ribbon. In other words, this conventional technology simply focuses on the composition of the cast metal and does not take into account the effect of the cooling rate during solidification, so it is not possible to sufficiently increase the amount of residual ferrite, and as a result, surface defects occur. It was not possible to prevent this from occurring.
上述したように、従来技術は、双ロール式薄帯連鋳機で
鋳造した薄帯の表面に発生する欠陥を、素材の成分を調
整することのみによって解決しようとしたために困難が
あった。すなわち、本発明者らの研究によると、双ロー
ル式連鋳機においては、鋳造後の薄帯の残留フェライト
率はロール表面が溶鋼に及ぼす冷却速度も強く影響する
ことが明らかとなり、それ故に、従来のように単に素材
の化学組成を調整しただけでは不十分であり、薄帯の表
面に発生する欠陥を防止することはできなかった。それ
に加えて、従来は、薄帯の表面で発生する欠陥を防止す
るための適切な残留フェライト率そのものが明確になっ
ていなかった。As described above, the prior art has had difficulties because it has attempted to solve defects occurring on the surface of the ribbon cast with a twin-roll continuous ribbon caster only by adjusting the ingredients of the raw material. That is, according to the research conducted by the present inventors, it has become clear that in twin-roll continuous casting machines, the residual ferrite percentage of the ribbon after casting is strongly influenced by the cooling rate that the roll surface exerts on the molten steel. Simply adjusting the chemical composition of the material as in the past was not sufficient, and it was not possible to prevent defects from occurring on the surface of the ribbon. In addition, until now, it has not been clear what the appropriate residual ferrite percentage is to prevent defects from occurring on the surface of the ribbon.
そこで、本発明の目的は、かような従来技術の問題点を
克服して、表面欠陥のないＣｒ＋ＮＩ含有鋼の薄帯を連
続鋳造する技術を確立することにある。SUMMARY OF THE INVENTION An object of the present invention is to overcome the problems of the prior art and to establish a technology for continuously casting a thin strip of Cr+NI-containing steel free of surface defects.
上期の目的の実現を目指して研究を進めた結果、本発明
者らは、以下に述べるような鋳造方法が有利に適合する
技術であるとの確信を得、本発明に想到した。As a result of conducting research aimed at realizing the objectives of the first half, the present inventors became convinced that the casting method described below is a technology that is advantageously suitable, and came up with the present invention.
すなわち本発明は、
水平もしくは傾斜配置した一対の冷却ロール間の湯溜り
部に鉄基合金溶湯を供給し、そのロール胴周面上に凝固
殻を生成させ、かつその凝固殻を次第に肥厚化させてか
らロール間のギャップから下方に引き抜き、鉄基合金の
薄帯を製造する方法において、鋳造後の残留フェライト
率が２．０％以上となるように、次の２つの手段により
制御することを特徴とするものである。That is, the present invention supplies molten iron-based alloy to a pool between a pair of horizontally or inclined cooling rolls, generates a solidified shell on the circumferential surface of the roll body, and gradually thickens the solidified shell. In the method of manufacturing a ribbon of iron-based alloy by pulling it downward from the gap between the rolls, the residual ferrite percentage after casting is controlled to be 2.0% or more by the following two means. This is a characteristic feature.
■ 双ロール式連鋳機により薄帯を鋳造する際に、鋳造
に用いる溶鋼の組成を、Ｃ≦０．２０ｉｙｔ％、Ｓｉ≦
５．００ｗｔ％、Ｍｎ≦３．００ｗｔ％、Ｓｉ≦５０ｗ
ｔ％、Ｃｒ ： １〜５０ｗｔ％およびＮ≦Ｑ、３ ｗ
ｔ％を含有し、残部が主としてＦｅ からなる組成と
し、かつＣｒｅｑ＝（％Ｃｒ） ＋（％Ｍｎ）＋１．５
（％Ｓｉ）Ｎｉ ｅｑ＝ （ＸＮｉ） ＋３０（％Ｃ）
＋３０（％Ｎ−０，０６） ＋０．５（％Ｍｎ）により
計算されるＣｒ当量およびＮｉ当量を、ＣｒＮｉ当量比
： Ｃｒ ｅｑ／Ｎｉ ｅｑ＞２．０５とすること、
■ 薄帯の表層から０．２胴までの領域における薄帯の
ロール面上での冷却速度を、５０〜４５０°Ｃ／ｓｅｃ
の冷却速度とする。■ When casting ribbon using a twin-roll continuous caster, the composition of the molten steel used for casting should be C≦0.20iyt%, Si≦
5.00wt%, Mn≦3.00wt%, Si≦50w
t%, Cr: 1-50wt% and N≦Q, 3w
t%, with the remainder mainly consisting of Fe, and Creq=(%Cr)+(%Mn)+1.5
(%Si)Ni eq= (XNi) +30(%C)
+30 (%N-0,06) +0.5 (%Mn) Cr equivalent and Ni equivalent calculated by CrNi equivalent ratio: Cr eq / Ni eq > 2.05,
■ The cooling rate on the roll surface of the ribbon in the area from the surface layer of the ribbon to 0.2 cylinders is set at 50 to 450°C/sec.
The cooling rate shall be .
また本発明は、その他に、上記合金成分として、Ｎｂを
添加した合金、さらにはＭｏ、 ＣｕおよびＴｉの１種
または２種以上を、前記Ｎｂとともに、あるいは単独に
添加した成分組成の合金についても、残留フェライト率
を２０％以上にすると表面欠陥のない薄帯を製造するの
に好適である。In addition, the present invention also relates to an alloy in which Nb is added as the alloy component, and further, an alloy in which one or more of Mo, Cu, and Ti are added together with or alone as the above-mentioned Nb. A residual ferrite ratio of 20% or more is suitable for producing a ribbon free of surface defects.
上述したように、双ロール式薄帯連鋳機による薄帯の鋳
造において、凝固後の残留フェライト率は、溶鋼の組成
と、ロール上で溶銅が凝固する際の凝固殻の冷却速度（
’Ｃ／５ｅｃ）により支配されることが判った。そこで
、双ロール式薄帯連鋳機による薄帯の鋳造において、ま
ず冷却速度については、薄帯の表層０〜０．２ Ｍｎの
深さまでの冷却速度を５０〜４５０°Ｃ／ｓｅｃとして
、前記Ｃｒ、 Ｎｉ当量比：Ｃｒ ｅｑ／Ｎｉ ｅｑ＞
２．０５とすることとした。この条件によって、凝固後
の鋳片（薄帯）の残留フェライト率が２．０％以上とな
って、鋳片表面での割れの発生が防止できる条件である
ことがわかった。As mentioned above, when casting ribbon using a twin-roll continuous ribbon caster, the residual ferrite rate after solidification is determined by the composition of the molten steel and the cooling rate of the solidified shell when the molten copper solidifies on the rolls (
'C/5ec). Therefore, when casting a ribbon using a twin-roll type continuous ribbon casting machine, first, the cooling rate is set to 50 to 450°C/sec from the surface layer of the ribbon to a depth of 0 to 0.2 Mn. Cr, Ni equivalent ratio: Cr eq/Ni eq>
It was decided to set it as 2.05. It was found that under these conditions, the percentage of residual ferrite in the slab (thin ribbon) after solidification was 2.0% or more, and the generation of cracks on the slab surface could be prevented.
以下にこのことを詳しく説明する。This will be explained in detail below.
■ 組成の影響について；
第２図は、上期のＣｒ当量、 Ｎｉ当量の計算式を用い
て算出するＣｒＮｉ当量比（Ｃｒ ｅｑ／Ｎｉ ｅｑ）
と、凝固後の鋳片を用いてフェライトメータにより計測
した残留フェライト率（χ）との関係を示したものであ
る。図中に示す×印は、凝固後の薄帯に鋳片割れおよび
不均一な凹凸が認められたケースであり、一方○印は、
鋳片割れが無くしかも表面が滑らかで凹凸が無いケース
の例である。■ Regarding the influence of composition; Figure 2 shows the CrNi equivalent ratio (Cr eq/Ni eq) calculated using the formula for Cr equivalent and Ni equivalent in the first half.
This figure shows the relationship between the residual ferrite ratio (χ) measured using a ferrite meter using a slab after solidification. The × marks in the figure are cases where slab cracking and non-uniform unevenness were observed in the ribbon after solidification, while the ○ marks are
This is an example of a case where there are no cracks in the slab and the surface is smooth and has no irregularities.
この図に示された結果から明らかなように、綱の組成は
、ＣｒＮｉ当量比： Ｃｒ ｅｑ／Ｎｉ ｅｑが２．０
５以上のときで、しかも鋳片の凝固組織中には残留フェ
ライト量が２．０％以上形成されている場合において、
鋳片は表面に割れや不均一な凹凸が無い良好な表面性状
のものが得られる。As is clear from the results shown in this figure, the composition of the steel is such that the CrNi equivalent ratio: Cr eq/Ni eq is 2.0.
5 or more, and when the amount of residual ferrite is 2.0% or more in the solidified structure of the slab,
The slab has a good surface quality with no cracks or unevenness on the surface.
なお、本発明の鉄基合金の組成限定の理由は次のとおり
である。The reason for limiting the composition of the iron-based alloy of the present invention is as follows.
Ｃ：Ｃは、強度向上のために添加されるが、０，２０ｗ
ｔ％を超えるとその効果は飽和するので、０．２０ｗｔ
％以下とする。C: C is added to improve strength, but at 0.20w
If it exceeds t%, the effect is saturated, so 0.20wt
% or less.
Ｓｉ ： Ｓｉは、脱酸剤、あるいは耐酸化性向上のた
めに添加されるが、５．００ｗｔ％を超えると脆化する
ため、５．００ｗｔ％以下とする。Si: Si is added as a deoxidizing agent or to improve oxidation resistance, but if it exceeds 5.00 wt%, it becomes brittle, so it should be kept at 5.00 wt% or less.
Ｍｎ ： Ｍｎは、脱酸剤として添加されるが、３．０
０ｗｔ％を超えるとその効果が飽和するので、３．００
ｗｔ％を上限として加える。Mn: Mn is added as a deoxidizing agent, but 3.0
If it exceeds 0 wt%, the effect is saturated, so 3.00
Add up to wt%.
Ｎｉ ： Ｎｉは、強力なオーステナイト形成元素であ
り、Ｃｒとバランスさせるため、また耐食性を向上させ
るため添加する。過度の添加は高価になるため５０ｗｔ
％以下とする。Ni: Ni is a strong austenite-forming element, and is added to balance it with Cr and to improve corrosion resistance. Adding too much will be expensive, so 50wt
% or less.
Ｃｒ ： Ｃｒは、耐食性、耐酸化性、高温強度のため
添加するが、１ｗｔ％未満ではその効果がなく、５０ｗ
ｔ％を超えてもその効果が飽和するので、１〜５０賀ｔ
％とする。Cr: Cr is added for corrosion resistance, oxidation resistance, and high-temperature strength, but if it is less than 1wt%, it has no effect, and if 50w
The effect is saturated even if it exceeds 1 to 50 t%.
%.
Ｎｂ ： Ｎｂは、耐食性や成形性向上のために添加す
ることができる。０．０１ｗｔ％未満ではその効果がな
く、３．００ｗｔ％を超えてもその効果は飽和するので
、０．Ｏ１〜３．００ｗｔ％とする。Nb: Nb can be added to improve corrosion resistance and formability. If it is less than 0.01 wt%, there is no effect, and if it exceeds 3.00 wt%, the effect is saturated, so 0.01 wt% is not effective. O1 to 3.00 wt%.
Ｎ：Ｎは、強度向上のために添加することができる。０
．３ｗｔ％をこえる添加は固溶度を超えブローホール等
の原因となるため、０．３ ｗｔ％以下とする。N: N can be added to improve strength. 0
．． Addition of more than 3 wt% exceeds the solid solubility and causes blowholes, etc., so the content should be 0.3 wt% or less.
Ｍｏ ： Ｍｏは、耐食性、高温強度、Ｃｕ、 Ｔｉは
耐食性。Mo: Mo has corrosion resistance and high temperature strength, and Cu and Ti have corrosion resistance.
成形性などの特性改善の目的で通常添加される元素であ
る。これは、ＣｒＮｉ当量にＣｒ、 Ｎｉはどの影響を
与えないため、計算式においては係数を０として扱う。It is an element that is usually added for the purpose of improving properties such as formability. This is because Cr and Ni have no effect on the CrNi equivalent, so the coefficient is treated as 0 in the calculation formula.
また、この他に他の特性改善の目的で微量成分を添加し
た場合も本発明に含まれることはもちろんである。In addition, it goes without saying that the present invention also includes the addition of trace components for the purpose of improving other characteristics.
■ 冷却速度の影響について；
双ロール式薄帯連鋳機において、ロール湯溜り部に溶鋼
を供給して、そのロール胴周面で凝固させる場合、生成
する凝固殻の冷却速度は、ロールの回転速度、ロール内
に供給する冷却水の流量、および鋳造直後の二次冷却時
の冷却水の流量などにより変更することができる。冷却
速度が５０’Ｃ／ｓｅｃ未溝の場合、鋳片に未凝固部が
存在し、鋳片がふくれるバルジング、さらには凝固殻を
やふって溶鋼が流出するブリードの危険がある。また、
４５０”Ｃ／ｓｅｃを超える場合、残留フェライト量を
２％以上とすることが困難である。そこで、−例として
、ロールの回転速度を変更した場合の結果を第３図に示
した。この第３図は、第２図と同様に、ＣｒＮ ｉ当量
比（Ｃｒ ｅｑ／Ｎｉ ｅｑ）と凝固後の残留フェライ
ト率との関係を示したものである。図中、ロール回転速
度が高速の場合をΔ印で示し、中速の場合を○印、低速
の場合を口中で示した。この図から判るように、ロール
回転速度が高速の場合は低速の場合と比べると、同じ組
成、同じＣｒＮ ｉ当量比であっても、鋳片の残留フェ
ライト率が高くなる。■ Regarding the effect of cooling rate: When molten steel is supplied to the roll pool in a twin-roll continuous strip casting machine and solidified on the roll body circumferential surface, the cooling rate of the solidified shell that is generated depends on the rotation of the rolls. It can be changed depending on the speed, the flow rate of cooling water supplied into the roll, the flow rate of cooling water during secondary cooling immediately after casting, etc. If the cooling rate is 50'C/sec without grooves, there will be unsolidified parts in the slab, and there is a risk of bulging, which causes the slab to swell, and furthermore, bleed, which destroys the solidified shell and causes molten steel to flow out. Also,
When it exceeds 450"C/sec, it is difficult to make the amount of residual ferrite 2% or more. Therefore, as an example, the results when the rotational speed of the roll is changed are shown in Fig. 3. Figure 3, similar to Figure 2, shows the relationship between the CrNi equivalent ratio (Cr eq/Nieq) and the residual ferrite percentage after solidification.In the figure, the case where the roll rotation speed is high is shown. It is indicated by Δ, medium speed is indicated by ○, and low speed is indicated in the mouth.As can be seen from this figure, when the roll rotation speed is high, the same composition and the same CrN i Even at an equivalent ratio, the residual ferrite rate of the slab becomes high.
従って、鋳片表面の割れの発生は、凝固後の鋳片におい
て２．０％以上の残留フェライト量を確保すれば防止で
きる。このことはまた、鋳片内部のフェライトは、オー
ステナイトよりもＰ、Ｓ等の不純物成分を固溶し易いた
めと推定される。Therefore, the occurrence of cracks on the surface of the slab can be prevented by ensuring a residual ferrite content of 2.0% or more in the slab after solidification. This is also presumed to be because the ferrite inside the slab is more likely to dissolve impurity components such as P and S as a solid solution than the austenite.
以上説明したように、双ロール薄板式連鋳機においては
、溶鋼の組成と共に、凝固殻の冷却速度を制御して鋳片
の残留フェライト量を２．０％以上に制御すれば、鋳片
表面での割れの発生を確実に防止することができるので
ある。As explained above, in a twin-roll thin plate continuous caster, if the composition of the molten steel and the cooling rate of the solidified shell are controlled to control the amount of residual ferrite in the slab to 2.0% or more, the surface of the slab This makes it possible to reliably prevent the occurrence of cracks.
この実施例は、各種の鉄基合金の薄帯を、双ロール式薄
帯連鋳機により鋳造した例を説明するものである。第１
表は、鋳造した薄帯の組成と、この組成より算出される
ＣｒＮｉ当量比、および薄帯の表面から０．２閣までの
深さ領域におけるデンドライト二次アーム間隔（μｍ）
の計測値より算出した凝固殻の平均冷却速度（”Ｃ／５
ｅｃ）とを示したものである。凝固殻の平均冷却速度（
”Ｃ／５ｅｅ）は、例えば、ロールの回転速度で制御す
ることができる。凝固殻の平均冷却速度と、ロールの回
転速度の関係を前記第１表に併せて示す。This example describes an example in which ribbons of various iron-based alloys were cast using a twin-roll continuous ribbon caster. 1st
The table shows the composition of the cast ribbon, the CrNi equivalent ratio calculated from this composition, and the dendrite secondary arm spacing (μm) in the depth region up to 0.2 mm from the surface of the ribbon.
The average cooling rate of the solidified shell ("C/5" calculated from the measured value of
ec). The average cooling rate of the solidified shell (
"C/5ee)" can be controlled, for example, by the rotational speed of the roll. The relationship between the average cooling rate of the solidified shell and the rotational speed of the roll is also shown in Table 1 above.
二の実施例の結果から判るように、組成とくにＣｒＮ
ｉ当量比が本発明の条件を満たさない場合（Ｎ。As can be seen from the results of the second example, the composition, especially CrN
When the i equivalent ratio does not satisfy the conditions of the present invention (N.
１５、１６） 、および冷却速度が本発明の条件を満た
さない場合（ｋ１４）は、いずれも実測フェライト率が
２．０を下まわり、鋳片割れが発生したが、本発明の条
件内であるもの（Ｎα１〜１３）は、このような現象は
観測されなかった。特に本発明実施測高は、表面はその
まま冷間圧延が可能な状態となっていた。15, 16), and when the cooling rate does not meet the conditions of the present invention (k14), the measured ferrite ratio was less than 2.0 and slab cracking occurred, but it was within the conditions of the present invention. (Nα1-13), such a phenomenon was not observed. In particular, in the height measurement carried out in accordance with the present invention, the surface was in a state where cold rolling could be performed as is.
〔発明の効果〕
以上説明したとおり本発明によれば、双ロール式薄帯連
鋳機により鋳造した薄帯の表面には、割れや細かなひび
割れ、あるいは不均一な凹凸の発生が確実に防止でき、
表面性状に優れたＣｒ、 Ｎｉ含有鋼の薄帯を製造する
ことができる。[Effects of the Invention] As explained above, according to the present invention, the occurrence of cracks, fine cracks, or uneven unevenness on the surface of the ribbon cast by the twin-roll type continuous ribbon casting machine can be reliably prevented. I can,
It is possible to produce a Cr- and Ni-containing steel ribbon with excellent surface properties.
第１図は、双ロール式薄帯連鋳機の路線図、第２図は、
鋳片表面性状に及ぼすＣｒＮｉ当量比と残留フェライト
率との関係を示すグラフ、第３図は、鋳片冷却速度に及
ぼすＣｒＮｉ当量比と残留フェライ
ト率との関係を示すグラフである。
ｌ・・・ノズル、
２・・・湯溜り、
３・・・ロール、
４・・・鋳片Figure 1 is a route map of the twin roll continuous ribbon casting machine, Figure 2 is
FIG. 3 is a graph showing the relationship between the CrNi equivalent ratio and the residual ferrite rate on the slab surface properties, and FIG. 3 is a graph showing the relationship between the CrNi equivalent ratio and the residual ferrite rate on the slab cooling rate. l...nozzle, 2...pool, 3...roll, 4...slab
Claims (1)
溜り部に鉄基合金溶湯を供給し、そのロール胴周面上に
凝固殻を生成させ、かつその凝固殻を次第に肥厚化させ
てからロール間のギャップから下方に引き抜き、鉄基合
金の薄帯を製造する方法において、 前記鉄基合金として、Ｃ≦０．２０ｗｔ％、Ｓｉ≦５．
００ｗｔ％、Ｍｎ≦３．００ｗｔ％、Ｎｉ≦５０ｗｔ％
、Ｃｒ：１〜５０ｗｔ％およびＮ≦０．３ｗｔ％を含有
し、残部が主としてＦｅからなる組成を有し、かつ下記
のＣｒＮｉ当量比がＣｒ ｅｑ／Ｎｉ ｅｑ＞２．０５
の条件を満足するものを用い、 薄帯の冷却速度を、該薄帯表面から０．２ｍｍまでの領
域については５０〜４５０℃／ｓｅｃの冷却速度となる
ように制御して、鋳造薄帯の板厚方向の平均残留フェラ
イト率を２．０％以上にすることを特徴とするＣｒ、Ｎ
ｉ含有鉄基合金の双ロール式薄帯連鋳機による鋳造方法
。 但し、ＣｒＮｉ当量比：Ｃｒ ｅｑ／Ｎｉ ｅｑを求め
るために、Ｃｒ当量：Ｃｒ ｅｑおよびＮｉ当量：Ｎｉ
ｅｑを、Ｃｒ ｅｑ＝（％Ｃｒ）＋（％Ｍｎ）＋１．
５（％Ｓｉ）Ｎｉ ｅｑ＝（％Ｎｉ）＋３０（％Ｃ）＋
３０（％Ｎ−０．０６）＋０．５（％Ｍｎ）２、水平も
しくは傾斜配置した一対の冷却ロール間の湯溜り部に鉄
基合金溶湯を供給し、そのロール胴周面上に凝固殻を生
成させ、かつその凝固殻を次第に肥厚化させてからロー
ル間のギャップから下方に引き抜き、鉄基合金の薄帯を
製造する方法において、 前記鉄基合金として、Ｃ≦０．２０ｗｔ％、Ｓｉ≦５．
００ｗｔ％、Ｍｎ≦３．００ｗｔ％、Ｎｂ：０．０１〜
３．００Ｗｔ％、Ｎｉ≦５０ｗｔ％、Ｃｒ：１〜５０ｗ
ｔ％およびＮ≦０．３ｗｔ％を含有し、残部が主として
Ｆｅからなる組成を有し、かつ下記のＣｒＮｉ当量比が
Ｃｒ ｅｑ／Ｎｉ ｅｑ＞２．０５の条件を満足するも
のを用い、 薄帯の冷却速度を、該薄帯表面から０．２ｍｍまでの領
域については５０〜４５０℃／ｓｅｃの冷却速度となる
ように制御して、鋳造薄帯の板厚方向の平均残留フェラ
イト率を２．０％以上にすることを特徴とするＣｒ、Ｎ
ｉ含有鉄基合金の双ロール式薄帯連鋳機による鋳造方法
。 但し、ＣｒＮｉ当量比：Ｃｒ ｅｑ／Ｎｉ ｅｑを求め
るために、Ｃｒ当量：Ｃｒ ｅｑおよびＮｉ当量：Ｎｉ
ｅｑをＣｒ ｅｑ＝（％Ｃｒ）＋（％Ｍｎ）＋１．５
（％Ｓｉ）＋０．５（％Ｎｂ）Ｎｉ ｅｑ＝（％Ｎｉ）
＋３０（％Ｃ）＋３０（％Ｎ−０．０６）＋０．５（％
Ｍｎ）３、請求項１または２に記載された鉄基合金中に
、さらに Ｍｏ：０．０１〜５ｗｔ％、Ｃｕ：０．０１〜５ｗｔ％
およびＴｉ：０．０１〜３ｗｔ％の１種または２種以上
を添加してなる組成の鉄基合金を用いることを特徴とす
る請求項１または２に記載のＣｒ、Ｎｉ含有鉄基合金の
双ロール薄帯連鋳機による鋳造方法。[Claims] 1. Supplying molten iron-based alloy to a pool between a pair of horizontally or inclined cooling rolls, producing a solidified shell on the circumferential surface of the roll body, and gradually displacing the solidified shell. In the method of manufacturing a thin ribbon of an iron-based alloy by thickening the ribbon and then drawing it downward from a gap between rolls, the iron-based alloy contains C≦0.20wt%, Si≦5.
00wt%, Mn≦3.00wt%, Ni≦50wt%
, Cr: 1 to 50 wt% and N≦0.3 wt%, the balance mainly consists of Fe, and the following CrNi equivalent ratio is Cr eq / Ni eq > 2.05
The cooling rate of the thin ribbon was controlled to be 50 to 450°C/sec for the region up to 0.2 mm from the surface of the thin ribbon, and the cast ribbon was Cr, N characterized by having an average residual ferrite percentage in the thickness direction of 2.0% or more
A method for casting i-containing iron-based alloys using a twin-roll continuous ribbon caster. However, in order to obtain the CrNi equivalent ratio: Cr eq/Ni eq, Cr equivalent: Cr eq and Ni equivalent: Ni
eq as Cr eq=(%Cr)+(%Mn)+1.
5(%Si)Ni eq=(%Ni)+30(%C)+
30(%N-0.06)+0.5(%Mn)2, molten iron-based alloy is supplied to the pool between a pair of horizontally or inclined cooling rolls, and a solidified shell is formed on the circumferential surface of the roll body. A method for producing a thin ribbon of an iron-based alloy by gradually thickening the solidified shell and pulling it downward from a gap between rolls, wherein the iron-based alloy contains C≦0.20wt%, Si ≦5.
00wt%, Mn≦3.00wt%, Nb: 0.01~
3.00wt%, Ni≦50wt%, Cr:1~50w
t% and N≦0.3wt%, the balance is mainly Fe, and the following CrNi equivalent ratio satisfies the condition of Cr eq/Ni eq>2.05. The cooling rate of the strip was controlled to a cooling rate of 50 to 450°C/sec for the region up to 0.2 mm from the ribbon surface, and the average residual ferrite rate in the thickness direction of the cast ribbon was reduced to 2. Cr, N characterized by having a content of .0% or more
A method for casting i-containing iron-based alloys using a twin-roll continuous ribbon caster. However, in order to obtain the CrNi equivalent ratio: Cr eq/Ni eq, Cr equivalent: Cr eq and Ni equivalent: Ni
eq=(%Cr)+(%Mn)+1.5
(%Si)+0.5(%Nb)Ni eq=(%Ni)
+30(%C)+30(%N-0.06)+0.5(%
Mn)3, in the iron-based alloy according to claim 1 or 2, further Mo: 0.01 to 5 wt%, Cu: 0.01 to 5 wt%
and Ti: 0.01 to 3 wt%. Casting method using a continuous roll ribbon casting machine.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP27058190A JPH0698460B2 (en) | 1990-10-11 | 1990-10-11 | Casting method of iron-based alloy containing Cr and Ni by twin roll type continuous casting machine |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP27058190A JPH0698460B2 (en) | 1990-10-11 | 1990-10-11 | Casting method of iron-based alloy containing Cr and Ni by twin roll type continuous casting machine |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH04147748A true JPH04147748A (en) | 1992-05-21 |
| JPH0698460B2 JPH0698460B2 (en) | 1994-12-07 |
Family
ID=17488125
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP27058190A Expired - Fee Related JPH0698460B2 (en) | 1990-10-11 | 1990-10-11 | Casting method of iron-based alloy containing Cr and Ni by twin roll type continuous casting machine |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0698460B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004509762A (en) * | 2000-09-19 | 2004-04-02 | ティッセンクルップ ニロスタ ゲー エム ベー ハー | Method for producing steel strip or sheet mainly composed of Mn-austenite |
-
1990
- 1990-10-11 JP JP27058190A patent/JPH0698460B2/en not_active Expired - Fee Related
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004509762A (en) * | 2000-09-19 | 2004-04-02 | ティッセンクルップ ニロスタ ゲー エム ベー ハー | Method for producing steel strip or sheet mainly composed of Mn-austenite |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0698460B2 (en) | 1994-12-07 |
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