JPH04314844A - Steel material excellent in toughness at low temperature and its production - Google Patents
Steel material excellent in toughness at low temperature and its productionInfo
- Publication number
- JPH04314844A JPH04314844A JP8003291A JP8003291A JPH04314844A JP H04314844 A JPH04314844 A JP H04314844A JP 8003291 A JP8003291 A JP 8003291A JP 8003291 A JP8003291 A JP 8003291A JP H04314844 A JPH04314844 A JP H04314844A
- Authority
- JP
- Japan
- Prior art keywords
- steel material
- surface layer
- oxides
- steel
- temperature toughness
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 48
- 239000010959 steel Substances 0.000 title claims abstract description 48
- 239000000463 material Substances 0.000 title claims abstract description 38
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- 239000002344 surface layer Substances 0.000 claims abstract description 20
- 238000000034 method Methods 0.000 claims abstract description 17
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 11
- 229910052684 Cerium Inorganic materials 0.000 claims abstract description 10
- 239000010410 layer Substances 0.000 claims abstract description 10
- 238000009749 continuous casting Methods 0.000 claims abstract description 9
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 8
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 6
- 230000003068 static effect Effects 0.000 claims description 8
- 239000002131 composite material Substances 0.000 claims description 6
- 230000004907 flux Effects 0.000 claims description 6
- 238000005266 casting Methods 0.000 claims description 5
- 229910052751 metal Inorganic materials 0.000 claims description 4
- 239000002184 metal Substances 0.000 claims description 4
- 239000002245 particle Substances 0.000 claims description 4
- 150000002739 metals Chemical class 0.000 claims description 3
- 230000001105 regulatory effect Effects 0.000 abstract 2
- 229910000576 Laminated steel Inorganic materials 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 5
- 238000001816 cooling Methods 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 238000005204 segregation Methods 0.000 description 3
- 229910052710 silicon Inorganic materials 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052735 hafnium Inorganic materials 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 229910000532 Deoxidized steel Inorganic materials 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000002788 crimping Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000007667 floating Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000005499 meniscus Effects 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 239000002356 single layer Substances 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Landscapes
- Continuous Casting (AREA)
- Treatment Of Steel In Its Molten State (AREA)
Abstract
Description
【0001】0001
【産業上の利用分野】本発明は、微細な酸化物が均一に
分散することによって得られる低温靭性に優れた鋼材お
よびそれを複合鋼材として連続鋳造する方法に関するも
のである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a steel material with excellent low-temperature toughness obtained by uniformly dispersing fine oxides, and a method for continuously casting the steel material as a composite steel material.
【0002】0002
【従来の技術】これまでに、連鋳鋳型内に鋳片の厚みを
横切る方向の直流磁束を全幅に亙って付与し、該直流磁
束によって鋳型上下方向に形成される静磁場帯を境界と
してその上下に組成の異なる金属を供給する複合金属材
の連続鋳造方法が特開昭63−108947号公報に開
示されている。[Prior Art] Until now, a direct current magnetic flux in the direction across the thickness of the slab is applied to the continuous casting mold over the entire width, and a static magnetic field band formed in the vertical direction of the mold by the direct current magnetic flux is used as the boundary. JP-A-63-108947 discloses a continuous casting method for a composite metal material in which metals having different compositions are supplied above and below.
【0003】一方、微細な酸化物を鋼中に分散させるこ
とで鋼の低温靭性を向上させる方法が特開昭61−23
8940号公報に開示されている。すなわち、少量のT
iを脱酸元素として添加し、2次脱酸生成物を微細分散
させることにより、これが変態核となって、オーステナ
イト粒内から微細なフェライトが生成して組織を微細化
し、特に溶接熱影響部の靭性が向上することが記述され
ている。また、本発明者らが特開平1−228643号
公報に開示した方法として、溶鋼中にZr,Ti,Ce
,YあるいはHfなどの脱酸元素を投入し、冷却凝固さ
せることで前記変態核の一つであるMnSを脱酸生成物
(ZrO2 ,Ti2 O3 ,Ce2 O3 など)
上に微細析出させる方法がある。これらの方法では酸化
物個数の増加に伴ってより微細な組織が得られることを
認めている。従って、上記いずれの方法においても目的
とするところはいかにして酸化物の個数を増やして均一
に分散させるかにある。On the other hand, a method for improving the low-temperature toughness of steel by dispersing fine oxides in the steel was disclosed in Japanese Patent Laid-Open No. 61-23.
It is disclosed in Japanese Patent No. 8940. That is, a small amount of T
By adding i as a deoxidizing element and finely dispersing the secondary deoxidizing product, this becomes a transformation nucleus, and fine ferrite is generated from within the austenite grains to refine the structure, especially in the weld heat affected zone. It has been described that the toughness of steel is improved. In addition, as a method disclosed by the present inventors in JP-A-1-228643, Zr, Ti, and Ce are added to molten steel.
By adding a deoxidizing element such as , Y or Hf and cooling and solidifying it, MnS, which is one of the transformation nuclei, is deoxidized to a product (ZrO2, Ti2 O3, Ce2 O3, etc.)
There is a method of making fine precipitation on top. It is recognized that these methods yield finer structures as the number of oxides increases. Therefore, the objective of any of the above methods is to increase the number of oxides and uniformly disperse them.
【0004】0004
【発明が解決しようとする課題】本発明は、鋼の組織の
微細化、それによる低温靭性の向上に着目し、前述した
粒内フェライトおよびMnSの変態・析出核となる酸化
物(脱酸生成物)を従来よりも多数分散させた鋼材およ
びその製造方法を提供することを目的とするものである
。[Problems to be Solved by the Invention] The present invention focuses on refining the structure of steel and thereby improving its low-temperature toughness, and aims to reduce the oxides (deoxidized The object of the present invention is to provide a steel material in which a larger number of materials are dispersed than before, and a method for manufacturing the same.
【0005】[0005]
【課題を解決するための手段】本発明の要旨とするとこ
ろは、(1)互いに成分の異なる表層及び内層からなり
、表層はTiを重量%で0.005%〜0.05%含有
した鋼で、内層はZr,Ca,Hf,Ce,Yのいずれ
か1種または2種以上の合計を0.005%〜0.05
%の範囲で含有した鋼であると共に、含有する酸化物の
最大粒径が50μm以下であり、該酸化物の(表層部の
個数)に対する(1/2厚部の個数)の比が60%より
大きいことを特徴とする鋼材であり、この鋼材は、(2
)連鋳鋳型内に鋳片の厚みを横切る方向の直流磁束を全
幅に亙って付与し、該直流磁束によって鋳型上下方向に
形成される静磁場帯を境界としてその上下に組成の異な
る金属を供給する複合鋼材の連続鋳造による製造方法に
おいて、表層となる静磁場帯上側に注入する溶鋼をMn
,Siで脱酸した後、Tiが重量%で0.005%〜0
.05%含まれるように添加し、内層となる静磁場帯下
側に注入する溶鋼をMn,Siで脱酸した後、Zr,C
a,Hf,Ce,Yのいずれか1種または2種以上の合
計が0.005%〜0.05%の範囲で含まれるように
添加することを特徴とする低温靭性に優れた鋼材の製造
方法によって得られる。また、これらの脱酸元素すなわ
ち、Ti,Zr,Ca,Hf,Ce,あるいはYワイヤ
ーによって添加供給することも可能である。[Means for Solving the Problems] The gist of the present invention is as follows: (1) A steel comprising a surface layer and an inner layer having different components, the surface layer containing 0.005% to 0.05% Ti by weight. The inner layer contains 0.005% to 0.05% of the total of one or more of Zr, Ca, Hf, Ce, and Y.
%, the maximum grain size of the oxides contained is 50 μm or less, and the ratio of (number of oxides in the 1/2 thick part) to (number of oxides in the surface layer) is 60%. This steel material is characterized by being larger than (2
) Direct current magnetic flux in the direction across the thickness of the slab is applied to the continuous casting mold over the entire width, and metals with different compositions are placed above and below the static magnetic field zone formed by the direct current magnetic flux in the vertical direction of the mold. In a manufacturing method using continuous casting of supplied composite steel materials, Mn
, after deoxidizing with Si, Ti is 0.005% to 0 by weight%.
.. After deoxidizing the molten steel to be injected under the static magnetic field zone, which will become the inner layer, with Mn and Si, Zr, C
Production of a steel material with excellent low-temperature toughness characterized by adding one or more of a, Hf, Ce, and Y in a total amount of 0.005% to 0.05%. Obtained by method. It is also possible to add and supply these deoxidizing elements, ie, Ti, Zr, Ca, Hf, Ce, or Y wire.
【0006】[0006]
【作用】以下に、本発明を作用とともに詳細に説明する
。本発明者らは従来の技術における問題点を解決すべく
詳細な研究を重ねた結果、脱酸元素の種類によって鋳片
厚み方向での酸化物の分散状態に大きな差がみられるこ
とを発見した。[Function] The present invention will be explained in detail below along with its function. The inventors of the present invention have conducted detailed research to solve the problems in the conventional technology, and have discovered that there are large differences in the dispersion state of oxides in the thickness direction of the slab depending on the type of deoxidizing element. .
【0007】すなわち、Ti脱酸した鋼の場合、酸化物
の個数は鋳片表層から内部にかけて減少する。これは、
Tiが弱脱酸元素であり、脱酸後の溶鋼の溶存酸素濃度
が高く、脱酸生成物は凝固中の偏析によって晶出する2
次生成物が主体となるためである。That is, in the case of Ti-deoxidized steel, the number of oxides decreases from the surface layer to the inside of the slab. this is,
Ti is a weak deoxidizing element, the dissolved oxygen concentration of molten steel after deoxidation is high, and the deoxidation products crystallize due to segregation during solidification.
This is because the next product is the main component.
【0008】その理由は、表層付近では冷却速度が大き
く偏析が著しいため、酸化物個数が多くなるが、鋳片1
/2厚部では冷却速度が小さく偏析が軽微なため、個数
が表層付近よりも少なくなる。一方、Zr,Ca,Hf
,Ce,Yなどは強脱酸元素であり、脱酸生成物は脱酸
直後に生成する1次生成物が主体である。[0008] The reason for this is that the cooling rate near the surface layer is high and segregation is significant, so the number of oxides increases.
In the /2 thick part, the cooling rate is low and segregation is slight, so the number is smaller than in the vicinity of the surface layer. On the other hand, Zr, Ca, Hf
, Ce, Y, etc. are strong deoxidizing elements, and deoxidizing products are mainly primary products produced immediately after deoxidizing.
【0009】したがって、酸化物個数に対する冷却速度
の影響がTi脱酸の場合よりも小さく、鋳片厚み方向に
おける分布がより均一になり、鋳片1/2厚部での酸化
物個数も十分に確保できる。しかし、凝固開始までの間
に凝集浮上するため、表層付近の酸化物個数がTi脱酸
に比べて少なくなる。Therefore, the influence of the cooling rate on the number of oxides is smaller than in the case of Ti deoxidation, the distribution in the thickness direction of the slab becomes more uniform, and the number of oxides in the 1/2 thick part of the slab becomes sufficient. Can be secured. However, since it aggregates and floats before solidification starts, the number of oxides near the surface layer is smaller than in Ti deoxidation.
【0010】以上述べてきたような2種類の脱酸方法で
準備したそれぞれの溶鋼、すなわち表層にTi脱酸溶鋼
、内層にZr,Ca,Hf,Ce,Yなどで脱酸した溶
鋼を用いて本発明では、前述の手段の項で説明したよう
に鋳型内に静磁場帯を形成し、2種類の溶鋼の混合を防
止しつつ連続鋳造することによって本発明の鋼材を製造
する。[0010] Using each of the molten steels prepared by the two types of deoxidizing methods described above, molten steel deoxidized with Ti in the surface layer and molten steel deoxidized with Zr, Ca, Hf, Ce, Y, etc. in the inner layer, In the present invention, the steel material of the present invention is manufactured by forming a static magnetic field zone in the mold and continuously casting while preventing the mixing of two types of molten steel, as explained in the section of the above-mentioned means.
【0011】こうして、本発明の方法によりはじめて複
合鋼材を連続鋳造する手段を用いて表層から連続的に十
分な個数の酸化物を均一に分散させた鋼材を製造するこ
とが可能となった。なぜならば、圧着法などの通常の複
合鋼材の製造方法では、図1に示すように、表層用鋼板
厚み方向のTi酸化物個数の急激な減少が回避できない
からである。[0011] Thus, by the method of the present invention, it has become possible for the first time to manufacture a steel material in which a sufficient number of oxides are uniformly dispersed continuously from the surface layer using means for continuously casting a composite steel material. This is because, as shown in FIG. 1, in a normal method of manufacturing composite steel materials such as a crimping method, a rapid decrease in the number of Ti oxides in the thickness direction of the surface steel sheet cannot be avoided.
【0012】溶鋼の脱酸に際しては、Mn,Si等で予
備脱酸した後でTiなどを添加する。脱酸元素の組成は
、目標組成が0.005%未満では、溶存酸素との反応
で生成する酸化物の量が実効上少なく、0.05%超で
は粗大な酸化物のクラスターが生成し、割れの発生起点
となるなどの悪影響がでるために、適正組成を0.00
5%〜0.05%とした。When deoxidizing molten steel, Ti or the like is added after preliminary deoxidation with Mn, Si, etc. Regarding the composition of the deoxidizing element, if the target composition is less than 0.005%, the amount of oxide produced by reaction with dissolved oxygen is effectively small, and if it exceeds 0.05%, coarse oxide clusters will be produced. The proper composition should be set to 0.00 to avoid negative effects such as becoming a starting point for cracks.
The content was set at 5% to 0.05%.
【0013】Zrなどの脱酸元素の添加は、合金を鉄パ
イプ内に充填してワイヤー状とし、一定速度でモールド
内に供給する方法が有効である。このワイヤー添加法は
、添加から凝固開始までの時間が短くなるため、特にZ
rなどの1次脱酸生成物の浮上量を少なくし、多くの酸
化物を分散させる目的に対して極めて有効である。[0013] An effective method for adding a deoxidizing element such as Zr is to fill an iron pipe with the alloy to form a wire, and to feed the alloy into a mold at a constant rate. This wire addition method shortens the time from addition to the start of solidification, especially for Z
It is extremely effective for reducing the floating amount of primary deoxidation products such as r and dispersing many oxides.
【0014】このようにして得られる鋼材は低温靭性に
優れている。その特徴は、図1に代表されるように、微
細な酸化物が均一に分散していること、すなわち、含有
する酸化物の最大粒径が50μm以下であり、該酸化物
の(表層部の個数)に対する(1/2厚部の個数)の比
が60%より大きいことである。なお、ここでいう表層
部とは、鋼材表面から10mmの深さの位置と定義する
。[0014] The steel material thus obtained has excellent low-temperature toughness. As represented in Figure 1, its characteristics are that fine oxides are uniformly dispersed, that is, the maximum particle size of the contained oxides is 50 μm or less, and the oxides (in the surface layer) are The ratio of (number of 1/2 thick parts) to (number of parts) is greater than 60%. Note that the surface layer portion here is defined as a position at a depth of 10 mm from the surface of the steel material.
【0015】[0015]
【実施例】表1に示したような組成の鋼材を前述の連続
鋳造方法により製造した。製造に際しては、鋳型内のメ
ニスカスより450mm〜700mmの範囲に5000
ガウスの強度を持つ静磁場を与えた。鋳型形状は厚み2
50mm×幅1000mm、鋳造速度は1m/分とした
。表層溶鋼と内層溶鋼の注湯量を調整し、表層の厚みを
25mmとした。EXAMPLE Steel materials having the compositions shown in Table 1 were produced by the continuous casting method described above. During manufacturing, 5000 mm is placed in the range of 450 mm to 700 mm from the meniscus in the mold.
A static magnetic field with Gaussian strength was applied. The mold shape has a thickness of 2
The size was 50 mm x width 1000 mm, and the casting speed was 1 m/min. The pouring amounts of the surface layer molten steel and the inner layer molten steel were adjusted so that the thickness of the surface layer was 25 mm.
【0016】鋼材FについてはZrをワイヤーによって
添加した。ワイヤーは5mm径で供給速度は3.5m/
分とした。また、比較材として、鋼材GはTi脱酸、鋼
材HはZr脱酸した溶鋼でそれぞれ単層の連続鋳造を行
った。得られた鋳片の厚み方向について表層から10,
50,125mmの各位置で粒径50μm以下の酸化物
個数をX線マイクロアナライザーを用いて調査した。[0016] Regarding steel material F, Zr was added using a wire. The wire has a diameter of 5mm and the feeding speed is 3.5m/
It was a minute. Further, as comparison materials, single-layer continuous casting was performed using molten steel that had been deoxidized with Ti for steel material G and deoxidized by Zr for steel material H. 10 from the surface layer in the thickness direction of the obtained slab
The number of oxides with a particle size of 50 μm or less was investigated at each position of 50 and 125 mm using an X-ray microanalyzer.
【0017】また、鋳片から12mm角60mm長さの
溶接再現熱サイクル処理用試料を採取し、最高加熱温度
が1350℃、800〜500℃の冷却時間が161s
ec 、相当入熱量が130kJ/cmの溶接再現熱サ
イクル処理を実施したのち、シャルピー試験により靭性
を評価した。[0017] In addition, a sample of 12 mm square and 60 mm length for welding reproduction heat cycle treatment was taken from the slab, and the maximum heating temperature was 1350°C, and the cooling time from 800 to 500°C was 161 seconds.
After carrying out a welding simulation thermal cycle treatment with an equivalent heat input of 130 kJ/cm, the toughness was evaluated by a Charpy test.
【0018】表1には各試料の破面遷移温度vTrsも
併せて示す。Table 1 also shows the fracture surface transition temperature vTrs of each sample.
【0019】[0019]
【表1】[Table 1]
【0020】[0020]
【表2】[Table 2]
【0021】図1は本発明材A、比較材G,Hの酸化物
分布を示した図である。この図から本発明材Aは鋳片厚
み方向のいずれの部分においても、比較材以上の十分な
酸化物個数が得られていることが確認できた。なお、表
1より本発明は低温靭性も比較材より優れており、酸化
物個数の均一性にも優れていることがわかる。FIG. 1 is a diagram showing the oxide distribution of the present invention material A and comparative materials G and H. From this figure, it was confirmed that material A of the present invention had a sufficient number of oxides than the comparative material in any part in the thickness direction of the slab. In addition, from Table 1, it can be seen that the low temperature toughness of the present invention is also superior to that of the comparative materials, and the uniformity of the number of oxides is also superior.
【0022】また、表2には、内層に添加する脱酸元素
を2種あるいはそれ以上添加した場合の結果を示す。Table 2 also shows the results when two or more types of deoxidizing elements were added to the inner layer.
【0023】[0023]
【表3】[Table 3]
【0024】[0024]
【表4】[Table 4]
【0025】これより、比較材Oのように、脱酸元素の
添加量の合計が0.05%を越えると低温靭性の低下を
招き、好ましくないことがわかった。その破面の観察か
ら、粒径50μmを越える大きさの酸化物クラスターが
靭性低下の原因であることを認めた。From this, it was found that, as in Comparative Material O, when the total amount of deoxidizing elements added exceeds 0.05%, this leads to a decrease in low temperature toughness, which is not preferable. From observation of the fracture surface, it was found that oxide clusters with a particle size exceeding 50 μm were the cause of the decrease in toughness.
【0026】[0026]
【発明の効果】本発明によって、多数の微細な酸化物が
鋼材中に均一に分散し、その結果、従来技術による方法
で製造するよりも、さらに低温靭性に優れた鋼材を得る
ことが可能となる。[Effects of the Invention] According to the present invention, a large number of fine oxides are uniformly dispersed in the steel material, and as a result, it is possible to obtain a steel material with even better low-temperature toughness than that produced by the conventional method. Become.
【図1】鋳片厚み方向の位置と酸化物個数の関係を本発
明材と比較材について示した図表である。FIG. 1 is a chart showing the relationship between the position in the slab thickness direction and the number of oxides for the present invention material and comparative material.
Claims (3)
なり、表層はTiを重量%で0.005%〜0.05%
含有した鋼で、内層はZr,Ca,Hf,Ce,Yのい
ずれか1種または2種以上の合計を0.005%〜0.
05%の範囲で含有した鋼であると共に、含有する酸化
物の最大粒径が50μm以下であり、該酸化物の(表層
部の個数)に対する(1/2厚部の個数)の比が60%
より大きいことを特徴とする低温靭性に優れた鋼材。Claim 1: Consisting of a surface layer and an inner layer having different components, the surface layer contains Ti in an amount of 0.005% to 0.05% by weight.
The inner layer contains one or more of Zr, Ca, Hf, Ce, and Y in a total amount of 0.005% to 0.00%.
05%, the maximum particle size of the contained oxide is 50 μm or less, and the ratio of the oxide (number in the 1/2 thick part) to (number in the surface layer) is 60 %
A steel material with excellent low-temperature toughness that is characterized by its larger size.
の直流磁束を全幅に亙って付与し、該直流磁束によって
鋳型上下方向に形成される静磁場帯を境界としてその上
下に組成の異なる金属を供給する複合鋼材の連続鋳造に
よる製造方法において、表層となる静磁場帯上側に注入
する溶鋼にTiが重量%で0.005%〜0.05%含
まれるように添加し、内層となる静磁場帯下側に注入す
る溶鋼にZr,Ca,Hf,Ce,Yのいずれか1種ま
たは2種以上の合計が0.005%〜0.05%の範囲
で含まれるように添加して鋳造することを特徴とする低
温靭性に優れた鋼材の製造方法。2. Direct current magnetic flux in the direction across the thickness of the slab is applied to the continuous casting mold over the entire width, and composition is applied above and below the static magnetic field zone formed by the direct current magnetic flux in the vertical direction of the mold. In a manufacturing method using continuous casting of a composite steel material that supplies different metals, Ti is added to the molten steel injected above the static magnetic field zone, which is the surface layer, so that it contains 0.005% to 0.05% by weight, and the inner layer is Addition of one or more of Zr, Ca, Hf, Ce, and Y in a total amount of 0.005% to 0.05% to the molten steel injected below the static magnetic field zone. A method for manufacturing steel materials with excellent low-temperature toughness, characterized by casting.
f,Ce,あるいはYを金属ワイヤーによって添加する
ことを特徴とする特許請求の範囲第2項記載の低温靭性
に優れた鋼材の製造方法。[Claim 3] Deoxidizing elements Ti, Zr, Ca, H
3. The method for manufacturing a steel material with excellent low-temperature toughness according to claim 2, characterized in that f, Ce, or Y is added using a metal wire.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
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JP8003291A JP2613699B2 (en) | 1991-04-12 | 1991-04-12 | Steel material excellent in low-temperature toughness and method for producing the same |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP8003291A JP2613699B2 (en) | 1991-04-12 | 1991-04-12 | Steel material excellent in low-temperature toughness and method for producing the same |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH04314844A true JPH04314844A (en) | 1992-11-06 |
JP2613699B2 JP2613699B2 (en) | 1997-05-28 |
Family
ID=13706928
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Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP8003291A Expired - Lifetime JP2613699B2 (en) | 1991-04-12 | 1991-04-12 | Steel material excellent in low-temperature toughness and method for producing the same |
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JP (1) | JP2613699B2 (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH07145450A (en) * | 1993-11-22 | 1995-06-06 | Nippon Steel Corp | Thin steel sheet in which surface and internal layers have different components and its production |
WO2003002771A1 (en) * | 2001-06-28 | 2003-01-09 | Nippon Steel Corporation | Low carbon steel sheet, low carbon steel cast piece and method for production thereof |
JP2008018453A (en) * | 2006-07-13 | 2008-01-31 | Sumitomo Metal Ind Ltd | Continuous casting method for molten metal, and immersion lance for continuous casting |
-
1991
- 1991-04-12 JP JP8003291A patent/JP2613699B2/en not_active Expired - Lifetime
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH07145450A (en) * | 1993-11-22 | 1995-06-06 | Nippon Steel Corp | Thin steel sheet in which surface and internal layers have different components and its production |
WO2003002771A1 (en) * | 2001-06-28 | 2003-01-09 | Nippon Steel Corporation | Low carbon steel sheet, low carbon steel cast piece and method for production thereof |
JPWO2003002771A1 (en) * | 2001-06-28 | 2004-10-21 | 新日本製鐵株式会社 | Low carbon steel sheet, low carbon steel slab, and method for producing the same |
AU2002313307B2 (en) * | 2001-06-28 | 2005-08-11 | Nippon Steel Corporation | Low carbon steel sheet, low carbon steel cast piece and method for production thereof |
US7347904B2 (en) | 2001-06-28 | 2008-03-25 | Nippon Steel Corporation | Low carbon steel sheet and low carbon steel slab and process for producing same |
US8048197B2 (en) | 2001-06-28 | 2011-11-01 | Nippon Steel Corporation | Low carbon steel sheet and low carbon steel slab and process for producing same |
JP2008018453A (en) * | 2006-07-13 | 2008-01-31 | Sumitomo Metal Ind Ltd | Continuous casting method for molten metal, and immersion lance for continuous casting |
Also Published As
Publication number | Publication date |
---|---|
JP2613699B2 (en) | 1997-05-28 |
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