JPH0319183B2 - - Google Patents
Info
- Publication number
- JPH0319183B2 JPH0319183B2 JP58166197A JP16619783A JPH0319183B2 JP H0319183 B2 JPH0319183 B2 JP H0319183B2 JP 58166197 A JP58166197 A JP 58166197A JP 16619783 A JP16619783 A JP 16619783A JP H0319183 B2 JPH0319183 B2 JP H0319183B2
- Authority
- JP
- Japan
- Prior art keywords
- powder
- nozzle
- carbon black
- graphite
- continuous casting
- 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
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 17
- 239000006229 carbon black Substances 0.000 claims description 16
- 238000009749 continuous casting Methods 0.000 claims description 13
- 239000000203 mixture Substances 0.000 claims description 13
- 229910002804 graphite Inorganic materials 0.000 claims description 10
- 239000010439 graphite Substances 0.000 claims description 10
- 229910052799 carbon Inorganic materials 0.000 claims description 8
- 239000002245 particle Substances 0.000 claims description 4
- MCMNRKCIXSYSNV-UHFFFAOYSA-N ZrO2 Inorganic materials O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 claims description 3
- 238000010521 absorption reaction Methods 0.000 claims description 3
- 239000000843 powder Substances 0.000 description 22
- 230000003628 erosive effect Effects 0.000 description 12
- 229910000831 Steel Inorganic materials 0.000 description 11
- 230000007797 corrosion Effects 0.000 description 11
- 238000005260 corrosion Methods 0.000 description 11
- 239000010959 steel Substances 0.000 description 11
- 239000000463 material Substances 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 7
- 239000011230 binding agent Substances 0.000 description 6
- 239000002893 slag Substances 0.000 description 6
- 238000004901 spalling Methods 0.000 description 6
- 238000004090 dissolution Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 238000010828 elution Methods 0.000 description 4
- 239000005011 phenolic resin Substances 0.000 description 4
- 150000001875 compounds Chemical class 0.000 description 3
- 238000007654 immersion Methods 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 238000000465 moulding Methods 0.000 description 3
- 229910018125 Al-Si Inorganic materials 0.000 description 2
- 229910018520 Al—Si Inorganic materials 0.000 description 2
- 229910000655 Killed steel Inorganic materials 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000004898 kneading Methods 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 239000011148 porous material Substances 0.000 description 2
- 239000011819 refractory material Substances 0.000 description 2
- 239000011863 silicon-based powder Substances 0.000 description 2
- 229910017082 Fe-Si Inorganic materials 0.000 description 1
- 229910017133 Fe—Si Inorganic materials 0.000 description 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 1
- 241000872198 Serjania polyphylla Species 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 229910003564 SiAlON Inorganic materials 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- RHZUVFJBSILHOK-UHFFFAOYSA-N anthracen-1-ylmethanolate Chemical compound C1=CC=C2C=C3C(C[O-])=CC=CC3=CC2=C1 RHZUVFJBSILHOK-UHFFFAOYSA-N 0.000 description 1
- 239000003830 anthracite Substances 0.000 description 1
- 150000001639 boron compounds Chemical class 0.000 description 1
- 239000011449 brick Substances 0.000 description 1
- 238000003763 carbonization Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003245 coal Substances 0.000 description 1
- 239000000571 coke Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 239000003822 epoxy resin Substances 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 229910001337 iron nitride Inorganic materials 0.000 description 1
- XWHPIFXRKKHEKR-UHFFFAOYSA-N iron silicon Chemical compound [Si].[Fe] XWHPIFXRKKHEKR-UHFFFAOYSA-N 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 229910003465 moissanite Inorganic materials 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 150000002989 phenols Chemical class 0.000 description 1
- 239000011295 pitch Substances 0.000 description 1
- 229920000647 polyepoxide Polymers 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- 229910010271 silicon carbide Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Continuous Casting (AREA)
- Compositions Of Oxide Ceramics (AREA)
Description
〔産業上の利用分野〕
本発明は、連続鋳造用パウダ溶融物に対する耐
食性に優れた連続鋳造用ノズル組成物に関する。
〔技術的背景〕
連続鋳造用ノズルの組成物として広く使用され
ているZrO2−鱗状黒鉛−SiもしくはSiC系の黒
鉛・ジルコニア質耐火物は、溶鋼の鋳造に使用さ
れるパウダの溶融物に対する耐食性が良好である
ことは良く知られている。この系の耐火物におい
て、ZrO2の含有量を上げると耐食性は向上する
が、ZrO2が高熱膨張性を持つために耐スポーリ
ング性が低下して操業時の安全性を低下し、さら
には、製造のコストアツプを齎すという問題があ
る。
他方、パウダ溶融物による連続鋳造用ノズルの
溶損は、単純にパウダ溶融物とノズルとの接触部
分に起こるのではなく、パウダ溶融部と溶鋼部の
境界で起る界面現象によるものであり、鱗状黒
鉛、バインダからくるカーボン、SiCが溶鋼中に
溶解し、それらの溶解に伴い組織の劣化が生じ、
それからZrO2粒のパウダ溶融物中への溶解が進
行することによるものと考えられている。
このように、連続鋳造用ノズルの損耗はカーボ
ンの溶鋼への溶解速度に律速されており、ノズル
のライフの向上を図るためにはカーボンの溶鋼中
への溶解を出来るだけ小さくしなければならな
い。
かかる見地から本発明者等は種々のカーボンの
特性を実験によつて比較検討した。
実験は、350メツシユ以下のSi粉60wt％に各種
カーボンを40wt％混合し、これにバインダとし
てフエノールレジンを外掛10wt％（仮燃無煙炭
の場合は外掛5wt％）添加混練して試料を作製し
て、電解鉄2.5Kgと高炉スラグ：転炉スラグ＝
１：１の混合スラグ125Kgの1600℃の溶湯のスラ
グ−メタル境界面に20分間暴露して溶損量を調べ
た。
[Industrial Field of Application] The present invention relates to a nozzle composition for continuous casting that has excellent corrosion resistance against powder melt for continuous casting. [Technical background] ZrO 2 -scale graphite-Si or SiC-based graphite/zirconia refractories, which are widely used as a composition for continuous casting nozzles, have excellent corrosion resistance against powder melts used for casting molten steel. is well known to be good. In this type of refractory, increasing the ZrO 2 content improves corrosion resistance, but because ZrO 2 has high thermal expansion, spalling resistance decreases, reducing operational safety, and However, there is a problem in that it increases manufacturing costs. On the other hand, erosion of a continuous casting nozzle due to powder melt does not simply occur at the contact area between the powder melt and the nozzle, but is due to an interfacial phenomenon that occurs at the boundary between the powder melt part and the molten steel part. Scale graphite, carbon from the binder, and SiC dissolve in molten steel, and as they dissolve, the structure deteriorates.
This is thought to be due to the progress of dissolution of the two ZrO grains into the powder melt. As described above, the wear and tear of continuous casting nozzles is determined by the rate of dissolution of carbon into molten steel, and in order to improve the life of the nozzle, it is necessary to minimize the dissolution of carbon into molten steel. From this standpoint, the present inventors conducted comparative studies on the properties of various carbons through experiments. In the experiment, a sample was prepared by mixing 40 wt% of various types of carbon with 60 wt% of Si powder of 350 mesh or less, and adding and kneading 10 wt% of phenol resin as a binder (5 wt% of outer layer in the case of pre-combusted anthracite coal). , 2.5Kg of electrolytic iron and blast furnace slag: converter slag =
The amount of corrosion loss was examined by exposing 125 kg of 1:1 mixed slag to the slag-metal interface of 1600°C molten metal for 20 minutes.
本発明は、溶鋼への溶解（溶出）速度が小さい
カーボンブラツクを使用した連続鋳造用ノズルの
組成物を提供することを目的とする。
〔発明の構成〕
前記の実験結果から明らかなように、カーボン
ブラツクは溶鋼への溶解（溶出）速度が小さく、
パウダ溶融部と溶鋼部の境界で起る界面現象によ
る連続鋳造用ノズルの溶損を著しく減少させる。
しかしながら、カーボンブラツクを含有する耐火
物は成形性が悪く、また耐スポーリング性に対し
ては、マイナス因子として作用するという欠点が
ある。
本発明は、かかるカーボンブラツクを連続鋳造
用ノズルの組成物に使用するに当たつての欠点
は、鱗状黒鉛とカーボンブラツクを組合せて使用
することによつて解消されるという知見に基づく
ものである。
この組合せ使用によつて、比表面積の大きいカ
ーボンブラツクが鱗状黒鉛とバインダカーボンの
表面を被覆して、これらの鱗状黒鉛とバインダカ
ーボンの溶出を遅延させて、溶鋼−パウダ界面で
の損耗を減少させる。これによつて前記ZrO2−
鱗状黒鉛−SiもしくはSiC系耐火物中のZrO2の含
有量をいたずらに上げることなく、耐食性と耐ス
ポーリング性を兼備した連続鋳造用ノズルを得る
ことが可能となつた。
本発明における組成物の特性は、使用するカー
ボンブラツクの粒径と吸湯量に影響される。
カーボンブラツクの粒径は、50ｍμを超えると
ノズルれんがの気孔中に入り込みにくく、前記の
カーボンブラツクによる効果が充分でないので50
ｍμ以下であることが望ましい。
カーボンブラツクの吸油量は、カーボンブラツ
クの分散に影響を与え、1.5ml／ｇを超えるとバ
インダに対する分散性が悪く、カーボンブラツク
の凝集が起こり、気孔中に均一に入り込まなくな
り、充分にカーボンブラツクの効果は発揮できな
くなる。
カーボンブラツクの添加量について言えば、全
量に対して0.5wt％未満ではその効果は認められ
ず、5wt％を超えるとカーボンブラツクが組織劣
化をもたらし耐食性が低下するので、0.5〜5wt％
の範囲内にする必要がある。
また、本発明において使用するZrO2について
言えば、粉末の粒度構成において、10μ以下が
10wt％以上ないと耐食性は充分ではなく、50wt
％を超えると対スポーリング性を低下させる。
ZrO2粉末の量が全量に対して60wt％未満では耐
食性が充分でなく、92wt％を超えると耐スポー
リング性に問題を生じる。
鱗状黒鉛は、その添加量が3wt％未満の場合に
は耐スポーリング性が劣化し、38wt％を超える
と耐食性が充分でなくなる。
固定カーボン量が85wt％未満では灰分量が多
くなり耐食性が低下し問題である。Siとしては、
金属シリコン粉末の他に、Fe−Si、Al−Si等の
シリコン合金粉末、SiC粉末、窒化珪素鉄、サイ
アロン、Si3N4粉末の中の１種、又は２種以上の
混合粉末を用いることができる。その添加量は全
量に対して1wt％未満では、強度、耐酸化性が充
分でなく、10wt％を超えると耐溶鋼性が低下し
て、結果として耐食性の低下をもたらす。
なお、耐酸化性が不足の場合には、必要に応じ
て、B4C、BN等の硼素化合物を少量添加しても
よい。
また、本発明の組成物の成形に当たつてのバイ
ンダとしては、混練時及び成形時の作業性、コス
ト、炭化収率のバランスの点から、フエノールレ
ジンが好適に使用できるが、その他、炭化収率の
高いレジン例えばピツチ、ピツチ変成フエノール
レジン、ピツチとフエノールレジンの併用、エポ
キシレジン等任意に使用できる。
〔実施例〕
以下実施例によつて本発明の詳細を説明する。
表２に示す組成と性質とを持つ配合物を部分的
に用いて第１図〜第３図に示すテスト用のノズル
１を作製した。各図において、ノズル１の母材３
はアルミナ−黒鉛からなる通常の材質のものを使
用し、前記の表２に示す組成と性質とを持つ配合
物の供試材をパウダライン部分４に使用してラバ
ープレスによつて一体成形後、1000℃でコーク
ス・ブリーズ中還元焼成して、内孔２を有するテ
スト用のノズルを作製した。第１図および第２図
は、浸漬ノズルであり、第３図に示すものはロン
グノズルである。
〔テスト１〕
母材３の肉厚が40mm、パウダライン部分４の厚
みが20mmの第１図に示すような形状を持つ浸漬ノ
ズル１を300t取鍋用２ストランドタイプタンデイ
シユに適用してAl−キルド鋼用に供した。ノズ
ルの交換の原因は、パウダライン部の溶損による
ものであつた。表２の１〜表２の２に各配合物の
実績を溶損速度指数によつて示す。同溶損速度指
数は、パウダライン部の直径を使用後測定し、溶
損速度（mm／min）を求め、比較例１として示す
従来品の場合の溶損速度を100として指数化した
ものである。
溶損指数が80以上のものについては、耐溶損性
の改良が少ないということで５本に試験を中止
し、他は10本使用した。
比較例３、９、12については、溶損量自体は少
なく示されているが、使用初期に亀裂が発生して
交換された結果であつて、実質的にはライフ延長
は図れなかつた。
〔テスト２〕
第２図に示す形状を持ち、母材３の厚みと供試
材のパウダライン部分４の厚みが35mmの浸漬ノズ
ル１を250t取鍋溶４ストランドタイプタンデイシ
ユに適用してAl−Siキルド鋼用に供した。
表２に示す実施例１と比較例２のものを使用し
たが、実施例１のものは20本問題なく使用され、
比較例２のものは５本中３本が亀裂発生により使
用初期に交換された。
溶損速度を比較したところ、比較例２のものを
100として指数化すると、実施例１はパウダライ
ン部で65、内孔部で86であつた。
〔テスト３〕
第３図に示す形状を持つ母材３の肉厚45mm、ス
ラグライン部分４の厚みが25mmのロングノズル１
を260t取鍋用に供した。
表２の比較例１のものを使用した場合には、ス
ラグライン部の溶損により６回のチヤージが限界
であつたが、実施例４のものを使用することで目
標の９回のチヤージを達成でき、その後も残厚が
あり、さらに、ライフの延長の可能性が示され
た。
上記のテストでは、部分的に本発明の組成物を
用いたが、実用に当つては上記テストの場合のよ
うに、パウダラインあるいはスラグラインのみに
使用しても充分効果があるし、またノズル全体を
同組成物によつて構成してもよい。
〔発明の効果〕
このように、本発明にかかる組成物は、溶鋼へ
の溶出速度が小さく、パウダ溶融部と溶鋼部の境
界で起る界面現象に基づく連続鋳造用ノズルの溶
損現象を効果的に防止するカーボンブラツクを、
成形性を劣化することなく添加でき、それによつ
て、連続鋳造用ノズルのライフを延長できるとい
う効果を奏する。
An object of the present invention is to provide a composition for a continuous casting nozzle using carbon black, which has a low dissolution (elution) rate into molten steel. [Structure of the Invention] As is clear from the above experimental results, carbon black has a low dissolution (elution) speed into molten steel;
Significantly reduces erosion of continuous casting nozzles due to interface phenomena that occur at the boundary between the powder molten zone and the molten steel zone.
However, refractories containing carbon black have poor moldability and have a negative effect on spalling resistance. The present invention is based on the finding that the disadvantages of using such carbon black in the composition of continuous casting nozzles can be overcome by using a combination of flaky graphite and carbon black. . By using this combination, carbon black with a large specific surface area coats the surfaces of scale graphite and binder carbon, delaying the elution of these scale graphite and binder carbon, and reducing wear at the molten steel-powder interface. . This results in the ZrO 2 −
It has become possible to obtain a continuous casting nozzle that has both corrosion resistance and spalling resistance without unnecessarily increasing the ZrO 2 content in the scale graphite-Si or SiC-based refractory. The properties of the composition according to the invention are influenced by the particle size and water absorption amount of the carbon black used. If the particle size of carbon black exceeds 50 mμ, it will be difficult to enter the pores of the nozzle brick, and the effect of the carbon black described above will not be sufficient.
It is desirable that it be less than mμ. The oil absorption amount of carbon black affects the dispersion of carbon black, and if it exceeds 1.5 ml/g, the dispersibility in the binder will be poor, carbon black will aggregate, and it will not be able to enter the pores uniformly. It will no longer be effective. Regarding the amount of carbon black added, if it is less than 0.5wt% of the total amount, no effect will be observed, and if it exceeds 5wt%, carbon black will cause structural deterioration and reduce corrosion resistance, so 0.5 to 5wt%.
Must be within the range. Regarding ZrO 2 used in the present invention, in the particle size structure of the powder, 10μ or less is
Corrosion resistance is not sufficient unless it is 10wt% or more, and 50wt%
If it exceeds %, anti-spalling properties will be reduced.
If the amount of ZrO 2 powder is less than 60 wt% of the total amount, corrosion resistance will not be sufficient, and if it exceeds 92 wt%, problems will arise in spalling resistance. When the amount of graphite added is less than 3 wt%, spalling resistance deteriorates, and when it exceeds 38 wt%, corrosion resistance becomes insufficient. If the amount of fixed carbon is less than 85 wt%, the amount of ash increases and corrosion resistance decreases, which is a problem. As Si,
In addition to metal silicon powder, use one type of silicon alloy powder such as Fe-Si, Al-Si, SiC powder, silicon iron nitride, SiAlON, Si 3 N 4 powder, or a mixed powder of two or more types. Can be done. If the amount added is less than 1wt% of the total amount, the strength and oxidation resistance will not be sufficient, and if it exceeds 10wt%, the resistance of molten steel will decrease, resulting in a decrease in corrosion resistance. Note that if the oxidation resistance is insufficient, a small amount of a boron compound such as B 4 C or BN may be added as necessary. In addition, as a binder for molding the composition of the present invention, phenol resin can be suitably used from the viewpoint of workability during kneading and molding, cost, and carbonization yield balance, but other Any resin with a high yield, such as pitch, modified phenol resin, a combination of pitch and phenol resin, or epoxy resin can be used. [Example] The details of the present invention will be explained below with reference to Examples. A test nozzle 1 shown in FIGS. 1 to 3 was prepared by partially using a compound having the composition and properties shown in Table 2. In each figure, the base material 3 of the nozzle 1
A normal material consisting of alumina-graphite was used, and a test material of a compound having the composition and properties shown in Table 2 was used for the powder line part 4, and after integral molding with a rubber press. A test nozzle having an inner hole 2 was prepared by reduction firing in a coke breeze at 1000°C. 1 and 2 are submerged nozzles, and the nozzle shown in FIG. 3 is a long nozzle. [Test 1] An immersion nozzle 1 having a shape as shown in Fig. 1 in which the base material 3 has a wall thickness of 40 mm and the powder line portion 4 has a thickness of 20 mm was applied to a two-strand type tundish for a 300-ton ladle. It was used for Al-killed steel. The reason for replacing the nozzle was due to erosion of the powder line. Table 2-1 to Table 2-2 show the results of each compound in terms of erosion rate index. The erosion rate index is calculated by measuring the diameter of the powder line part after use, determining the erosion rate (mm/min), and converting it into an index by setting the erosion rate of the conventional product shown as Comparative Example 1 as 100. be. For those with an erosion index of 80 or higher, the test was stopped at 5 pieces because the improvement in erosion resistance was small, and 10 pieces were used for the others. Regarding Comparative Examples 3, 9, and 12, the amount of erosion itself is shown to be small, but this is the result of cracks occurring in the early stages of use and replacement, and the life could not be substantially extended. [Test 2] An immersion nozzle 1 having the shape shown in Fig. 2, in which the thickness of the base material 3 and the thickness of the powder line portion 4 of the test material are 35 mm, was applied to a 250-ton ladle-molded 4-strand type tundish. It was used for Al-Si killed steel. The products of Example 1 and Comparative Example 2 shown in Table 2 were used, and 20 products of Example 1 were used without any problem.
In Comparative Example 2, 3 out of 5 were replaced at the beginning of use due to cracking. When comparing the erosion rate, it was found that those of Comparative Example 2
When expressed as an index of 100, Example 1 had an index of 65 in the powder line area and 86 in the inner hole area. [Test 3] Long nozzle 1 having the shape shown in Fig. 3, with a base material 3 having a wall thickness of 45 mm and a slug line portion 4 having a thickness of 25 mm.
was used for a 260t ladle. When Comparative Example 1 in Table 2 was used, the limit was 6 charges due to melting of the slag line, but by using Example 4, the target 9 charges could be achieved. This was achieved, and there was still some residual thickness, indicating the possibility of extending the life. In the above test, the composition of the present invention was partially used, but in practice, as in the case of the above test, it is sufficiently effective even when used only on the powder line or slag line, and also on the nozzle. The whole may be composed of the same composition. [Effects of the Invention] As described above, the composition according to the present invention has a low elution rate into molten steel, and is effective in reducing the erosion phenomenon of continuous casting nozzles caused by the interface phenomenon that occurs at the boundary between the powder molten part and the molten steel part. carbon black that prevents
It can be added without deteriorating the moldability, which has the effect of extending the life of the continuous casting nozzle.
第１〜第３図は本発明の組成物を適用した供試
用の連続鋳造用ノズルの構造を示す。
１：浸漬ノズル、１′：ロングノズル、２：内
孔部分、３：母材、４：パウダラインまたはスラ
グライン部分。
1 to 3 show the structure of a test nozzle for continuous casting to which the composition of the present invention is applied. 1: Immersion nozzle, 1': Long nozzle, 2: Inner hole portion, 3: Base material, 4: Powder line or slag line portion.
Claims (1)
1.5ml／ｇ以下であるカーボンブラツクを0.5〜
5wt％の黒鉛を含有する黒鉛・ジルコニア質耐火
物において、前記黒鉛が85wt％以上の固定カー
ボンを有する鱗状黒鉛であることを特徴とする連
続鋳造用ノズル組成物。1 The average particle size is 50mμ or less, and the oil absorption is
0.5~1.5ml/g or less of carbon black
A nozzle composition for continuous casting in a graphite-zirconia refractory containing 5 wt% graphite, characterized in that the graphite is scaly graphite having 85 wt% or more of fixed carbon.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP58166197A JPS6060978A (en) | 1983-09-08 | 1983-09-08 | Nozzle composition for continuous casting |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP58166197A JPS6060978A (en) | 1983-09-08 | 1983-09-08 | Nozzle composition for continuous casting |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6060978A JPS6060978A (en) | 1985-04-08 |
| JPH0319183B2 true JPH0319183B2 (en) | 1991-03-14 |
Family
ID=15826886
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP58166197A Granted JPS6060978A (en) | 1983-09-08 | 1983-09-08 | Nozzle composition for continuous casting |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6060978A (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6424069A (en) * | 1987-07-15 | 1989-01-26 | Kurosaki Refractories Co | Brick of sliding nozzle plate for special steel |
| JP2001037295A (en) * | 1999-07-15 | 2001-02-09 | Hitachi Ltd | Control of induction machine |
| JP2009221031A (en) * | 2008-03-13 | 2009-10-01 | Kurosaki Harima Corp | Zirconia-carbon-containing refractory and method for producing the same |
| JP6148476B2 (en) * | 2013-01-25 | 2017-06-14 | 新日鐵住金株式会社 | Zirconia-carbon-containing refractory and immersion nozzle for continuous casting of steel, and zirconia-carbon-containing refractory manufacturing method and steel continuous casting immersion nozzle |
-
1983
- 1983-09-08 JP JP58166197A patent/JPS6060978A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6060978A (en) | 1985-04-08 |
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