JP4073059B2 - Fired magnesia-chromic brick - Google Patents
Fired magnesia-chromic brick Download PDFInfo
- Publication number
- JP4073059B2 JP4073059B2 JP27943697A JP27943697A JP4073059B2 JP 4073059 B2 JP4073059 B2 JP 4073059B2 JP 27943697 A JP27943697 A JP 27943697A JP 27943697 A JP27943697 A JP 27943697A JP 4073059 B2 JP4073059 B2 JP 4073059B2
- Authority
- JP
- Japan
- Prior art keywords
- brick
- magnesia
- zro
- cao
- furnace
- 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 - Fee Related
Links
Landscapes
- Compositions Of Oxide Ceramics (AREA)
Description
【0001】
【発明の属する技術分野】
本発明は、主にAOD炉に内張りされる焼成マグネシア−クロム質れんが(以下マグクロ質れんがと称す)に関するものである。
【0002】
【従来の技術】
炉外精錬炉の中でステンレス鋼を精錬するAOD炉は酸素吹き込みとArガス吹込みによる強攪拌による脱炭を主目的とする精錬炉であり、操業温度は最高1750℃、スラグ塩基度(CaO/SiO2)は1.0〜2.5程度の範囲で変動する。従ってAOD炉の内張り材として高耐食性かつ高熱間強度を有するマグクロ質れんがで、とりわけ緻密質な電融マグクロクリンカーを母材とするセミリボンド型マグクロ質れんがが最も優れた耐用を示している。他にはマグネシア−ドロマイト質、ダイレクトボンド型マグクロ質れんが等も挙げられるが、熱間強度が低いことやスラグ成分の変化等で大巾に低い耐用を示している。AOD炉において更なる耐用向上、あるいは特殊ステンレス鋼の精錬のために更に長時間、高温、強攪拌精錬の傾向を有しており、れんが特性としては益々熱間強度を高める必要性が生じている。
【0003】
この手法については最も有効的な手法としては焼成温度の上昇であるが一般的にトンネルキルンにおける温度の昇温・降温はトンネルキルンの短命を招き、品質のバラツキ、トンネルキルン自身の能力が限定されている等の理由で安易に焼成温度は上げられず、通常は1800℃程で焼成されている。従って、その温度域における改善が種々行われてきた。その一つとしては気孔を生じる天然クロム鉱石を減少させる。つまり電融マグクロクリンカー使用比率を増加させ緻密体とすることである。しかし、この方法は気孔率を減少させることは可能であるが、耐熱スポ−ルリング性を低下させ、総合的な効果が小さい結果となっている。その他の手法についても同様に効果は小さく、今後の操業の過酷化には対応できるものではない。従って、1800℃程の焼成温度で適正な気孔率を保持したままで焼結による結合を強化せしめる技術が必要である。
【0004】
【発明が解決しようとする課題】
主にAOD炉で使用されるセミリボンド型マグクロ質れんがの耐摩耗性、つまり熱間強度の向上を図ることを課題とした。
【0005】
【課題を解決するための手段】
電融マグクロクリンカーを主体とするセミリボンド型を基本配合として種々の添加物を検討した結果、ZrO2成分が最も強度が増加する傾向を示した。これはマトリックスの中のCaO成分とCaO・ZrO2を形成する為である。ZrO2成分はスラグ中のCaO成分とも容易にCaO・ZrO2を形成する可能性を持っており、CaO成分はマグクロ質れんがの組織を崩壊させる傾向を有しており、CaOの安定化をする必要性があると考えられた。
【0006】
そこで、超微粉域の活性品も検討し一般的な微粉とした。(表1)
添加量の増加に伴い熱間曲げ強さは増加した。但し焼成条件とれんが中の他成分との反応により各々のピーク添加量は異なり、粒径が小さいほど、少量添加で効果があった。これは、より活性が高いためCaO・ZrO2を形成安定化し、れんが中にCaOの浸透を抑制するためである。過剰の添加は、れんが中の他成分、SiO2と低融点化合物を形成し軟化してしまう。一方AOD炉の使用条件において重要な耐食性について高周波誘導炉内張り法にて評価した。はやりZrO2成分の添加はスラグ中のCaO成分と反応し、CaO・ZrO2を形成し、添加量とともに相関して増加する。但し、添加物の粒子径が小さい程強固な結合を生じているためSiO2との反応性が抑制されていると考えられる。
以上のことからZrO2成分の添加粒度はより小さく、より少量が望ましいが各々の上限を耐食性の低下を考慮すれば実施例の本発明品を表1No5〜No8の平均粒径15μm以下のZrO 2 微粉を添加量1〜7重量%と設定した。また、1重量%未満は効果が小さいので範囲外とした。尚、AOD炉用セミリボンド型のマグクロ質れんがにおいて電融マグクロクリンカ−を60重量%未満であると必然的にフラックス組成を含む天然クロム鉱石が増加することから、ZrO2成分の効果も無いため範囲外とした。
【0007】
【実施例】
本発明は焼成マグクロ質れんがを表1に示す配合比率で製造した。表1の一般品(基本配合)のマグクロ質及び比較品と同様に水系バインダ−を2重量%添加し、混合し、フリクションプレス又は油圧プレスにて成形、トンネルキルンで1800℃にて焼成した。物質特性値及び品質試験測定結果を表1に示す。
【0008】
【表1】
【0009】
【発明の効果】
実施例の本発明品を表1のNo6の平均粒径15μm以下のZrO2を、3重量%添加した焼成マグクロ質れんがを60tonAOD炉の羽口周辺及びスラグラインに一般品(基本配合)と張り分けテストした。実炉使用結果溶損量は一般品溶損量2.10mm/chに対し本発明品は1.82mm/chと約13%少なく大きな効果が認められた。[0001]
BACKGROUND OF THE INVENTION
The present invention mainly relates to a fired magnesia-chromic brick (hereinafter referred to as magchromatic brick) lined in an AOD furnace.
[0002]
[Prior art]
The AOD furnace for refining stainless steel in the out-of-furnace refining furnace is a refining furnace whose main purpose is decarburization with strong stirring by oxygen blowing and Ar gas blowing. The operating temperature is up to 1750 ° C, slag basicity (CaO / SiO 2 ) varies in the range of about 1.0 to 2.5. Therefore, magchromic bricks having high corrosion resistance and high hot strength as lining materials for AOD furnaces, especially semi-ribboned magchromic bricks based on a dense electrofused magcroclinker, exhibit the best durability. Other examples include magnesia-dolomite and direct bond-type magchrom bricks, which show a significantly low durability due to low hot strength and changes in slag components. In the AOD furnace, there is a tendency for high-temperature, strong stirring refining for a longer time for further improvement of durability or refining of special stainless steel, and there is a need to increase hot strength as a brick property. .
[0003]
For this method, the most effective method is to raise the firing temperature, but generally the temperature rise / fall in the tunnel kiln leads to short life of the tunnel kiln, resulting in variations in quality and the ability of the tunnel kiln itself to be limited. For example, the firing temperature cannot be easily increased, and the firing is usually performed at about 1800 ° C. Accordingly, various improvements in the temperature range have been made. One is to reduce the natural chromium ore that produces pores. In other words, it is to increase the usage ratio of electrofused magcro clinker to make a dense body. However, although this method can reduce the porosity, the heat resistant sparkling property is lowered and the overall effect is small. The other methods are similarly less effective and cannot cope with the severe operation of the future. Therefore, there is a need for a technique for strengthening the bonding by sintering while maintaining an appropriate porosity at a firing temperature of about 1800 ° C.
[0004]
[Problems to be solved by the invention]
It was an object to improve the wear resistance, that is, the hot strength, of semi-ribboned type bricks mainly used in AOD furnaces.
[0005]
[Means for Solving the Problems]
As a result of examining various additives based on a semi-ribboned type mainly composed of an electrofused magcro clinker, the ZrO 2 component tended to increase in strength most. This is because the CaO component in the matrix and CaO.ZrO 2 are formed. The ZrO 2 component has the possibility of easily forming CaO · ZrO 2 with the CaO component in the slag, and the CaO component has a tendency to collapse the structure of the macular brick and stabilizes the CaO. It was considered necessary.
[0006]
Therefore, an active product in the ultrafine powder region was also examined to obtain a general fine powder. (Table 1)
The hot bending strength increased with the addition amount. However, the amount of each peak added differs depending on the firing conditions and the reaction with other components in the brick. The smaller the particle size, the more effective the addition. This is because the activity is higher and CaO · ZrO 2 is formed and stabilized, and the penetration of CaO into the brick is suppressed. Excessive addition forms other components in the brick, SiO 2 and a low melting point compound, and softens. On the other hand, the corrosion resistance important in the use conditions of the AOD furnace was evaluated by the high frequency induction furnace lining method. The addition of ZrO 2 component reacts with the CaO component in the slag to form CaO · ZrO 2 , which increases in correlation with the added amount. However, it is considered that the reactivity with SiO 2 is suppressed because the smaller the particle diameter of the additive is, the stronger the bond is formed.
In view of the above, the added particle size of the ZrO 2 component is smaller, and a smaller amount is desirable. However, considering the lowering of the corrosion resistance, the upper limit of each is ZrO 2 with the average particle size of 15 μm or less in Table 1 No5 to No8. The fine powder was set to 1 to 7 % by weight. Also, if less than 1% by weight, the effect is small, so it was out of range. In addition, since the amount of natural chromium ore containing the flux composition inevitably increases when the amount of the electrofused magcrocliner in the semi-ribbon type brick for AOD furnace is less than 60% by weight, there is no effect of the ZrO 2 component. Out of range.
[0007]
【Example】
In the present invention, baked mug brick was produced at a blending ratio shown in Table 1. In the same manner as in the general product (basic composition) of Table 1 and the comparative product, 2% by weight of an aqueous binder was added, mixed, molded with a friction press or a hydraulic press, and fired at 1800 ° C. with a tunnel kiln. Table 1 shows the material property values and the quality test measurement results.
[0008]
[Table 1]
[0009]
【The invention's effect】
Inventive products of the examples were baked mug bricks added with 3% by weight of No. 6 of ZrO 2 having an average particle size of 15 μm or less in Table 1 with a general product (basic composition) around the tuyere and slag line of a 60 ton AOD furnace. Tested separately. As a result of using the actual furnace, the amount of erosion caused by the present furnace was 1.82 mm / ch, which was about 13% less than that of the general product erosion amount 2.10 mm / ch.
Claims (1)
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP27943697A JP4073059B2 (en) | 1997-09-26 | 1997-09-26 | Fired magnesia-chromic brick |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP27943697A JP4073059B2 (en) | 1997-09-26 | 1997-09-26 | Fired magnesia-chromic brick |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH11100254A JPH11100254A (en) | 1999-04-13 |
JP4073059B2 true JP4073059B2 (en) | 2008-04-09 |
Family
ID=17611051
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP27943697A Expired - Fee Related JP4073059B2 (en) | 1997-09-26 | 1997-09-26 | Fired magnesia-chromic brick |
Country Status (1)
Country | Link |
---|---|
JP (1) | JP4073059B2 (en) |
Families Citing this family (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102295461B (en) * | 2011-06-02 | 2013-10-30 | 江苏君耀耐磨耐火材料有限公司 | Red brick for petrochemical heater and preparation process thereof |
-
1997
- 1997-09-26 JP JP27943697A patent/JP4073059B2/en not_active Expired - Fee Related
Also Published As
Publication number | Publication date |
---|---|
JPH11100254A (en) | 1999-04-13 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP4527905B2 (en) | Castable refractories for blast furnace firewood | |
JP4073059B2 (en) | Fired magnesia-chromic brick | |
JPH0118030B2 (en) | ||
JPH082975A (en) | Refractory for casting application | |
JP2022060911A (en) | Method of producing lf-ladle magnesia-carbon brick | |
JP2000178074A (en) | Castable refractory for blast furnace tapping spout | |
JPH06345550A (en) | Castable refractory | |
JPH11100255A (en) | Burned magnesia-chrome brick | |
JPH10287466A (en) | Burned magnesia-chrome brick | |
JPH11100256A (en) | Burned magnesia-chrome brick | |
JP2868809B2 (en) | Magnesia carbon brick | |
JP2951430B2 (en) | Fired magnesia spinel brick | |
KR100203460B1 (en) | A brick | |
RU1768560C (en) | Fettling material | |
JPH03141152A (en) | Carbon-containing unburned refractory brick | |
JPH06172044A (en) | Castable refractory of alumina spinel | |
JP2922998B2 (en) | Irregular refractories for blast furnace gutters | |
JPH0782004A (en) | Refractory for furnace bed of converter made of stainless steel | |
JPH07108804B2 (en) | Process for producing unfired magnesia-carbon brick | |
JP3400494B2 (en) | Basic refractories for molten metal | |
JPH07110792B2 (en) | Basic amorphous refractory | |
JPH0867572A (en) | Refractory for casting execution | |
JP2000128624A (en) | Basic refractory | |
RU2574236C2 (en) | Fused refractory material | |
JPH0637334B2 (en) | Castable refractory for molten steel ladle floor |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20040917 |
|
A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20070614 |
|
A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20070618 |
|
A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20070806 |
|
A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20071211 |
|
A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20071211 |
|
TRDD | Decision of grant or rejection written | ||
A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20080122 |
|
A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20080122 |
|
FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20110201 Year of fee payment: 3 |
|
R150 | Certificate of patent or registration of utility model |
Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20110201 Year of fee payment: 3 |
|
FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20120201 Year of fee payment: 4 |
|
FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20120201 Year of fee payment: 4 |
|
FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130201 Year of fee payment: 5 |
|
FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20140201 Year of fee payment: 6 |
|
R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
LAPS | Cancellation because of no payment of annual fees |