JPH03189055A - Manufacture of refractory for continuous casting - Google Patents
Manufacture of refractory for continuous castingInfo
- Publication number
- JPH03189055A JPH03189055A JP1325323A JP32532389A JPH03189055A JP H03189055 A JPH03189055 A JP H03189055A JP 1325323 A JP1325323 A JP 1325323A JP 32532389 A JP32532389 A JP 32532389A JP H03189055 A JPH03189055 A JP H03189055A
- Authority
- JP
- Japan
- Prior art keywords
- mgo
- refractory
- aggregate
- zro2
- parts
- 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
- 238000009749 continuous casting Methods 0.000 title claims abstract description 11
- 238000004519 manufacturing process Methods 0.000 title claims description 9
- 239000011819 refractory material Substances 0.000 claims abstract description 25
- 238000010304 firing Methods 0.000 claims abstract description 9
- 239000002994 raw material Substances 0.000 claims abstract description 8
- 238000000034 method Methods 0.000 claims abstract description 7
- 238000004898 kneading Methods 0.000 claims abstract 2
- 239000002245 particle Substances 0.000 claims description 16
- 238000000465 moulding Methods 0.000 claims description 2
- MCMNRKCIXSYSNV-UHFFFAOYSA-N ZrO2 Inorganic materials O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 abstract description 38
- 230000007797 corrosion Effects 0.000 abstract description 12
- 238000005260 corrosion Methods 0.000 abstract description 12
- 230000035939 shock Effects 0.000 abstract description 11
- 239000011230 binding agent Substances 0.000 abstract description 4
- 229910052799 carbon Inorganic materials 0.000 description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical compound [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 description 5
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 4
- 238000005452 bending Methods 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 238000007796 conventional method Methods 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910052596 spinel Inorganic materials 0.000 description 3
- 239000011029 spinel Substances 0.000 description 3
- 229910052581 Si3N4 Inorganic materials 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- QDOXWKRWXJOMAK-UHFFFAOYSA-N dichromium trioxide Chemical compound O=[Cr]O[Cr]=O QDOXWKRWXJOMAK-UHFFFAOYSA-N 0.000 description 2
- 235000012245 magnesium oxide Nutrition 0.000 description 2
- 239000000395 magnesium oxide Substances 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 2
- 229910010271 silicon carbide Inorganic materials 0.000 description 2
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000008646 thermal stress Effects 0.000 description 2
- 210000001519 tissue Anatomy 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- WGLPBDUCMAPZCE-UHFFFAOYSA-N Trioxochromium Chemical compound O=[Cr](=O)=O WGLPBDUCMAPZCE-UHFFFAOYSA-N 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- 229910000423 chromium oxide Inorganic materials 0.000 description 1
- 210000002808 connective tissue Anatomy 0.000 description 1
- 230000008602 contraction Effects 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 238000005470 impregnation Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 239000003870 refractory metal Substances 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 238000004901 spalling Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Casting Support Devices, Ladles, And Melt Control Thereby (AREA)
- Compositions Of Oxide Ceramics (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明は、連続鋳造の鋳型とタンデイシエとの間に介在
されるスライドゲート、ノズル等の連続鋳造用耐火物の
製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention relates to a method for producing refractories for continuous casting, such as slide gates and nozzles, which are interposed between a continuous casting mold and a tandem.
［従来の技術］
通常、連続鋳造用耐火物としては、ＭｇＯ（マグネシア
）を含むＭｇＯ系耐火物が、溶鋼との接触角が大きいこ
とから、他の材質に比べ高耐食性を期待でき、広く用い
られている。[Prior Art] Usually, MgO-based refractories containing MgO (magnesia) are widely used as refractories for continuous casting because they have a large contact angle with molten steel and are expected to have higher corrosion resistance than other materials. It is being
しかし、ＭｇＯ系耐火物は、熱膨張率が大きいことから
、熱衝撃抵抗性に劣る欠点がある。However, MgO-based refractories have a drawback of poor thermal shock resistance due to their large coefficient of thermal expansion.
従来、上記欠点に対処するため、
（１）ＭｇＯ系骨材の他にＣ（カーボン）を多量に耐火
物骨材として含有させ、熱膨張率を低くあるいは熱伝導
性をよくしたり、
（２）単斜晶型ＺｒＯ２（ジルコニア）骨材を併用し、
耐火物製造時にマトリックス中にマイクロクラックを得
る。Conventionally, in order to deal with the above drawbacks, (1) in addition to MgO-based aggregates, a large amount of C (carbon) was contained as a refractory aggregate to lower the coefficient of thermal expansion or improve thermal conductivity; (2) ) Monoclinic type ZrO2 (zirconia) aggregate is used in combination,
Microcracks are obtained in the matrix during refractory production.
等の方法により、熱ｍ撃抵抗性の向上を図る連続鋳造用
耐火物の製造方法が考えられている。Methods for producing continuous casting refractories that improve thermal shock resistance have been considered.
［発明が解決しようとする課題］
しかしながら、多量のＣを耐火物骨材として併用する従
来の製造方法によるＭｇ０−Ｃ系連続鋳造用耐火物にお
いては、カーボンの酸化・脱炭による組織の脆弱化ある
いは極低炭素鋼種に対する耐食性劣化の問題がある。[Problems to be Solved by the Invention] However, in Mg0-C continuous casting refractories manufactured by conventional manufacturing methods that use a large amount of C as a refractory aggregate, the structure becomes weak due to oxidation and decarburization of carbon. Alternatively, there is a problem of deterioration in corrosion resistance for ultra-low carbon steel types.
又、単斜晶型ＺｒＯ，を耐火物骨材として併用する従来
の製造方法によるＭ ｇ Ｏ−Ｚ ｒ Ｏｚ系連続鋳造
用耐火物においては、ＺｒＯ２の使用量が少ないと、Ｍ
ｇＯによって安定化された立方晶型ＺｒＯ２の比率が増
し、単斜晶型→正方晶型の相変態に起因するマイクロク
ラックが減少して効果が減少する一方、ＺｒＯ２の使用
量が多い、あるいは粗角として使用すると、結合組織内
に多数のクラックが発生し、強度が著しく劣化する問題
がある。In addition, in MgO-ZrOz series continuous casting refractories manufactured by conventional manufacturing methods that use monoclinic ZrO as a refractory aggregate, if the amount of ZrO2 used is small, Mg
The ratio of cubic ZrO2 stabilized by gO increases, and the microcracks caused by monoclinic → tetragonal phase transformation decrease, reducing the effect. When used as a corner, there is a problem in that many cracks occur within the connective tissue and the strength deteriorates significantly.
そこで、本発明は、耐食性、熱衝撃抵抗性に優れ、かつ
組織の結合強度を高め得る連続鋳造用耐火物の製造方法
の提供を目的とする。Therefore, an object of the present invention is to provide a method for producing a refractory for continuous casting that has excellent corrosion resistance and thermal shock resistance, and can increase the bonding strength of the structure.
［課題を解決するための手段］
前記課題を解決するため、本発明は、ＭｇＯのみ又はＭ
ｇＯを含む耐火材料１００重量部に対しＺｒＯ２を５〜
５０重量部添加して粒径４４〜１００００μｍに調製し
たＭｇＯ−ＺｒＯ２系骨材（以下、ＭＺ系骨材と称す）
２０〜ｉｏｏ重量％、残部が主としてＭｇＯ系骨材から
なる耐火物原料を混練して、成形、焼成する方法である
。[Means for Solving the Problems] In order to solve the above problems, the present invention provides MgO only or MgO.
5 to 5 parts of ZrO2 per 100 parts by weight of refractory material containing gO
MgO-ZrO2-based aggregate prepared by adding 50 parts by weight to have a particle size of 44 to 10,000 μm (hereinafter referred to as MZ-based aggregate)
In this method, a refractory raw material containing 20 to 100% by weight and the remainder mainly consisting of MgO-based aggregate is kneaded, molded, and fired.
ここで、ＭｇＯを含む耐火材料とは、ＭｇＯの他に、酸
化物、炭化物、はう化物、もしくは窒化物耐火材料又は
金属の１種以上を添加したものをいい、例えばＡＪ２２
０３（アルミナ）、ｃｒ２０ｓ（酸化クロム）、ＺｒＢ
ｘ （はう化ジルコニウム）あるいは５ｉｓＮ４ （
窒化けい素）ウィスカ、ｓｉｃ （炭化けい素）ウィス
カ等が用いられる。ＭｇＯ以外の耐火材料は、ＭＺ系骨
材自身の耐食性や強度を高めるもので、その添加量の割
合は、ＭＺ系骨材全体のうち８０重量％以下であること
が好ましい。８０重量％を超えると、ＭｇＯの配合量が
減少し、高い耐食性を期待できなくなるおそれがあり、
かつＭｇＯとＺｒＯ２のバランスがくずれ、不適である
。Here, the refractory material containing MgO refers to a refractory material containing one or more of oxide, carbide, ferride, or nitride refractory material or metal in addition to MgO, such as AJ22
03 (alumina), cr20s (chromium oxide), ZrB
x (zirconium pyridide) or 5isN4 (
Silicon nitride (silicon nitride) whiskers, SIC (silicon carbide) whiskers, etc. are used. The refractory material other than MgO increases the corrosion resistance and strength of the MZ aggregate itself, and the amount added thereof is preferably 80% by weight or less of the entire MZ aggregate. If it exceeds 80% by weight, the amount of MgO mixed may decrease and high corrosion resistance may not be expected.
In addition, the balance between MgO and ZrO2 is lost, making it unsuitable.
又、ＭｇＯ系骨材とは、ＭｇＯ％ＭｇＯ・Ａｊ２ｉ０ｓ
（スピネル）又はＭｇＯ・Ｃｒ２０ｓ（クロムスピネル
）の１種以上、あるいはこれらの他にＡ１□０．そのも
の若しくはＣを添加したものをいい、より一層の耐スポ
ーリング性あるいは耐食性向上のために、やや多めにＣ
を併用する、いわゆるＭｇ０−Ｃ系の骨材も有効であり
、本願のＭｇＯ系骨材に含まれるものである。In addition, MgO aggregate is MgO%MgO・Aj2i0s
(spinel) or one or more of MgO・Cr20s (chromium spinel), or in addition to these, A1□0. It refers to C as it is or to which C is added.In order to further improve spalling resistance or corrosion resistance, slightly more C is added.
A so-called MgO-C aggregate, which is used in combination with MgO-C, is also effective and is included in the MgO aggregate of the present application.
［作 用］
ＭＺ系骨材は、バブレアイト（ｂａｄｄｅｌｅｙｌｔｅ
）とペリクレース（ｐｅｒｉｃｌａｓｅ）あるいはスピ
ネル等を原料として溶融製造したタリンカーだけでなく
、１５００℃以上の温度で焼結させたものを破砕調製し
たものでもよいが、ＺｒＯ２結晶の大きさを制御する面
及び現状の製造技術、コスト面で電融品が特に望ましい
。[Function] MZ aggregate is similar to bubble light.
), periclase, spinel, etc. as raw materials, and sintered at a temperature of 1,500°C or higher and crushed and prepared. Electric fusion products are particularly desirable in terms of current manufacturing technology and cost.
ＺｒＯ，は、ＭｇＯ，Ａ、Ｑ２０ｓ ％ Ｃｒ２ｏ３に
はほとんど固溶しないため、ＭＺ系骨材は、ＭｇＯある
いはＭｇ０−Ａ℃、Ｏ，、ＭｇＯ・Ｃｒ２Ｏ，やフリー
のＡＪ１２０３やＣｒ２Ｏ５等のマトリックス中にＺｒ
Ｏ２粒子が分散した組織を呈する。Since ZrO hardly dissolves in solid solution in MgO, A, Q20s % Cr2O3, MZ-based aggregates contain MgO or Mg0-A℃, O,, MgO・Cr2O, or free AJ1203, Cr2O5, etc. in the matrix. Zr
It exhibits a structure in which O2 particles are dispersed.
このＺｒＯ２は、ＭｇＯの固溶量に応じて単斜晶型、正
方晶型あるいは立方晶型として存在する。そして、ＭＺ
系骨材を耐火物に使用した場合、焼成時あるいは実使用
時の熱履歴により以下のようにしてマイクロクランクを
生じる。This ZrO2 exists as a monoclinic type, a tetragonal type, or a cubic type depending on the amount of solid solution of MgO. And MZ
When aggregates are used in refractories, micro-cranks are generated as described below depending on the thermal history during firing or actual use.
ＭＺ系骨材中のＺｒＯ，粒子が単斜晶型であった場合に
は、単斜晶型→正方晶型の相変態における膨張収縮によ
りＺｒＯ２粒子周辺部にマイクロクラックを生ずる。When the ZrO particles in the MZ aggregate are monoclinic, microcracks are generated around the ZrO2 particles due to expansion and contraction during the phase transformation from monoclinic to tetragonal.
又、ＺｒＯ，粒子が正方晶型であった場合には、熱応力
の増減によって一部が単斜晶型に相変態して同様のマイ
クロクラックを生ずる。Furthermore, if the ZrO particles are tetragonal, a portion of the ZrO particles undergo phase transformation to monoclinic due to an increase or decrease in thermal stress, resulting in similar microcracks.
更に、ＺｒＯ２粒子が立方晶型であった場合には、１３
００〜１４００℃でアニールされて膜安定化し、一部が
正方晶型に相変態し、かつ単斜晶型に相変態することで
マイクロクラックを生ずる。Furthermore, when the ZrO2 particles are cubic crystal type, 13
The film is stabilized by annealing at 00 to 1,400° C., and part of the film undergoes a phase transformation to a tetragonal phase and then to a monoclinic phase, thereby producing microcracks.
従って、ＭＺ系骨材中のＺｒＯ，相の違いにかかわらず
、焼成時あるいは製品使用時の熱履歴においてマイクロ
クラックが得られ、このマイクロクランクが外部から製
品に加わる熱応力を吸収、緩和することで、骨材自体及
び耐火物の熱衝撃抵抗性を高めることができる。しかも
、このマイクロクラックは、ＭＺ系骨材中のＺｒＯ，粒
子及びその周囲にのみ発生するので、組織の結合強度を
劣化させるには至らない。Therefore, regardless of the difference in the ZrO phase in the MZ aggregate, microcracks are obtained during the thermal history during firing or product use, and these microcracks absorb and alleviate the thermal stress applied to the product from the outside. This can improve the thermal shock resistance of the aggregate itself and the refractory. Furthermore, since these microcracks occur only in the ZrO and particles in the MZ aggregate and their surroundings, they do not deteriorate the bonding strength of the tissue.
ＺｒＯ２は、ＭｇＯによって立方晶型ＺｒＯ。ZrO2 is cubic type ZrO due to MgO.
に安定化されるため、ＭＺ系骨材調製時のＺｒＯ２の添
加量が、ＭｇＯのみ又はＭｇＯを含む耐火材料１００重
量部に対し５重量部未満では、マイクロクラックの発生
量が減少して効果がなく、５０重量部を超えると、立方
晶型ＺｒＯ２が増加して線熱膨張係数が大きくなり、熱
衝撃抵抗性が改善されない。Therefore, if the amount of ZrO2 added when preparing MZ-based aggregate is less than 5 parts by weight per 100 parts by weight of refractory material containing only MgO or MgO, the amount of microcracks generated will be reduced and the effect will be less. If the amount exceeds 50 parts by weight, cubic ZrO2 increases and the coefficient of linear thermal expansion increases, and thermal shock resistance is not improved.
ＭＺ系骨材の粒径は、４４μｍ未満であると、耐火物の
マトリックスにもマイクロクランクを生ずることになり
、その結果、組織の結合強度を劣化させることとなり、
１００００μｍを超えると、耐火物の製造が困難となる
。If the particle size of the MZ-based aggregate is less than 44 μm, micro-cranks will also occur in the refractory matrix, resulting in a deterioration of the bonding strength of the tissue.
If it exceeds 10,000 μm, it becomes difficult to manufacture refractories.
耐火物原料中におけるＭＺ系骨材の配合量が２０重量％
未満となると、ＭＺ系骨材粒子におけるマイクロクラッ
クの総量が少なく、通常のＭｇＯ系耐火物の欠点である
低熱衝撃抵抗性が改善されない。The amount of MZ aggregate in the refractory raw material is 20% by weight.
If it is less than this, the total amount of microcracks in the MZ-based aggregate particles will be small, and the low thermal shock resistance, which is a drawback of ordinary MgO-based refractories, will not be improved.
［実施例］ 以下、本発明の詳細な説明する。[Example] The present invention will be explained in detail below.
ＭｇＯ１００重量部に対しＺｒＯ２を′ｓ１表に示すよ
うに所要量ずつ添加し、又、ＭｇＯを含む耐火材料（Ｍ
ｇ Ｏ−Ａ ｊ！ ２０ ｓ）に対しＺｒＯ２を第２
表に示すように所要量ずつ添加し、焼結法又は溶融法に
より粒径４４〜５０００μ■の粉末からなる１２種類の
ＭＺ系骨材を調製した。Add ZrO2 in the required amount to 100 parts by weight of MgO as shown in Table 's1, and add refractory material containing MgO (M
g O-A j! 20 s) with ZrO2
Twelve types of MZ-based aggregates were prepared by adding the required amounts as shown in the table and using a sintering method or a melting method to prepare 12 types of MZ-based aggregates consisting of powders with a particle size of 44 to 5000 μm.
調製したＭＺ系骨材と、粒径０．５〜５０００μｍのＭ
ｇＯ粉末を第１，２表に示す割合で配合し、更に所要量
のバインダー（実施例３．１２は、更に外車で３重量％
のカーボンを含有する）と共に混練し、１ 、５ ｋｇ
／ａｍ”の圧力で成形した後、酸化又は還元雰囲気中に
おいて１６００℃の温度で焼成してスライドゲート用耐
火物を得た。The prepared MZ aggregate and M with a particle size of 0.5 to 5000 μm
gO powder was blended in the proportions shown in Tables 1 and 2, and the required amount of binder was added (in Example 3.12, 3% by weight was added for foreign cars).
(containing 1.5 kg of carbon)
The refractories for slide gates were obtained by molding at a pressure of /am'' and firing at a temperature of 1600° C. in an oxidizing or reducing atmosphere.
上記各スライドゲート用耐火物の曲げ強さ、耐食指数、
熱衝撃試験結果及び実用寿命は、単斜晶型ＺｒＯ２を耐
火物骨材として併用した従来の方法によるスライドゲー
ト用耐火物その他を併記する第１．２表に示すようにな
フた。The bending strength and corrosion resistance index of each slide gate refractory mentioned above,
Thermal shock test results and service life are as shown in Table 1.2, which also lists refractories for slide gates and others prepared by the conventional method using monoclinic ZrO2 as a refractory aggregate.
第１表中、実施例１のＺｒＯ２含有量は、比較例１のそ
れに相当し、実施例２．３のＺｒＯ，含有量は、比較例
２のそれに相当する。In Table 1, the ZrO2 content of Example 1 corresponds to that of Comparative Example 1, and the ZrO content of Example 2.3 corresponds to that of Comparative Example 2.
又、曲げ強さその他の特性は、焼成後のピッチ含浸・揮
発分除去後に測定した。In addition, bending strength and other properties were measured after pitch impregnation and removal of volatile matter after firing.
従フて、実施例１〜１２のように、ＭＺ系骨材調製時に
、ＭｇＯのみ又はＭｇＯを含む耐火材料ｉｏｏ重量部に
対するＺｒＯ，の添加量を５〜５０重量部とし、かつ耐
火物原料全体（バインダーを除く）におけるＭＺ茶系骨
材配合量を２０〜１００重量％とすることにより、曲げ
強さ及び耐食指数を従来の方法によるスライドゲート用
耐火物とほぼ同等とし得、かつ熱衝撃抵抗性及び実用寿
命を従来の方法によるものより飛躍的に向上し得ること
がわかる。Therefore, as in Examples 1 to 12, when preparing the MZ-based aggregate, the amount of ZrO added is 5 to 50 parts by weight based on the weight of the refractory material containing only MgO or MgO, and the entire refractory raw material is By setting the blending amount of MZ brown aggregate to 20 to 100% by weight (excluding the binder), the bending strength and corrosion resistance index can be almost the same as that of refractories for slide gates made by conventional methods, and the thermal shock resistance It can be seen that the performance and practical life can be dramatically improved compared to conventional methods.
これは、調製温度の違いによるＭＺ系骨材中のＺｒＯ２
の結晶型の相違に影響されることなく、耐火物の焼成時
あるいは実使用時の熱履歴においてＭＺ系骨材粒子内に
マイクロクラックが適当量得られ、骨材を結合する耐火
物のマトリックスには、クランクが生じないためである
。This is because the ZrO2 in MZ aggregate due to the difference in preparation temperature.
Regardless of the difference in the crystal type of the refractory, an appropriate amount of microcracks are obtained within the MZ aggregate particles during the firing or actual use of the refractory, and the matrix of the refractory that binds the aggregates. This is because no crank occurs.
又、実施例３，１２には、カーボンを単独で添加し、か
つバインダーを多めにして還元焼成したカーボン含有耐
火物であるが、表かられかるように、曲げ強さ、耐熱衝
軍性及び耐食性が優れていることがわかる。Furthermore, in Examples 3 and 12, carbon-containing refractories were obtained by adding carbon alone and reducing and firing with a large amount of binder, but as can be seen from the table, the bending strength, heat shock resistance, and It can be seen that the corrosion resistance is excellent.
［発明の効果］
以上のように本発明によれば、ＭＺ系骨材中のＺｒＯ，
の結晶型の相違に影響されることなく、耐火物の焼成時
あるいは実使用時の熱履歴において、配合された耐火物
原料のうちのＭＺ系骨材粒子内にのみマイクロクラック
が得られるので、従来の方法によるものより、耐食性、
熱衝撃抵抗性に優れ、かつ組織の結合強度が高い連続鋳
造用耐火物を得ることができる。[Effects of the Invention] As described above, according to the present invention, ZrO,
Microcracks are obtained only in the MZ aggregate particles of the blended refractory raw material during the firing or actual use of the refractory, without being affected by the difference in the crystal type of the refractory. Corrosion resistance than that by traditional methods,
A refractory for continuous casting that has excellent thermal shock resistance and high structural bonding strength can be obtained.
Claims (1)
部に対しＺｒＯ＿２を５〜５０重量部添加して粒径４４
〜１００００μｍに調製したＭｇＯ−ＺｒＯ＿２系骨材
２０〜１００重量％、残部が主としてＭｇＯ系骨材から
なる耐火物原料を混練して、成形、焼成することを特徴
とする連続鋳造用耐火物の製造方法。(1) Add 5 to 50 parts by weight of ZrO_2 to 100 parts by weight of refractory material containing only MgO or MgO to obtain particles with a particle size of 44
Production of refractories for continuous casting, characterized by kneading, molding, and firing refractory raw materials consisting of 20 to 100% by weight of MgO-ZrO_2 aggregate prepared to ~10,000 μm, and the remainder mainly consisting of MgO aggregate. Method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1325323A JPH0714832B2 (en) | 1989-12-15 | 1989-12-15 | Method for manufacturing refractory for continuous casting |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1325323A JPH0714832B2 (en) | 1989-12-15 | 1989-12-15 | Method for manufacturing refractory for continuous casting |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03189055A true JPH03189055A (en) | 1991-08-19 |
| JPH0714832B2 JPH0714832B2 (en) | 1995-02-22 |
Family
ID=18175538
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1325323A Expired - Fee Related JPH0714832B2 (en) | 1989-12-15 | 1989-12-15 | Method for manufacturing refractory for continuous casting |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0714832B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1999038818A1 (en) * | 1998-01-28 | 1999-08-05 | Krosaki Corporation | Alumina-magnesia-graphite type refractory |
| JP2015193509A (en) * | 2014-03-31 | 2015-11-05 | 黒崎播磨株式会社 | Magnesia-spinel-zirconia brick |
-
1989
- 1989-12-15 JP JP1325323A patent/JPH0714832B2/en not_active Expired - Fee Related
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1999038818A1 (en) * | 1998-01-28 | 1999-08-05 | Krosaki Corporation | Alumina-magnesia-graphite type refractory |
| JP2015193509A (en) * | 2014-03-31 | 2015-11-05 | 黒崎播磨株式会社 | Magnesia-spinel-zirconia brick |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0714832B2 (en) | 1995-02-22 |
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