KR20020016130A - High functional ZrO2 C refractory - Google Patents

High functional ZrO2 C refractory Download PDF

Info

Publication number
KR20020016130A
KR20020016130A KR1020000049289A KR20000049289A KR20020016130A KR 20020016130 A KR20020016130 A KR 20020016130A KR 1020000049289 A KR1020000049289 A KR 1020000049289A KR 20000049289 A KR20000049289 A KR 20000049289A KR 20020016130 A KR20020016130 A KR 20020016130A
Authority
KR
South Korea
Prior art keywords
refractory
zro
zro2
weight
binder
Prior art date
Application number
KR1020000049289A
Other languages
Korean (ko)
Other versions
KR100515188B1 (en
Inventor
박세민
한상무
이근화
Original Assignee
이구택
포항종합제철 주식회사
신현준
재단법인 포항산업과학연구원
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by 이구택, 포항종합제철 주식회사, 신현준, 재단법인 포항산업과학연구원 filed Critical 이구택
Priority to KR10-2000-0049289A priority Critical patent/KR100515188B1/en
Publication of KR20020016130A publication Critical patent/KR20020016130A/en
Application granted granted Critical
Publication of KR100515188B1 publication Critical patent/KR100515188B1/en

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
    • C04B35/48—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on zirconium or hafnium oxides, zirconates, zircon or hafnates
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
    • C04B35/52—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbon, e.g. graphite
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B2111/00—Mortars, concrete or artificial stone or mixtures to prepare them, characterised by specific function, property or use
    • C04B2111/20—Resistance against chemical, physical or biological attack
    • C04B2111/28—Fire resistance, i.e. materials resistant to accidental fires or high temperatures
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
    • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
    • C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
    • C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
    • C04B2235/3244—Zirconium oxides, zirconates, hafnium oxides, hafnates, or oxide-forming salts thereof
    • C04B2235/3248—Zirconates or hafnates, e.g. zircon
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
    • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
    • C04B2235/42—Non metallic elements added as constituents or additives, e.g. sulfur, phosphor, selenium or tellurium
    • C04B2235/422—Carbon
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
    • C04B35/63—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B using additives specially adapted for forming the products, e.g.. binder binders
    • C04B35/632—Organic additives
    • C04B35/634—Polymers
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
    • C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/66—Monolithic refractories or refractory mortars, including those whether or not containing clay

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Ceramic Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Materials Engineering (AREA)
  • Structural Engineering (AREA)
  • Organic Chemistry (AREA)
  • Compositions Of Oxide Ceramics (AREA)
  • Composite Materials (AREA)

Abstract

PURPOSE: A zirconia carbon(ZrO2-C)-based refractory is provided, which has much improved corrosion-resistance and high temperature characteristics, and lowered production cost compared with a conventional zirconia carbon-based refractory by substituting coal- or petroleum-based pitch for solid phenol-based resin used as a binder. CONSTITUTION: The refractory is produced by the following steps: preparing ZrO2-C-based compact by mixing 70-85wt.% of ZrO2 clinker and 15-30wt.% of crystalline, adding 1-5pts.wt.(based on the mixture) of solid pitch powder based on coal and petroleum, being used as a binder, with 100-250deg.C of softening point, and 2-4pts.wt.(based on the mixture) of liquid phenolic resin; thermal polymerizing under 200deg.C; and thermal treating at 1000deg.C for carbonization of the binder.

Description

고기능성 지르코니아 탄소계 내화물 {High functional ZrO2 C refractory}High Functional Zirconia Carbon Refractory {High functional ZrO2 C refractory}

본 발명은 지르코니아(ZrO2)-탄소(C)계 내화물에 관한 것으로, 더욱 상세하게는 기존의 내화물 조성에서 결합재로 사용하고 있는 고상 페놀계 수지를 일정한 연화점 이상의 석탄계 또는 석유계 핏치로 대체함으로써 기존의 내화물보다 고온 특성이 개선되고 내식성이 향상된 고기능성 ZrO2-C계 내화물에 관한 것이다.The present invention relates to a zirconia (ZrO 2 ) -carbon (C) -based refractory, more specifically, by replacing the solid phenolic resin used as a binder in the existing refractory composition with a coal or petroleum pitch of a certain softening point or more. The present invention relates to a high-performance ZrO 2 -C-based refractory with improved high temperature properties and improved corrosion resistance.

ZrO2-C계 내화물은 제철소의 연속주조 공정에서 사용하는 노즐류에 사용되는 내화벽돌로서, 그 중에서 가장 높은 내식성이 요구되는 침지노즐의 슬래그 라인 부위에 사용된다.ZrO 2 -C type refractory is a refractory brick used in the nozzles used in the continuous casting process of steel mills, and is used in the slag line portion of the immersion nozzle which requires the highest corrosion resistance among them.

연주공정의 노즐류에 사용되는 내화물은 1600℃ 부근의 용강을 턴디쉬에서 몰드로 연결하여 주는 역할을 하므로, 내부로는 용강이 통과하고 외부는 용융된 몰드 파우더에 기인한 슬래그와 접촉한 상태로 사용된다. 따라서 노즐류의 내화물은 알루미나(Al2O3)-탄소(C)계 조성의 내화벽돌에서 슬래그와 접촉하여 침식이 극심한 부위만을 ZrO2-C계 재질로 보강하여 사용하고 있다.Refractories used in the nozzles of the playing process connect molten steel around 1600 ℃ to the mold from the tundish, so molten steel passes through the inside and the slag is caused by molten mold powder. Used. Therefore, the refractory materials of the nozzles are reinforced with ZrO 2 -C materials only in areas where the erosion is severe due to contact with slag in the refractory bricks having alumina (Al 2 O 3 ) -carbon (C) composition.

이와 같이 슬래그 라인 부위에 사용되는 ZrO2-C계 내화물은 고비중과 고온의 용강을 지지하고 슬래그와 접촉하므로 상온강도 및 고온강도 등의 기계적 물성이 우수하여야 할뿐만 아니라, 용강이나 슬래그에 대한 내침식성이 우수해야 한다.As described above, ZrO 2 -C-based refractory used in the slag line part supports high specific gravity and high temperature molten steel and contacts with slag, so it should not only have excellent mechanical properties such as room temperature strength and high temperature strength but also resistance to molten steel or slag. Erosion must be excellent.

현재까지는 내침식성의 향상을 위해 ZrO2골재형태나 배합비를 제어하거나, 또는 타 화합물을 첨가하는 등의 연구를 해왔으나, 큰 효과를 보지 못하고 있으며, 따라서, ZrO2-C계 내화물의 내침식성 향상이 요구되고 있는 실정이다.Until now, researches on controlling ZrO 2 aggregate form and compounding ratio or adding other compounds to improve erosion resistance have not been carried out. Therefore, the erosion resistance of ZrO 2 -C-based refractory is improved. This situation is required.

ZrO2-C계 내화물은 ZrO2및 흑연골재로 구성된다. 그러나 이들 두 종류의 골재만으로는 성형체를 제작하기 어렵기 때문에, 분해반응에 의해서 탄소가 가능한 한 많이 잔류하는 수지를 성형조제인 결합재로 사용하여 성형하는 것이 보편적이다.ZrO 2 -C-based refractory is composed of ZrO 2 and graphite aggregate. However, since these two types of aggregates are difficult to produce a molded body, it is common to mold by using a resin that retains as much carbon as possible by the decomposition reaction as a binding aid.

일반적인 결합재로서는 액상, 고상 또는 액상과 고상의 복합형인 페놀수지가 있으나, 이들 수지의 가격은 고가이며, 실제 연속주조 조업 중에 사용할 때에는 흑연으로 결정화하기 어려운 난흑연화성 탄소를 생성하여 취성을 가지며, 내식성도 열등한 결점이 있다.Common binders include liquid, solid or liquid and solid phenolic resins. However, these resins are expensive, and when used during continuous casting, they produce brittle, brittle, hardly graphitized carbon that is difficult to crystallize into graphite. There is also an inferior flaw.

본 발명은 상기한 바와 같은 문제점을 해결하기 위한 것으로, 그 목적은 생산원가가 낮으면서도 고온특성 및 내식성이 향상된 ZrO2-C계 내화물을 제공하는 데 있다.The present invention has been made to solve the problems described above, and its object is to provide a ZrO 2 -C-based refractory, which has a low production cost and improved high temperature characteristics and corrosion resistance.

상기한 바와 같은 목적을 달성하기 위하여, 본 발명은 기존의 ZrO2-C계 내화물 조성에서 결합재 중 고상 페놀수지를 일정한 연화점 이상의 석탄계 또는 석유계 핏치로 대체하는 것을 특징으로 한다.In order to achieve the object as described above, the present invention is characterized by replacing the solid phenolic resin of the binder with a coal or petroleum pitch of a predetermined softening point or more in the existing ZrO 2 -C-based refractory composition.

이하, 본 발명에 따른 고기능성 ZrO2-C계 내화물에 대해 상세히 설명한다.Hereinafter, the highly functional ZrO 2 -C based refractory according to the present invention will be described in detail.

먼저, ZrO2클링커 70∼85 중량%와, 인상흑연 15∼30 중량%을 혼합하고, 이 혼합물의 중량 100에 대해서 연화점이 100℃∼250℃인 석탄계 또는 석유계 고상 핏치 분말을 1∼5 중량부 첨가하고 액상 페놀수지를 2∼4 중량부 첨가하여 ZrO2-C 성형체를 제조한다.First, ZrO 2 clinker and 70-85% by weight, raise mixing graphite 15 to 30% by weight, the coal-based or petroleum-based solid powder pitch softening point of 100 ℃ ~250 ℃ respect to 100 parts by weight of the mixture 1 to 5 wt. Part is added, and 2 to 4 parts by weight of the liquid phenol resin is added to prepare a ZrO 2 -C molded body.

다음, 성형체를 200℃ 이하의 비교적 낮은 온도에서 열중합 처리한 후, 1000℃ 부근에서 결합재의 탄소화를 유도하는 열처리를 함으로써 ZrO2-C계 내화물의 제조를 완료한다.Next, the molded article is thermally polymerized at a relatively low temperature of 200 ° C. or lower, and then subjected to a heat treatment to induce carbonization of the binder at about 1000 ° C., thereby completing the production of the ZrO 2 -C refractory.

이 때 내화물의 열적 특성은 결합재 수지 중합체로부터 유도된 탄소재의 특성에 의존하게 되는데, 본 발명에서 사용한 연화점이 100℃∼250℃인 석탄계 또는 석유계 고상 핏치는, 저탄성, 저팽창성, 고열 전도성의 탄소를 생성하여 골재간의 결합을 흑연으로 결정화하기 쉽게 하므로, ZrO2-C계 내화물의 고온특성이 개선되고, 내식성도 향상된다.At this time, the thermal properties of the refractory will depend on the properties of the carbon material derived from the binder resin polymer. The coal- or petroleum solid-phase pitch having a softening point of 100 ° C. to 250 ° C. used in the present invention is low elasticity, low expansion property, and high thermal conductivity. By forming carbon, it is easy to crystallize the bond between the aggregates with graphite, so that the high temperature characteristics of the ZrO 2 -C-based refractory are improved, and the corrosion resistance is also improved.

이것은 기존의 페놀계 수지만을 사용할 경우, 결합재로부터 고탄성, 고팽창성, 저열전도성의 유리질 탄소가 생성되어 골재간에 위치하여 고온특성 및 내식성 등이 저하하였던 것이 개선된 것이다.This is an improvement in that high elasto-plastic, high-expansion, low-thermal conductivity glassy carbon is generated from the binder when the existing phenolic resin is used, and the high temperature characteristics and corrosion resistance are reduced.

고상 핏치의 첨가량이 1 중량부 미만일 경우에는 결합재의 흑연으로의 전환에 의한 효과가 미흡하고, 5 중량부를 초과할 경우에는 핏치의 분해에 의해 생성되는 기공율이 과도하게 증가하여 내화물의 특성이 오히려 열화되므로, 고상 핏치의 첨가량은 ZrO2클링커와 인상흑연의 혼합물 중량 100에 대해서 1∼5 중량부인 것이 바람직하다.If the amount of solid phase pitch is less than 1 part by weight, the effect of conversion of the binder to graphite is insufficient. If it exceeds 5 parts by weight, the porosity produced by decomposition of the pitch is excessively increased and the characteristics of the refractory are deteriorated. therefore, the addition amount of the solid pitch is preferably 1 to 5 parts by weight with respect to 100 parts by weight of ZrO 2 clinker and the mixture impression graphite.

기존의 결합재로 사용된 고상 페놀수지는 약 40∼50%의 탄화수율을 나타내며, 이와 대등한 탄화수율이 요구된다. 고상 핏치의 연화점이 100℃일 경우 탄화수율이 40∼50%를 나타내며, 연화점이 증가할수록 탄화수율은 향상된다. 그러나 연화점이 250℃ 이상인 핏치는 코크스화가 상당부분 진행된 것으로서, 제조시의 열처리 공정에서 용융 후의 유동성이 크게 저하되므로 결합재로서의 역할이 열등하다. 따라서, 고상 핏치의 연화점은 100℃∼250℃인 것이 바람직하다.The solid phenolic resin used as a conventional binder shows a carbon yield of about 40 to 50%, and an equivalent carbon yield is required. When the softening point of the solid pitch is 100 ° C, the carbonization yield is 40 to 50%. As the softening point is increased, the carbonization yield is improved. However, pitches having a softening point of 250 ° C. or more have undergone a significant portion of coking, and since the fluidity after melting is greatly reduced in the heat treatment process during manufacture, the role as a binder is inferior. Therefore, it is preferable that the softening point of a solid pitch is 100 degreeC-250 degreeC.

이하, 본 발명의 실시예를 통해 고기능성 ZrO2-C계 내화물을 구체적으로 설명한다.Hereinafter, the highly functional ZrO 2 -C-based refractory will be described in detail through examples of the present invention.

실시예 1Example 1

ZrO2클링커 75 중량%와, 인상흑연 25 중량%을 혼합하고, 이 혼합물의 중량 100에 대해서 연화점이 250℃인 고상 핏치를 2 중량부 첨가하고 액상 페놀수지를 3 중량부 첨가하여 ZrO2-C 성형체를 제조한 다음, 성형체를 180℃에서 열중합 처리하고, 1000℃에서 탄화 소성처리하여 ZrO2-C계 내화물의 제조하였다.75 weight% ZrO 2 clinker and 25 weight% impression graphite were mixed, and 2 weight parts of solid phase pitches having a softening point of 250 ° C. were added to the weight 100 of the mixture, and 3 weight parts of liquid phenol resin was added to ZrO 2 -C. After the molded product was prepared, the molded product was thermally polymerized at 180 ° C., and carbonized at 1000 ° C. to prepare a ZrO 2 -C-based refractory body.

이러한 방법으로 제조된 ZrO2-C계 내화물에 대해 7초 내에 소정의 온도에 도달하는 급속승온에 의해 내부에 균열이 발생하는 온도를 측정하는 열충격 특성을 측정한 결과, 균열의 발생이 관측되지 않았다.As a result of measuring the thermal shock characteristics of the ZrO 2 -C-based refractory material prepared in this way to measure the temperature at which the cracks occurred due to the rapid rise in temperature within 7 seconds, no crack was observed. .

이것은, 고상 핏치 대신에 기존의 고상 페놀수지를 사용하여 동일한 공정으로 제조한 기존의 ZrO2-C계 내화물이 1850℃ 부근에서 내부에 균열이 발생하는 것으로 관측된 것에 비해 열충격 특성이 상당히 개선된 것임을 나타낸다.This indicates that the thermal shock characteristics of the ZrO 2 -C refractories manufactured by the same process using the conventional solid phenolic resin instead of the solid pitch are significantly improved in comparison with that observed in the interior at around 1850 ° C. Indicates.

실시예 2Example 2

ZrO2클링커 75 중량%와, 인상흑연 25 중량%을 혼합하고, 이 혼합물의 중량 100에 대해서 연화점이 200℃인 고상 핏치를 2 중량부 첨가하고 액상 페놀수지를 3 중량부 첨가하여 ZrO2-C 성형체를 제조한 다음, 성형체를 180℃에서 열중합 처리하고, 1000℃에서 탄화 소성처리하여 ZrO2-C계 내화물의 제조하였다.75% by weight of ZrO 2 clinker and 25% by weight of impression graphite are mixed, and 2 parts by weight of solid phase pitch having a softening point of 200 ° C. is added to 3 parts by weight of liquid phenolic resin, and 3 parts by weight of liquid phenol resin are added to ZnO 2 -C. After the molded product was prepared, the molded product was thermally polymerized at 180 ° C., and carbonized at 1000 ° C. to prepare a ZrO 2 -C-based refractory body.

이러한 방법으로 제조된 ZrO2-C계 내화물의 슬래그에 대한 침식율을 측정하였다. 이 때, 고상 핏치 대신에 기존의 고상 페놀수지를 사용하여 동일한 공정으로 제조한 기존의 ZrO2-C계 내화물의 침식율을 100으로 하고, 이를 기준으로 하여 측정한 본 발명의 실시예 2에 의해 제조된 ZrO2-C계 내화물의 침식율은 80 이었으며, 이로 인해 본 발명의 실시예 2에 의해 제조된 ZrO2-C계 내화물의 내침식성이 기존에비해 상당히 개선되었음을 알 수 있었다.The erosion rate on the slag of the ZrO 2 -C-based refractory prepared in this way was measured. At this time, the erosion rate of the existing ZrO 2 -C-based refractory prepared in the same process using a conventional solid phenolic resin instead of the solid pitch of 100 was prepared by Example 2 of the present invention measured based on this The erosion rate of the ZrO 2 -C-based refractory was 80, which shows that the corrosion resistance of the ZrO 2 -C-based refractory prepared by Example 2 of the present invention was significantly improved.

상기한 바와 같이, 본 발명에서는 고상 페놀수지 대신에 골재간의 결합을 흑연으로 결정화하기 쉬운 석탄계 또는 석유계 핏치를 사용함으로써, ZrO2-C계 내화물의 고온특성 및 내식성이 크게 향상되는 효과가 있다.As described above, in the present invention, by using coal-based or petroleum-based pitches in which bonds between aggregates are easily crystallized into graphite instead of solid phenolic resins, the high-temperature characteristics and corrosion resistance of ZrO 2 -C-based refractory materials are greatly improved.

또한, 기존에는 고가의 페놀계 수지만을 사용했던 것에 비해 본 발명에서는 고상 페놀수지를 석탄계 또는 석유계 핏치로 대체하므로 생산원가가 절감되는 효과가 있다.In addition, in the present invention, compared to the use of only expensive phenolic resins, the production cost is reduced because the solid phenolic resins are replaced by coal or petroleum pitches.

Claims (1)

ZrO2클링커가 70∼85 중량%, 인상흑연이 15∼30 중량%, 상기 ZrO2클링커와 인상흑연 혼합물의 중량 100에 대해서 연화점이 100℃∼250℃인 석탄계 또는 석유계 고상 핏치가 1∼5 중량부, 액상 페놀수지가 2∼4 중량부 포함된 고기능성 ZrO2-C계 내화물.Coal or petroleum solid pitches having a softening point of 100 ° C. to 250 ° C. with a ZrO 2 clinker of 70 to 85% by weight, 15 to 30% by weight of graphite, and a weight of 100% of the ZrO 2 clinker to the graphite mixture. A high functional ZrO 2 -C type refractory including 2 parts by weight and 2 to 4 parts by weight of a liquid phenol resin.
KR10-2000-0049289A 2000-08-24 2000-08-24 High functional ZrO2 C refractory KR100515188B1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
KR10-2000-0049289A KR100515188B1 (en) 2000-08-24 2000-08-24 High functional ZrO2 C refractory

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
KR10-2000-0049289A KR100515188B1 (en) 2000-08-24 2000-08-24 High functional ZrO2 C refractory

Publications (2)

Publication Number Publication Date
KR20020016130A true KR20020016130A (en) 2002-03-04
KR100515188B1 KR100515188B1 (en) 2005-09-16

Family

ID=19684951

Family Applications (1)

Application Number Title Priority Date Filing Date
KR10-2000-0049289A KR100515188B1 (en) 2000-08-24 2000-08-24 High functional ZrO2 C refractory

Country Status (1)

Country Link
KR (1) KR100515188B1 (en)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR100472003B1 (en) * 2000-12-22 2005-03-07 재단법인 포항산업과학연구원 A carbonaceous binder having carbonaceous powder and a method for preparing the same
KR100908704B1 (en) * 2002-12-24 2009-07-22 주식회사 포스코 Carbon-containing acid neutral refractory composition
US10407349B2 (en) 2015-04-24 2019-09-10 Corning Incorporated Bonded zirconia refractories and methods for making the same
CN113845746A (en) * 2021-09-30 2021-12-28 四川大学 Mesophase asphalt modified ablation-resistant resin matrix material and preparation method and application thereof

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR101020098B1 (en) 2009-01-21 2011-03-09 조선내화 주식회사 refractories for ladle of molen steel

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH02172862A (en) * 1988-12-23 1990-07-04 Harima Ceramic Co Ltd Production of immersion nozzle for continuous casting
JPH05117057A (en) * 1991-04-02 1993-05-14 Kawasaki Refract Co Ltd Production of fire-resistant porous ring
JPH0777979B2 (en) * 1991-09-27 1995-08-23 ハリマセラミック株式会社 Carbon-containing refractory
JPH08259309A (en) * 1995-03-17 1996-10-08 Toshiba Ceramics Co Ltd Production of carbon-containing refractory
JP3155217B2 (en) * 1995-12-13 2001-04-09 品川白煉瓦株式会社 Carbon-containing refractory and production method thereof
KR100286663B1 (en) * 1996-12-13 2001-04-16 이구택 Basic flame retardant for timing ladle
KR20000006654A (en) * 1999-09-17 2000-02-07 신현준 MgO-C BASED REFRACTORY

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR100472003B1 (en) * 2000-12-22 2005-03-07 재단법인 포항산업과학연구원 A carbonaceous binder having carbonaceous powder and a method for preparing the same
KR100908704B1 (en) * 2002-12-24 2009-07-22 주식회사 포스코 Carbon-containing acid neutral refractory composition
US10407349B2 (en) 2015-04-24 2019-09-10 Corning Incorporated Bonded zirconia refractories and methods for making the same
CN113845746A (en) * 2021-09-30 2021-12-28 四川大学 Mesophase asphalt modified ablation-resistant resin matrix material and preparation method and application thereof
CN113845746B (en) * 2021-09-30 2023-12-08 四川大学 Mesophase pitch modified ablation-resistant resin matrix material, and preparation method and application thereof

Also Published As

Publication number Publication date
KR100515188B1 (en) 2005-09-16

Similar Documents

Publication Publication Date Title
CN112028613B (en) Magnesia carbon brick using catalyst-added phenolic resin
CN104649263A (en) Preparation method of carbon-graphite composite material
KR100967408B1 (en) Carbon containing eco-friendly refractory material composition
CN102898157B (en) Al4O4C/Al-Al2O3 composite carbon-free sliding plate and preparation method thereof
US4208214A (en) Refractory compositions
CN100453211C (en) Method for preparing dry working lining
CN115321956B (en) High-temperature liquid phase toughened magnesia carbon brick and preparation method thereof
US9534845B2 (en) Method for manufacturing a refractory for an inner lining of a blast furnace and blast furnace having the inner lining
KR102061807B1 (en) Magnesia-carbon basic castable for secondary refining furnace
KR100515188B1 (en) High functional ZrO2 C refractory
CN104341163B (en) A kind of ladle pocket block joint filler
CN111732417B (en) Scouring-resistant ultra-low-carbon magnesia-carbon brick with excellent oxidation resistance and preparation method thereof
KR101798843B1 (en) Refractory composition and well block for steel casting by using it
KR100613259B1 (en) A zirconia-carbon refractory composition
JPS6324953B2 (en)
KR20000006654A (en) MgO-C BASED REFRACTORY
KR940005080B1 (en) Process for preparation of magnesia-carbon stamp material
JPH0243701B2 (en)
JPH01167268A (en) Carbon-containing uncalcined refractory
KR100977448B1 (en) A base plate composition for side dam in twin-roll strip caster
KR20020052828A (en) Refractory composition
KR20040016493A (en) High intensity castable refractories with good adiabatic and high thermal shock resistance
KR100908704B1 (en) Carbon-containing acid neutral refractory composition
RU2465245C1 (en) Magnesian gun mixture
KR100567918B1 (en) Dolomite Refractories Composition With Carbon

Legal Events

Date Code Title Description
A201 Request for examination
E902 Notification of reason for refusal
E701 Decision to grant or registration of patent right
GRNT Written decision to grant
FPAY Annual fee payment

Payment date: 20120821

Year of fee payment: 8

FPAY Annual fee payment

Payment date: 20130807

Year of fee payment: 9

FPAY Annual fee payment

Payment date: 20140903

Year of fee payment: 10

FPAY Annual fee payment

Payment date: 20150902

Year of fee payment: 11

FPAY Annual fee payment

Payment date: 20160824

Year of fee payment: 12

FPAY Annual fee payment

Payment date: 20170908

Year of fee payment: 13

FPAY Annual fee payment

Payment date: 20180906

Year of fee payment: 14

FPAY Annual fee payment

Payment date: 20190812

Year of fee payment: 15