CROSS REFERENCE TO RELATED APPLICATION

This application claims priority under 35 U.S.C. Â§119 to Japanese Patent Application No. 2011-191830 on Sep. 2, 2011, the entire contents of which are incorporated herein by reference.

TECHNICAL FIELD

The present invention relates to an aluminum oxycarbide composition usable as a ceramic or refractory material or a raw material therefor, a production method for the aluminum oxycarbide composition, and a refractory material using the aluminum oxycarbide composition.

BACKGROUND ART

As an aluminum oxycarbide, the following two types: Al₂OC and Al₄O₄C, have been known. In particular, Al₄O₄C is characterized by high-temperature stability, anti-oxidation effect, excellent corrosion resistance, and low thermal expansion coefficient. It is expected as a refractory or ceramic material or a raw material therefor, in the future. Especially, Al₄O₄C is expected as a raw material for a carbon-containing refractory material, such as an alumina-carbon based refractory material or a magnesia-carbon based refractory material, used as a refractory material for use with molten metal such as molten iron or steel.

As a method of producing an aluminum oxycarbide composition containing such Al₄O₄C (aluminum oxycarbide), the following Non-Patent Document 1 discloses a method in which alumina and graphite are subjected to a heat treatment in an argon atmosphere. Specifically, after adding ethanol to alumina having an average particle size of 0.1 Î¼m, and graphite reagent having a particle size of 45 Î¼m or less, they are mixed together in an agate mortar, and then dried. A powder (2 g) of the mixture is put into a graphite crucible, and burnt at 1700Â° C. in a preliminarily evacuated electric furnace, while supplying argon gas thereinto. The following Non-Patent Document 2 discloses a method of producing an aluminum oxycarbide composition using an arc furnace. However, the Non-Patent Document 2 mentions that, along with an increase in amount of carbon in the aluminum oxycarbide composition obtained by the disclosed production method, Al₄C₃reactive with water is formed in a larger amount.

On the other hand, the following Patent Document 1 discloses a technique for suppressing the formation of Al₄C₃, wherein a carbon-based raw material and alumina are homogeneously mixed together to eliminate a dispersion in C component.

However, it is known that in ambient atmosphere, Al₄O₄C is oxidized at about 850Â° C. and transformed into alumina. Particularly, in cases where Al₄O₄C having fine crystal grains is used as a raw material for a refractory material, it will be oxidized. Thus, it is difficult to maintain the advantageous effects such as oxidation resistance, corrosion resistance and low thermal expansion coefficient, for a long time.

LIST OF PRIOR ART DOCUMENTSPatent Documents

Patent Document 1: WO 2010/113972 A

Non-Patent Documents

Non-Patent Document 1: REFRACTORIES, Vol. 59, p 288, 2007

Non-Patent Document 2: REFRACTORIES, Vol. 35, p 316, 1983

SUMMARY OF THE INVENTIONTechnical Problem

The technical problem to be solved by the present invention is to provide an aluminum oxycarbide composition capable of suppressing oxidation of Al₄O₄C during use to maintain advantageous effects of Al₄O₄C for a long time, a production method for the aluminum oxycarbide composition, and a carbon-containing refractory material using the aluminum oxycarbide composition.

Solution to the Technical Problem

The present invention provides an aluminum oxycarbide composition comprising Al₄O₄C crystals. The aluminum oxycarbide composition is characterized in that the Al₄O₄C crystals have an average diameter of 20 Î¼m or more, based on an assumption that a cross-sectional area of each Al₄O₄C crystal during observation of the aluminum oxycarbide composition in an arbitrary cross-section thereof is converted into a diameter of a circle having the same area as the cross-sectional area.

Preferably, the aluminum oxycarbide composition of the present invention comprises corundum crystals, in addition to the Al₄O₄C crystals. More preferably, the corundum crystals and the Al₄O₄C crystals alternately lie in layered relationship. In addition to Al₄O₄C and corundum, the aluminum oxycarbide composition of the present invention may contain Al₂OC, oxynitride such as AlON, and/or Î³-Al₂O₃, in a small amount. Preferably, the aluminum oxycarbide composition of the present invention contains carbon in an amount of 3.2 to 6.3 mass %.

The present invention also provides a method of producing the above aluminum oxycarbide composition. The method is characterized in that it comprises subjecting a carbon-based raw material and an alumina-based raw material to melting in an arc furnace and then cooling within the arc furnace.

Preferably, in the method of the present invention, one or more selected from the group consisting of silicon carbide, boron carbide, aluminum nitride, boron nitride and a metal are added to the carbon-based raw material and the alumina-based raw material in an amount of 0.2 to 10.0 mass % with respect to and in addition to a total amount of the carbon-based raw material and the alumina-based raw material. More preferably, the raw materials, such as the carbon-based raw material, the alumina-based raw material and the silicon carbide, are homogeneously mixed together to allow a dispersion in C component to fall within Â±10%.

Effect of the Invention

In the present invention, the Al₄O₄C crystals have an average diameter of 20 Î¼m or more, based on the assumption that a cross-sectional area of each Al₄O₄C crystal is converted into a diameter of a circle having the same area as the cross-sectional area. This makes it possible to suppress oxidation of Al₄O₄C during use to maintain advantageous effects of Al₄O₄C for a long time.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a photograph of a microstructure of an aluminum oxycarbide composition according to the present invention (inventive sample 2 in Table 1).

FIG. 2 is a photograph of a microstructure of a conventional aluminum oxycarbide composition (comparative sample 1 in Table 1).

FIG. 3 shows Table 1.

FIG. 4 shows Table 2.

FIG. 5 shows Table 3.

DESCRIPTION OF EMBODIMENTS

An aluminum oxycarbide composition of the present invention comprises Al₄O₄C crystals, and is characterized in that the Al₄O₄C crystals have an average diameter of 20 Î¼m or more, based on an assumption that a cross-sectional area of each Al₄O₄C crystal during observation of the aluminum oxycarbide composition in an arbitrary cross-section thereof is converted into a diameter of a circle having the same area as the cross-sectional area.

Al₄O₄C crystals in an aluminum oxycarbide composition belong to the orthorhombic system, so that they have a columnar or prismatic structure, in many cases. Although a crystal shape in microscopic observation varies depending on in what cross-section the observation is performed, each of the Al₄O₄C crystals in the present invention has a length of about 10 to 2000 Î¼m in a short-side direction, as measured by observing columnar structures.

As used in this specification, the term â€œaverage diameter based on the assumption that a cross-sectional area of each Al₄O₄C crystal is converted into a diameter of a circle having the same area as the cross-sectional areaâ€ means an average value of diameters based on an assumption that respective cross-sectional areas of the Al₄O₄C crystals are cumulatively added in descending order of cross-sectional area until a cumulative addition value becomes greater than a half of the entire area of an observation field of view during microscopic observation of the aluminum oxycarbide composition, and a cross-sectional area of each of a plurality of specific ones of the Al₄O₄C crystals subjected to the cumulative addition is converted into a diameter of a circle having the same area as the cross-sectional area. A cross-sectional area of each Al₄O₄C crystal, and a diameter of a circle converted from the cross-sectional area, can be calculated using image processing software.

For example, the aluminum oxycarbide composition comprising Al₄O₄C crystals having an average diameter of 20 Î¼m or more can be produced by subjecting a carbon-based raw material and an alumina-based raw material to melting in an arc furnace, and then cooling within the arc furnace, i.e., slow cooling.

Heretofore, in the field of grinding materials or the like, in a method of producing an aluminum oxycarbide composition by means of arc melting, a mixture of raw materials is subjected to melting in an arc furnace, and a resulting molten mixture is cast into a die outside the arc furnace to form an ingot. However, in this production method, after melting in the arc furnace, the molten mixture is cast into the die outside the arc furnace. Thus, a cooling rate after the melting becomes greater than 10Â° C./min, i.e., the molten mixture is subjected to rapid cooling, so that resulting Al₄O₄C crystals are finely formed to have an average diameter of less than 10 Î¼m.

Differently, in the case where a mixture of raw materials is subjected to melting in an arc furnace and then cooling within the arc furnace without any transfer, the cooling rate becomes equal to or less than 10Â° C./min, i.e., a molten mixture is subjected to slow cooling, so that Al₄O₄C crystals grow in the course of the slow cooling to have an average diameter of 20 Î¼m or more. In some cases, in addition to Al₄O₄C crystals, the aluminum oxycarbide composition comprises corundum crystals, and further contains Al₂OC, oxynitride such as AlON, and/or Î³-Al₂O₃, in a small amount.

As above, the Al₄O₄C crystals have an average diameter of 20 Î¼m or more. This makes it possible to suppress oxidation of Al₄O₄C during use to maintain advantageous effects of Al₄O₄C for a long time. In addition, when the aluminum oxycarbide composition contains corundum crystals, the corundum crystals can function as barrier to suppress the oxidation of Al₄O₄C, so that it becomes possible to more reliably maintain the advantageous effects of Al₄O₄C for a long time. Although an upper limit of the average diameter of the Al₄O₄C crystals is not particularly limited, it is preferably set to 3 mm or less, because a particle size usable as an aggregate raw material for a refractory material is generally about 3 mm in a coarse particle fraction.

Preferably, the aluminum oxycarbide composition of the present invention has a layered microstructure in which the Al₄O₄C crystals and the corundum crystals alternately lie in layered relationship. As mentioned above, it is known that Al₄O₄C is oxidized in an oxidation atmosphere at 850Â° C. and transformed into alumina If Al₄O₄C is oxidized and transformed into alumina, it becomes impossible to obtain an anti-oxidation effect, a corrosion resistance enhancement effect and an effect based on low thermal expansion coefficient, which are innate features of Al₄O₄C. In the microstructure where corundum crystals lie in layers, the corundum crystal layers are effective in protecting Al₄O₄C crystals from oxidation, and highly effective in suppressing oxidation of the entire aluminum oxycarbide composition, so that it becomes possible to maintain the above features of Al₄O₄C for a long time.

Preferably, the aluminum oxycarbide composition of the present invention contains carbon in an amount of 3.2 to 6.3 mass %. This carbon content gives an indication of an amount of Al₄O₄C contained in an aluminum oxycarbide composition. Specifically, a theoretical carbon content in Al₄O₄C is 6.52 mass %. When a carbon content in an aluminum oxycarbide composition is 6.52 mass %, an Al₄O₄C content in the aluminum oxycarbide composition is 100 mass %. If the carbon content in the aluminum oxycarbide composition is less than 3.2 mass %, an amount of Al₄O₄C is reduced, so that it is likely that the advantageous effects of Al₄O₄C cannot be sufficiently obtained. On the other hand, if the carbon content is greater than 6.3 mass %, formation of aluminum carbide susceptible to hydration becomes more likely to occur, resulting in poor microstructural stability. Moreover, an amount of corundum crystals becomes reduced or zero, so that an oxidation suppression effect of Al₄O₄C is deteriorated, which causes difficulty in maintaining Al₄O₄C in an oxidation atmosphere for a long time.

As mentioned above, the aluminum oxycarbide composition of the present invention may be produced by subjecting a carbon-based raw material and an alumina-based raw material to melting in an arc furnace and then cooling (slowly cooling) within the arc furnace.

As the carbon-based raw material, it is possible to use a carbon-based raw material which is commonly used as a raw material for a refractory material. For example, the usable carbon-based raw material includes pitch, graphite, coke, carbon black and powdered organic resin. Among them, as graphite, it is possible to use flaky graphite, earthy (amorphous) graphite, expanded graphite and/or artificial graphite. A content rate of carbon (C content rate) of the carbon-based raw material may be 90 mass % or more, preferably, 95 mass % or more.

As the alumina-based raw material, it is possible to use an alumina-based raw material which is commonly used as a raw material for a refractory material. For example, the usable alumina-based raw material includes fused alumina, sintered alumina and/or calcinated alumina, which are prepared by artificially refining natural bauxite or the like through a Bayer process or the like, to allow an Al₂O₃purity to become 95 mass % or more. It is also possible to use China bauxite, bauxite, clay and/or brick dust to an extent that an Al₂O₃purity in the entire alumina-based raw material is preferably 90 mass % or more, more preferably, 95 mass % or more

In the present invention, a refractory material containing carbon and alumina, such as an alumina-carbon based or alumina-graphite based refractory material, may be used as the carbon-based raw material and the alumina-based raw material. In this case, a total content of carbon and alumina with respect to the entirety of the carbon-based raw material and the alumina-based raw material is adjusted to 90 mass % or more, preferably, 95 mass % or more. Further, it is preferable that a mole ratio of carbon to alumina (C/Al₂O₃) in the entirety of the carbon-based raw material and the alumina-based raw material is adjusted to a range of 0.8 to 2.0.

Al₄O₄C is formed through the following reaction (1). Thus, ideally, a mole ratio of the carbon-based raw material to the alumina-based raw material is set to 1.5.

2Al₂O₃+3C=Al₄O₄C+2 COâ€ƒâ€ƒ(1)

The carbon content (Al₄O₄C content) in the aluminum oxycarbide composition can be controlled to some extent by adjusting a content of the carbon-based raw material. However, in typical melting conditions, carbon is oxidized to form a large amount of corundum (Al₂O₃), although the reason is not clear. Moreover, local formation of Al₄C₃and other problem occur.

It is believed that the local formation of Al₄O₃is due to an influence of a melting atmosphere depending on a type of arc furnace, a voltage condition, etc. Considering practical mass production, it is necessary to use a large arc furnace and perform melting at high voltage or electric power. In this case, the melting atmosphere becomes an oxidation atmosphere. Thus, it is considered that Al₄O₄C is less likely to be formed, and formation of corundum (Al₂O₃) is accelerated.

Therefore, preferably, one or more selected from the group consisting of silicon carbide, boron carbide, aluminum nitride, boron nitride and a metal, are added to the carbon-based raw material and the alumina-based raw material in an amount of 0.2 to 10.0 mass % with respect to and in addition to a total amount of the carbon-based raw material and the alumina-based raw material, whereafter the obtained mixture is subjected to melting in the arc furnace.

Based on adding an antioxidant such as a metal in the above manner, it becomes possible to suppress oxidation of the carbon-based raw material due to an atmosphere during melting and cooling, to efficiently induce reaction between and melting of the carbon-based raw material and the alumina-based raw material, although details of the mechanism is unclear. A melting point of Al₄O₄C is in a high-temperature region of 1850Â° C. or less. On the other hand, it is considered that formation of Al₄O₄C occurs at an appropriate temperature ranging from 1000Â° C. (which would cause sintering reaction) to 1850Â° C. (which causes formation of a liquid phase). Thus, the metal to be added in the present invention is required to have oxygen affinity stronger than that of carbon, in a temperature range of 1000Â° C. or more.

It is believed that the added metal in the present invention reacts with carbon monoxide generated by a reaction between alumina and carbon, e.g., an aftermentioned reaction (2), to immobilized carbon which would otherwise disappear as the carbon monoxide to exert an effect of increasing the yield of carbon.

When silicon is added as the metal, the following reaction (2) occurs.

2CO+Si=SiO₂+2Câ€ƒâ€ƒ(2)

The metal to be added in the present invention is used in the form of a metal power or a solid metal blank, to suppress oxidation of the carbon-based raw material and Al₄O₄C due to an atmosphere during melting and cooling (i.e., during production). Therefore, a metal is used which has oxygen affinity stronger than that of carbon, in a temperature range equal to or greater than 500Â° C. at which oxidation of carbon starts, preferably, equal to or greater than 1000Â° C. which would cause formation of Al₄O₄C. Specifically, for example, it is possible to use one or more selected from the group consisting of Si, Mn, Al, Ca, Mg, Zr, and Ti. Further, an alloy containing one or more of the above metals may also be used. Although a purity of the metal or alloy is not particularly limited, the metal or alloy preferable has a purity of 90% or more.

In another embodiment of the present invention, instead of or in addition to a metal, one or more selected from the group consisting of silicon carbide, boron carbide, aluminum nitride and boron nitride are added.

It is assumed that each of silicon carbide (SiC), boron carbide (B₄C), aluminum nitride (AlN) and boron nitride (BN) exerts a function of suppressing oxidation of the carbon-based raw material during melting and cooling due to an atmosphere, to efficiently induce reaction between and melting of the carbon-based raw material and the alumina-based raw material, as with the metal, although details of the mechanism is unclear. For example, in the case of adding SiC, it is assumed that carbon is efficiently eluted therefrom into the molten raw materials to contribute to formation of Al₄O₄C.

As the silicon carbide, boron carbide, aluminum nitride or boron nitride to be added in the present invention, it is possible to use a type which is commonly used as an antioxidant for carbon, or the like, in the technical field of refractory materials. Although a purity thereof is not particularly limited, it preferable has a purity of 90% or more.

Preferably, the raw materials in the present invention, such as the carbon-based raw material, the alumina-based raw material, the metal and the silicon carbide, are homogeneously mixed together to allow a dispersion in C component to fall within Â±10%. Based on preliminarily homogeneously mixing the raw materials, it becomes possible to increase the yield of Al₄O₄C, while suppressing formation of Al₄C₃.

As used here, the term â€œhomogeneously mixed (homogeneous mixing)â€ means a state in which dispersion is significantly reduced when the mixture of the raw materials is sampled. In the present invention, an index of the homogeneous mixing is represented by a dispersion in C component. As used here, the term â€œdispersion in C componentâ€ means a ratio (%) of a difference between a specific one of a plurality of analysis values, and a preset target value of the C component, to the preset target value, wherein the plurality of analysis values are obtained by taking a sample three times from the mixture of the raw materials, and analyzing respective C components of the sampled mixtures, and the specific analysis value has the largest difference with the preset target value. The dispersion in C component is set to fall, preferably, within Â±10%, more preferably within Â±5%. In order to achieve the homogeneous mixing, it is preferable to perform mixing using a commercially available powder mixer. The term â€œpreset target value (%)â€ means [a ratio (%) of the carbon-based raw material to the mixture of the raw materials]Ã—[a content rate (%) of C component in the carbon-based raw material], wherein the content rate (%) of the C component in the carbon-based raw material is a measurement value before the mixing.

As the arc furnace, it is possible to use a type which is commonly used to melt a refractory material such as magnesia or alumina so as to produce a refractory material. In the arc furnace, the mixture of the carbon-based raw material and the alumina-based raw material with other raw material added thereto according to need, such as the metal, is melted. Specifically, the mixture is melted at a temperature of about 1850 to 2400Â° C. After the melting, the molten mixture is cooled to form an ingot, and the ingot is pulverized to obtain an aluminum oxycarbide composition.

In the present invention, a mole ratio of carbon in the carbon-based raw material to alumina in the alumina-based raw material (C/Al₂O₃) may be controlled in a range of 0.8 to 2.0 to control a content rate of Al₄O₄C.

The aluminum oxycarbide composition of the present invention can be suitably used as a raw material for a refractory material, particularly, aggregate (particle size: 0.2 mm or more). When the aluminum oxycarbide composition of the present invention is used as a raw material for a refractory material, it is preferably contained in an amount of 15 to 95 mass %. If the content of the aluminum oxycarbide composition is less than 15 mass %, it is likely that the advantageous effects of the aluminum oxycarbide composition cannot be sufficiently obtained. On the other hand, if the content is greater than 95 mass %, an amount of carbon to be added in order to reduce an elastic modulus, an amount of a metal to be added as a anti-oxidation or sintered material or an antioxidant such as a metal, a carbide, a nitride or a boride, and an amount of phenolic resin to be added as a binder, are restricted, so that it becomes difficult to obtain sufficient characteristics as a refractory material, such as strength, elastic modulus and oxidation resistance.

EXAMPLES

Aluminum oxycarbide compositions were produced by the method of the present invention designed to subject a mixture of raw materials to melting in an arc furnace and then cooling (slow cooling) within the arc furnace, and by the conventional method designed to subject the mixture to melting in an arc furnace, and then a resulting molten mixture is cast into a die outside the arc furnace and subjected to rapid cooling, and characteristics thereof were evaluated. A result of the evaluation is illustrated in the following Table 1.

TABLE 1 is shown in FIG. 3.

At respective ratios illustrated in Table 1, calcinated alumina (Al₂O₃component: 99.9 mass %) and flaky graphite (C component: 99 mass %) were weighted by a total amount of 500 kg. As for the inventive samples 1 to 6, 8 and 9 and the comparative sample 2, Al, Si or SiC was added thereto with respect to and in addition to a total 100 mass % of the calcinated alumina and the flaky graphite

As for the inventive samples 1 to 5, 8 and 9 and the comparative sample 2, the above raw materials were blended, and mixed together by a V-Cone mixer for 5 minutes. As for the inventive samples 6 and 7 and the comparative sample 1, the homogeneous mixing treatment was not performed. The dispersion in C component of the raw material mixture was evaluated by the aforementioned method.

The raw material mixture was put in a 1000 KVA arc furnace, and subjected to melting. Then, the molten mixture in each of the inventive samples was subjected to slow cooling without transfer to the outside, and the molten mixture in each of the comparative samples was cast into a die outside the arc furnace. In this way, ingots of inventive and comparative aluminum oxycarbide compositions were produced. A cooling rate in each of the inventive samples was set to about 0.7Â° C./min, and a cooling rate in each of the comparative samples was set to about 15Â° C./min.

Each of the produced ingots of the aluminum oxycarbide compositions was subjected to pulverization and particle size regulation, and then an apparent porosity and an apparent specific gravity were measured according to JIS-R2205. In regard to a chemical composition, a C content was measured according to JIS-R2011. The C content was evaluated by a total carbon amount which is a sum of free carbon described in JIS-R2205, and carbon in silicon carbide. Specifically, considering that oxidation of Al₄O₄C starts at a temperature of 820Â° C. or more, the carbon content was evaluated by a sum of a carbon amount measured at 900Â° C. and a carbon amount in silicon carbide measured at 1350Â° C. The theoretical C content in Al₄O₄C is 6.52 mass %.

A mineral phase was quantified by an internal reference method based on X-ray diffractometry.

A microstructure of the aluminum oxycarbide composition was observed by a microscope. As mentioned above, an average diameter of Al₄O₄C crystals means an average value of diameters based on the assumption that respective cross-sectional areas of the Al₄O₄C crystals are cumulatively added in descending order of cross-sectional area until a cumulative addition value becomes greater than a half of the entire area of an observation field of view during microscopic observation of the aluminum oxycarbide composition, and a cross-sectional area of each of a plurality of specific ones of the Al₄O₄C crystals subjected to the cumulative addition is converted into a diameter of a circle having the same area as the cross-sectional area.

A rectangular columnar sample having a size of 8Ã—8Ã—12 mm was directly cut from each of the ingots, and a thermal expansion coefficient was measured in an ambient atmosphere up to 1000Â° C. by thermo-mechanical analysis (TMA). Further, in order to evaluate a thermal expansion coefficient maintenance ratio after oxidation of the aluminum oxycarbide composition, the rectangular columnar sample of 8Ã—8Ã—12 mm was subjected to an oxidation treatment under an ambient atmosphere at 1500Â° C. for 3 hours, and the thermal expansion coefficient was measured in an ambient atmosphere up to 1000Â° C. by thermo-mechanical analysis (TMA) in the same manner.

Alumina transformation rate=[(Al₄O₄C amount before oxidation testâˆ’Al₄O₄C amount after oxidation test)/Al₄O₄C amount before oxidation test]Ã—100â€ƒâ€ƒ[Formula 1]

In view of the fact that when Al₄O₄C is oxidized, it is transformed to alumina (corundum), oxidation resistance was evaluated by calculating an alumina transformation rate indicative of an Al₄O₄C decrease rate (corundum increase rate). The alumina transformation rate is expressed as the following formula:

Specifically, a sample having a size of 10Ã—10Ã—10 mm was cut from each of the ingots, and subjected to an to an oxidation treatment under an ambient atmosphere at a temperature of 1500Â° C. for 3 hours using a rotary furnace. Then, a carbon content was measured, and the alumina transformation rate was calculated by comparison with a carbon content preliminarily measured before the oxidation test. The aluminum oxycarbide composition primarily consists of corundum and Al₄O₄C, and contains other components in an extremely small amount. Thus, an Al₄O₄C content can be calculated by measuring a carbon content. Therefore, carbon contents before and after the oxidation test were measured to derive Al₄O₄C contents before and after the oxidation test, and calculate the alumina transformation rate.

As is evident from Table 1, all of the inventive samples in which the average diameter of Al₄O₄C is 20 Î¼m or more, are excellent in oxidation resistance. On the other hand, the comparative samples in which the average diameter of Al₄O₄C is less than 10 Î¼m, are inferior in terms of oxidation resistance.

In regard to a thermal expansion coefficient of the aluminum oxycarbide composition oxidized at 1500Â° C. in an ambient atmosphere, all of the inventive samples 1 to 9 in which the average diameter of Al₄O₄C is 20 Î¼m or more, maintain a low thermal expansion coefficient. On the other hand, the comparative samples 1 and 2 in which the average diameter of Al₄O₄C is less than 10 Î¼m, have an increased thermal expansion coefficient.

A comparison between the inventive sample 2 and the inventive sample 6 shows that the yield (content rate) of Al₄O₄C is enhanced by preliminarily homogenously mixing the raw materials. However, from a comparison between the inventive sample 2 and the comparative sample 2, it is proven that an effect of enhancing the oxidation resistance cannot be obtained only by the preliminarily homogenous mixing of the raw materials.

A comparison between each of the inventive samples 6, 8 and 9 and the inventive sample 7 shows that the yield (content rate) of Al₄O₄C is enhanced by adding an antioxidant such as a metal.

FIG. 1 illustrates a microstructure of the inventive sample 2, and FIG. 2 illustrates a microstructure of the comparative sample 1. It is proven that, in the inventive sample 2, columnar Al₄O₄C crystals having a short diameter of about 50 to 250 Î¼m, and columnar corundum crystals having a short diameter of about 30 to 300 Î¼m or corundum-Al₄O₄C co-crystals, grow while alternately lying in layered relationship. On the other hand, in the comparative sample 1, each of Al₄O₄C crystals and corundum crystals is finely formed to have an average diameter of less than 10 Î¼m.

Then, three types of carbon-containing refractory materials were produced by using the aluminum oxycarbide compositions of the inventive sample 2 and the comparative samples 1 and 2, and characteristics thereof were evaluated. A result of the evaluation is illustrated in the following Table 2.

TABLE 2 is shown in FIG. 4.

The various raw materials were blended at respective ratios illustrated in Table 2, and, after adding a phenolic resin as a binder thereto in an amount of 5 mass % with respect to and in addition to a total amount of the raw materials, subjected to mixing and shaping. Then, the resulting shaped body was heated at a temperature of 300Â° C. to produce a carbon-containing refractory material.

The produced carbon-containing refractory material was evaluated in terms of bulk specific gravity, apparent porosity, thermal expansion coefficient, corrosion resistance, oxidation resistance, liquid-phase oxidation resistance and thermal shock resistance.

The bulk specific gravity and the apparent porosity were evaluated by the method described in JIS-R2205. The thermal expansion coefficient was evaluated in a nitrogen atmosphere up to 1000Â° C. by the non-contact method described in JIS-R2207-1.

The corrosion resistance was evaluated by melting an SS material and an iron oxide powder using a high-frequency induction furnace to prepare synthetic slag having a CaO/Al₂O₃ratio of 2.2, and subjecting a sample to a corrosion resistance test in the synthetic slag at 1600Â° C. for 3 hours to measure a wear amount. Then, the obtained measurement value was converted into an index value on an assumption that a wear amount of the comparative sample 5 in the aftermentioned Table 3 is 100. A smaller value indicates better corrosion resistance.

The liquid-phase oxidation resistance was evaluated by melting an SS material using a high-frequency induction furnace, and subjecting a sample to a liquid-phase oxidation resistance test in the molten steel at 1600Â° C. for 5 hours to measure a thickness of an oxide layer on a steel bath portion. Then, the obtained measurement value was converted into an index value on an assumption that a thickness of an oxide layer of the comparative sample 5 in the aftermentioned Table 3 is 100. A smaller value indicates better liquid-phase oxidation resistance.

The thermal shock resistance was evaluated by repeating a cycle of immersing a sample in molten steel at 1600Â° C. for 3 minutes and subjecting the sample to air cooling, to determine quality based on the number of cycles before occurrence of peeling (spalling). Specifically, the thermal shock resistance was evaluated by an average cycle number in two samples before the occurrence of peeling. A larger value indicates better thermal shock resistance.

Table 2 shows that the inventive sample 10 using the aluminum oxycarbide composition of the inventive sample 2 in Table 1 is superior to the comparative samples 3 and 4 using respective ones of the aluminum oxycarbide compositions of the comparative samples 1 and 2 in Table 1, in terms of corrosion resistance, liquid-phase oxidation resistance and thermal shock resistance. In the inventive sample 10, Al₄O₄C was maintained for a long time without being oxidized even under the high-temperature testing condition. It is considered that the result comes from excellent corrosion resistance based on improvement in wettability with slag, which is one feature of Al₄O₄C. Further, in view of the fact that Al₄O₄C is also maintained in the liquid-phase oxidation test, it is believed that oxidation resistance in a high temperature region is enhanced. It is considered that the effect of enhancing liquid-phase oxidation resistance comes from a high oxidation suppression effect based on a dense Al₂O₃layer formed through a reaction between Al₄O₄C and FeO. Further, in view of the fact that Al₄O₄C is maintained under the repetitive high-temperature heat treatments in the thermal shock resistance test, it is believed that spalling resistance is improved by the low thermal expansion coefficient-based effect. In contrast, each of the aluminum oxycarbide compositions of the comparative samples 3 and 4 were oxidized and transformed into Al₂O₃under the high-temperature testing condition, within a short period of time. It is considered that the result is due to deterioration in corrosion resistance caused by deterioration in wettability with slag, deterioration in oxidation resistance, and deterioration in spalling resistance caused by increase in thermal expansion coefficient.

Then, a carbon-containing refractory material using the aluminum oxycarbide composition of the inventive sample 5 in Table 1 was produced, and characteristics thereof were evaluated. A result of the evaluation is illustrated in the following Table 3. In Table 3, the comparative sample 5 is a carbon-containing refractory material using no aluminum oxycarbide composition.

TABLE 3 is shown in FIG. 5.

Various raw materials were blended at respective ratios illustrated in Table 3, and carbon-containing refractory materials were produced by the same method as that for the samples in Table 2. Characteristics of each of the produced carbon-containing refractory materials were evaluated by the same method as that for the samples in Table 2.

All of the inventive samples were superior to the comparative sample 5 in terms of corrosion resistance, liquid-phase oxidation resistance and thermal shock resistance.