KR101900674B1 - Ceramic long fiber and ceramic short fiber using slag, base material for the same, insulation using the same, and method of fabricating of the same - Google Patents

Abstract

Provided is a method for manufacturing a ceramic long fiber using slag. The method for manufacturing a ceramic long fiber using slag comprises: a step of manufacturing first slag powder by dry-grinding slag; a step of manufacturing second slag powder by wet-grinding the first slag powder; a step of firstly manufacturing first rock powder by dry-grinding first rock; a step of secondly manufacturing the first rock powder by wet-grinding the first rock powder; a step of firstly manufacturing second rock powder by dry-grinding second rock; a step of secondly manufacturing second rock powder by wet-grinding the second rock powder; a step of mixing the second slag powder, the first rock powder, and the second rock powder, melting, draining, and cooling the same, and manufacturing an amorphous melting body; and a step of manufacturing a ceramic fiber by melting and spinning the amorphous melting body. The first rock includes higher Al_2O_3 and CaO contents than the second rock. The second rock includes higher K_2O and Na_2O contents than the first rock. The present invention can reduce manufacturing costs.

Description

TECHNICAL FIELD The present invention relates to a ceramic short fiber and a ceramic short fiber using slag, a raw material thereof, an insulating material using the same, and a method for manufacturing the same. same}

The present invention relates to a ceramic long fiber and a ceramic short fiber using slag, a raw material thereof, a heat insulating material using the same, and a manufacturing method thereof, and more particularly, to a slag and a ceramic slag, The present invention relates to a ceramic long fiber and a ceramic short fiber using the slag produced by the method, a raw material thereof, a heat insulating material using the raw material, and a manufacturing method thereof.

A wide variety of composite materials such as automotive, buses, bicycles, building cores and interior and exterior walls, tiles, fishing rods, racquets, golf clubs, musical instruments, medical devices, turbine blades for thermal power generation, aircraft bodies, defense structural materials, Are used. Such composite materials are expected to have light weight, high strength (impact strength, tensile strength, bending strength) and high reliability, while the use of composite materials is expected to increase gradually along with industrial development.

Particularly, various research and development on ceramic fibers having light weight and high strength characteristics among composites have been carried out.

For example, in Korean Patent Registration No. 10-1783911, it is possible to adjust the content of ceramics in the ceramic fibers by appropriately setting the amount of lamination of the ceramic fibers having the same specifications, and by controlling the content of aluminum impregnated in the compressed ceramic fibers, There is disclosed a method of manufacturing a composite having a specific thermal expansion coefficient using ceramic fibers by adjusting a ratio of a ceramic content and an aluminum content in a composite manufacturing process to a specific thermal expansion coefficient required for an electronic component.

For example, in Korean Patent Registration No. 10-0624094, a carbon fiber reinforced resin composite molded from a mixture containing a carbon fiber and a carbon-containing polymer precursor is prepared, the carbon fiber reinforced resin composite is heat-treated at a temperature of 700 to 2200 ° C , A pyrolytic carbon is deposited by a rapid thermal gradient chemical vapor deposition process while increasing the deposition rate from the inside to the outside of the heat-treated carbon fiber-reinforced resin composite to produce a carbon fiber-reinforced carbon composite, A method of manufacturing a carbon fiber-reinforced ceramic composite material capable of improving the physical properties of the carbon fiber-reinforced ceramic composite material and depositing the pyrolytic carbon layer at a deposition rate of 5 to 10 times or more as compared with the conventional chemical vapor phase infiltration process Lt; / RTI >

SUMMARY OF THE INVENTION The present invention provides a ceramic filament and a ceramic filament using slag as an industrial waste, a raw material thereof, a heat insulating material using the raw material, and a manufacturing method thereof.

It is another object of the present invention to provide a method for producing ceramic filament and ceramic filament using slag capable of improving mechanical strength characteristics.

It is another object of the present invention to provide a method for producing ceramic filament and ceramic filament using slag with a simplified manufacturing process.

Another object of the present invention is to provide a ceramic filament and a ceramic filament using the slag having a reduced manufacturing cost, a raw material thereof, a heat insulating material using the raw material, and a method of manufacturing the same.

The technical problem to be solved by the present invention is not limited to the above.

The present invention provides a method for producing ceramic filaments using slag.

According to an embodiment of the present invention, there is provided a method of manufacturing ceramic filament using slag, comprising the steps of: dry-grinding slag to produce a primary slag powder; wet-milling the primary slag powder to produce a secondary slag powder; A step of dry crushing the first rock to produce a first primary rock powder, wet crushing the primary primary rock powder to produce a secondary primary rock powder, A step of producing a first secondary rock powder, a step of wet pulverizing the primary secondary rock powder to produce a secondary secondary rock powder, a step of mixing the secondary slag powder, the secondary primary rock powder, And melting and spinning the second secondary rock powder to produce an amorphous melt, and melting and spinning the amorphous melt to produce ceramic fibers, wherein the first rock , The second rock Is a high Al ₂ O ₃ and CaO content, it said second mesas, than that of the first mesas, may be higher the K ₂ O and Na ₂ O content.

 According to one embodiment, the step of producing the primary slag powder, the primary primary rock powder, and the primary secondary rock powder may be performed by sequentially using a jaw crusher and a disk crusher ), The step of crushing the slag, the first rock, and the second rock.

According to one embodiment, the step of producing the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder may be carried out by using a pot mill, Powder, the primary primary rock powder, and the primary secondary rock powder.

According to one embodiment, in the step of manufacturing the amorphous molten body, the strength of the ceramic fiber can be controlled by adjusting the ratio of the secondary first rock powder.

According to one embodiment, in the step of manufacturing the amorphous molten material, the melting point of the amorphous molten material can be controlled by controlling the ratio of the secondary second rock powder.

According to one embodiment, the first rock may be a rock arch, and the second rock may be a feldspar.

According to one embodiment, the step of preparing the amorphous melt may comprise adding a binder to the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder.

According to one embodiment, in the step of producing the ceramic fiber, the molten amorphous melt may be in an amorphous state.

According to the embodiment of the present invention, the slag, the first rock, and the second rock are dry-milled and wet-milled, respectively, so that the secondary slag powder, the secondary primary rock powder, 2 rock powder is produced, and the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder are mixed, melted, and crushed to form the secondary slag powder, the secondary primary rock powder , And the amorphous molten material in which the secondary second rock powder is substantially uniformly mixed can be produced, and the ceramic fiber can be produced using the amorphous molten material. Accordingly, the ceramic fiber can be produced in the form of a long fiber in a state where the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder are substantially uniformly mixed and melted.

In addition, according to the embodiment of the present invention, ceramic short fibers can be manufactured according to the above-described manufacturing method, and in this case, manufacturing cost of the ceramic short fibers can be reduced and productivity can be improved.

The ceramic filament and the ceramic filament made according to the embodiment of the present invention may be used as a material of the FRP and the heat insulating material, respectively.

1 is a flowchart illustrating a method of manufacturing ceramic filament using slag according to an embodiment of the present invention.
FIG. 2 shows weight ratios of the secondary slag powder, the secondary ring mortar powder, and the secondary feldspar powder in the process of manufacturing the amorphous molten material according to the embodiments of the present invention.
3 is a graph showing the results of melting tests at 1400 ° C for amorphous melts according to Examples 1-1 to 1-9.
4 is a graph showing the results of melting tests at 1400 ° C for amorphous melts according to Examples 2-1 to 2-10.
5 is a graph showing the results of melting tests at 1350 ° C for amorphous melts according to Examples 3-1 to 3-3.
FIG. 6 is a high-temperature microscopic measurement result of a raw sample of slag used in the production of an amorphous molten metal according to an embodiment of the present invention.
7 is a graph showing the results of melting test of slag, ring arm, and feldspar used in the production of the amorphous molten metal according to the embodiment of the present invention.
Figs. 8 to 11 are the results of high-temperature microscopic measurement of the combination magnification according to Examples 2-6, 2-8, 2-9, and 2-10, respectively.
Fig. 12 is a photograph of a cut surface of a melt specimen of combination magnification according to Example 2-6, Example 2-8, Example 2-9, and Example 2-10 of the present invention.
13 shows the XRD measurement results for confirming the crystallinity of the amorphous melt according to Examples 2-6, 2-8, 2-9, and 2-10.
Fig. 14 shows results of melting tests of amorphous melts according to Examples 2-6, 2-8, 2-9, and 2-10 of the present invention.
Fig. 15 is a photograph of a cut surface of a molten specimen at 1500 DEG C at a combination magnification according to Examples 2-6, 2-8, 2-9, and 2-10 of the present invention.
Fig. 16 shows the results of XRD measurement for confirming the crystallinity of the amorphous molten material according to Examples 2-6, 2-8, 2-9, and 2-10 of the present invention.
17 is a graph of high temperature viscosity measurement of amorphous melts according to Examples 2-6 and 2-10 of the present invention.
18 is a photograph and an optical microscope photograph of a ceramic short fiber prepared using the amorphous molten material according to Example 2-6 of the present invention.
FIG. 19 is a photomicrograph of a ceramic filament produced using the amorphous molten material according to Example 2-6 of the present invention. FIG.
20 is a graph of XRD results of ceramic fibers produced using the amorphous molten material according to Example 2-6 of the present invention.

Hereinafter, preferred embodiments of the present invention will be described in detail with reference to the accompanying drawings. However, the technical spirit of the present invention is not limited to the embodiments described herein but may be embodied in other forms. Rather, the embodiments disclosed herein are provided so that the disclosure can be thorough and complete, and will fully convey the scope of the invention to those skilled in the art.

Also, while the terms first, second, third, etc. in the various embodiments of the present disclosure are used to describe various components, these components should not be limited by these terms. These terms have only been used to distinguish one component from another. Thus, what is referred to as a first component in any one embodiment may be referred to as a second component in another embodiment. Each embodiment described and exemplified herein also includes its complementary embodiment. Also, in this specification, 'and / or' are used to include at least one of the front and rear components.

The singular forms "a", "an", and "the" include plural referents unless the context clearly dictates otherwise. It is also to be understood that the terms such as " comprises "or" having "are intended to specify the presence of stated features, integers, Should not be understood to exclude the presence or addition of one or more other elements, elements, or combinations thereof.

In the following description of the present invention, a detailed description of known functions and configurations incorporated herein will be omitted when it may make the subject matter of the present invention rather unclear.

1 is a flowchart illustrating a method of manufacturing ceramic filament using slag according to an embodiment of the present invention.

Referring to FIG. 1, slag is prepared. The slag may be blast furnace slag. The slag may be dry pulverized to produce a primary slag powder (S110). According to one embodiment, the slag may be sequentially pulverized using a jaw crusher and a disk crusher. More specifically, for example, the slag may be pulverized to a standard netting range of 10 to 60 mesh using a Jaw Crusher and then pulverized using a disk crusher to a standard of 60 to 140 mesh Can be pulverized into a netted area.

The primary slag powder produced by crushing the slag may be wet pulverized to produce a secondary slag powder (S115). According to one embodiment, the primary slag powder may be pulverized using a pot mill. More specifically, for example, the primary slag powder may be pulverized to a standard netting range of 200 to 325 mesh using a pot mill.

The first rock is prepared. The first rock may be a rock having a relatively high Al ₂ O ₃ and CaO content. Specifically, the first rock may have a higher content of Al ₂ O ₃ and CaO than the second rock described later. For example, the first rock may be a rocking arm.

The first rock may be dry-pulverized to produce a first primary rock powder (S120). According to one embodiment, the first rock may be sequentially pulverized using a jaw crusher and a disk crusher. More specifically, for example, the first rock is pulverized to a standard netting range of 10 to 60 mesh using a Jaw Crusher, and then pulverized using a disk crusher to a size of 60 to 140 mesh Lt; RTI ID = 0.0 > of < / RTI >

The first primary rock powder produced by crushing the first rock may be wet pulverized to produce a secondary primary rock powder (S125). According to one embodiment, the primary rock powder may be pulverized using a pot mill. More specifically, for example, the primary first rock powder may be pulverized to a standard netting range of 200 to 325 mesh using a pot mill.

A second rock is prepared. The second rock may be a rock having a relatively high K ₂ O and Na ₂ O content. Specifically, the second rock may have a higher K ₂ O and Na ₂ O content than the first rock. For example, the second rock may be a feldspar.

The second rock may be dry pulverized to produce a primary second rock powder (S130). According to one embodiment, the second rock may be sequentially pulverized using a jaw crusher and a disk crusher. More specifically, for example, the second rock is pulverized to a standard netting range of 10 to 60 mesh using a jaw crusher, and then pulverized using a disk crusher to a size of 60 to 140 mesh Lt; RTI ID = 0.0 > of < / RTI >

The secondary second rock powder may be produced by wet pulverizing the primary secondary rock powder produced by crushing the secondary rock (S135). According to one embodiment, the secondary rock powder may be pulverized using a pot mill. More specifically, for example, the primary second rock powder may be pulverized to a standard netting range of 200 to 325 mesh using a pot mill.

(S110, S115) of preparing the secondary slag powder by dry and wet pulverizing the slag as described above, and dry and wet pulverizing the primary rock to produce the secondary primary rock powder (S130, S125), and the second secondary rock powder (S130, S135) are sequentially performed by dry and wet pulverizing the secondary rock. However, in the manufacturing of the secondary slag powder, The order of performing the second primary rock powder preparation step and the secondary secondary rock powder production step is not limited. Also, the step of producing the secondary slag powder, the step of producing the secondary first rock powder, and the step of producing the second secondary rock powder may be performed in parallel.

Further, as described above, dry grinding and wet grinding can be sequentially performed on the slag, the first rock, and the second rock, respectively. Thereby, the slag, the first rock, and the secondary slag powder produced from the second rock, the secondary primary rock powder, and the secondary secondary rock powder have a substantially uniform size, It can be easily pulverized.

The amorphous molten material may be prepared by mixing, melting and cooling the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder (S140).

In the amorphous molten material, the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder may be mixed, melted, drained, and then quenched . Accordingly, the amorphous molten material may be produced in an amorphous state. As a result, as described later, the amorphous molten material is easily melted and radiated, so that the ceramic fiber can be easily produced.

The slag powder, the secondary slag powder, the secondary slag powder, the secondary slag powder, the secondary slag powder, the secondary slag powder, the secondary slag powder, the secondary slag powder, And the ratio of the secondary second rock powder can be controlled. Thus, the ratio of the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder in the ceramic fiber produced from the amorphous molten material can be easily controlled. In other words, in the ceramic fiber, the composition ratio of the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder is such that the secondary slag powder, the secondary primary rock powder, And the second secondary rock powder composition ratio.

Specifically, as described above, when the first rock has a higher Al ₂ O ₃ and CaO content than the second rock, in the step of producing the amorphous molten material, the ratio of the secondary first rock powder is So that the strength of the ceramic fiber can be controlled. For example, the higher the ratio of the secondary first rock powder, the greater the strength of the ceramic fiber.

As described above, when the second rock has a higher content of K ₂ O and Na ₂ O than the first rock, in the step of producing the amorphous molten mass, the ratio of the second secondary rock powder is By controlling, the melting point of the amorphous melt can be controlled. For example, the higher the ratio of the secondary second rock powder, the lower the melting point of the amorphous melt.

According to one embodiment, the secondary slag powder is 50 to 80 wt%, the secondary primary rock powder is 10 to 40 wt%, the secondary secondary rock powder is 10 to 40 wt%, the heating rate is 2 to 3 Deg.] C / min and the maximum melting temperature is maintained at 1500 [deg.] C for 2 hours, the amorphous molten material may be provided in an amorphous state.

According to one embodiment, in the manufacturing process of the amorphous molten material, depending on the ratio of the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder, the secondary slag powder, The cooling rate (temperature-sensing rate) can be controlled in the course of cooling, mixing, melting and draining the first rock powder and the second secondary rock powder. Concretely, for example, when the ratio of the slag powder or the secondary first rock powder is high as compared with the secondary secondary rock powder, the cooling rate may be fast. Thus, the melt can be easily produced in an amorphous state.

According to one embodiment, the size of the secondary first rock powder and the secondary second rock powder may be different from each other. Specifically, the size of the secondary second rock powder may be smaller than the size of the secondary primary rock powder. Accordingly, the filling ratio of the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder can be improved during the production of the amorphous molten material. In addition, as described above, when the second rock has a higher K ₂ O and Na ₂ O content than the first rock, the secondary second rock powder is more uniformly dispersed, and the melting point of the amorphous melt Can be improved. Accordingly, the ceramic filament can be easily produced using the amorphous molten material.

In the process of producing the amorphous molten material, a binder (for example, PVA) may be added to the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder. In this case, according to one embodiment, a binder may be added after the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder are melted. Thus, the bubbles trapped between the binder and the powder can minimize the generation of bubbles in the amorphous melt.

The amorphous molten material may be melted and spun to produce the ceramic fiber (S150). The ceramic fiber may be a long fiber. Melting and spinning of the amorphous melt can be performed using a variety of equipment to the extent that those skilled in the art can employ it.

According to one embodiment, in the step of producing the ceramic fiber, the molten amorphous melt may be in an amorphous state.

According to an embodiment, the step of melting the amorphous molten material may include a step of firstly heating the amorphous molten material to a reference temperature at a first temperature increasing rate, a step of heating the amorphous molten material at a second temperature increasing rate lower than the first temperature increasing rate Melting the amorphous melt at the melting temperature for a reference time, heating the amorphous melt to a stabilization temperature higher than the reference temperature and lower than the melting temperature, and heating the amorphous melt at the stabilization temperature To the melting temperature at a third heating rate may be repeated a plurality of times. Thus, the amorphous molten material can be stably melted and a homogeneous melt in which the bubbles are removed can be produced. As a result, the ceramic filament can be easily produced from the melt.

As described above, according to the embodiment of the present invention, the slag, the first rock, and the second rock are dry-milled and wet-milled, respectively, so that the secondary slag powder, the secondary primary rock powder, Mixing, melting, draining and cooling the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder to produce the secondary slag powder, the secondary slag powder, The amorphous molten material in which the secondary first rock powder and the secondary second rock powder are mixed substantially uniformly can be produced and the ceramic filament can be produced using the amorphous molten material. Accordingly, the ceramic filament can be produced in a state where the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder are substantially uniformly mixed and melted.

In addition, the technical idea according to the embodiment of the present invention described above can be applied to a method of manufacturing a ceramic short fiber. In this case, the melting temperature of the amorphous melt for producing the ceramic staple fiber can be lowered by about 300 DEG C or more, thereby saving energy required for manufacturing the ceramic staple fiber, improving the productivity, Refractories in electric furnaces or gas furnaces are saved, so that the manufacturing cost can be reduced.

The ceramic filament made according to the embodiment of the present invention may be used in an FRP (fiber reinforced plastic) composite material, and the FRP composite material including the ceramic filament produced according to an embodiment of the present invention may be used in automobiles. aircraft. Ship and other transport and construction. Can be widely used as industrial fibers for civil engineering and the like, thereby contributing to industrial development.

In addition, the ceramic staple fibers produced according to the embodiment of the present invention can be used as a raw material for a heat insulating material, and the insulating shortening property of the heat insulating material can be improved by the ceramic staple fibers produced according to the embodiment of the present invention have.

Hereinafter, specific experimental examples according to the embodiments of the present invention described above will be described.

Slag, Palladium Arm, and Feldspar Preparation

The blast furnace slag produced as industrial waste during the pig iron process was prepared with the slag, and the feldspar rock produced from Gyeongnam Sancheong was prepared as the first rock, and the feldspar produced from the second rock was produced at Jangam -

<Table 1> shows the chemical composition analysis results of slag, ring rock and feldspar. As shown in Table 1, the ignition loss of the slag was obtained by melting the slag raw material powder in a platinum crucible at a melting temperature of 1400 ° C.

use
Raw material Chemical composition (wt%) SiO ₂ Al ₂ O ₃ Fe ₂ O ₃ CaO MgO K ₂ O Na ₂ O TiO ₂ Weight loss Slag 32.8 13.1 0.49 41.2 3.47 0.45 0.75 0.64 1.75 Bowel cancer 49.6 31.7 1.04 13.7 0.36 0.52 2.78 0.14 - Seaweed 76.02 14.16 0.14 0.33 0.03 4.05 4.22 - -

Slag, pearl arm, and feldspar crushing

The slag was first crushed into a jaw crusher in a standard mesh of 10 meshes in a 60 mesh range and then pulverized in a disk grinder in a secondary crusher in a standard mesh of 60 mesh to 140 mesh to prepare a primary slag powder. Then, 2.5 Kg of the primary slag powder was put into a 3 Kg pot mill for wet granulation to prepare a secondary slag powder. In order to obtain a powder having a particle size of 325 mesh at a mesh size of 200 mesh, the mesh mesh was reduced to less than 1% in a standard mesh of 200 mesh after wet grinding for 10 hours. The secondary slag powder was excluded and dried in a dryer at 110 ± 5 ° C for 3 hours.

Secondary feldspathic rock and secondary feldspar powder were prepared by the same method as that of slag in order to obtain granular rocks and feldspar as fine granular materials.

Manufacture of amorphous melt

Secondary slag powder, secondary feldspar powder, and feldspar powder prepared by the above-mentioned method and PVA (0.5%) as a molding binder were prepared. Secondary slag powder, secondary feldspar powder and secondary feldspar powder and 5 mL of PVA were added to a 250 ml alumina crucible to control the concentration pressure to 250 kg / cm 2 and the temperature raising rate to 1500 Deg.] C, and the melt holding time was controlled to be 2 hours at the maximum temperature to prepare an amorphous molten body.

The weight ratios of the secondary slag powder, the secondary ring mortar powder, and the secondary feldspar powder prepared according to the examples are summarized in Table 2 below and FIG. FIG. 2 shows weight ratios of the secondary slag powder, the secondary ring mortar powder, and the secondary feldspar powder in the process of manufacturing the amorphous molten material according to the embodiments of the present invention.

Category 1 Category 2 Slag Bowel cancer feldspar Example 1 Example 1-1 4 One 5 Examples 1-2 3 2 5 Example 1-3 2 3 5 Examples 1-4 3 3 4 Examples 1-5 4 4 2 Examples 1-6 2 One 7 Examples 1-7 3 One 6 Examples 1-8 2 6 2 Examples 1-9 2 4 4 Example 2 Example 2-1 8 One One Example 2-2 7 2 One Example 2-3 7 One 2 Examples 2-4 6 3 One Example 2-5 6 2 2 Examples 2-6 6 One 3 Examples 2-7 5 4 One Examples 2-8 5 3 2 Examples 2-9 5 2 3 Examples 2-10 5 One 4 Example 3 Example 3-1 8 2 - Example 3-2 7 3 - Example 3-3 6 4 -

As shown in Table 2 and FIG. 2, the composition table was divided into Examples 1 to 3.

In the case of Example 1, the slag, which is a main raw material, was adjusted from 20% to 40%, and amorphous melts were produced while varying the range of the arm length from 60% to 10% and the feldspar from 20% to 70%. In FIG. 2, it can be seen that the first embodiment is formed at the lower end portion as shown in the triangular coordinates. In this case, the slag used as the blast furnace slag is relatively small, and the use of relatively large amount of the feldspar and feldspar as additives is intended to lower the melting temperature of the composition.

In the case of Example 2, the slag composition range was increased by 10% from 50% to 80%, and from 10% to 40%, and feldspar was changed from 10% to 40% An amorphous melt was prepared. In the case of such a composition, the composition range of the slag is increased, and a good melting point range is confirmed, so as to obtain economical production effect in the future. In the case of Example 2, as shown in Fig. 2, it can be seen that the composition range is concentrated in the upper portion.

In the case of Example 3, the range of the slag as the main raw material was changed from 60% to 80%, the change of the ring arm was changed from 20% to 40%, and the melting state when feldspar was not added was examined.

<Table 3> to <Table 11>, <Table 12> to <Table 21>, and <Table 22> to <Table 24> are shown in Examples 1-1 to 1-9, The chemical compositions of the compositions of the amorphous melts according to Example 2-10 and Examples 3-1 to 3-3 were analyzed.

Example 1-1 Slag (4) Arm rests (1) Feldspar (5) Composition SiO ₂ 13.12 4.96 38.01 56.808 Al2O ₃ 5.24 3.17 7.08 20.964 CaO 16.48 1.37 0.165 13.852 MgO 1.388 0.036 0.015 0.85 Na ₂ O 0.3 0.278 2.11 2.95 K ₂ O 0.18 0.052 2.025 1.918 Fe ₂ O ₃ 0.196 0.104 0.07 0.57 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.256 0.014 0 0.184

Examples 1-2 Slag (3) Arm rests (2) Feldspar (5) Composition SiO ₂ 9.84 9.92 38.01 57.77 Al2O ₃ 3.93 6.34 7.08 17.35 CaO 12.36 2.74 0.165 15.265 MgO 1.041 0.072 0.015 1.128 Na ₂ O 0.225 0.556 2.11 2.891 K ₂ O 0.135 0.104 2.025 2.264 Fe ₂ O ₃ 0.147 0.208 0.07 0.425 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.192 0.028 0 0.22

Example 1-3 Slag (2) Arm prostheses (3) Feldspar (5) Composition SiO ₂ 6.56 14.88 38.01 59.45 Al2O ₃ 2.62 9.51 7.08 19.21 CaO 8.24 4.11 0.165 12.52 MgO 0.69 0.11 0.015 0.82 Na ₂ O 0.15 0.83 2.11 3.09 K ₂ O 0.135 0.104 2.025 2.264 Fe ₂ O ₃ 0.09 0.16 0.07 0.48 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.13 0.04 0 0.17

Examples 1-4 Slag (3) Arm prostheses (3) Feldspar (4) Composition SiO ₂ 9.84 14.88 30.41 55.13 Al2O ₃ 3.93 9.51 5.66 19.10 CaO 12.36 4.11 0.13 16.60 MgO 1.041 0.11 0.01 1.16 Na ₂ O 0.225 0.83 1.69 2.75 K ₂ O 0.135 0.16 1.62 1.91 Fe ₂ O ₃ 0.147 0.31 0.06 0.52 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.192 0.04 0 0.23

Examples 1-5 Slag (4) Arm rests (4) Feldspar (2) Composition SiO ₂ 13.12 19.84 15.204 48.164 Al2O ₃ 5.24 12.68 2.832 20.752 CaO 16.48 5.48 0.066 22.026 MgO 1.388 0.144 0.006 1.538 Na ₂ O 0.3 1.112 0.844 2.256 K ₂ O 0.18 0.208 0.81 1.198 Fe ₂ O ₃ 0.196 0.416 0.028 0.64 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.256 0.056 0 0.312

Examples 1-6 Slag (2) Arm rests (1) Feldspar (7) Composition SiO ₂ 6.56 4.96 53.214 58.73 Al2O ₃ 2.62 3.17 9.912 15.702 CaO 8.24 1.37 0.231 13.84 MgO 0.694 0.036 0.021 0.751 Na ₂ O 0.15 0.278 2.954 3.382 K ₂ O 0.09 0.052 2.835 2.977 Fe ₂ O ₃ 0.098 0.104 0.098 0.3 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.128 0.014 0 0.142

Examples 1-7 Slag (3) Arm rests (1) Feldspar (6) Composition SiO ₂ 9.84 4.96 45.612 59.412 Al2O ₃ 3.93 3.17 8.496 16.596 CaO 12.36 1.37 0.198 13.928 MgO 1.041 0.036 0.018 1.095 Na ₂ O 0.225 0.278 2.532 3.035 K ₂ O 0.135 0.052 2.43 2.617 Fe ₂ O ₃ 0.147 0.104 0.084 0.335 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.192 0.014 0 0.206

Examples 1-8 Slag (2) Arm shield (6) Feldspar (2) Composition SiO ₂ 6.56 29.76 15.204 51.524 Al2O ₃ 2.62 19.02 2.832 24.472 CaO 8.24 8.22 0.066 16.526 MgO 0.694 0.216 0.006 0.916 Na ₂ O 0.15 1.668 0.844 2.662 K ₂ O 0.09 0.312 0.81 1.212 Fe ₂ O ₃ 0.098 0.624 0.028 0.75 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.128 0.084 0 0.212

Examples 1-9 Slag (2) Arm rests (4) Feldspar (4) Composition SiO ₂ 6.56 19.84 30.408 56.808 Al2O ₃ 2.62 12.68 5.664 20.964 CaO 8.24 5.48 0.132 13.852 MgO 0.694 0.144 0.012 0.85 Na ₂ O 0.15 1.112 1.688 2.95 K ₂ O 0.09 0.208 1.62 1.918 Fe ₂ O ₃ 0.098 0.416 0.056 0.57 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.128 0.056 0 0.184

Example 2-1 Slag (8) Arm rests (1) Feldspar (1) Composition SiO ₂ 26.24 4.96 7.602 38.802 Al2O ₃ 10.48 3.17 1.416 15.066 CaO 32.96 1.37 0.033 34.363 MgO 2.776 0.036 0.003 2.815 Na ₂ O 0.6 0.278 0.422 1.3 K ₂ O 0.36 0.052 0.405 0.817 Fe ₂ O ₃ 0.392 0.104 0.014 0.51 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.512 0.014 0 0.526

Example 2-2 Slag (7) Arm rests (2) Feldspar (1) Composition SiO ₂ 22.96 9.92 7.602 40.482 Al2O ₃ 9.17 6.34 1.416 16,926 CaO 28.84 2.74 0.033 31.613 MgO 2.429 0.072 0.003 2.504 Na ₂ O 0.525 0.556 0.422 1.503 K ₂ O 0.315 0.104 0.405 0.824 Fe ₂ O ₃ 0.343 0.208 0.014 0.565 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.448 0.028 0 0.476

Example 2-3 Slag (7) Arm rests (1) Feldspar (2) Composition SiO ₂ 22.96 4.96 15.204 43.124 Al2O ₃ 9.17 3.17 2.832 15.172 CaO 28.84 1.37 0.066 30.276 MgO 2.429 0.036 0.006 2.471 Na ₂ O 0.525 0.278 0.844 1.647 K ₂ O 0.315 0.052 0.81 1.177 Fe ₂ O ₃ 0.343 0.104 0.028 0.475 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.448 0.014 0 0.462

Examples 2-4 Slag (7) Arm rests (1) Feldspar (2) Composition SiO ₂ 19.68 14.88 7.602 42.162 Al2O ₃ 7.86 9.51 1.416 18.786 CaO 24.72 4.11 0.033 28.863 MgO 2.082 0.108 0.003 2.193 Na ₂ O 0.45 0.834 0.422 1.706 K ₂ O 0.27 0.156 0.405 0.831 Fe ₂ O ₃ 0.294 0.312 0.014 0.62 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.384 0.042 0 0.426

Example 2-5 Slag (6) Arm rests (2) Feldspar (2) Composition SiO ₂ 19.68 9.92 15.204 44.804 Al2O ₃ 7.86 6.34 2.832 17.032 CaO 24.72 2.74 0.066 27.526 MgO 2.082 0.072 0.006 2.16 Na ₂ O 0.45 0.556 0.844 1.85 K ₂ O 0.27 0.104 0.81 1.184 Fe ₂ O ₃ 0.294 0.208 0.028 0.53 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.384 0.028 0 0.412

Examples 2-6 Slag (6) Arm rests (1) Feldspar (3) Composition SiO ₂ 19.68 4.96 22.806 47.446 Al2O ₃ 7.86 3.17 4.248 15.278 CaO 24.72 1.37 0.099 26.189 MgO 2.082 0.036 0.009 2.127 Na ₂ O 0.45 0.278 1.266 1.994 K ₂ O 0.27 0.052 1.215 1.537 Fe ₂ O ₃ 0.294 0.104 0.042 0.44 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.384 0.014 0 0.398

Examples 2-7 Slag (5) Arm rests (4) Feldspar (1) Composition SiO ₂ 16.4 19.84 7.602 43.842 Al2O ₃ 6.55 12.68 1.416 20.646 CaO 20.6 5.48 0.033 26.113 MgO 1.735 0.144 0.003 1.882 Na ₂ O 0.375 1.112 0.422 1.909 K ₂ O 0.225 0.208 0.405 0.838 Fe ₂ O ₃ 0.245 0.416 0.014 0.675 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.32 0.056 0 0.376

Examples 2-8 Slag (5) Arm prostheses (3) Feldspar (2) Composition SiO ₂ 16.4 14.88 15.204 46.484 Al2O ₃ 6.55 9.51 2.832 18.892 CaO 20.6 4.11 0.066 24.776 MgO 1.735 0.108 0.006 1.849 Na ₂ O 0.375 0.834 0.844 2.053 K ₂ O 0.225 0.156 0.81 1.191 Fe ₂ O ₃ 0.245 0.312 0.028 0.585 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.32 0.042 0 0.362

Examples 2-9 Slag (5) Arm rests (2) Feldspar (3) Composition SiO ₂ 16.4 9.92 22.806 49.126 Al2O ₃ 6.55 6.34 4.248 17.138 CaO 20.6 2.74 0.099 23.439 MgO 1.735 0.072 0.009 1.816 Na ₂ O 0.375 0.556 1.266 2.197 K ₂ O 0.225 0.104 1.215 1.544 Fe ₂ O ₃ 0.245 0.208 0.042 0.495 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.32 0.028 0 0.348

Examples 2-10 Slag (5) Arm rests (1) Feldspar (4) Composition SiO ₂ 16.4 4.96 30.408 51.768 Al2O ₃ 6.55 3.17 5.664 15.384 CaO 20.6 1.37 0.132 22.102 MgO 1.735 0.036 0.012 1.783 Na ₂ O 0.375 0.278 1.688 2.341 K ₂ O 0.225 0.052 1.62 1.897 Fe ₂ O ₃ 0.245 0.104 0.056 0.405 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.32 0.014 0 0.334

Example 3-1 Slag (8) Arm rests (2) Feldspar (0) Composition SiO ₂ 26.24 9.92 0 36.16 Al2O ₃ 10.48 6.34 0 16.82 CaO 32.96 2.74 0 35.7 MgO 2.776 0.072 0 2.848 Na ₂ O 0.6 0.556 0 1.156 K ₂ O 0.36 0.104 0 0.464 Fe ₂ O ₃ 0.392 0.208 0 0.6 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.512 0.028 0 0.54

Example 3-2 Slag (7) Arm prostheses (3) Feldspar (0) Composition SiO ₂ 22.96 14.88 0 37.84 Al2O ₃ 9.17 9.51 0 18.68 CaO 28.84 4.11 0 32.95 MgO 2.429 0.108 0 2.537 Na ₂ O 0.525 0.834 0 1.359 K ₂ O 0.315 0.156 0 0.471 Fe ₂ O ₃ 0.343 0.312 0 0.655 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.448 0.042 0 0.49

Example 3-3 Slag (6) Arm rests (4) Feldspar (0) Composition SiO ₂ 19.68 19.84 0 39.52 Al2O ₃ 7.86 12.68 0 20.54 CaO 24.72 5.48 0 30.2 MgO 2.082 0.144 0 2.226 Na ₂ O 0.45 1.112 0 1.562 K ₂ O 0.27 0.208 0 0.478 Fe ₂ O ₃ 0.294 0.416 0 0.71 B ₂ O ₃ 0 0 0 0 TiO ₂ 0.384 0.056 0 0.44

The melting test (1350 ° C) of the amorphous melts according to Examples 1-1 to 1-9,

3 is a graph showing the results of melting tests at 1400 ° C for amorphous melts according to Examples 1-1 to 1-9.

Referring to FIG. 3, the results of the melting test at 1400 ° C. for the amorphous melts according to Examples 1-1 to 1-9 are shown in FIG. As shown in FIG. 3, in the case of Examples 1-4, 1-6 and 1-9, there was no bubble phenomenon on the melted surface, while in the other samples, And the surface is unfired.

The melting test (1350 ° C) of the amorphous melts according to Examples 2-1 to 2-10,

4 is a graph showing the results of melting tests at 1400 ° C for amorphous melts according to Examples 2-1 to 2-10.

Referring to FIG. 4, the results of the melting test at 1400 ° C for the amorphous melts according to Examples 2-1 to 2-10 are shown in FIG.

As shown in FIG. 4, the melting result at 1400 ° C. at a melting temperature of 1400 ° C. shows that as the slag increases, the melting effect decreases, but as the slag increases from 60% to 50%, the feldspar increases from 20% to 40% Lt; / RTI &gt; As shown in FIG. 4, the cases of Examples 2-6, 2-8, 2-9, and 2-10 were shown to be good. In Example 2-6, the slag was 60%, the rock arm was 10%, and the feldspar was 30%. In Example 2-8, the slag was 50%, the pitch arm was 30%, and the feldspar was 20% 50%, arm cylinder arm 20%, feldspar 30%, Example 2-10 is slag 50%, arm cylinder arm 10%, feldspar 40%.

Melting tests (1350 ° C) of the amorphous melts according to Examples 3-1 to 3-3

5 is a graph showing the results of melting tests at 1350 ° C for amorphous melts according to Examples 3-1 to 3-3.

Referring to FIG. 5, the results of melting test at 1350 ° C for amorphous melts according to Examples 3-1 to 3-3 are shown in FIG. As shown in Fig. 5, it shows a very unstable melting state, which is judged to be the unfavorable influence of feldspar to maintain the stabilization of melting.

Slag High Temperature Melting Test

FIG. 6 is a high-temperature microscopic measurement result of a raw sample of slag used in the production of an amorphous molten metal according to an embodiment of the present invention.

Referring to FIG. 6, for the slag used in the above-described embodiments, for the measurement of the high-temperature microscope of the slag, the raw sample was finely pulverized from the agate mortar into a standard net 200 mesh, and the diameter of the mold mold was 0.5 mm, The pressure was set at 1000 kgf, and the temperature was measured at a heating rate of 3 DEG C / min up to a measurement temperature of 1350 DEG C using an ODA high-temperature microscope.

Melting test of slag, ring arm, and feldspar (1400 ℃)

7 is a graph showing the results of melting test of slag, ring arm, and feldspar used in the production of the amorphous molten metal according to the embodiment of the present invention.

Referring to FIG. 7, the secondary slag powder, the secondary feldspar powder, and the secondary feldspar powder were placed in a mold having a diameter of 5 mm, followed by molding at a pressure of 250 kg / cm 2 and firing at 1400 ° C. As shown in FIG. 7, in the case of slag, the spread after firing was expanded to about 2.5 times more unstable than that of the circular mold. In the case of the ring arm, the firing state was the same as the circular shape, Giving. However, it is considered that the firing condition of the slag is somewhat unstable due to the mixed effect of the impurities in the light state, and the firing results of Examples 1-1 to 1-9 and Examples 2-1 to 2-10 It can be seen that the ring arm and feldspar have a positive influence on stable firing.

Melting tests of combination magnification according to Examples 2-6, 2-8, 2-9, and 2-10

Figs. 8 to 11 are the results of high-temperature microscopic measurement of the combination magnification according to Examples 2-6, 2-8, 2-9, and 2-10, respectively.

Referring to Figs. 8 to 11, melting tests were performed according to the combination magnifications according to Examples 2-6, 2-8, 2-9, and 2-10 and photographed under a high-temperature microscope . Figs. 8 to 11 are high-temperature micrographs of the combination magnification according to Examples 2-6, 2-8, 2-9, and 2-10, respectively.

 The high temperature microscope measurement range is the result of measuring up to 1350 ° C at intervals of 1000 ° C to 20 ° C. In the case of the composition of Example 2-6, the rim of the test piece did not react at all until 1180 ° C., but the melt started to slowly melt at 1200 ° C., and the melt rate rapidly occurred at 1220 ° C. and completely melted at 1350 ° C. It is believed that this kind of melting is due to the addition of 30% feldspar with low melting point, while the addition of high melting point feldspar is less. Example 2-8 Composition and Example 2-9 It can be seen that the rim of the specimen does not react at 1200 ° C in the composition. This is because the addition ratio of the additive agent is 30% and 20%, respectively . In addition, even in the composition of Example 2-10, the phenomenon that the edge ruptures at the melting temperature of 1200 ° C is similar to that of Example 2-6, but the melting state of Example 2-6 is somewhat higher at 1350 ° C, 50%, which is lower than the slag content (60%) of Examples 2-6.

As can be seen from the observation of the high-temperature microscope, the composition blending test results show that the composition of Example 2-6 has good melting properties in the fiberization.

(1400 ° C) of the melt specimen of the combination magnification according to Examples 2-6, 2-8, 2-9, and 2-10,

Fig. 12 is a photograph of a cut surface of a melt specimen of combination magnification according to Example 2-6, Example 2-8, Example 2-9, and Example 2-10 of the present invention.

12, the amorphous melts according to Examples 2-6, 2-8, 2-9, and 2-10 were melted at 1400 ° C, and the side and upper surfaces were photographed as shown in FIG. 12 Respectively. As shown in Fig. 12, after melting at 1400 deg. C, bubbles appear after melting, which indicates that the gas does not completely blow out at a melting temperature of 1400 deg.

Crystallization analysis of amorphous melts according to Examples 2-6, 2-8, 2-9 and 2-10 (1400 ° C)

13 shows the XRD measurement results for confirming the crystallinity of the amorphous melt according to Examples 2-6, 2-8, 2-9, and 2-10.

Referring to FIG. 13, the amorphous melts according to Examples 2-6, 2-8, 2-9, and 2-10 were melted at 1400 ° C, and XRD characteristics were measured. As shown in FIG. 13, the results of X-ray reading at a melting temperature of 1400 ° C for each composition show the amorphous results in Example 2-6, but the results of Examples 2-8, 2-9, 2-10 shows the crystal peak of α-Quartz at a measurement angle of 2Θ = 26.8. It is considered that α-Quartz having a high melting point exists because the melting temperature is as low as 1,400 ° C. Such a crystalline peak is difficult to form into long fibers, and therefore, it is difficult to continuously spin the fibers.

Melting tests (1500 ° C) of the amorphous melts according to Examples 2-6, 2-8, 2-9, and 2-10,

Fig. 14 shows results of melting tests of amorphous melts according to Examples 2-6, 2-8, 2-9, and 2-10 of the present invention.

Referring to Fig. 14, the amorphous melts according to Examples 2-6, 2-8, 2-9, and 2-10 were melted at 1500 ° C and the results were confirmed. As shown in Fig. 14, the melting state of each composition is low, and it is expected that a smooth spinning effect will be obtained when spinning fiber after manufacturing amorphous melt.

(1500 ° C) of the melt specimen of the combination magnification according to Examples 2-6, 2-8, 2-9, and 2-10,

Fig. 15 is a photograph of a cut surface of a molten specimen at 1500 DEG C at a combination magnification according to Examples 2-6, 2-8, 2-9, and 2-10 of the present invention.

15, the amorphous melts according to Examples 2-6, 2-8, 2-9, and 2-10 were melted at 1500 ° C and the side and top surfaces were photographed Respectively. As shown in FIG. 16, the bubble phenomenon of the amorphous melt, which was observed at a melting temperature of 1400 ° C, did not appear at a melting temperature of 1500 ° C. This phenomenon is confirmed that the gas observed at 1400 ° C during the melting process is removed during the temperature rise at 1500 ° C.

Crystallization analysis (1500 ° C) of amorphous melts according to Examples 2-6, 2-8, 2-9 and 2-10,

Fig. 16 shows the results of XRD measurement for confirming the crystallinity of the amorphous molten material according to Examples 2-6, 2-8, 2-9, and 2-10 of the present invention.

Referring to FIG. 16, the amorphous melts according to Examples 2-6, 2-8, 2-9, and 2-10 were melted at 1500.degree. C. and XRD characteristics were measured. As shown in FIG. 16, X-ray measurement results of each composition showed stable amorphous results at a melting temperature of 1500 ° C. These results indicate that the gas was not completely released at 1400 ° C because the melting temperature was rather low. However, at 1500 ° C, it was evident that the gas was completely released and became a stable molten amorphous state. do.

Measurement of high-temperature viscosity of amorphous melts according to Examples 2-6 and 2-10

17 is a graph of high temperature viscosity measurement of amorphous melts according to Examples 2-6 and 2-10 of the present invention.

17, with respect to the amorphous melt composition according to Examples 2-6 and 2-10 in which an amorphous phase having a good quality of fiberization was observed as described with reference to Fig. 16, the fiberization temperature The high temperature viscosity was measured.

As shown in FIG. 17, the maximum melting temperature was measured up to 1450 ° C, and the rate of temperature rise was 3 ° C / min. In the case of the amorphous melt composition according to Example 2-6, it is confirmed that the suitable spinning temperature is 1210 ° C, and in the case of the amorphous melt composition according to Example 2-10, the spinning temperature is 1250 ° C. The melt flow rate during the melt viscosity measurement process was such that the composition of the amorphous melt according to Example 2-6 was better than the composition of the amorphous melt according to Example 2-10, Radiation was performed as described below.

Production of ceramic staple fibers using the amorphous molten material according to Example 2-6

18 is a photograph and an optical microscope photograph of a ceramic short fiber prepared using the amorphous molten material according to Example 2-6 of the present invention.

18, the amorphous molten material according to Example 2-6 was melted and the temperature was raised from 5.5 ° C / min to 1000 ° C from room temperature. The temperature was raised to 2 ° C / min to stabilize the melt until it reached 1200 ° C , The temperature was raised to 1260 占 폚 and maintained at this temperature for 1 hour.

Then, the melt was stabilized by repeating 2 ~ 3 min of the change from 1210 ° C to 1260 ° C at a rate of 2 ° C / min so that the melt was stabilized at a high temperature and a homogeneous melt was removed from the bubbles. After stabilization, fiber spinning was initiated from a Pt-Rh 20% bushing to initially establish short fiberization conditions.

As shown in FIG. 18, the fiber thickness can radiate a fiber having a good thickness of about 0.60 mu m, ranging from 24.703 mu m to 25.30 mu m, because the flow rate of the melt is constant and homogeneous.

Production of ceramic filament using amorphous melt according to Example 2-6

FIG. 19 is a photograph and optical microscope photograph of a ceramic filament made using the amorphous molten material according to Example 2-6 of the present invention, and FIG. 20 is a photograph of the ceramic filament prepared using the amorphous molten material according to Example 2-6 of the present invention XRD &lt; / RTI &gt; of the resulting ceramic fiber.

Referring to Fig. 19, long fibers were produced by the method described with reference to Fig. Specifically, the individual fiber filaments coming out from the bushing were wound around a winder in a state where the viscosity of the melt at 1210 to 1230 ° C was the optimum long filament, and the long fibers were produced by continuously spinning the fibers. 20 (b) and (c), it is possible to control the melting temperature and thus the viscosity at a high temperature and to control the winding speed of 100 to 1000 rpm to emit long fibers of various diameters.

Referring to FIG. 20, it was confirmed that the produced ceramic fiber exhibited an amorphous phase. These results can be said to be the optimum blend composition capable of forming long fibers through the slag composition, and the long fiber spinning was carried out as described below.

As described in the various embodiments of the present invention, it can be confirmed that long fibers and short fibers can be produced through composition composition using slag as a raw material for regeneration, control of the melting temperature according to composition, and winder speed control.

While the present invention has been particularly shown and described with reference to exemplary embodiments thereof, it is to be understood that the scope of the present invention is not limited to the disclosed exemplary embodiments. It will also be appreciated that many modifications and variations will be apparent to those skilled in the art without departing from the scope of the present invention.

Claims (8)

Dry-milling the slag to produce a primary slag powder;
Wet-milling the primary slag powder to produce a secondary slag powder;
Dry-milling the first rock to produce a first primary rock powder;
Wet pulverizing the primary primary rock powder to produce a secondary primary rock powder;
Dry-milling the second rock to produce a primary second rock powder;
Wet pulverizing the primary second rock powder to produce a secondary secondary rock powder;
The second slag powder, 20 to 80 wt% of the secondary slag powder, 10 to 60 wt% of the secondary primary rock powder, and 10 to 70 wt% of the secondary secondary rock powder are dry mixed, melted and crushed to obtain an amorphous melt ; And
Melting and spinning the amorphous melt to produce a ceramic fiber,
Wherein the first rock comprises a foldable arm having a higher content of Al ₂ O ₃ and CaO than the second rock,
Wherein the second rock comprises a potassium feldspar having a higher K ₂ O and Na ₂ O content than the first rock.
The method according to claim 1,
The step of producing the primary slag powder, the primary primary rock powder, and the primary secondary rock powder comprises:
A method for producing ceramic filaments using slag comprising crushing the slag, the first rock, and the second rock, respectively, sequentially using a jaw crusher and a disk crusher .
The method according to claim 1,
The step of producing the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder comprises:
A method for producing ceramic filaments using slag comprising grinding the primary slag powder, the primary primary rock powder, and the primary secondary rock powder using a pot mill, respectively .
The method according to claim 1,
And controlling the strength of the ceramic fiber by adjusting a ratio of the secondary first rock powder in the step of manufacturing the amorphous molten slab.
The method according to claim 1,
And controlling the melting point of the amorphous melt by controlling a ratio of the secondary second rock powder in the step of producing the amorphous molten slag.
delete The method according to claim 1,
Wherein the step of preparing the amorphous molten body comprises:
And adding a binder to the secondary slag powder, the secondary primary rock powder, and the secondary secondary rock powder.
The method according to claim 1,
Wherein the molten amorphous melt is in an amorphous state in the step of producing the ceramic fiber.

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