KR101325509B1 - Manufacturing method of ceramic ware with high plasticity and high strength - Google Patents

Manufacturing method of ceramic ware with high plasticity and high strength Download PDF

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KR101325509B1
KR101325509B1 KR1020120131824A KR20120131824A KR101325509B1 KR 101325509 B1 KR101325509 B1 KR 101325509B1 KR 1020120131824 A KR1020120131824 A KR 1020120131824A KR 20120131824 A KR20120131824 A KR 20120131824A KR 101325509 B1 KR101325509 B1 KR 101325509B1
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silica
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김은경
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The present invention comprises the steps of (a) pulverizing pottery and feldspar to a size smaller than 40 μm, and (b) mixing and drying at least one inorganic nanomaterial selected from alumina sol, titania sol and zirconia sol in silica Modifying the surface of the silica with an inorganic nanomaterial, wherein the solids contained in the inorganic nanomaterial are mixed in an amount of 0.01 to 10 parts by weight based on 100 parts by weight of the silica, and (c) the silica is modified with the inorganic nanomaterial. Mixing clay, micronized pottery stone and feldspar, and (d) forming a resultant mixture of silica, clay, micronized stone and feldspar surface-modified with inorganic nanomaterials; And (e) relates to a method of manufacturing ceramics exhibiting high plasticity and high strength comprising the step of firing the molded product. According to the present invention, by uniformly adding the inorganic nanoparticles to the surface of the silica, surface modification and mixing with other raw materials to produce ceramics, the particle slip of the silica by the inorganic nanoparticles is promoted in the ceramic substrate to improve plasticity, This makes it possible to produce compact shaped bodies and to produce low shrinkage, deformation stability and densified ceramics.

Description

Manufacturing method of ceramics with high plasticity and high strength {Manufacturing method of ceramic ware with high plasticity and high strength}
The present invention relates to a method of manufacturing porcelain, and more particularly, by adding inorganic nanoparticles uniformly to the surface of silica, which adversely affects plasticity, surface modification and mixing with other raw materials to produce porcelain, The particle slip is enhanced in the porcelain base to improve plasticity, thereby making a compact molded body, and a method for producing a low shrinkage, deformation stability, densified porcelain.
Pottery is a term that includes pottery and porcelain. Ceramics are mainly made of materials such as clay, feldspar, silica, pyrophyllite, and stonite. Ceramics are products obtained by mixing and molding these materials at a certain ratio, followed by firing and curing. Pottery has a high absorption rate, so it produces a dull sound when tapped and has a relatively low durability. It has a low absorption rate and gives a clear sound when touched and has excellent durability.
In recent years, ceramics such as household appliances such as jangpok and earthenware, sanitary pottery such as bidet, toilet bowl, and washbasin, tiles, etc. are required to have products that are light, thin and have large new physical properties. It is required.
Nanotechnology is contributing greatly to the development of materials in the semiconductor, flat panel display, and battery industries, which are considered to be the three key components of the information, electronics, and information and communications industries.
In the field of ceramics, nanotechnology is being introduced, raw material synthesis technology is important, importing high quality clay raw materials is becoming increasingly difficult, and the price is rising.
Although ceramics companies are conducting research on process development to improve productivity, they are unable to market differentiated products based on technology, and it is time to develop raw materials and materials for producing high value-added products.
The problem to be solved by the present invention is to uniformly add the inorganic nanoparticles to the surface of the silica, surface modification and mixing with other raw materials to produce porcelain, the particle slip of the silica by the inorganic nanoparticles is promoted in the porcelain base plasticity The present invention provides a method for improving compactness, thereby making compact shaped bodies, and producing low shrinkage, deformation stability, and densified ceramics.
The present invention is a method for producing ceramics using at least a ceramic material containing at least clay, pottery stone, feldspar, silica, (a) pulverizing the pottery stone and feldspar to a size smaller than 40㎛, and (b) At least one inorganic nanomaterial selected from alumina sol, titania sol, and zirconia sol is mixed with the silica and dried to modify the surface of the silica with the inorganic nanomaterial, and the solid content of the inorganic nanomaterial is 0.01 to 100 parts by weight of the silica. (C) mixing the surface-modified silica, clay, micronized pottery stone and feldspar with the inorganic nanomaterial, and (d) the silica-modified surface with the inorganic nanomaterial, Shaping the resultant mixture of clay, micronized pottery stone and feldspar; And (e) calcining the molded product, wherein plasticity of porcelain raw materials is increased by surface modification of the surface of the silica with the inorganic nanomaterial, and the production of mullite is promoted in the firing process, so that the plastic shrinkage rate of porcelain is increased. Provided is a method of producing ceramics, characterized in that ceramics smaller than 9% and plastic deformation of ceramics are less than 15 mm are obtained.
At the time of the mixing in step (b), 0.01 to 10 parts by weight of aluminum titanate (Al 2 TiO 5 ) may be further mixed with respect to 100 parts by weight of silica, and the aluminum titanate (Al 2 TiO 5 ) may be 10 to 10 parts by weight. Preference is given to using materials having a particle size of 900 nm.
0.01 to 10 parts by weight of Yb 2 O 3 may be further mixed during the mixing in the step (b), and the Yb 2 O 3 is preferably used as a material having a particle size of 10 to 900 nm.
When the mixing in the step (b) may be mixed with 0.01 to 10 parts by weight of hydroxyapatite, the hydroxyapatite is to use a material having a particle size of 10 ~ 900nm size desirable.
0.01 to 10 parts by weight of tungsten carbide (WC) may be further mixed during the mixing in the step (b), and the tungsten carbide (WC) may preferably be a material having a particle size of 10 to 900 nm. .
As the inorganic nanomaterial, it is preferable to use a material having a particle size of 10 to 900 nm.
The step (d) may further comprise the step of mixing the water glass to the resultant mixture before molding.
According to the present invention, by adding inorganic nanoparticles uniformly to the surface of silica, which adversely affects plasticity, surface modification and mixing with other raw materials to produce ceramics, the particle slip of silica is promoted in ceramic materials by inorganic nanoparticles. It improves plasticity, which makes it possible to produce compact shaped bodies, and to produce low shrinkage, deformation stability and densified ceramics.
By pulverizing feldspar, pottery, clay and silica to 40 micrometers (µm) or less, high molding density can reduce not only thermal deformation but also sintering temperature, thereby saving energy.
In addition, by adding at least one inorganic nanomaterial selected from alumina sol, titania sol, and zirconia sol to silica, the plasticity of the base is increased, so the moldability is very excellent, and the production of mullite that forms at high temperature is promoted or heat is generated. The deformation reduction and the strength of the fired body can be improved.
In addition, aluminum titanate (Al 2 TiO 5 ), Yb 2 O 3 , hydroxyapatite or tungsten carbide (WC) can be added to the silica to modify the surface to reduce heat deformation and enhance the strength of the fired body. have.
1 is a photograph of alumina sol mixed with silica and dried to modify the surface of silica with alumina.
2 is a graph showing a firing curve (firing curve) showing a firing temperature section with a firing time.
3 is a schematic of a mold for plasticity testing.
4 is a schematic of a mold for dry strength testing.
5 is a schematic of a mold for shrinkage testing.
6 is a schematic of a fire brick for deformation testing.
7 is a schematic diagram illustrating hot strain measurement.
Hereinafter, preferred embodiments of the present invention will be described in detail with reference to the accompanying drawings. However, it should be understood that the following embodiments are provided so that those skilled in the art will be able to fully understand the present invention, and that various modifications may be made without departing from the scope of the present invention. It is not.
One of the most important physical properties among the properties required for porcelain holding is high plasticity, and the present invention provides a method of manufacturing a porcelain holding having high plasticity.
Depending on the purpose of use, the properties required for porcelain holding, such as chemical composition, the structure and shape of the particles, and the amount of impurities allowed, are different, but the base required for the production of the most popular and profitable high-quality porcelain has high plasticity. It should contain a small amount of iron. For this reason, various researches have been attempted to improve the physical properties by modifying the low plasticity produced in Korea, but there are no results satisfying both technical and economic aspects. In order to increase exports, a large amount of foreign clay, which has a low iron content and high plasticity, is imported from China, Southeast Asia, and New Zealand every year.
In the present invention, an inorganic nanomaterial is added to a silica surface which affects plasticity deterioration of porcelain bases, thereby developing porcelain bases having improved physical properties. Unlike the technology for making physical changes in raw materials such as particle size control and pulverization of raw materials, which have been tested to improve plasticity, the surface of raw materials will be modified with inorganic nanomaterials to change the overall physical properties of raw materials.
According to a preferred embodiment of the present invention, a method of manufacturing ceramics having high plasticity and high strength is a method of manufacturing ceramics using at least a ceramic material including at least clay, pottery, feldspar, and silica, wherein (a) pottery and feldspar Pulverizing to a size smaller than 40 μm and micronizing, and (b) mixing the silica with at least one inorganic nanomaterial selected from alumina sol, titania sol, and zirconia sol and drying to modify the surface of the silica with inorganic nano material, Allowing 0.01 to 10 parts by weight of solids contained in the inorganic nanomaterial to be mixed with respect to 100 parts by weight of silica, and (c) mixing silica, clay, micronized stone and feldspar whose surface is modified with the inorganic nanomaterial. (D) shaping the mixed result; And (e) firing the shaped result. By modifying the surface of the silica with the inorganic nanomaterial, the plasticity of the porcelain raw material is increased and the production of mullite is promoted in the firing process, so that the porcelain having a plastic shrinkage of less than 9% and a plastic deformation of the porcelain is less than 15 mm. Obtained.
At the time of the mixing in step (b), 0.01 to 10 parts by weight of aluminum titanate (Al 2 TiO 5 ) may be further mixed with respect to 100 parts by weight of silica, and the aluminum titanate (Al 2 TiO 5 ) may be 10 to 10 parts by weight. Preference is given to using materials having a particle size of 900 nm.
0.01 to 10 parts by weight of Yb 2 O 3 may be further mixed during the mixing in the step (b), and the Yb 2 O 3 is preferably used as a material having a particle size of 10 to 900 nm.
When the mixing in the step (b) may be mixed with 0.01 to 10 parts by weight of hydroxyapatite, the hydroxyapatite is to use a material having a particle size of 10 ~ 900nm size desirable.
0.01 to 10 parts by weight of tungsten carbide (WC) may be further mixed during the mixing in the step (b), and the tungsten carbide (WC) may preferably be a material having a particle size of 10 to 900 nm. .
As the inorganic nanomaterial, it is preferable to use a material having a particle size of 10 to 900 nm.
The step (d) may further comprise the step of mixing the water glass to the resultant mixture before molding.
Hereinafter, a method of manufacturing ceramics exhibiting high plasticity and high strength according to a preferred embodiment of the present invention will be described in more detail.
The potter's stone and feldspar are pulverized to a size smaller than 40 mu m. Herein, the method of grinding and micronizing may be various, and an example using a ball milling process will be described in detail. In order to micronize feldspar and pottery stone, these porcelain raw materials are charged to a ball milling machine, and wet-mixed with a solvent. The ball mill is rotated at a constant speed to grind the porcelain raw material mechanically and uniformly. The ball used for ball milling may be a ball made of ceramics such as alumina or zirconia, and the balls may be all the same size or may be used together with balls having two or more sizes. The size of the balls, the milling time, and the rotation speed per minute of the ball miller are adjusted so as to be crushed to the target particle size. For example, in consideration of the particle size, the size of the ball can be set in the range of about 1 to 50, and the rotational speed of the ball mill can be set in the range of about 100 to 400 rpm. Ball milling is carried out for 12 to 36 hours in consideration of the target particle size and the like. Ball milling causes the raw materials to be ground into finely sized particles, to have a uniform particle size distribution, and to be mixed uniformly.
At least one inorganic nanomaterial selected from alumina sol, titania sol and zirconia sol is mixed with the silica and dried to modify the surface of the silica with the inorganic nanomaterial. The amount of the inorganic nanomaterial added is preferably such that the solid content contained in the inorganic nanomaterial is mixed in an amount of 0.01 to 10 parts by weight based on 100 parts by weight of silica.
When the body is made of silica with inorganic nanomaterials added, it promotes crystallization of the liquid phase to reduce heat deformation and enhance the strength of the fired body. The inorganic nanomaterial includes at least one selected from alumina sol, titania sol and zirconia sol. The inorganic nanomaterial is modified to have a good plasticity by modifying the surface of the silica, and to increase the crystallization of the molten body during firing to reduce the amount of plastic shrinkage or plastic deformation.
As the addition amount of the inorganic nanomaterial is increased, high strength is obtained, and the plastic deformation amount is small, but when the amount exceeds the limit, the firing temperature is slightly increased. Therefore, in consideration of this point, the content of the inorganic nanomaterial is added so that the solid content of the sol is mixed with 0.01 to 10 parts by weight with respect to 100 parts by weight of silica, and preferably 2 to 7 parts by weight.
It is preferable that the particle diameter of an inorganic nanomaterial is about 10-900 nm. When the inorganic nanomaterial is added, the plastic shrinkage rate can be reduced to 9% or less, and the plastic deformation amount can be reduced to 15 mm or less.
In addition, the inorganic nanomaterial raises the viscosity of the liquid phase, promotes crystallization of the liquid phase, thereby reducing heat deformation and enhancing the strength of the fired body.
When the inorganic nanomaterial is mixed with the silica, 0.01 to 10 parts by weight of aluminum titanate (Al 2 TiO 5 ) may be further mixed with respect to 100 parts by weight of silica, and the aluminum titanate (Al 2 TiO 5 ) may be 10 to 10 parts by weight. Preference is given to using materials having a particle size of 900 nm. The aluminum titanate (Al 2 TiO 5 ) serves to reduce heat deformation and enhance strength of the fired body.
In addition, 0.01 to 10 parts by weight of Yb 2 O 3 may be further mixed when the inorganic nanomaterial is mixed with the silica, and the Yb 2 O 3 is preferably used as a material having a particle size of 10 to 900 nm. . The Yb 2 O 3 serves to reduce heat deformation and enhance the strength of the fired body.
In addition, when the inorganic nanomaterial is mixed with the silica, 0.01 to 10 parts by weight of hydroxyapatite may be further mixed, and the hydroxyapatite may be a material having a particle size of 10 to 900 nm. It is desirable to. The hydroxyapatite serves to reduce heat deformation and enhance the strength of the fired body.
In addition, when the inorganic nanomaterial is mixed with the silica, 0.01 to 10 parts by weight of tungsten carbide (WC) may be further mixed, and the tungsten carbide (WC) may be a material having a particle size of 10 to 900 nm. desirable. The tungsten carbide (WC) serves to reduce the heat deformation and to enhance the strength of the fired body.
Surface-modified silica, clay, micronized pottery stone and feldspar are mixed with inorganic nanomaterials. If the raw material is made by mixing silica and clay whose surface is modified with inorganic nanomaterials with ceramic materials such as fine feldspar and pottery, it promotes liquid crystallization, which reduces heat deformation and enhances the strength of the fired body. The inorganic nanomaterial is modified to have a good plasticity by modifying the surface of the silica, and to increase the crystallization of the molten body during firing to reduce the amount of plastic shrinkage or plastic deformation.
As the porcelain raw material of the present invention, the glass phase component which forms a glass phase upon firing contains 20 to 50% by weight of the total porcelain raw material, and the inorganic nanomaterial (solid content of the sol) contains 0.01 to 10 parts by weight with respect to 100 parts by weight of silica. It is desirable to. The glass phase component preferably comprises 40~70% by weight of SiO 2, Na 2 O and K 2 O 2~7% by weight. If the amount of SiO 2 in the glass phase exceeds 70% by weight, plasticity will be degraded. When the content of Na 2 O and K 2 O exceeds 7% by weight, the strength of the fired ceramics is reduced and the plastic deformation of the ceramics during the firing is greatly increased. If the content of Na 2 O and K 2 O is less than 2% by weight, the densification becomes less and the firing temperature becomes higher. The relative amounts of Na 2 O and K 2 O are not specified and are determined based on the total content of Na 2 O and K 2 O. If the amount of the inorganic nanomaterial exceeds 10 parts by weight, the firing temperature is high, and if the amount of the inorganic nanomaterial is less than 0.01 parts by weight, it is difficult to expect a sufficient reduction in the amount of plastic shrinkage or plastic deformation.
The result is a mixture of silica, clay, micronized pottery stone and feldspar with a surface-modified inorganic nanomaterial. The above-mentioned molding can be variously adopted, such as injection molding, extrusion molding, etc. In the case of injection molding, water glass may be mixed with the resultant product mixed before the molding to facilitate injection molding.
The molded product is fired at 1100 to 1500 占 폚.
Hereinafter, the firing step will be described in detail.
The molded product is charged into a furnace such as an electric furnace, and a sintering process is performed. The firing step is preferably performed at a temperature of about 1100 to 1500 DEG C for about 1 to 48 hours. It is desirable to keep the pressure inside the furnace constant during firing.
The firing is preferably performed at a temperature in the range of 1100 to 1500 占 폚. If the firing temperature is less than 1100 ℃, the thermal or mechanical properties of ceramics may not be good due to incomplete firing. If the firing temperature is higher than 1500 ℃, energy consumption is excessive due to high energy consumption. It may not be good.
The firing temperature is preferably raised at a heating rate of 1 to 50 ° C / min. If the heating rate is too slow, the time is long and productivity is deteriorated. If the heating rate is too high, thermal stress is applied due to a rapid temperature rise It is preferable to raise the temperature at the temperature raising rate in the above range.
The firing is preferably carried out at a firing temperature for 1 to 48 hours. If the firing time is too long, it is not economical since the energy consumption is high. Further, it is difficult to expect further firing effect. If the firing time is small, the physical properties of the ceramic material may not be good due to incomplete firing.
The firing is preferably carried out in an oxidizing atmosphere (for example, oxygen (O 2 ) or air atmosphere) or a reducing atmosphere.
After the firing process is performed, the furnace temperature is lowered to unload the ceramics. The furnace cooling may be effected by shutting down the furnace power source to cool it in a natural state, or optionally by setting a temperature decreasing rate (for example, 10 DEG C / min). It is preferable to keep the pressure inside the furnace constant even while the furnace temperature is being lowered.
The invention is described in more detail with reference to the following examples, which are not intended to limit the invention.
≪ Examples 1 to 9 &
In the examples, the ceramic specimen was prepared by modifying the surface of the silica using inorganic nanomaterials, mixing the modified quartz with clay, pottery, and feldspar, and molding and firing.
Clay, pottery stone, silica and feldspar were used as raw materials for ceramics. As the silica, the surface was modified by adding a certain amount of at least one inorganic nanomaterial selected from alumina sol, titania sol, and zirconia sol.
Specific specimen manufacturing process in the embodiments are as follows.
The silica was mixed with alumina sol, titania sol or zirconia sol, which were inorganic nanomaterials, and dried to modify the surface of the silica with inorganic nanomaterials. The drying was carried out in a drying oven at 150 ℃ for 12 hours. Figure 1 shows a photo of the surface of the silica modified with alumina by mixing and drying the alumina sol in the silica. 1 is a case where 4 parts by weight of alumina sol is added to 100 parts by weight of silica.
Pottery and feldspar, which is a raw material of porcelain, was put in an alumina pot to be pulverized at 200 rpm for 12 hours using an alumina ball having a size of 30 mm, and then passed through a 325 mesh sieve to slip. slip). This slip was mixed with silica and clay whose surface was modified with inorganic nanomaterials, adjusted by adding water glass, and then cast molded into gypsum mold to prepare a dry specimen, and a maximum section temperature of 1250 ° C. and an operating time of 13 hours. By firing in the curve shown in Figure 2 to prepare a specimen.
[Test Items and Comparative Tests]
The combination ratio of test body was compared with that of standard body as shown in Table 1, and the characteristics of ceramic specimens prepared according to the combination ratio of standard body and test body are shown in Table 2. As shown in Table 1, the base material represents a case in which 35% by weight of clay, 25% by weight of quartz, 15% by weight of pottery stone and 25% by weight of feldspar were used as porcelain raw materials. The unit of the value shown in Table 1 is the weight%, the content of the inorganic nanomaterial means the amount of the inorganic nanomaterial added to the content of silica (25% by weight of the entire ceramic material) of the total raw material, for example 1 is a case where 2 parts by weight is added to 100 parts by weight of silica, Example 2 is a case where 4 parts by weight is added to 100 parts by weight of silica, and Example 3 is a case where 6 parts by weight is added to 100 parts by weight of silica . In Table 1 and Table 2, Examples 1 to 3 are examples of adding an alumina sol as an inorganic nanomaterial, and Examples 3 to 6 are examples of adding a titania sol as an inorganic nanomaterial, and Examples 7 to 7. Example 9 shows the case of adding zirconia sol as the inorganic nanomaterial.
Standard Example 1 Example 2 Example 3 Example 4 Example 5 Example 6 Example 7 Example 8 Example 9
clay 35 35 35 35 35 35 35 35 35 35
burr 25 25 25 25 25 25 25 25 25 25
Pottery 15 15 15 15 15 15 15 15 15 15
feldspar 25 25 25 25 25 25 25 25 25 25
Content of Inorganic Nanomaterials 0 2 parts by weight 4 parts by weight 6 parts by weight 2 parts by weight 4 parts by weight 6 parts by weight 2 parts by weight 4 parts by weight 6 parts by weight
Standard possession Example 1 Example 2 Example 3 Example 4 Example 5 Example 6 Example 7 Example 8 Example 9
Viscosity (sec) 31.4 29.5 29.3 29.2 29.4 29.3 29.2 29.5 29.2 29.0
Plasticity (number of cracks) 6 3 3 2 3 3 3 3 3 2
Drying Strength (kgf / ㎠) 34.0 38.0 38.7 39.0 38.0 38.6 39.0 39.3 39.9 39.9
Dry Shrinkage (%) 2.7 2.8 2.4 2.6 2.7 2.7 2.8 2.8 2.9 2.8
Plastic Shrinkage (%) 8.9 8.8 8.9 8.8 8.8 8.9 8.7 8.8 8.8 8.8
Total Shrinkage (%) 10.9 11.2 11.2 10.8 11.1 11.2 11.2 10.8 11.4 10.3
Plastic deformation (mm) 24.5 15.0 14.5 14.0 15.0 14.0 15.0 14.0 13.0 14.5
Loss on ignition (%) 6.2 6.1 6.0 5.9 5.8 6.3 6.1 6.2 6.0 6.3
Breaking Strength (MPa) 105 130 145 155 110 115 120 130 140 145
Absorption Rate (%) 0.89 0.50 0.45 0.50 0.50 0.50 0.50 0.40 0.35 0.45
1. Viscosity
In order to measure the viscosity of the slip, the discharge time was measured using a container having a volume of 500 ml and a nozzle diameter of 8 mm.
As shown in Table 2, the viscosity of the test body of Examples 1 to 9 was lower than that of the standard body.
2. Plasticity
Gypsum molds (a) and (b) shown in FIG. 3 were combined to inject slip, maintained for 1 hour, and then the plaster molds (a) were removed. And the cracking was observed for 1 hour at 5 minutes intervals for the molded specimen that did not demould in the plaster (b) to compare the plasticity.
As shown in Table 2, the plasticity of test materials of Examples 1 to 9 was larger than that of standard materials.
3. dry strength
The slip was injected by combining gypsum molds (a) and (b) shown in Figure 4 and demolded after 40 minutes. The demolded molded specimens were dried for 24 hours at a temperature of 110 ± 5 ° C. using a dryer, and the three-point bending strengths were measured and calculated using the following equation.
Strength (kgf / cm 2) = (3 × N × L) / (2 × B × D × g)
Where N = kgf · m / sec 2 , L = distance between supports (cm), B = width of the specimen (cm), D = thickness of the specimen (cm), and g = gravity acceleration (m / sec 2 ).
The dry strength of the test body of Examples 1 to 9 was higher than that of the standard body.
4. Shrink and Deformation
Slip and deformation were measured using a molded specimen demolded 40 minutes after combining the plaster molds (a) and (b) shown in FIG. The deformation was fired on the refractory shown in FIG. 6, and then the L value was measured as shown in FIG. 7, and the shrinkage ratio was calculated using the following equation.
Dry shrinkage (%) = (molding length-drying length) / molding length * 100
Plastic shrinkage rate (%) = (drying length-baking length) / drying length * 100
Total shrinkage (%) = (molding length-firing length) / molding length * 100
The dry shrinkage was similar between the standard body and the test body of Examples 1 to 9. The plastic shrinkage was similar to the test body of Example 1 to Example 9 and the standard body. The plastic strain showed a small test body of Examples 1 to 9, and a large deformation of the standard body.
5. Ignition loss
After drying the molded specimens at a temperature of 110 ± 5 ℃ in a dryer for 24 hours, cooled to room temperature in a desiccator, weighed, calcined and dried for 24 hours at a temperature of 110 ± 5 ℃ in a dryer, then desiccated After cooling to room temperature in the chamber, the weight was measured, and the ignition loss was calculated using the following equation.
Ig.-loss (%) = (dry weight-firing weight) / dry weight × 100
As shown in Table 2, the loss of ignition of the test body of Examples 1 to 9 was similar to that of the standard body.
6. Absorption rate
Dry the fired specimen at 110 ± 5 ℃ for 24 hours in a dryer, cool it to room temperature in a desiccator, weigh it, leave it in water for 24 hours, remove it, wipe the surface with a wet towel, and weigh it. It was calculated using the following formula.
Absorption rate (%) = (weight after absorption-weight before absorption) / weight before absorption × 100
The water absorption of the test bodies of Examples 1 to 9 was smaller than that of the standard substrate.
7. Bending Strength of Plastic Body
The bending strength was measured using the multi-purpose tester according to the Korean Industrial Standard KSL 1591 (2002). The bending strength test is the most common method of the ceramic strength test. The test was conducted using a specimen fired at 1250 ° C. The roughness of the upper and lower surfaces of the specimen was, in principle, set to 0.8 S or less specified in KSB0161 (Surface Roughness). The width (w) and thickness (h) of the specimen were measured up to 0.1 mm using a digital vernier caliper. The specimen was placed on a support with a distance of 30 mm between the lower points and the crosshead speed of 0.5 mm / min was applied to the load point to determine the maximum load until the specimen failed. The bending strength was calculated by the following Equation 1.
Figure 112012095655726-pat00001
Where σ: three-point bending strength (MPa)
P: maximum load when the specimen is broken (N)
L: Distance between lower points (m)
w: width of the specimen (m)
t: thickness of the specimen (m)
The strength of the fired body of the test body of Examples 1 to 9 was larger than that of the fired body of the standard body.
High plasticity and low deformation and high strength properties of the plastic body are not only advantageous for the enlargement of ceramics, but are also absolutely necessary for the flatness of small porcelains to ensure that the product does not bend.
As described above, in order to increase the densification and lower the calcination temperature, raw materials such as feldspar and pottery stone are micronized to 40 micrometers (μm) or less, and at least one inorganic nano material selected from alumina sol, titania sol, and zirconia sol is silica Modification by addition to the surface of the catalyst promoted crystallization of the liquid phase formed at high temperature, thereby reducing thermal deformation and enhancing the strength of the fired body.
As mentioned above, although preferred embodiment of this invention was described in detail, this invention is not limited to the said embodiment, A various deformation | transformation by a person of ordinary skill in the art within the scope of the technical idea of this invention is carried out. This is possible.

Claims (7)

  1. In the method of manufacturing ceramics using a ceramic raw material containing at least clay, pottery stone, feldspar, quartzite,
    (a) grinding and pulverizing the potter's stone and feldspar into a size smaller than 40 mu m;
    (b) mixing the silica with at least one inorganic nanomaterial selected from alumina sol, titania sol and zirconia sol and drying to modify the surface of the silica with an inorganic nanomaterial, wherein the solids contained in the inorganic nanomaterial are 100 parts by weight of silica 0.01 to 10 parts by weight relative to the mixture;
    (c) mixing the surface-modified silica, clay, micronized pottery stone and feldspar with the inorganic nanomaterial;
    (d) forming a resultant mixture of silica, clay, micronized pottery stone and feldspar whose surface is modified with the inorganic nanomaterial; And
    (e) firing the molded product,
    Further comprising the step of mixing the water glass in the mixed product before molding in the step (d),
    The step (b), and the mixture during further mixing 100 parts by weight of silica to the aluminum titanate (Al 2 TiO 5) 0.01~10 parts by weight, with respect to in the aluminum titanate (Al 2 TiO 5) is 10~900㎚ Using a material with a particle size of the size,
    0.01 to 10 parts by weight of Yb 2 O 3 is further mixed during the mixing in the step (b), and the Yb 2 O 3 uses a material having a particle size of 10 to 900 nm,
    0.01 to 10 parts by weight of hydroxyapatite is further mixed during the mixing in the step (b), and the hydroxyapatite is made of a material having a particle size of 10 to 900 nm.
    0.01 to 10 parts by weight of tungsten carbide (WC) is further mixed during the mixing in the step (b), and the tungsten carbide (WC) uses a material having a particle size of 10 to 900 nm,
    By modifying the surface of the silica with the inorganic nanomaterial, the plasticity of the porcelain raw material is increased and the production of mullite is promoted in the firing process, so that the porcelain having a plastic shrinkage of less than 9% and a plastic deformation of the porcelain is less than 15 mm. A method for producing a ceramic ware, which is obtained.
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  6. The method of claim 1, wherein the inorganic nanomaterial is a material having a particle size of 10 to 900nm size.
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KR1020120131824A 2012-11-20 2012-11-20 Manufacturing method of ceramic ware with high plasticity and high strength KR101325509B1 (en)

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Publication number Priority date Publication date Assignee Title
KR20200040568A (en) * 2018-10-10 2020-04-20 유미숙 Buncheong Ceramic Composition and Manufacturing Method thereof

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JPH0753257A (en) * 1993-08-09 1995-02-28 Harima Ceramic Co Ltd Production of aluminum titanate-based sintered body
JP2000302542A (en) 1999-04-22 2000-10-31 Shin Etsu Chem Co Ltd Jig used for sintering
KR20070111706A (en) * 2006-05-18 2007-11-22 요업기술원 Modified clay complex comprising organic or inorganic plasticizer, and method for preparing the same
KR20090113497A (en) * 2008-04-28 2009-11-02 한국세라믹기술원 Manufacturing method of ceramic ware with low deformation

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JPH0753257A (en) * 1993-08-09 1995-02-28 Harima Ceramic Co Ltd Production of aluminum titanate-based sintered body
JP2000302542A (en) 1999-04-22 2000-10-31 Shin Etsu Chem Co Ltd Jig used for sintering
KR20070111706A (en) * 2006-05-18 2007-11-22 요업기술원 Modified clay complex comprising organic or inorganic plasticizer, and method for preparing the same
KR20090113497A (en) * 2008-04-28 2009-11-02 한국세라믹기술원 Manufacturing method of ceramic ware with low deformation

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20200040568A (en) * 2018-10-10 2020-04-20 유미숙 Buncheong Ceramic Composition and Manufacturing Method thereof
KR102208096B1 (en) * 2018-10-10 2021-01-27 유미숙 Buncheong Ceramic Composition and Manufacturing Method thereof

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