CN114394842A - Preparation method of sintered compact high-zirconium brick - Google Patents
Preparation method of sintered compact high-zirconium brick Download PDFInfo
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- CN114394842A CN114394842A CN202210149617.4A CN202210149617A CN114394842A CN 114394842 A CN114394842 A CN 114394842A CN 202210149617 A CN202210149617 A CN 202210149617A CN 114394842 A CN114394842 A CN 114394842A
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- 239000011449 brick Substances 0.000 title claims abstract description 35
- 238000002360 preparation method Methods 0.000 title claims abstract description 26
- 229910052726 zirconium Inorganic materials 0.000 title claims abstract description 26
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 claims abstract description 86
- 239000002994 raw material Substances 0.000 claims abstract description 22
- 238000000034 method Methods 0.000 claims abstract description 18
- 238000004519 manufacturing process Methods 0.000 claims abstract description 11
- 229910004298 SiO 2 Inorganic materials 0.000 claims abstract description 3
- 239000000843 powder Substances 0.000 claims description 49
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N silicon dioxide Inorganic materials O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims description 31
- 239000002002 slurry Substances 0.000 claims description 18
- 239000003381 stabilizer Substances 0.000 claims description 17
- 239000007788 liquid Substances 0.000 claims description 15
- 239000000377 silicon dioxide Substances 0.000 claims description 14
- 229910052681 coesite Inorganic materials 0.000 claims description 13
- 229910052906 cristobalite Inorganic materials 0.000 claims description 13
- 239000000463 material Substances 0.000 claims description 13
- 239000002245 particle Substances 0.000 claims description 13
- 229910052682 stishovite Inorganic materials 0.000 claims description 13
- 229910052905 tridymite Inorganic materials 0.000 claims description 13
- 239000008187 granular material Substances 0.000 claims description 12
- 230000008569 process Effects 0.000 claims description 12
- RMAQACBXLXPBSY-UHFFFAOYSA-N silicic acid Chemical compound O[Si](O)(O)O RMAQACBXLXPBSY-UHFFFAOYSA-N 0.000 claims description 8
- 235000012239 silicon dioxide Nutrition 0.000 claims description 8
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 8
- 239000002270 dispersing agent Substances 0.000 claims description 7
- 239000000203 mixture Substances 0.000 claims description 6
- 239000002904 solvent Substances 0.000 claims description 6
- 238000003756 stirring Methods 0.000 claims description 6
- 229910052721 tungsten Inorganic materials 0.000 claims description 5
- 238000003723 Smelting Methods 0.000 claims description 4
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 4
- 238000000498 ball milling Methods 0.000 claims description 4
- 239000011230 binding agent Substances 0.000 claims description 4
- 239000005350 fused silica glass Substances 0.000 claims description 4
- 239000008367 deionised water Substances 0.000 claims description 3
- 229910021641 deionized water Inorganic materials 0.000 claims description 3
- 238000001035 drying Methods 0.000 claims description 3
- 238000003825 pressing Methods 0.000 claims description 3
- 238000001694 spray drying Methods 0.000 claims description 3
- 238000005507 spraying Methods 0.000 claims description 3
- 238000009694 cold isostatic pressing Methods 0.000 claims description 2
- RTZKZFJDLAIYFH-UHFFFAOYSA-N ether Substances CCOCC RTZKZFJDLAIYFH-UHFFFAOYSA-N 0.000 claims description 2
- 125000001033 ether group Chemical group 0.000 claims description 2
- 238000010304 firing Methods 0.000 claims description 2
- 238000000227 grinding Methods 0.000 claims description 2
- JEGUKCSWCFPDGT-UHFFFAOYSA-N h2o hydrate Chemical compound O.O JEGUKCSWCFPDGT-UHFFFAOYSA-N 0.000 claims description 2
- 229920005646 polycarboxylate Polymers 0.000 claims description 2
- 238000005086 pumping Methods 0.000 claims description 2
- 239000012798 spherical particle Substances 0.000 claims description 2
- 239000004094 surface-active agent Substances 0.000 claims description 2
- 239000011521 glass Substances 0.000 abstract description 34
- 238000005245 sintering Methods 0.000 abstract description 11
- 230000003628 erosive effect Effects 0.000 abstract description 7
- 238000000462 isostatic pressing Methods 0.000 abstract description 3
- 238000005469 granulation Methods 0.000 abstract 1
- 230000003179 granulation Effects 0.000 abstract 1
- 238000004537 pulping Methods 0.000 abstract 1
- 239000007921 spray Substances 0.000 abstract 1
- 238000002844 melting Methods 0.000 description 25
- 230000008018 melting Effects 0.000 description 25
- 230000000694 effects Effects 0.000 description 8
- 230000008859 change Effects 0.000 description 6
- 239000003365 glass fiber Substances 0.000 description 6
- 239000011819 refractory material Substances 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 4
- 239000006060 molten glass Substances 0.000 description 4
- RVTZCBVAJQQJTK-UHFFFAOYSA-N oxygen(2-);zirconium(4+) Chemical compound [O-2].[O-2].[Zr+4] RVTZCBVAJQQJTK-UHFFFAOYSA-N 0.000 description 4
- 229910052710 silicon Inorganic materials 0.000 description 4
- 239000010703 silicon Substances 0.000 description 4
- 229910001928 zirconium oxide Inorganic materials 0.000 description 4
- 230000009286 beneficial effect Effects 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 239000000156 glass melt Substances 0.000 description 3
- 239000007767 bonding agent Substances 0.000 description 2
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical compound [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 229910052735 hafnium Inorganic materials 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000010309 melting process Methods 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000004321 preservation Methods 0.000 description 2
- 230000035939 shock Effects 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 230000008646 thermal stress Effects 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910000421 cerium(III) oxide Inorganic materials 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000005187 foaming Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000003110 molding sand Substances 0.000 description 1
- MGRWKWACZDFZJT-UHFFFAOYSA-N molybdenum tungsten Chemical compound [Mo].[W] MGRWKWACZDFZJT-UHFFFAOYSA-N 0.000 description 1
- 229910002077 partially stabilized zirconia Inorganic materials 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 229910052594 sapphire Inorganic materials 0.000 description 1
- 239000010980 sapphire Substances 0.000 description 1
- 238000009991 scouring Methods 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
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- C04B35/48—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on zirconium or hafnium oxides, zirconates, zircon or hafnates
- C04B35/486—Fine ceramics
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- C03B5/16—Special features of the melting process; Auxiliary means specially adapted for glass-melting furnaces
- C03B5/42—Details of construction of furnace walls, e.g. to prevent corrosion; Use of materials for furnace walls
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- C04B35/481—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on zirconium or hafnium oxides, zirconates, zircon or hafnates containing silicon, e.g. zircon
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- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
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Abstract
The invention discloses a sintered compact high-zirconium brick and a preparation method thereof, wherein the method comprises pulping, spray granulation, isostatic pressing and high-temperature sintering; the preparation method mainly uses a micron-sized Y2O3 partially-stabilized electrically-fused zirconia raw material with monoclinic zirconia in a proportion of 40-70%, and introduces 1-5% of nano-SiO 2; the method obtains a uniform structure that zirconia is uniformly dispersed in a small amount of glass phase, and the prepared sintered compact high-zirconium brick has the characteristics of low porosity, high strength, good erosion resistance and low production cost, and can realize the preparation of large-size products.
Description
Technical Field
The invention relates to a refractory material and a preparation method thereof, in particular to a preparation method of a sintered compact high-zirconium brick.
Background
The glass or glass fiber melting furnace is a thermal device for melting various glass and glass fiber raw materials into uniform glass liquid at high temperature, and the heat source of the glass or glass fiber melting furnace generally adopts one or two of electrode heating or burner heating; the glass melting furnace directly contacts the molten glass, the investment is high, the operation is continuous, and the glass melting furnace directly relates to the quality and the production cost of glass and glass fiber products; in the using process, if the inner wall of the melting furnace is gradually eroded and abraded by the glass liquid and enters the glass liquid, the quality of the glass liquid and the quality of a formed product of the glass liquid can be directly influenced, and meanwhile, the service life of the glass melting furnace is related to the production cost of glass and glass fiber products; therefore, the refractory material forming the inner wall (tank wall, roof and bottom) of the melting furnace has the characteristics of high temperature resistance, high strength, erosion resistance, low thermal conductivity and the like; in addition, in view of the structural design requirements of the glass melting furnace and the abnormal erosion condition of the glass melt to the brick joints of the refractory bricks in the use process, besides the performance, the refractory material is required to have larger size to reduce the brick joints, so that the weight of the refractory bricks at a plurality of positions in the glass melting furnace is more than 300 kilograms, and the weight of part of the refractory bricks exceeds 1000 kilograms; the large size of the refractory material brings many limitations to the preparation process of the refractory material, and the large-size refractory bricks used in the current glass melting furnaces are mostly formed by casting, such as the cast AZS bricks and the like.
In recent years, along with the upgrading and transformation of the domestic glass industry and the high-grade development of products, especially the rapid development of electronic glass, more severe performance requirements are provided for refractory materials of melting furnaces; in addition to the above performance requirements, it is also desirable to have properties such as extremely low foaming rate, calculus rate, and high temperature resistivity as high as possible; the zirconia material is the preferred material of the key part of the electronic glass melting furnace due to the excellent characteristics; at present, most of electronic glass melting furnaces at home and abroad use an electric melting high-zirconium brick with the zirconium oxide content of more than 85 percent, but the product has great preparation difficulty, only very individual suppliers in the global range have the preparation technology of the product at present, and the product cannot be produced at home.
As is known, zirconia materials have three crystal forms of monoclinic, tetragonal and cubic, the monoclinic phase and tetragonal phase are transformed at about 1170 ℃, and are accompanied by large volume change, and since pure zirconia exists in the monoclinic phase, the volume change of the monoclinic phase at about 1170 ℃ can cause cracking of products, so that the zirconia cannot be used for producing refractory bricks; the raw material used for zirconia refractory is zirconia having a large amount of cubic phase containing a sufficient amount of stabilizer (Y)2O3、MgO、CaO、Ce2O3One or more of the above) stable zirconia, which does not undergo phase transition during the preparation process, such as a sintered zirconia product widely used in the fields of steel continuous casting and smelting systems, tungsten-molybdenum sintering intermediate frequency furnaces, sapphire crystal growth furnaces, fused quartz furnaces, etc., is mainly the stable zirconia, which contains a certain proportion of a stabilizer. The existing preparation process of the sintered zirconia product is relatively mature, but the sintered zirconia product can not be applied to a glass kiln, in particular to an electronic glass kiln; the reasons for this are as follows: (1) in order to reduce the phase change volume effect in the sintering process as much as possible, the existing sintered zirconia product contains at least more than 70 percent of cubic phase, even all the cubic phase, but the cubic phase has a large thermal expansion coefficient, and when a temperature gradient exists, a large thermal stress is generated in the product, so that large-scale preparation is difficult to realize and the product has extremely poor thermal shock stability; (2) when the glass melt stabilizing agent is used for a long time, a large amount of stabilizing agent can react with components in the glass melt to form a new substance, so that the stabilizing agent is subjected to desolventization (the stabilizing agent is separated out from zirconia crystal lattices), and the stable cubic phase zirconia after the desolventization is converted into a monoclinic phase along with a subsequent volume effect; (3) the existing sintered zirconia product contains a certain proportion of granules with the granularity of more than 0.1mm, and the granules are used for a long timeOnce entering the molten glass, the quality of the molten glass is seriously influenced; (4) the prior sintered zirconia product has high porosity and low strength and can not resist the permeation, erosion and scouring of molten glass.
Zirconia in the existing electric melting high-zirconium brick is basically all monoclinic phase, thereby avoiding the problems of desolventization, poor thermal shock stability and the like of a stabilizer in the using process; more than 10 percent of SiO is introduced into the electric melting high-zirconium brick2In the course of electric melting, SiO2The glass state exists, the glass state existing form can buffer the volume effect when the monoclinic phase is subjected to phase change, and the probability of cracks is reduced, so that the large-scale preparation of the electric melting high-zirconium brick is realized; however, because of the limitation of the self-process of electric melting preparation, the content of glass phase in the electric melting high-zirconium brick is high, and in the process of cooling the melt, the density, the distribution of the glass phase, the size of crystal grains and the like of different parts of the product have certain differences, which may cause the defects of glass phase precipitation, calculus and the like in use; in view of the manufacturing cost, the electric smelting preparation process has low discharge rate, long process period and large consumption of consumables such as molding sand, and the product is expensive.
Therefore, it would be beneficial to the application of glass fiber kilns to find a high zirconia product that is resistant to high temperatures, erosion and has a range of zirconia material-specific properties, and to implement a manufacturing technique that is large in size and low in manufacturing cost.
Disclosure of Invention
The invention aims to overcome the defects of the prior art and aims to provide a preparation method of a sintered compact zirconia brick, which has a uniform structure, lower porosity, excellent erosion resistance, higher strength and relatively lower production cost and can realize large-scale preparation.
In order to solve the problems in the prior art, the invention adopts the following technical scheme:
the preparation method of the sintered compact high-zirconium brick comprises the preparation of slurry, wherein the powder raw material of the slurry comprises 95-100 parts of partially-stabilized fused zirconia fine powder and 0-5 parts of high-purity SiO2Powder; said partially stabilized electrofusion oxidationThe zirconium powder is obtained by an electric melting process, the phase composition of the zirconium powder contains 40 to 70 percent of monoclinic phase, and the stabilizing agent is Y2O34 to 7 percent of stabilizer, wherein 1.2 to 1.8 percent of Hf is associated2O3(ii) a The partially stabilized fused zirconia powder consists of three particle sizes: d50 is 20 mu m of powder marked as Z1, accounting for 10-40 percent of the total weight of the powder; d50 is 5 mu m marked as Z2 powder accounting for 30-70%, D50 is 2 mu m marked as Z3 powder accounting for 5-20%; the high-purity SiO2 powder is one or two of nano silicon dioxide powder or fused quartz powder, the particle size of the powder is 20-200 nm, and the content of SiO2 is more than 99.7%; the powder raw material, a liquid binder, a dispersant and a solvent are subjected to ball milling, stirring, grinding and dispersing to obtain uniform slurry; pumping the slurry to a centrifugal spray drying tower to form granules at the temperature of 200-300 ℃; putting the granulated material into a mold, and pressing by cold isostatic pressing under the pressure of 150-200 Mpa to form a green body; firing the green body at 1800 ℃ to form a sintered body; the sintered green body is mechanically processed into a sintered compact high-zirconium brick; the sintered compact high-zirconium brick has the porosity of less than 10%, the compressive strength of more than 200MPa, W (Hf 2O3+ ZrO 2) ≥ 90%, W (Y2O 3) = 3-7%, and W (SiO 2) = 1-5%.
The liquid bonding agent comprises a silica sol solution and a PVA solution, the adding amount of the liquid bonding agent is 1-5% and 2-6% of the weight of the powder raw material respectively, and SiO in the silica sol solution2The content is 30-40%, and the average particle size is 5-10 nm.
The dispersing agent is an ether polycarboxylate surfactant with the trade name of FS20, and the adding amount of the dispersing agent is 0.2-0.3% of the weight of the powder.
The solvent is one of water and deionized water, and the adding amount of the solvent is 25-50% of the weight of the powder raw material.
The granulating material is a nearly spherical particle formed by centrifuging, spraying and drying slurry powder, the particle size is less than 0.2mm, the water content is about 0.2-0.3%, and the granulating material has excellent fluidity and compressibility.
Due to the adoption of the technical scheme, compared with the prior art, the invention has the following positive effects and characteristics:
(1) different from zirconia without stabilizer in monoclinic modeThe fused high-zirconium brick comprises fused high-zirconium bricks or sintered zirconia materials which are all zirconia and a stabilizing agent thereof, wherein the stabilizing agent Y is 3-7 percent of the components2O3And also contains 1 to 5% of SiO2The component design is more beneficial to the sintering of large-scale blanks; y is2O3The existence of the composite material ensures that the selected raw material is partially stable zirconia containing monoclinic phase with a proportion of 40-70%, and the monoclinic phase with a certain proportion ensures that the material has moderate thermal expansion coefficient and phase change volume effect, so that the cracking caused by overlarge phase change volume effect or the thermal stress cracking caused by overlarge thermal expansion coefficient in the sintering process of the material can be relieved; SiO22The introduction purpose of the method is to form a glass phase in a high-temperature process, a solid or liquid silicon source with nanometer granularity is uniformly dispersed around a micron-sized zirconium oxide raw material in a liquid ball milling medium, and the formed glass phase can relieve the volume effect of zirconium oxide and release the internal stress inside a blank body during high-temperature sintering. The component design is more beneficial to realizing the preparation of large-size zirconia products.
(2) SiO in the invention2The content is less, the glass phase is below 6%, compared with an electric melting high-zirconium brick, the glass liquid precipitation degree in the using process is smaller, and meanwhile, an electric melting zirconia raw material instead of a sintering zirconia raw material is selected, so that the dispersion of a stabilizer in the electric melting zirconia is more uniform, the crystal grain in the raw material is better developed, and the erosion resistance is facilitated.
(3) The invention does not use the particle material with the granularity larger than 0.1mm, and all the raw materials are ball-milled and dispersed in a liquid medium, and then are molded by isostatic pressing, and the sintered blank has uniform structure and components, low porosity and high strength, and is suitable for the use working condition of the glass melting furnace.
(4) The invention adopts isostatic pressing and sintering processes, and has more advantages in preparation period and discharge rate compared with the electric melting process.
Detailed Description
Example (b):
a sintered compact high zirconium brick and a method for preparing the same, wherein a slurry is prepared by mixing various raw materials listed in Table 1 according to the following scheme, and the slurry is prepared by the following steps: adding part of stable electrofusion zirconium oxide powder, high-purity silicon dioxide powder, a dispersing agent and deionized water into a ball-milling stirring mill, stirring for 30 minutes, then adding a silica sol solution, continuously stirring for 60 minutes, and finally adding a PVA solution, and stirring for 30 minutes to obtain uniformly dispersed slurry;
TABLE 1 slurry composition
TABLE 1
As shown in table 1, the more monoclinic zirconia proportion in the selected raw material, the more solid or liquid silicon source is introduced correspondingly, and only several combinations are selected in the examples; the silicon source is introduced through high-purity silicon dioxide powder and also comprises a binding agent silica sol; the high-purity SiO2 powder is one or two of nano silicon dioxide powder or fused quartz powder, the granularity of the powder is 20-200 nm, and the content of SiO2 is more than 99.7%; the content of SiO2 in the silica sol solution is 30-40%, the average particle size is 5-10 nm, and the adding amount is 1-5% of the weight of the powder.
The raw material of the partially stabilized electrically-fused zirconia powder in the slurry composition is obtained by an electric smelting process, the phase composition of the partially stabilized electrically-fused zirconia powder comprises 40-70% of monoclinic phase, and the stabilizer is Y2O34 to 7 percent of stabilizer, wherein 1.2 to 1.8 percent of Hf is associated2O3(ii) a The partially stabilized fused zirconia powder consists of three particle sizes: d50 is 20 mu m of powder marked as Z1, accounting for 10-40 percent of the total weight of the powder; d50 is 5 mu m marked as Z2 powder accounting for 30-70%, D50 is 2 mu m marked as Z3 powder accounting for 5-20%; the PVA solution is added in an amount of 2-6% of the weight of the powder raw materials respectively;
preparing a granulating material:
the slurry is pumped to a centrifugal spray drying tower to form granules in an environment of 200-300 ℃, the granules are approximately spherical granules formed by centrifuging, spraying and drying slurry powder, the granularity is less than 0.2mm, the water content is about 0.2-0.3%, and the granules have excellent fluidity and compressibility;
preparing a green body:
directly putting the granulated material into a mold, pressing the granulated material into a green body in an isostatic press under the pressure of 150-200 MPa, wherein the green body can be in the shape of a thin plate, a cuboid or a cylinder according to the selection of the mold;
preparation of the sintered body
The green body is directly subjected to heat preservation sintering at 1800 ℃ in a high-temperature kiln without being dried to obtain a sintered body, and the heat preservation time of the sintered body can be selected from 6 to 50 hours according to the size of the sintered body; the sintered compact high-zirconium brick has porosity less than 10%, compressive strength greater than 200MPa and W (Hf)2O3+ZrO2）≥90，，W（Y2O3）=3～7%，W（SiO2) = 1-5%, and table 2 lists the sintered body compositions and properties obtained for several example slurries.
TABLE 2
As listed in tables 1 and 2, the more monoclinic phase ratio in the zirconia raw material selected in the examples, the more glass phase is used to buffer the phase transition volume effect during sintering, i.e. the more silicon source is introduced, and the limited number of ways are listed in the examples.
As shown in tables 1 and 2, the partially stabilized zirconia powders with different particle sizes have different sintering activities, and the shrinkage of the green body can be controlled by adjusting the proportion thereof, which reflects the properties of the sintered body, i.e., porosity or density. Different particle size combinations can obtain sintered bodies with different densities and strengths.
Claims (5)
1. A preparation method of a sintered compact high-zirconium brick is characterized by comprising the following steps: the preparation method of the sintered compact zirconium brick comprises the preparation of slurry, wherein the powder raw material of the slurry comprises 95-100 parts of partially-stabilized fused zirconia fine powder and 0-5 parts of high-purity SiO2Powder; the partially stabilized electrically fused zirconia powder is obtained by an electric smelting process, the phase composition of the partially stabilized electrically fused zirconia powder contains 40 to 70 percent of monoclinic phase, and the stabilizer is Y2O3The content of the stabilizer is4 to 7% of Hf with 1.2 to 1.8%2O3(ii) a The partially stabilized fused zirconia powder consists of three particle sizes: d50 is 20 mu m of powder marked as Z1, accounting for 10-40 percent of the total weight of the powder; d50 is 5 mu m marked as Z2 powder accounting for 30-70%, D50 is 2 mu m marked as Z3 powder accounting for 5-20%; the high-purity SiO2 powder is one or two of nano silicon dioxide powder or fused quartz powder, the particle size of the powder is 20-200 nm, and the content of SiO2 is more than 99.7%; the powder raw material, a liquid binder, a dispersant and a solvent are subjected to ball milling, stirring, grinding and dispersing to obtain uniform slurry; pumping the slurry to a centrifugal spray drying tower to form granules at the temperature of 200-300 ℃; putting the granulated material into a mold, and pressing by cold isostatic pressing under the pressure of 150-200 Mpa to form a green body; firing the green body at 1800 ℃ to form a sintered body; the sintered green body is mechanically processed into a sintered compact high-zirconium brick; the sintered compact high-zirconium brick has the porosity of less than 10%, the compressive strength of more than 200MPa, W (Hf 2O3+ ZrO 2) ≥ 90%, W (Y2O 3) = 3-7%, and W (SiO 2) = 1-5%.
2. The sintered dense high-zirconium brick and the method of manufacturing the same according to claim 1, wherein: the liquid binder comprises a silica sol solution and a PVA solution, the adding amount of the silica sol solution is 1-5% and 2-6% of the weight of the powder raw material respectively, the content of SiO2 in the silica sol solution is 30-40%, and the average particle size is 5-10 nm.
3. The sintered dense high-zirconium brick and the method of manufacturing the same according to claim 1, wherein: the dispersing agent is an ether polycarboxylate surfactant with the trade name of FS20, and the adding amount of the dispersing agent is 0.2-0.3% of the weight of the powder.
4. The sintered dense high-zirconium brick and the method of manufacturing the same according to claim 1, wherein: the solvent is one of water and deionized water, and the adding amount of the solvent is 25-50% of the weight of the powder raw material.
5. The sintered dense high-zirconium brick and the method of manufacturing the same according to claim 1, wherein: the granulating material is a nearly spherical particle formed by centrifuging, spraying and drying slurry powder, the particle size is less than 0.2mm, the water content is about 0.2-0.3%, and the granulating material has excellent fluidity and compressibility.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN115894018A (en) * | 2023-01-05 | 2023-04-04 | 郑州方铭高温陶瓷新材料有限公司 | Glass kiln material flowing nozzle brick and preparation method thereof |
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| US20120046156A1 (en) * | 2009-02-25 | 2012-02-23 | Saint-Gobain Centre De Recherches Et D'etudes Europeen | Refractory product with high zirconia content |
| CN110845245A (en) * | 2019-12-13 | 2020-02-28 | 中钢集团洛阳耐火材料研究院有限公司 | Compact high-purity zirconia refractory product |
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| US20120046156A1 (en) * | 2009-02-25 | 2012-02-23 | Saint-Gobain Centre De Recherches Et D'etudes Europeen | Refractory product with high zirconia content |
| CN110845245A (en) * | 2019-12-13 | 2020-02-28 | 中钢集团洛阳耐火材料研究院有限公司 | Compact high-purity zirconia refractory product |
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Cited By (2)
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| CN115894018A (en) * | 2023-01-05 | 2023-04-04 | 郑州方铭高温陶瓷新材料有限公司 | Glass kiln material flowing nozzle brick and preparation method thereof |
| CN115894018B (en) * | 2023-01-05 | 2023-09-22 | 郑州方铭高温陶瓷新材料有限公司 | Glass kiln material flow nozzle brick and preparation method thereof |
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