WO2005068393A1 - Fusion-cast refractory with high electrical resistivity - Google Patents
Fusion-cast refractory with high electrical resistivity Download PDFInfo
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- WO2005068393A1 WO2005068393A1 PCT/US2004/044042 US2004044042W WO2005068393A1 WO 2005068393 A1 WO2005068393 A1 WO 2005068393A1 US 2004044042 W US2004044042 W US 2004044042W WO 2005068393 A1 WO2005068393 A1 WO 2005068393A1
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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
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Definitions
- the present invention relates to fusion-cast zirconia materials, and in particular, to a fusion-cast zirconia refractory having high electrical resistivity suitable for use in glass-melting furnaces.
- Fused refractories comprising primarily Zr0 2 (“zirconia”) are traditionally used in glass melting furnaces.
- the zirconia provides excellent corrosion resistance to the molten glass.
- Refractories utilizing AI 2 0 3 -Zr ⁇ 2 -Si0 2 known as AZS refractories are well known in the art. Such refractories that have a Zr0 2 concentration of 80 wt % or higher are referred to as high- zirconia fused refractories.
- the refractory used in the glass melting furnace have high electrical resistivity. It is also generally desirable that the refractory provides superior resistance to corrosion and thermal cycling.
- the '643 Patent discloses a fused zirconia refractory that utilizes 0.05 to 1.0% of P 2 0 5 in order to soften the matrix glass. Though this refractory exhibits an acceptable level of electrical resistance, its main objective was to improve the thermal cycling resistance and it does so by increasing the total amount of the glassy phase, which may decrease the corrosion resistance of the refractory.
- the '612 Patent discloses a fused zirconia refractory that eliminates the use of P 2 0 5 , but adds in 0.05 to 3% of BaO, SrO and MgO in total, in order to reduce the stresses on the glassy phase of the refractory that are caused by the elimination of P 2 0 5 .
- the '612 Patent further discloses the use of Na 2 0 (in an amount greater than .05%) and K 2 0 to reduce the tensile stress that is caused by the addition of the alkaline earth metal oxides listed above. The presence of
- the present invention seeks to achieve high electrical resistance in the fused
- Zirconia refractory while minimizing the concentration of BaO, SrO, MgO, CaO, P 2 0 5 , Na 2 0 and
- a fusion-cast refractory comprises 0.8% to 2.5% Al 2 0 3 , 4.0% to 10.0% Si0 2 , 86% to 95% Zr0 2 , 0.1% to 1.2% B 2 0 3 , up to 0.04% Na 2 0, up to 0.4% CaO, up to 0.1 % Fe 2 0 3 and up to 0.25% Ti0 2 .
- the refractory comprises 0.8% to 2.5% Al 2 0 3 , 4.0% to 10.0% Si0 2 , 86% to 95% Zr0 2 , 0.1% to 1.2% B 2 0 3 , up to 0.04% Na 2 0, up to 0.4% CaO, up to 0.1 % Fe 2 0 3 and up to 0.25% Ti0 2 .
- the present invention is a fusion-cast refractory comprising 0.8% to 2.5% Al 2 0 3 , 4.0% to 10.0% Si0 2l 86% to 95% Zr0 2 , 0.1% to 1.2% B 2 0 3 , up to 0.04% Na 2 0, up to 0.4% CaO, up to 0.1% Fe 2 0 3 and up to 0.25% Ti0 2 .
- Refractories made in accordance with the present invention are characterized by an electrical resistivity of at least 80 ohm-cm at 1625°C.
- the present invention is a fusion-cast refractory comprising 0.9% to 2.0% Al 2 0 3 , 6.0% to 8.0% Si0 2 , 88% to 92% Zr0 2 , 0.3% to 0.9% B 2 0 3 , up to 0.04% Na 2 0, up to 0.2% CaO, up to 0.05% Fe 2 0 3 and up to 0.15% Ti0 2 .
- the Zr0 2 content of the refractory according to the invention is 86 to 94%, and preferably is 88 to 94%.
- the Si0 2 content of the refractory according to the invention is 4 to 10%, or preferably 6 to 8%.
- the glass phase cannot be formed as a continuous matrix phase at a content of less than 4%, while poor resistance to molten glass may be expected at a content of higher than 10%.
- the Al 2 0 3 content of the refractory according to the present invention is 0.8 to 2.5%, and preferably 0.9 to 2.0%. Al 2 0 3 improves the flowability of the melt at a content higher than 0.8%, but content higher than 2.5% leads to instability of the glass phase, rendering the product prone to failure.
- the B 2 0 3 content of the refractory according to the present invention is 0.1 to 1.2%, and is preferably 0.3 to 0.9%.
- the addition of B 2 0 3 aids in suppressing cracks in the refractory during fabrication. This benefit is not realized at a content of less than 0.1%, and concentrations over 1.2% can cause an anomalous behavior of the glassy phase.
- CaO is an optional component of the refractory according to the present invention, and is present in an amount from 0.0 to 0.4% of the refractory.
- the CaO may be added in order to help reduce the stresses in the refractory and to reduce cracking during fabrication.
- the addition of CaO is also beneficial when the refractory of the present invention is used in a glass melting furnace where TFT-LCD glass or plasma display panels are formed, as those molten glasses may also contain CaO.
- Na 2 0 and K 2 0 are also optional components of the refractory according to the present invention, present in an amount from 0.0 to 0.04% of the refractory.
- the alkali is a preferably eliminated from the refractory, as it is the major source of electrical conduction in the glass.
- Ti0 2 and Fe 2 0 3 may be present as impurities, but their individual concentrations should not exceed 0.25% for the Ti0 2 , 0.1% for the Fe 2 0 3 , and the total concentration should not exceed 0.35% because they may encourage defect forming potential of the refractory. Examples
- the raw materials include zirconia (derived from zircon sand by removing most of its silica), zircon sand, calcined alumina, boric oxide, calcium carbonate, and dead-burned magnesia. These raw materials are selected such that the impurities (such as Fe 2 0 3 , Ti0 2 , Na 2 0, K 2 0) are reduced to a minimum level.
- the raw materials were carefully weighed and blended into a homogeneous mixture, and subsequently discharged into a large steel crucible for melting.
- the steel crucible was powered by graphite electrodes using 3 phase current supply.
- the outside of crucible was cooled by water continuously during the operation.
- the liquid in this container is allowed to cool rapidly.
- the resulting sample is tested for chemistry using an X-ray Fluorescence Spectrometer. All but one constituents of the zirconia refractory can be analyzed quantitatively using the X-ray Fluorescence Spectrometer.
- B 2 0 3 is analyzed using either Inductively Coupled Plasma Spectrometer (ICP) or DC Arc Emission method. The chemistries of the various samples are listed in the table below.
- the density may be obtained from a small cylindrical core sample, about 25mm in diameter and 100mm long, using Archimedes Water Immersion method, or by weighing the complete casting (after it has been machined to remove the mold skin) and dividing the weight by the casting's external volume.
- the electrical resistivity was measured on a cylindrical sample, 25mm in diameter and 50mm long, using a 4-point electrode assembly. The ends of the sample are coated with platinum ink. Platinum ink was also placed on the circumference of the sample at two places, 25 mm apart and 12.5 mm from each end. Platinum wire was then wrapped around under each end of the sample, as well as on the two internal places mentioned above. Current was applied along the ends and voltage drop is measured across the 25mm band in the guage section described above. Resistivity is measured both using alternating and direct current. [0024] The microstructure is checked on a series of samples, each about 25mm long by 15mm wide mounted in an epoxy resin and polished to 1 micron surface finish.
- These samples can be taken from a cylindrical core, typtcally drilled on a perpendicular through the center of the broadest face of the block so as to represent the average microstructure. Polished sections are typically prepared from regions close to the outside face of the casting as well as its core The microstructure can be checked using both an Optical microscope and Electron Microscope. Identification of crystalline phases is done using an X-ray diffractometer. Glass phase chemistry can be defined using Energy Dispersive Spectrometry (EDS) in the electron microscope. Mean boron content of the glass phase can be estimated by difference of the total analysis from 100%. It can also be more accurately computed from data derived from bulk chemical analysis on powder obtained from the same sample - by ratio with the Silicon content determined by both EDS and bulk chemistry methods.
- EDS Energy Dispersive Spectrometry
- Resistance to thermal cycling is typically performed on samples, 25mm in diameter by 50mm long, taken from various locations in the casting
- the samples are cycled from 1250C to 800C at least 20 times using a controlled heat-up and cool down rate in an electric furnace.
- the change in sample volume can be measured using Water Immersion method.
- the presence of cracks can be documented using a photograph.
- Examples 4-13 were produced using the method described above Comparative Examples 1-3 were produced using the same method
- the chemical makeup of each example is listed in the table below.
- the electrical resistivity for each example is also provided in the table below.
- examples 4, 12 and 13 provided the most desirable results. All of the examples 4-13 achieved the desired resistivity of at least 80 ohm-cm. All of the examples were also acceptable in terms of resistance to thermal cycling.
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Abstract
Description
Claims
Priority Applications (8)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
AT04816024T ATE510804T1 (en) | 2004-01-02 | 2004-12-30 | FELTS-CAST REFRIGERANT MATERIALS BASED ON ZIRCONIUM OXIDE WITH HIGH ELECTRICAL RESISTANCE |
AU2004313955A AU2004313955B2 (en) | 2004-01-02 | 2004-12-30 | Fusion-cast refractory with high electrical resistivity |
US10/585,165 US7598195B2 (en) | 2004-01-02 | 2004-12-30 | Fusion-cast refractory with high electrical resistivity |
EP04816024A EP1711445B1 (en) | 2004-01-02 | 2004-12-30 | Fusion - cast zirconia refractory with high electrical resistivity |
JP2006547592A JP4714697B2 (en) | 2004-01-02 | 2004-12-30 | Melt cast zirconia refractory with high electrical resistance |
CN200480039608XA CN1902142B (en) | 2004-01-02 | 2004-12-30 | Fusion-cast refractory with high electrical resistivity |
BRPI0418269A BRPI0418269B1 (en) | 2004-01-02 | 2004-12-30 | refractory |
ZA2006/05017A ZA200605017B (en) | 2004-01-02 | 2006-06-19 | Fusion-cast refractory with high electrical resistivity |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US53399004P | 2004-01-02 | 2004-01-02 | |
US60/533,990 | 2004-01-02 |
Publications (1)
Publication Number | Publication Date |
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WO2005068393A1 true WO2005068393A1 (en) | 2005-07-28 |
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ID=34794245
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/US2004/044042 WO2005068393A1 (en) | 2004-01-02 | 2004-12-30 | Fusion-cast refractory with high electrical resistivity |
Country Status (10)
Country | Link |
---|---|
US (1) | US7598195B2 (en) |
EP (1) | EP1711445B1 (en) |
JP (1) | JP4714697B2 (en) |
CN (1) | CN1902142B (en) |
AT (1) | ATE510804T1 (en) |
AU (1) | AU2004313955B2 (en) |
BR (1) | BRPI0418269B1 (en) |
RU (1) | RU2006124609A (en) |
WO (1) | WO2005068393A1 (en) |
ZA (1) | ZA200605017B (en) |
Cited By (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2007099253A3 (en) * | 2006-02-24 | 2007-11-15 | Saint Gobain Ct Recherches | High-resistivity refractory having a high zirconia content |
FR2920152A1 (en) * | 2007-08-24 | 2009-02-27 | Saint Gobain Ct Recherches | REFRACTORY WITH HIGH ZIRCONIA CONTENT AND HIGH SILICA CONTENT. |
FR2920153A1 (en) * | 2007-08-24 | 2009-02-27 | Saint Gobain Ct Recherches | REFRACTORY PRODUCT HAVING A HIGH DOPE ZIRCONE CONTENT. |
JP2009155150A (en) * | 2007-12-26 | 2009-07-16 | Saint-Gobain Tm Kk | High electric resistance high zirconia cast refractory |
WO2009153517A1 (en) | 2008-06-16 | 2009-12-23 | Saint-Gobain Centre De Recherches Et D'etudes Europeen | High zirconia refractory material |
WO2010097769A1 (en) | 2009-02-25 | 2010-09-02 | Saint-Gobain Centre De Recherches Et D'etudes Europeen | Refractory product having a high zirconia content |
FR2953825A1 (en) * | 2009-12-16 | 2011-06-17 | Saint Gobain Ct Recherches | REFRACTORY PRODUCT HAVING A HIGH ZIRCONY CONTENT. |
FR2955578A1 (en) * | 2010-01-28 | 2011-07-29 | Saint Gobain Ct Recherches | REFRACTORY PRODUCT HAVING A HIGH ZIRCONY CONTENT |
WO2011092658A1 (en) | 2010-01-28 | 2011-08-04 | Saint-Gobain Centre De Recherches Et D'etudes Europeen | Refractory product having high zirconia content |
KR101277403B1 (en) | 2006-06-28 | 2013-06-20 | 산고반.티에무 가부시키가이샤 | High-electric resistivity, high-zirconia fused cast refractories |
WO2016125317A1 (en) | 2015-02-02 | 2016-08-11 | Saint-Gobain Tm K.K. | High zirconia electrically fused cast refractory |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR2913013B1 (en) * | 2007-02-23 | 2009-12-18 | Saint Gobain Ct Recherches | REFRACTORY REFRACTOR BLOCK AND CASTING WITH HIGH ZIRCONY CONTENT |
KR101706397B1 (en) | 2009-04-06 | 2017-02-13 | 아사히 가라스 가부시키가이샤 | Highly zirconia-based refractory and melting furnace |
KR101206365B1 (en) * | 2010-02-24 | 2012-11-29 | 주식회사 케이씨씨 | A composition for preparing ceramic fiber and a biosoluble ceramic fiber prepared therefrom for heat insulating material at high temperature |
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WO2016172274A1 (en) * | 2015-04-24 | 2016-10-27 | Corning Incorporated | Bonded zirconia refractories and methods for making the same |
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- 2004-12-30 CN CN200480039608XA patent/CN1902142B/en not_active Expired - Fee Related
- 2004-12-30 AT AT04816024T patent/ATE510804T1/en not_active IP Right Cessation
- 2004-12-30 JP JP2006547592A patent/JP4714697B2/en not_active Expired - Fee Related
- 2004-12-30 BR BRPI0418269A patent/BRPI0418269B1/en not_active IP Right Cessation
- 2004-12-30 EP EP04816024A patent/EP1711445B1/en not_active Not-in-force
- 2004-12-30 RU RU2006124609/03A patent/RU2006124609A/en not_active Application Discontinuation
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Also Published As
Publication number | Publication date |
---|---|
AU2004313955A1 (en) | 2005-07-28 |
ZA200605017B (en) | 2008-01-08 |
AU2004313955B2 (en) | 2009-09-10 |
EP1711445B1 (en) | 2011-05-25 |
CN1902142B (en) | 2010-12-22 |
US7598195B2 (en) | 2009-10-06 |
EP1711445A1 (en) | 2006-10-18 |
JP4714697B2 (en) | 2011-06-29 |
EP1711445A4 (en) | 2008-12-03 |
BRPI0418269B1 (en) | 2016-03-08 |
JP2007517754A (en) | 2007-07-05 |
BRPI0418269A (en) | 2007-05-02 |
US20070249481A1 (en) | 2007-10-25 |
CN1902142A (en) | 2007-01-24 |
ATE510804T1 (en) | 2011-06-15 |
RU2006124609A (en) | 2008-01-20 |
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