foamable particulate cement is capable of forming sintered cordierite foamed ceramic masses. It consists essentially, by weight, of 1-40% cordierite grog, 99-60% ceramic base material and foaming agent, such as SiC. The ceramic base material is raw ceramic material that has an analytical molar composition consisting essentially of about 1.7-2.4 MO.1.2-2.4 Al2 O3.4.5-5.4 SiO2 wherein MO comprises about 0-55 mole % MgO and at least 45 mole % MnO. The grog is ceramic material that has been previously fired and comminuted, and that has an analytical molar composition consisting essentially of about 1.7-2.4 RO.1.9-2.4 Al2 O3.4.5-5.2 SiO2 wherein RO comprises MnO in an amount of 0 mole % up to a mole % that is about 20 mole % lower than the mole % of MO that is MnO and the balance is substantially MgO.
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1. A foamable particulate ceramic cement capable of forming a sintered cordierite foamed ceramic mass and consisting esentially, by weight, of:
1-40% cordierite grog, 99-60% ceramic base material and an effective amount of a foaming agent to effect foaming of the cement upon firing to produce the foamed ceramic mass,
the base material being raw ceramic material that has an analytical molar composition consisting essentially of about: 1.7-2.4 MO·1.2-2.4 Al2 O3 ·4.5-5.4 SiO2 wheein MO and at least 45% MnO, and the grog being ceramic material that has been previously first and comminuted, and that has an analytical molar composition consisting essentially of about: 1.7-2.4 RO·1.9-2.4 Al2 O3 ·4.5-5.2 SiO2 wherein RO comprises, as mole % of RO, MnO in an amount of 0% up to a mole % that is about 20 mole % lower than the mole % of MO that is MnO and the balance is substantially MgO. 2. cement of
4. cement of
5. cement of
1.7-2.4 MO·1.9-2.4 Al2 O3 ·4.5-5.2 SiO2.
9. cement of
1.8-2.1 RO·1.9-2.1 Al2 O3 ·4.9-5.2 SiO2 and MO is wholly MnO where RO comprises 8-12 mole % MnO and the balance MgO.
11. cement of
1.8-2.1 MO·1.9-2.1 Al2 O3 ·4.9-5.2 SiO2 and MO is wholly MnO.
12. A ceramic structure comprising at least two closely spaced cordierite ceramic surfaces having a sintered cordierite foamed ceramic mass in the space between and bonded to those surfaces, and the foamed ceramic mass being formed of the cement of
13. A method of providing a sintered cordierite foamed ceramic mass between and bonded to at least two closely spaced cordierite ceramic surfaces of a ceramic structure, which method comprises:
disposing the cement of firing the strucutre with the cement so disposed to foaming temperature in the range of about 1160°-1325°C, and thereafter cooling the structure with the cement converted to the foamed ceramic mass.
14. The method of
15. The method of
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In fabricating products or structures comprising open celled or honeycomb ceramic components, it is sometimes necessary to utilize a ceramic cement to bond a plurality of such components together or to solid ceramic components, or to fill or plug selected cells (in whole or in part) within such components.
For joining lithium aluminosilicate ceramic components having low coefficients of thermal expansion U.S. Pat. Nos. 3,189,512 and 3,634,111 disclose foaming ceramic cements comprising SiC foaming agent mixed lithium aluminosilicate ceramic material to form foamed ceramic cement bonds with and to fill the spaces between adjacent surfaces of those components. Thus, the components and the foamed cement have comparable properties (e.g. low coefficients of thermal expansion, chemical durability, etc.)
In recent years, occasions have arisen where it has been desirable to form the products or structures of cordierite ceramics also having low coefficients of thermal expansion because the cordierite ceramics provide properties (e.g. thermal and chemical) which are more beneficial than those of lithium aluminosilicate ceramics. Thus, for example, cordierite ceramic honeycomb structures have higher use (melting point) temperatures and are more resistant to sodium present in gas streams flowed through the cells of such structures (as in industrial heat recovery wheels). It is also desirable, then, to use foaming ceramic cements withthese cordierite components that develop foamed cordierite cement bonds or plugs of comparable beneficial properties.
It is further desirable to form the cement mixture from unfired ceramic bath materials so as to avoid the expenditure of extra energy for prefiring or fusing such materials and from such materials as will form manganese cordierite (2MnO·2Al2 ·5SiO2), which has a distinctly lower melting point than other types of cordierites but that is still suitably high for the desired uses. However, attempts to formulate foaming cements based on SiC foaming agent mixed with wholly raw (unfired) ceramic batch materials of combined composition designed to yield manganese cordierite resulted in foamed sintered clement cement masses that did not contain any significant codierite crystal phase. Rather, those resultant fired cements comprised mainly mullite and sometimes other noncordierite silicate phases lacking the desirable characteristics (e.g. durability) of cordierite. Similar undesirable results of failing to produce cordierite foamed cement were founded with mixtures of silicon carbide with devitrifiable glass frit of the type shown in U.S. Pat. No. 4,191,583 to form Mg-Mn cordierite glass-ceramic when not mixed with SiC.
It has now been discovered that a foamable particulate ceramic cement capable of forming a sintered cordierite foamed ceramic mass can be made by seeding ceramic base material of controlled composition with cordierite grog of another controlled composition and adding thereto a foaming agent in an effective amount to effect foaming of the cement upon firing to produce the foamed ceramic mass.
The cement of the present invention consists essentially, by weight, of 1-40% cordierite grog, 99-60% ceramic base material and foaming agent. The base material is raw ceramic material that has an analytical molar composition consisting essentially of about 1.7-2.4 MO·1.2-2.4 Al2 O3 ·4.5-5.4 SiO2 wherein MO comprises, as mole % of MO, about 0.55% MgO and at least 45% MnO. The grog is ceramic material that has been previously fired and comminuted, and that has an analytical molar composition consisting esentially of about 1.7-2.4 RO·1.9-2.4 Al2 O3 ·4.5-5.2 SiO2 wherein RO comprises, as mole % of RO, MnO in an amount of 0% up to a mole % that is about 20 mole % lower than the mole % of MO that is MnO and the balance is substantially MgO. Minor portions of MgO in either or both of MO and RO can be replaced by equal molar amounts of other oxides such as NiO, CoO, FeO and TiO2 as noted in U.S. Pat. No. 3,885,977, which is incorporated herein by reference. Foaming agent can be selected from a variety of substances that decompose to give off gas at about the foaming temperature of the cement, i.e. the temperature at which the grog and base material are in a softened condition adequate to be foamed by the gas. Among such substances are compounds such as carbides, carbonates, sulfates, etc., preferably of cations that are in the grog and/or base material. Silicon carbide is the preferred foaming agent and can be employed in any effective amount (usually at least 0.25 wt. %) up to a practical amount of about 5% by weight of grog plus base material. Larger amounts can be employed without additional benefit, but they dilute the amount of ceramic in the foamed mass. Generally 1-2 wt. % SiC (by weight of grog plus base material is preferred.
To insure thorough cordierite crystallization in the foamed ceramic masses, it is advantageous for the grog in the cement to be at least 5 wt.% and correspondingly for the base material to not exceed 95 wt. %. Preferred proportions are 5-20 wt. % grog and 95-80 wt. % base material.
While the invention can broadly utilize base compositions within the aforesaid molar composition range embracing both the stoichiomeric cordierite area and the nonstoichrometric eutectic cordierite area, it is preferred to use base compositions of the generally stoichiometric type having an analytical molar composition consisting essentially of about 1.7-2.4 MO·1.9-2.4 Al2 O3 ·4.5-5.2 SiO2 wherein MO is as previously stated. Most preferably, such molar composition is about 1.8-2.1 MO·1.9-2.1 Al2 O3 ·4.9-5.2 SiO2 and MO is wholly MnO.
The requisite minimum difference of about 20 mole % for MnO in MO and RO provides the grog with adequately higher melting point vis a vis melting point of the base material so as to insure proper cordierite crystallization seeding effect by the grog at foaming temperature. To enhance such effect, it is preferred to have MO of the base composition comprise not more than about 15 mole % MgO.
The most preferable grog has an analytical composition of about 1.8-2.1 RO·1.9-2.1 Al2 O3 ·4.9-5.2 SiO2, and RO comprises 8-12 mole % MnO and the balance MgO.
If desired, optional customary fluxes may be included in the cement in minor amounts up to 5 wt. % or so of the grog plus base material. Such fluxes are illustratively disclosed in U.S. Pat. Nos. 3,189,512 and 3,634,111, which are incorporated herein by reference.
The present invention also encompasses ceramic structures employing the novel sintered cordierite foamed ceramic mass and the method providing such mass in the structures. The structure broadly comprises at least two closely spaced cordierite ceramic surfaces having the mass in the space between and bonded to those surfaces. In the method, the cement is disposed between such surfaces, then the structure with the cement so disposed is fired to foaming temperature in the range of about 1160°-1325°C and therafter cooled with the cement converted to the foamed ceramic mass. Preferably the foaming temperature is in the range of 1170°-1250°C, expecially for attaining foamed ceramic mass that is substantially impervious to fluids. Lower temperatures fail to develop an adequate foaming of the cement. Also, it is desirable to fire to the foaming temperature at an average rate of at least about 100°C per hour (preferably at least about 200° C. per hour) to avoid the possible adverse effect of much slower (e.g. 50°C/hr.) heating rates that may cause loss of foaming agent gas before the ceramic constituents of the cement are soft enough to be foamed .
A series of foamable particulate ceramic cement samples according to this invention were prepared by thoroughly mixing the batch materials as shown in Table I to form pastes of these samples.
The analytical molar composition of the combined raw base materials of clay, silica and MnCO3 for Samples 1-4 and 6 was 1.84 MnO·2.04 Al2 O3 ·5.11 SiO2. Such composition for Sample 5 was 2.36 MnO·1.29 Al2 O3 ·5.35 SiO2.
| TABLE I |
| ______________________________________ |
| Batch Compositions - weight % of total ceramic materials |
| (excluding SiC) |
| Samples |
| Batch materialsa |
| 1 2 3 4 5 6 |
| ______________________________________ |
| Georgia-Kaolin Kaopaque |
| 60.77 57.57 51.17 |
| 38.38 |
| 25.04 |
| 57.57 |
| 10 clay (APS 10) |
| Penn. Glass Sand Minusil |
| 7.43 7.04 6.26 4.69 12.57 |
| 7.04 |
| silica (APS 5) |
| Baker reagent MnCO3 |
| 26.80 25.39 22.57 |
| 16.93 |
| 22.39 |
| 25.39 |
| powder |
| Mn--Mg cordierite grog |
| 5.0 10.0 20.0 40.0 40.0 10.0 |
| (95 wt. % - 200 mesh) |
| Norton RA 600 SiC |
| 1.96 1.91 1.80 1.60 1.60 1.0 |
| (600 grit) |
| Methyl cellulose binder/ |
| 2.4 2.3 2.0 1.5 1.5 2.0 |
| plasticizer |
| Distilled water plasticizerc |
| 50-100 |
| Foaming temperature °C. |
| 1170 1185 1210 1250 1250 1185 |
| Coefficient of Thermal |
| -- 19.6 17.2 17.7 27.3 17.7 |
| Expansion × 10-7 /°C. |
| ______________________________________ |
| a APS means average particle size in micrometers |
| b Over 25-1000°C. |
| c Amounts varied among different trials of each Sample to provide |
| different cement viscosities suitable for each cementing trial. |
The Mn-Mg cordierite grog in the cement batches in Table 1 was a dense ceramic product of the type described and claimed in copending application Ser. No. 165,111 of Irwin M. Lachman and entitled Dense Cordierite Containing Manganese, which was filed on the same date as this application and is assigned to the assignee of this application. In particular, the grog was made of the following batch composition (in weight % of the total ceramic batch materials):
| ______________________________________ |
| Mg Cordierite grog (95% - 200 mesh) |
| 84.48 |
| Georgia-Kaolin Kaopaque 10 clay (APS 10) |
| 10.00 |
| Baker reagent MnCO3 powder |
| 4.15 |
| Penn. Glass Sand Minusil silica (APS 5) |
| 0.78 |
| Pfizer MP 96-28 talc (APS 20) |
| 0.59 |
| Methyl cellulose binder/plasticizer |
| 4.0 |
| Alkali stearate extrusion aid |
| 0.5 |
| Distilled water plasticizer |
| 26.0 |
| ______________________________________ |
This Mn-Mg cordierite grog was fired generally in accordance with the following firing schedule:
80°C to 1405°C within about 60 hours.
Hold about 10 hours at 1405°C
Cool 1405°C to room temperature within about 24 hours.
The Mg cordierite grog (in the batch for form the Mn-Mg cordierite grog) was made of the following batch composition (in weight % of the total ceramic batch materials):
| ______________________________________ |
| Georgia-Kaolin Hydrite MP clay (APS 9.7) |
| 25.15 |
| Georgia-Kaolin Glomax LL clay (APS 1.9) |
| 21.17 |
| Pfizer MP 96-28 talc (APS 20) |
| 40.21 |
| Alcoa A-2 alumina (APS 5.8) |
| 13.47 |
| Methyl cellulose binder/plasticizer |
| 4.0 |
| Alkali stearate extrusion aid |
| 0.5 |
| Distilled water plasticizer |
| 32.5 |
| ______________________________________ |
This Mg cordierite grog was fired generally in accordance with the same firing schedule as for the Mn-Mg cordierite grog, except that the maximum temperature was 1425°C
The analytical molar composition of Mn-Mg cordierite grog was 2.03 RO·20.4 Al2 O3 ·4.92 SiO2 wherein RO consisted of 9.7 mole 5 MnO and 90.3 and % MgO.
Pieces of ceramic honeycomb monolith were extruded in accordance with U.S. Pat. Nos. 3,790,654 and 3,919,384 from the same batch composition as described for the Mn-Mg cordierite grog. Those extruded green honeycomb bodies were then fired in the manner as disclosed in U.S. Pat. No. 3,899,326 and in accordance with the same first schedule as described for the Mn-Mg cordierite grog. A series of pairs of these honeycomb pieces were cemented together by applying the sample pastes described in Table 1 to the cordierite surfaces of these pieces that were to be joined and then pressing those paste-coated surfaces together. These assembled pairs of cemented pieces were dried in air at least 22°-75°C, then fired at about 300°C/hr. to the foaming temperature set forth in Table 1, held at the foaming temperature for about one hour and thereafter cooled at furnace rate to at least 200°C, at which time the foam cemented pieces were removed from the furnace for further cooling in ambient air atmosphere. The coefficients of thermal expansion (CTE) of the foamed cemented samples are set forth in Table 1, which are closely similar to the typical CTE of 18×10-7 /°C (25°-1000°C) for the pieces except the CTE of Sample 5.
All of those sintered foamed cement samples had a substantially wholly cordierite crystal structure.
Upon subjecting the foam cemented pieces to a cycling thermal shock test of 50 cycles of heating from 250°C to 800°C in 3 minutes and then cooling back to 250°C in 3 minutes, the foam cemented pieces with cement Samples 1-4 and 6 showed good resistance to thermal shock whereas the foam cemented pieces with cement Sample 5 showed moderate resistance to thermal shock. However, cement Sample 5 should serve well with pieces having CTE more closely similar to the CTE of foamed Sample 5 so as to exhibit good resistance to thermal shock.
Foamable cement Sample 6 has also been used to plug the end portions of cells in extruded ceramic honeycomb bodies made of the same and similar compositions and fired in the same manner as the Mg cordierite grog previously described. In those cases, the Mn-Mg coriderite grog was 95 wt. %-325 mesh, and the cement batch was formed with 2.0 wt. % methyl cellulose and 70.0 wt. % water to provide a paste that was injected into the cell ends, between the surfaces of opposed cell walls, by means of an air pressure operated sealant or caulking gun with an appropriately shaped nozzle. Those bodies with the green pugs were then fired generally in accordance with the following typical firing schedule:
Room temperature to 1210°C within about 6 hours.
Cool 1210°C to room temperature within about 18 hours.
The cement foamed during firing to develop a sintered cordierite mass having good sealing to the cell walls and being generally impervious to fluids.
The particle sizes of cordierite grog and SiC or other foaming agent in the cement can be varied as desired. For example, the grog may be a coarse as -20 mesh. All mesh sizes herein are according to the U.S. Standard Sieve series.
| Patent | Priority | Assignee | Title |
| 4557962, | Aug 24 1981 | Corning Glass Works | Masking apparatus for selectively charging honeycomb structures |
| 4591383, | Sep 30 1982 | Corning Glass Works | Apparatus and method of filtering molten metal using honeycomb structure of sintered alumina as filter element |
| 4752516, | Jul 15 1981 | Corning Glass Works | Apparatus for high speed manifolding of honeycomb structures |
| 4849274, | Jun 19 1987 | Engelhard Corporation | Honeycomb fluid conduit |
| 5733352, | Aug 22 1995 | TYK Corporation | Honeycomb structure, process for its production, its use and heating apparatus |
| 8029737, | Feb 05 2002 | IBIDEN CO , LTD | Honeycomb filter for exhaust gas decontamination, adhesive, coating material and process for producing honeycomb filter for exhaust gas decontamination |
| 8128722, | Feb 05 2002 | Ibiden Co., Ltd. | Honeycomb filter for purifying exhaust gases, adhesive, coating material, and manufacturing method of honeycomb filter for purifying exhaust gases |
| 8480780, | Feb 05 2002 | Ibiden Co., Ltd. | Honeycomb filter for purifying exhaust gases, adhesive, coating material, and manufacturing method of honeycomb filter for purifying exhaust gases |
| 8814974, | Aug 24 2007 | Corning Incorporated | Thin-walled porous ceramic wall-flow filter |
| Patent | Priority | Assignee | Title |
| 3272686, | |||
| 3634111, | |||
| 3885977, | |||
| 3929494, | |||
| 4191583, | Apr 24 1978 | Corning Glass Works | Manganese cordierite glass-ceramics |
| Executed on | Assignor | Assignee | Conveyance | Frame | Reel | Doc |
| Sep 29 1982 | Corning Glass Works | (assignment on the face of the patent) | / |
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