WO2008018957A2

WO2008018957A2 - High porosity filters for 4-way exhaust gas treatment

Info

Publication number: WO2008018957A2
Application number: PCT/US2007/015055
Authority: WO
Inventors: Isabelle M Melscoet-Chauvel; Gregory A Merkel; Steven B Ogunwumi; Tinghong Tao; Jianguo Wang
Original assignee: Corning Inc
Current assignee: Corning Inc
Priority date: 2006-06-30
Filing date: 2007-06-28
Publication date: 2008-02-14
Anticipated expiration: 2008-12-30
Also published as: JP5687681B2; WO2008018957A3; JP2009542570A; US20080004171A1; JP2013100221A; US7923093B2; EP2043965A2; CN103482968A

Abstract

Cordierite ceramic articles with high volume percent porosities of at least 64% but less than 80% have controlled median pore sizes and mean coefficients of thermal expansion that impart substantially improved modulus of rupture strengths (MOR) and thermal shock resistance (TSR) to the ceramic articles.

Description

HIGH POROSITY FILTERS FOR 4-WAY EXHAUST GAS TREATMENT

[0001] This application claims the benefit of U.S. Provisional Application No. 60/817,722, filed 06/30/2006, entitled "High Porosity Filters for 4-Way Exhaust Gas Treatment".

Background of the Invention

[0002] The present invention is in the field of technical ceramics and particularly relates to refractory cordierite ceramics of low thermal expansion and high porosity that exhibit high strengths rendering them particularly suitable for the production of strong, wall-flow filters for the treatment of combustion exhaust gases. [0003] Cordierite ceramic bodies, especially those formed as honeycomb multicellular structures, are utilized in a number of high temperature applications such as catalytic converters, NOx adsorbers, electrically heated catalysts, molten metal filters, regenerator cores, chemical process substrates, catalysts for hydrodesulfurization, hydrocracking, or hydro treating, and filters such as diesel exhaust particulate filters.

[0004] In diesel exhaust filtration, cordierite, being a low-cost material, in combination with offering a low coefficient of thermal expansion (CTE), has been a material of choice. Porous cordierite ceramic filters of the wall-flow type have been utilized for the removal of particles in the exhaust stream from some diesel engines since the early 1980s. A diesel particulate filter (DPF) ideally combines low CTE (for thermal shock resistance), low pressure drop (for engine efficiency), high filtration efficiency (for removal of most particles from the exhaust stream), high strength (to survive handling, canning, and vibration in use), and low cost. [0005] In applications requiring the removal of nitrogen oxides, NOx, from diesel engine exhaust gas, large amounts of catalyst or NOx adsorbers are typically required. In order to minimize increase in pressure drop, high porosity and coarse pore sizes are desired to accommodate the additional NOx catalyst/adsorber. However, both an increase in porosity and larger pore sizes tend to reduce the strength of the ceramic honeycomb. [0006] Further, very low CTE has often been pursued as a means for increasing thermal shock resistance (TSR), and low CTEs in cordierite and some other advanced ceramics have generally been achieved by the presence of microcracking in the ceramic material. Unfortunately, however, the microcracking also serves to further lower the strength of these high-porosity bodies.

[0007] Cordierite ceramics offering a combination of high porosity and coarse pore size, e.g. 64-80% porosity with median pore diameters of 10 to 45 μm, have been produced with either very low or very high CTEs. The high CTE ceramics tended to exhibit poor thermal shock performance, while the extensive microcracking associated with the very low CTE ceramics yielded low strength and poor mechanical durability. The latter ceramics are generally of insufficient physical strength as determined by modulus of rupture (MOR) testing for practical use in the mechanically harsh environment of a typical diesel engine exhaust system. [0008] It would thus be an advancement in the art to provide cordierite ceramic bodies that combine both high porosity and coarse median pore diameter for low catalyzed pressure drop, and at the same time intermediate CTEs insuring an improved combination of thermal shock resistance and strength.

Summary of the Invention

[0009] The present invention provides cordierite ceramic honeycomb articles having a novel combination of high volume percent porosity with controlled median pore sizes and mean coefficients of thermal expansion. Control over both the median pore sizes and mean coefficients of expansion has unexpectedly been found to enable substantially improved modulus of rupture strength (MOR) and thermal shock resistance (TSR) to these high porosity ceramics. In specific embodiments, the cordierite ceramic articles of the invention exhibit volume porosities of at least 64% and less than 80%, but with strengths and mean coefficients of thermal expansion that are generally higher than observed in the high porosity ceramics produced in accordance with the prior art.

[0010] The ceramic articles of the invention are particularly well suited for use as catalyzed wall-flow diesel particulate filters, in that the guiding limitations on CTE and pore size distribution provide high modulus of rupture (MOR) strengths in combination with good thermal shock resistance, and in that the pore microstructure of the ceramics insures low clean and soot-loaded pressure drop even when coated with effective amounts of catalysts and/or NOx adsorbers. The retention of higher MOR strengths in the cordierite ceramics of the invention is thought to result from reduced levels of microcracking, as manifested in the somewhat higher permissible CTEs, of the products, when compared with prior art products of similar porosity. Thus, in some embodiments, the invention includes cordierite ceramic articles having a porosity of ≥ 64% and < 80% and a median pore size and average coefficient of thermal expansion from 25-800⁰C (CTE) falling within one of the following ranges: (i) a CTE < 6.0x10^"7/°C at a median pore diameter (d₅₀) > 10 μm and < 18 μm; (ii) a CTE < 9.0x10^"7/°C at a median pore diameter (d₅₀) ≥ 18 μm and < 22 μm; (iii) a CTE < 10.0x10^"7/°C at a median pore diameter (d₅o) ≥ 22 μm and < 25 μm; (iv) a CTE < 13.0 at a median pore diameter (d₅₀) > 25μm and < 29μm; or (v) a CTE < 17.0x10^" ⁷/°C and ≥ 3.0x10^"7/°C at a median pore diameter (d₅₀) ≥ 29 μm and ≤ 45 μm. For purposes of the present description the median pore diameter (dso) of a cordierite ceramic material is conventionally defined as that pore diameter at which 50% of the pore volume of the material is of finer pore diameter, all pore diameters and percent pore volumes being determined by standard mercury porosimetry methods. [0011] In another aspect more directly reflecting the important relationship between permissible CTE levels and median pore diameters (d₅o), the invention comprises high porosity cordierite ceramic articles having a median pore diameter (d₅₀) of at least 10 μm and not more than 45 μm, and a mean CTE in the axial direction as measured over the temperature range (25-800⁰C) satisfying the relationship: 0.5(d₅o-24.0) < CTE(25-800°C) < 0.5(d₅₀-5.0), when d₅₀ is expressed in micrometers and CTE(25-800°C) is expressed in units of 10^"7/°C. Again these are high porosity cordierite ceramics with volume porosities of at least 64% and less than 80%

[0012] In accordance with certain further embodiments of the invention, a narrow pore size distribution provides for a more uniform distribution of the catalyst on the surfaces of the pore walls. A more uniform thickness of the catalyst coating on the pore walls provides a low clean and soot-loaded pressure drop, and also provides for greater contact between the catalyst and the soot and the catalyst and the exhaust gas, thereby promoting a more efficient use of the catalyst. Narrow pore size distribution further provides a lower pressure drop for the catalyzed filter, a higher filtration efficiency, and higher strength.

Description of the Drawings

[0013] The invention is further described below with reference to the appended drawings, wherein:

[0014] Figs. 1 and 2 are plots of median pore diameter versus mean CTE from 25 to 800⁰C (10^"7/°C) for selected cordierite ceramics of the invention; [0015] Figs. 3 and 4 are plots of median pore diameter versus porosity for selected cordierite ceramics of the invention;

[0016] Fig. 5 is a plot of median pore diameter (d₅o) versus mean CTE from 25 to 800⁰C (10^'7/°C) for selected cordierite ceramics of the invention exhibiting a narrow pore size distribution; and

[0017] Fig. 6 is a plot of median pore diameter (d₅o), versus mean CTE from 25 to 800⁰C (10^'7/°C) for selected cordierite ceramics of the invention having narrow pore size distributions and small volume fractions of very fine pores.

Detailed Description

[0018] As noted above, cordierite ceramic articles for applications such as advanced honeycomb supports and filters for the treatment of combustion engine exhaust gases will necessarily include ceramics of very high porosity, but that must also exhibit a mechanical strength sufficiently high, and a thermal expansion coefficient sufficiently low, to insure high thermal shock resistance. Ceramic articles meeting the high porosity requirement include those of at least 64% volume porosity but less than 80% volume porosity. Ceramics of such high porosity are typically relatively weak, especially in the case of low-CTE cordierite ceramics which are necessarily highly mlcrocracked.

[0019] The invention provides cordierite ceramic articles exhibiting the required combination of porosity and strength for high TSR through careful control of the thermal expansion and pore size distribution of the cordierite material. Thus we have found that high porosity cordierite ceramics of low to moderate CTEs can in fact offer surprisingly good MOR strengths if the mean pore sizes of the ceramics are reduced in the lower CTE materials.

[0020] The areas of [mean-CTE x median-pore-size] ceramic design space providing the required combination of high strength and high thermal shock resistance are graphically illustrated in Fig. 1 of the drawings, being indicated by five adjoining outlined blocks of acceptable [CTE-pore size] design space in the broader field of the graph. The mean CTEs and median pore sizes (d₅₀) for a number of cordierite ceramic articles provided in accordance with the invention are plotted in the drawing, the distribution of those articles on the plot indicating the general trend permitting lower CTEs for cordierite ceramics of lower mean pore sizes. [0021] As summarized above and reflected in the areas outlined in Fig. 1 , high- porosity cordierite ceramics according to the invention that will fall within the ranges of acceptable ceramic properties will have a median pore size (d₅₀) (as determined by standard mercury porosimetry) and a mean coefficient of thermal expansion as averaged over the temperature range 25-800⁰C (CTE) in the axial direction falling within one of the following ranges: (i) a CTE < 6.0x10^'7/°C at a median pore diameter (d₅o) ≥ 10 μm and < 18 μm, or (ii) a CTE < 9.0x10^"7/°C at a median pore diameter (dso) > 18 μm and < 22 μm, or (iii) a CTE < 10.0x10^"7/°C at a median pore diameter (d_δo) ≥ 22 μm and ≤ 25 μm, or (iv) a CTE < 13.0 x10^"7/°C at a median pore diameter (d₅o) > 25μm and < 29μm, or (v) a CTE < 17.0x10^"7/°C and > 3.0x10^'7/°C at a median pore diameter (dso) ≥ 29 μm and ≤ 45 μm. Preferred cordierite ceramics of the present invention have median pore diameters and mean coefficients of thermal expansion from 25 to 800⁰C that fall within one of the following ranges: (i) a CTE > 2.0 x10^'7/°C and < 5.0x10^"7/°C at a median pore diameter (d₅₀) ≥ 10 μm and < 18 μm, or (ii) a CTE > 3.0 x10^"7/°C and < 8.0x10^"7/°C at a median pore diameter (d₅₀) ≥ 18 μm and < 22 μm, or (iii) a CTE > 4.0 x10^"7/°C and < 9.0x10^"7/°C at a median pore diameter (d₅₀) ≥ 22 μm and < 25 μm, or (iv) a CTE > 5.0 x10^"7/°C and < 11.0 x10^" ⁷/°C at a median pore diameter (d₅o) > 25μm and < 29μm, or (v) a CTE > 6.0 x10^" ⁷/°C and < 14.0x10^"7/°C and > 3.0x10^"7/°C at a median pore diameter (d₅₀) ≥ 29 μm and ≤ 39 μm.

[0022] Fig. 2 of the drawings is a plot outlining a field of ceramic design space overlying the exemplary compositions plotted in Fig. 1 that more closely indicates the trend toward reduced median (d₅₀) pore sizes in ceramics of lower mean CTE. That field, outlined by the polygon (A-B-C-D-E) in Fig 2, includes those embodiments of the present invention that exhibit mean coefficients of thermal expansion (CTE) as averaged over the temperature range (25-800⁰C) in at least one dimension of the ceramic article satisfying the relationship O.5(d₅o-24.O) < CTE(25-800°C) < O.5(d₅o- 5.0), when dβo is expressed in micrometers and mean CTE(25-800°C) is in units of 10^"7/°C, and wherein the porosity is at least 64% and less than 80%, and the median pore diameter (dso) is at least 10 μm and not more than 45 μm. In accordance with a preferred embodiment, the mean coefficient of thermal expansion (CTE) satisfies the relationship 0.5(d₅₀-24.0) < CTE(25-800°C) < O.5(d₅o-5.O), when d₅o is expressed in micrometers and mean CTE(25-800°C) is in units of 10^'7/°C, and wherein the porosity is at least 64% and less than 80%, and the median pore diameter (d₅₀) is at least 13 μm and not more than 40 μm, and the mean CTE is at least 3x10^'7/°C and not more than 13x10^"7/°C.

[0023] The invention is further described below with reference to particular examples thereof, which are intended to be illustrative and not limiting. Suitable raw materials for the preparation of such examples are set forth in Table 1 below; these and similar materials for such use are desirably selected to insure high mineralogical and chemical purity. Included in Table 1 where determined on selected raw materials are median particle sizes for those materials as measured by standard laser diffraction and/or sedimentation methods.

Table 1 - Exemplary Raw Materials

Median Particle Median Particle

Diameter by Laser Diameter by

Raw Material Diffraction (μm) Sedimentation (μm)

Talc A 69

TaIc B 28

Talc C 23 8

Talc D 22

Talc E 14 8

TaIc F 5 I₁O

Kaolin A 11 7

Kaolin B 3 1

Alumina A 15 -

Alumina B 10 -

Alumiπa C 3 -

Alumina D 0.6 -

Alumina E 4 -

Activated Alumina A 16 -

Aluminum Hydroxide A 13 -

Aluminum Hydroxide B 12 -

Aluminum Hydroxide C 5 3

Quartz A 25 -

Quartz B 23 -

Graphite A 125

Graphite B 49

Graphite C 35

Graphite D 9

Starch A 45

Starch B 48

Starch C 45

Polyethylene Wax A 18

Polyethylene Wax B 38

Farina Flour 42

[0024] Illustrative combinations of raw materials for manufacturing cordierite ceramics in accordance with the invention, including combinations of the above constituent materials and some others, are set forth in Tables 2 to 8 below.

Table 2 - Batch Mixtures

Batch Composition Number Al A2 A3 A4

TaIc C 40.7 0 20.35 0

TaIc A 0 40.7 20.35 40.7

Kaolin B 16.0 16.0 16.0 16.0

Alumina C 14.8 14.8 14.8 14.8

Aluminum Hydroxide C 16.0 16.0 16.0 16.0

Quartz B 12.5 12.5 12.5 12.5

Graphite A 0 60.0 60.0 60.0

Starch A 40.0 0 0 0 Table 3 - Batch Mixtures

Batch Composition Number B l B2 B3 B4 B5 B6 B7 B8 B9 BlO BI l

TaIc C 0 40.7 0 40.7 40.7 39.69 37.74 40.7 40.7 40.7 0

TaIc D 40.7 0 40.7 0 0 0 0 0 0 0 38.5

Kaolin B 16.0 16.0 16.0 16.0 16.0 15.6 14.8 16.0 16.0 0.0 0.0

Kaolin A 0 0 0 0 0 0 0 0 0 16.0 12.8

Alumina D 0 0 0 0 0 0 0 0 0 14.8 0

Alumina C 14.8 14.8 14.8 14.8 14.8 9.8 0 14.8 14.8 0 0

Alumina B 0 0 0 0 0 0 0 0 0 0 12.3

Aluminum Hydroxide C 16.0 16.0 16.0 16.0 16.0 22.8 35.83 16.0 16.0 16.0 21.0

Quartz B 12.5 12.5 12.5 7.5 12.5 12.19 11.59 12.5 12.5 12.5 15.4

SiO₂ from Silicone Resin 0 0 0 4.8 0 0 0 0 0 0 0

Graphite A 0 0 0 0 0 0 0 20.0 60.0 0 0

Graphite B 0 0 0 0 0 0 0 0 0 60.0 0

Graphite C 60.0 60.0 80.0 0 0 0 O 0 0 0 80.0

Starch A 0 0 0 40.0 40.0 40.0 40.0 20.0 0 0 0

Table 4 - Batch Mixtures

Batch Composition Number B12 B13 B 14 B15 B16 B17 B18 B19 B20

TaIc C 38.5 0 38.5 40.7 0 0 0 0 0

TaIc D 0 38.5 Q 0 39.7 39.7 40.7 0 0

TaIc A 0 0 0 0 0 0 0 40.7 40.7

Kaolin B 0 0 0 0 0 0 0 16.0 16.0

Kaolin A 12.8 12.8 12.S 16.0 4.97 4.97 16.0 0 0

Alumina C 0 0 0 0 0 0 0 14.8 14.8

Alumina B 12.3 12.3 12.3 0 19.4 19.4 0 0 0

Alumina A 0 0 0 14.8 0 0 14.8 0 0

Aluminum Hydroxide C 21.0 21.0 21.0 16.0 0 0 16.0 16.0 16.0

Aluminum HydroxideA 0 0 0 0 16.2 16.2 0 0 0

Quartz B 15.4 15.4 15.4 12.5 19.7 19.7 12.5 9.81 11.8

SiC>₂ from Silicone Resin 0 0 0 0 0 0 0 2.58 0.72

Graphite A 0 0 0 0 0 0 0 60.0 60.0

Graphite B 60.0 80.0 80.0 80.0 60.0 80.0 80.0 0 0

Graphite D 0 0 0 0 0 0 0 0 0

Table 5 - Batch Mixtures

Batch Composition Number Cl C2 C3 C4 C5

TaIc D 41.28 38.52 : S8.52 38.52 38.52

Kaolin A 13.60 12.84 12.84 12.84 12.84

Alumina B 12.62 12.27 12.27 12.27 12.27

Aluminum Hydroxide C 0 20.99 : 20.99 20.99 20.99

Activated Alumina A 15.94 0 0 0 0

Quartz B 16.56 15.38 15.38 15.38 15.38

Graphite B 0 80.1 3 0 20.0 25.0

Graphite C 50.0 0 0 0 0

Starch A 0 0 40.0 0 0

StarchB 0 0 0 20.0 25.0 Table 6 - Batch Mixtures

Batch Composition Number C8 C9 ClO CI l C12 C13 C14 C15

TaIc D 38.52 38.52 38.52 28.89 28.89 38.52 38.52 19.26

TaIc B 0 0 0 9.63 9.63 0 0 19.26

Kaolin A 12.84 12.84 12.84 12.84 12.84 12.84 12.84 12.84

Alumina B 12.27 12.27 12.27 12.27 12.27 12.27 12.27 12.27

Aluminum Hydroxide C 20.99 20.99 20.99 20.99 20.99 20.99 20.99 20.99

Quartz A 15.38 0 0 0 0 0 0 0

Quartz B 0 15.38 15.38 15.38 15.38 15.38 15.38 15.38

Graphite B 0 0 20.0 0 0 0 0 0

Graphite C 0 0 0 0 0 80.0 0 0

Starch A 0 0 20.0 35.0 30.0 0 50.0 30.0

Starch C 0 20.0 0 0 0 0 0 0

Farina Flour 35.0 0 0 0 0 0 0 0

Table 7 - Batch Mixtures

Batch Composition Number Dl D3 D4 D5 D6

TaIc D 38.52 38.52 38.52 38.52 38.52

Kaolin A 12.84 12.84 12.84 12.84 12.84

Alumina B 12.27 12.27 7.27 2.27 7.27

Alumina E 0 0 0 0 5.00

Aluminum Hydroxide C 20.99 20.99 20.99 20.99 20.99

Aluminum Hydroxide B 0 0 5.00 10.00 0

Quartz A 15.38 15.38 15.38 15.38 15.38

Graphite B 50.0 50.0 80.0 80.0 80.0

Polyethylene Wax A 20.0 10.0 0 0 0

Table 8 - Batch Mixtures

Batch Composition Number D7 D8 D9 DlO DH D12

TaIc D 38.52 40.80 38.52 0 0 38.52

TaIc E 0 0 0 38.52 0 0

TaIc F 0 0 0 0 38.52 0

Kaolin A 12.84 13.60 12.84 12.84 12.84 12.84

Alumina B 12.27 13.00 12.27 12.27 12.27 12.27

Aluminum Hydroxide C 20.99 0 20.99 20.99 20.99 20.99

Activated Alumina A 0 16.31 0 0 0 0

Quartz B 0 0 0 15.38 15.38 0

Quartz A 15.38 16.29 15.38 0 0 15.38

Graphite B 80.0 50.0 0 0 80.0 50.0

Graphite C 0 0 0 80.0 0 0

Graphite D 0 0 80.0 0 0 0

Polyethylene Wax A 0 0 0 0 0 0

Polyethylene Wax B 0 0 0 0 0 10.0 [0025] In a typical procedure for the manufacture of cordierite ceramic honeycombs from batch mixtures such as reported above in Tables 2-8, the inorganic raw materials and graphite, starch, flour, or polymer pore formers are mixed with 4% to 6% methylcellulose binder and 0.5 to 1 % of a sodium stearate lubricant, and water is worked into the resulting mixture in a stainless steel muller to form a plasticized batch. The plasticized batches thus formed are then extruded to form 2-inch or 5.66-inch diameter cylindrical honeycomb preforms having approximately 200 to 300 cells/inch² of honeycomb cross-section with cell walls of 0.012 to 0.020-inch thickness. In some cases, plasticized batches were also extruded to form rods having approximately a 0.3-inch diameter cross section. These extruded honeycombs and rods are then dried and subsequently fired in gas or electric kilns to convert the raw materials in the extruded honeycombs into ceramic honeycombs wherein cordierite constitutes the principal crystalline phase (greater than 87% by weight of the crystalline phases comprising the honeycombs). Minor crystalline phases (less than 13% total by weight of the total crystalline phases) of residual mullite, spinel + sapphirine, and alpha-alumina can be detected by x-ray diffractometry in some of these fired honeycombs.

[0026] Tables 9 to 18 below report firing and product performance data typical of fired cordierite materials and honeycomb products provided from extruded honeycombs having batch compositions as set forth in Tables 2-8 above. Included in those Tables for each of the products reported are firing parameters useful for initiating and completing the reaction-sintering of the raw batch honeycomb components into cordierite in a manner enabling control over the CTEs and median pore sizes of the ceramics. Also reported for many of the products are selected physical properties typical of the fired materials, as determined on the fired honeycombs or rods.

[0027] Referring more particularly to the data in Tables 9-18, the CTE values correspond to the mean coefficients of thermal expansion of the products averaged over the temperature range 25 to 800⁰C in units of 10^"7/°C, as measured by dilatometry on specimens oriented parallel to the lengths of the channels of the honeycombs ("axial direction"). The % porosities are the volume percentages of porosity in the walls of the article as measured by mercury porosimetry. The terms dio, d₅o, and d₉₀ denote the pore diameters, in microns (micrometers - i.e., 10^"6 meters), at which 10%, 50%, and 90% of the total pore volume are of a finer pore diameter, respectively, also as measured by mercury porosimetry. Thus, for example, dg₀ is the pore diameter at which 90% (by volume) of the pores have a smaller diameter (equal to the pore diameter at which the cumulative mercury intrusion volume equals 10% of the total mercury intrusion volume). [0028] The reported flexural strength or modulus of rupture (MOR) values for the fired honeycombs are as measured in four-point bending on either 0.3-inch diameter rods or on 1 inch x VT. inch x 5 inch (long) cellular bars with lengths measured parallel to the axial direction of the honeycombs. Elastic modulus values at room temperature are measured by sonic resonance techniques on similar 1 inch x Vz inch x 5 inch cellular bars with lengths parallel to the axial honeycomb direction. Cell geometries are listed as "N/w" where "N" is the cell density in numbers of cells per square inch of honeycomb cross-section and "w" is the channel wall thickness in units of 10^~3 inches.

[0029] Tables 9-18 also report the axial XRD l-ratio (l-ratio measured on the axial cross section of the honeycomb) and the transverse XRD l-ratio (l-ratio measured on the transverse, as-fired wall surface) for some examples. The l-ratio is defined by the relationship: l-ratio = 1(110) / [1(110)+l(002)] where 1(110) and 1(002) are the peak heights of the XRD reflections from the (110) and (002) planes in the cordierite crystal lattice, based upon hexagonal indexing of the XRD peaks. The l-ratio is measured by x-ray diffractometry using copper Ka radiation on either the axial cross section (orthogonal to the length of the channels) or the transverse surface (as-fired surface of the honeycomb walls). The l-ratios provide a quantitative measure of the degree to which the cordierite crystallites in the honeycomb article are oriented with their negative thermal expansion c-axes parallel to the plane of the honeycomb wall. A high degree of such orientation is desirable because it reduces the CTE of the honeycomb article in both the axial direction (within the plane of the wall, parallel to the lengths of the channels) and radial direction (within the plane of the wall, orthogonal to the lengths of the channels). For randomly oriented cordierite crystals, the axial and transverse l-ratios are both equal to approximately 0.65. Values of transverse l-ratio greater than 0.65 and values of axial l-ratio lower than 0.65 indicate that the cordierite crystals are preferentially oriented with their c-axes parallel to the plane of the wall. If all of the cordierite crystals were to lie with their c-axes in the plane of the wall, the value of the transverse l-ratio would be 1.0.

[0030] Tables 9 to 18 also report the weight percentages of residual spinel, mullite, and alpha-alumina as measured by x-ray diffractometry on pulverized samples for some of the fired honeycombs.

Table 9 - Honeycomb Products

Example Number 1 2 3 4

Batch ID Al A2 A3 A4

840-950⁰C Heating Rate (⁰Oh) 75 75 75 75

1150-1200°C Heating Rate (°C/h) 25 25 25 25

1200-1300⁰C Heating Rate (°C/h) 25 25 25 25

1300-1360⁰C Heating Rate (⁰CZh) 25 25 25 25

1360-1400⁰C Heating Rate (°C/h) 5 5 5 5

Maximum Temperature (⁰C) 1412 1412 1412 1412

Time above 1400⁰C (hours) 13 13 13 13

CTE, 25-800⁰C (10-⁷/°C) 4.2 8.3 4.9 6.3

Pore Volume (ml/g) 0.6460 0.7031 0.7075 0.7185

% Porosity 65.3 64.5 68.5 65.1

d_so (μm) 12.1 23.5 24.5 31.3 d₉₀ (μm) 21.3 40.7 60.9 81.2

(d_So-dio)/d₅o 0.49 0.69 0.78 0.65

(d_go-d_w)/ά_5O 1.25 1.42 2.27 2.25

Table 10 - Honeycomb Products

Example Number 5 6 7 8 9 10 11

Batch ED Bl B2 B3 B4 B5 B6 B7

840-950°C Heating Rate (°C/h) 75 75 75 75 75 75 75

1150-1200⁰C Heating Rate (°C/h) 25 25 25 25 25 25 25

1200-1300⁰C Heating Rate (°C/h) 25 25 25 25 25 25 25

1300-1360⁰C Heating Rate (°C/h) 25 25 25 25 25 25 25

1360-1400°C Heating Rate (°C/h) 5 5 5 5 5 5 5

Maximum Temperature (⁰C) 1412 1412 1412 1412 1412 1412 1412

Time above 1400⁰C (hours) 13 13 13 13 13 13 13

CTE, 25-800⁰C (10^"7/°C) 4.2 6.4 7.0 2.7 4.7 3.2 4.6

Transverse XRD I-Ratio 0.87 0.85 - - - - -

Axial XRD I-ratio 0.39 0.42 - - - - -

% Mullite 0 0 0 - - - -

% Spinel 4.3 3.9 3.6 - - - -

% α-Alumina 0 0 0 - - - -

Pore Volume (ml/g) 0.7482 0.7099 0.7889 0.6549 0.6545 0.7548 0.7391

% Porosity 66.9 74.1 65.8 65.0 66.3 65.2 64.7 dio (μm) 5.2 5.1 6.5 2.8 6.8 3.4 5.1 dso (μm) 10.5 10.9 12.2 13.2 14.2 14.8 15.6 dβo (μm) 20.9 28.9 20.9 39.4 26.9 28.9 31.6

(d5O-dlo)/^d5O 0.50 0.53 0.47 0.79 0.52 0.77 0.67

(d₉o-dio)/d₅₀ 1.50 2.18 1.18 2.77 1.42 1.71 1.70

Cell geometry 200/12 - 200/12 - - - -

Closed Frontal Area (CFA) 0.31^" - 0.31 - - - -

MOR, cellular (psi) 235 - 319 - - - -

MOR/CFA (psi) 758 1029

E, cellular (10⁵ psi) 3.20 - - - - - -

MOR/E 0.074% - - - - - -

Table 11 - Honeycomb Products

Product Number 12 13 14 15 16 17 18

Batch ID B8 B9 BlO BI l B12 B13 B14

840-950⁰C Heating Rate (°C/h) 35 35 75 75 75 75 75

1150-1200⁰C Heating Rate (°C/h) 25 25 25 25 25 25 25

1200-1300⁰C Heating Rate (°C/h) 25 25 25 25 25 25 25

1300-1360⁰C Heating Rate (°C/h) 18 18 25 25 25 25 25

1360-1400°C Heating Rate (⁰Oh) 5 5 5 5 5 5 5

Maximum Temperature (⁰C) 1400 1400 1412 1412 1412 1412 1412

Time above 1400⁰C (hours) 11 11 13 13 13 13 13

CTE, 25-800⁰C (10-⁷/°C) 3.4 4.8 3.8 8.6 5.3 8.0 6.6

Transverse XRD I-Ratio - - 0.85 0.87 - 0.88 0.88

Axial XRD I-ratio - - 0.38 0.38 - 0.39 0.38

% Mullite - 0 0 1.4 0.6 1.9 1.4

% Spinel - 3.4 3.7 3.7 3.3 2.6 3.6

% α- Alumina - 0 0 0 0 0 0

Pore Volume (ml/g) 0.7125 0.6800 0.9004 0.9437 0.8202 0.9640 0.9492

% Porosity 66.8 64.0 67.4 71.7 66.9 72.0 72.1 dio (μm) 2.6 5.5 8.0 10.6 9.7 11.1 11.2 d₅o (μm) 16.1 17.7 17.7 18.2 19.6 20.0 21.0 d₉o (μm) 32.9 37.6 33.0 32.2 38.8 35.5 42.2

(Aso-d_ιo)/d_So 0.84 0.69 0.55 0.41 0.51 0.45 0.47

(dso-dioVdso 1.88 1.81 1.42 1.19 1.49 1.22 1.48

Cell geometry - - 275/14 275/14 200/12 200/12 200/12

Closed Frontal Area (CFA) - - 0.41 0.41 0.31 0.31 0.31

MOR, cellular (psi) - - 186 208 284 213 212

MOR/CFA (psi) 454 507 916 687 684

E, cellular (10⁵ psi) - - - 1.84 2.42 1.66 1.88

MOR/E - - - 0.113% 0.117% 0.128% 0.113%

Table 12 - Honeycomb Products

Product Number 19 20 21 22 23 24

Batch ID B15 B16 B17 B18 B19 B20

840-950⁰C Heating Rate (°C/h) 75 75 75 75 75 75

1 150-1200°C Heating Rate (°C/h) 25 25 25 25 25 25

1200-1300⁰C Heating Rate (°C/h) 25 25 25 25 25 25

1300-1360⁰C Heating Rate (°C/h) 25 25 25 25 25 25

1360-1400⁰C Heating Rate (°C/h) 5 5 5 5 5 5

Maximum Temperature (⁰C) 1412 1412 1412 1412 1412 1412

Time above 1400⁰C (hours) 13 13 13 13 13 13

CTE, 25-800⁰C (10-⁷/°C) 7.9 13.3 11.4 9.6 10.8 12.4

Transverse XRD I-Ratio - - - 0.81 - -

Axial XRD I-ratio - - - 0.43 - -

% MuUite 0 0.9 0.8 0 - -

% Spinel 4.4 5.4 5.8 4.5 - -

% α-Alumina 0 0 0 0 - -

Pore Volume (ml/g) 0.9615 0.8621 1.0011 1.0512 0.6233 0.7077

% Porosity 70.9 68.5 73.2 74.5 65.2 67.4 d_I0 (μm) 11.7 15.1 17.0 16.6 17.2 16.7 dso (μm) 23.2 25.4 28.2 28.3 37.7 37.8 dso (μ∞) 50.3 45.5 51.1 50.7 90.4 86.2

(άV-d _H))Ai_5O 0.50 0.40 0.40 0.41 0.54 0.56

(d₉o-dio)/d₅₀ 1.66 1.20 1.21 1.21 1.94 1.84

Cell Geometry 200/12 275/14 200/12 200/12 200/12 -

Closed Frontal Area (CFA) 0.31 0.41 0.31 0.31 0.31 -

MOR, cellular (psi) 113 303 233 121 185 -

MOR/CFA (psi) 365 758 752 390 597

E, cellular (10^s psi) - - 1.34 1.23 - -

MOR/E - - 0.174% 0.098% - -

Table 13 - Honeycomb Products

Product Number 26 27 28 29 30

Batch ID Cl Cl C2 C2 C3

840-950⁰C Heating Rate (°C/h) 75 110 75 110 110

1150-1200⁰C Heating Rate (°C/h) 25 40 25 40 40

1200-1300⁰C Heating Rate (⁰Oh) 25 30 25 30 30

1300-1360⁰C Heating Rate (°C/h) 25 30 25 30 30

1360-1400⁰C Heating Rate (°C/h) 5 30 5 30 30

Maximum Temperature (⁰C) 1410 1410 1410 1410 1410

Time above 1400⁰C (hours) 13 18 13 18 18

CTE, 25-800⁰C (10^"7/°C) 13.9 16.3 3.3 6.5 8.8

Pore Volume (ml/g) 0.8090 0.7163 0.9910 0.9279 0.7595

% Porosity 67.3 65.0 72.7 70.8 66.0 d,₀ (μm) 16.0 18.5 9.0 13.4 14.3 d_so (μm) 29.7 29.1 19.0 22.6 25.3 dgo (μm) 82.2 55.7 33.4 30.5 47.8

(d₅o-dio)/d₅o 0.46 0.36 0.53 0.41 0.44

(d9o-d_lo)/d₅o 2.24 1.28 1.29 0.76 1.32

MOR, rod (psi) 645 - - 1014 907

E, rod (10⁵ psi) - - - 6.16 -

MOR/E - - - 0.165% -

Table 14 - Honeycomb Products

Product Number 31 32 33 34

Batch ID C4 C4 C5 C5

840-950⁰C Heating Rate (°C/h) 75 110 75 110

1150-1200⁰C Heating Rate (°C/h) 25 40 25 40

1200-1300⁰C Heating Rate (°C/h) 25 30 25 30

1300-1360⁰C Heating Rate (°C/h) 25 30 25 30

1360-1400°C Heating Rate (°C/h) 5 30 5 30

Maximum Temperature (⁰C) 1410 1410 1410 1410

Time above 1400⁰C (hours) 13 18 13 18

CTE, 25-800⁰C (10⁷/°C) 7.7 5.7 7.4 9.3

% Mullite - - 1.2 -

% Spinel - - 3.1 -

% α-Ahimina - - 0 -

Pore Volume (ml/g) 0.8007 0.7575 - 1.0229

% Porosity 68.2 67.4 69.4 71.6 d₁₀ (μm) 11.5 13.2 8.3 15.4 dso (μm) 20.7 24.5 19.2 25.4

Cl₉₀ (μm) 39.7 47.1 33.5 71.0

(d_So-d₁₀)/d₅o 0.54 0.46 0.57 0.39

(d₉₀-dio)/d₅o 1.29 1.39 1.31 2.19

MOR, rod (psi) - 765 191 665

E, rod (10^s psi) - - 2.54 4.27

MOR/E - - 0.075% 0.156%

Table 15 - Honeycomb Products

Product Number 37 38 39 40 41

Batch ID C8 C9 ClO CIl C12

840-950⁰C Heating Rate (⁰Oh) 110 75 110 110 110

1150-1200⁰C Heating Rate (°C/h) 40 20 40 40 40

1200-1300⁰C Heating Rate (°C/h) 30 50 30 30 30

1300-1360⁰C Heating Rate (°C/h) 30 50 30 30 30

1360-1400⁰C Heating Rate (°C/h) 30 50 30 30 30

Maximum Temperature (⁰C) 1410 1420 1410 1410 1410

Time above 1400⁰C (hours) 18 15 18 18 18

CTE, 25-800⁰C (10-⁷/°C) 11.6 5.8 8.0 5.2 8.7

% Mullite - - 0.9 - -

% Spinel - - 3.7 - -

% α- Alumina - - 0 - -

Pore Volume (ml/g) 0.7439 - 0.8251 0.7591 1.0252

% Porosity 67.8 64.9 68.1 67.3 72.9 dio (μm) 10.5 9.4 12.8 17.2 17.6 d₅o (μm) 19.7 20.2 22.5 28.0 38.7 d₉₀ (μm) 38.3 39.7 37.2 62.7 93.1

(d_So-d₁₀)/d₅o 0.46 0.53 0.43 0.39 0.55

(d₉₀-d,o)/d₅o 1.41 1.50 1.08 1.63 1.95

MOR, rod (psi) 910 - 1042 501 512

E, rod (10^s psi) - 3.59 7.38 - -

MOR/E - - 0.141% - -

Table 16 - Honeycomb Products

Product Number 42 43 44 45 46 47

Batch ID C13 C13 C13 C13 C14 C15

840-950⁰C Heating Rate (°C/h) 75 110 60 120 110 110

1150-1200⁰C Heating Rate (⁰CZh) 25 40 60 120 40 40

1200-1300⁰C Heating Rate (⁰CZh) 25 30 60 120 30 30

1300-1360⁰C Heating Rate (⁰CZh) 25 30 60 120 30 30

1360-1400⁰C Heating Rate (⁰CZh) 5 30 60 120 30 30

Maximum Temperature (⁰C) 1410 1410 1415 1400 1410 1410

Time above 1400⁰C (hours) 13 18 15 6 18 18

CTE, 25-800⁰C (10-⁷Z⁰C) 9.3 5.7 10.8 15.6 6.4 7.7

Transverse XRD I-Ratio 0.86 - - - - -

Axial XRD I-ratio 0.39 - - - - -

% Mullite 0 - - - - -

% Spinel 4.0 - - - - -

% α- Alumina 1.1 - - - - -

Pore Volume (mlZg) 0.9782 0.8986 0.9023 0.7700 0.9462 0.7688

% Porosity 74.8 68.2 70.8 66.5 71.1 68.2 d,o (μm) 10.4 18.4 22.6 25.6 17.1 18.1 d₅₀ (μm) 18.9 29.8 36.0 42.3 29.0 30.8 dgo (μm) 34.2 54.6 80.6 109.8 69.9 80.3

(d5o-dio)/dso 0.45 0.38 0.37 0.39 0.41 0.41

(d₉o-djo)/d₅o 1.25 1.22 1.61 1.99 1.82 2.02

MOR, rod (psi) - 690 700 503 540 520 .

psi) MORZE

Table 17 - Honeycomb Products

Product Number 48 50 51 52 54 55

Batch ID Dl D3 D3 D4 D5 D6

840-950⁰C Heating Rate (°C/h) 75 110 75 110 110 75

1150-1200⁰C Heating Rate (°C/h) 25 40 25 40 40 25

1200-1300⁰C Heating Rate (°C/h) 25 30 25 30 30 25

1300-1360⁰C Heating Rate (°C/h) 25 30 25 30 30 25

1360-1400⁰C Heating Rate (°C/h) 5 30 5 30 30 5

Maximum Temperature (⁰C) 1410 1410 1410 1410 1405 1410

Time above 1400⁰C (hours) 13 18 13 18 12 13

CTE, 25-800⁰C (10-⁷/°C) 7.4 9.7 8.1 9.8 - 10.4

Transverse XRD I-Ratio 0.87 0.87 0.86 0.86 0.87 0.88

Axial XRD I-ratio 0.37 0.39 0.40 0.38 0.44 0.37

% Mullite 0.9 0.0 1.2 1.0 0.6 1.9

% Spinel 3.4 4.5 3.1 3.2 4.7 4.2

% α-Alumina 0.0 0.6 0.0 0.0 0.0 0.0

Pore Volume (ml/g) 0.9588 0.8341 0.8806 0.8685 0.8533 0.8850

% Porosity 71.0 66.3 69.2 71.3 70.5 68.2 dio (μm) 12.3 15.9 12.4 21.1 21.6 17.7 d₅₀ (μm) 20.6 24.9 20.6 31.1 33.3 26.6

U₉₀ (μm) 36.4 47.4 39.4 52.9 64.9 47.0

(d_5o-dio)/dso 0.40 0.36 0.40 0.32 0.35 0.33

(d₉₀-dio)/d_So 1.17 1.27 1.31 1.02 1.30 1.11

MOR, rod (psi) 732 821 905 - - 825

Table 18 - Honeycomb Products

Product Number 56 57 58 59 60 61

Batch ID D7 D8 D9 DlO DIl D12

840-950⁰C Heating Rate (°C/h) 110 110 110 110 75 75

1150-1200⁰C Heating Rate (°C/h) 40 40 40 40 25 25

1200-1300⁰C Heating Rate (°C/h) 30 30 30 30 25 25

1300-1360⁰C Heating Rate (°C/h) 30 30 30 30 25 25

1360-1400⁰C Heating Rate (°C/h) 30 30 30 30 5 5

Maximum Temperature (⁰C) 1405 1405 1405 1405 1410 1410

Time above 1400⁰C (hours) 12 12 12 12 13 13

CTE, 25-800⁰C (10-⁷/°C) 10.7 13.7 14.3 12.6 7.0 -

Transverse XRD I-Ratio 0.88 0.83 0.84 0.87 0.82 0.85

Axial XRD I-ratio 0.38 0.41 0.39 0.42 0.46 0.40

% Mullite 2.7 1.5 2.5 1.4 0.6 1.4

% Spinel 3.9 8.5 7.4 6.8 2.4 3.3

% α- Alumina 0.0 0.6 1.0 1.3 0.0 0.0

Pore Volume (ml/g) 0.8698 0.6869 0.8928 0.9048 0.9917 0.9363

% Porosity 69.6 67.6 69.6 71.4 74.7 69.8 d₁₀ (μm) 20.1 18.1 17.7 14.3 6.0 10.8 d₅₀ (μm) 28.6 29.4 26.8 20.9 14.6 20.2 dpo (μm) 48.8 54.7 57.8 34.7 25.9 37.8 ^"

(d₅o-dio)/d₅o 0.30 0.39 0.34 0.32 0.59 0.46

(d₉o-d₁₀)/d₅₀ 1.00 1.24 1.50 0.98 1.36 1.34

MOR, rod (psi) - - 437 - 605 837

[0031] The porosity, median pore size, and mean CTEs of the bodies of the present invention as exemplified above are selected to provide a high strength while maintaining low pressure drop and high thermal shock resistance when the bodies are configured for use as honeycomb wall flow filters. For best performance in that configuration the honeycombs should be formed of ceramics having a modulus of rupture (flexural strength) as measured by the four-point bending method on a (non- cellular) rod or (non-cellular) bar of the ceramic material that is at least 500 psi, more preferably at least 700 psi, still more preferably at least 900 psi, and most preferably at least 1000 psi. When measured on cellular bodies the values of MOR are proportional to the closed frontal area (CFA) of a cross section of the cellular body taken transverse to the axial direction of the honeycomb structure. The CFA is defined as the solid fraction of the cross sectional area of the specimen, i.e., the combined areas of the porous walls and wall intersections. Thus, the CFA is equal to {w[2(N^"α5)-w]N}, where w is the wall thickness in inches and N is the cell density in units of (inches)^"2. Desirably the value of MOR/CFA for cellular structures to be used for wall flow filter construction will be at least 500 psi, preferably at least 700 psi, still more preferably at least 900 psi, and most preferably at least 1000 psi. [0032] Cordierite ceramics selected for wall flow filters will advantageously also exhibit a high strain tolerance, defined as the ratio of the MOR of the ceramic to its elastic modulus E, again where the MOR of the ceramic is its modulus of rupture at room temperature and E is its elastic modulus at room temperature. Both of the MOR and E values should be determined on solid rods, or both should be determined on cellular honeycomb samples as measured along axes parallel with the direction of channel orientation through the body. In the later case the honeycombs should also be of the same cell geometry (same w and N). For wall flow filter applications, it is preferred that materials exhibit a strain tolerance as fired of at least 0.09%, preferably 0.10%, more preferably at least 0.12%, still more preferably at least 0.14%, and especially at least 0.16%. A high strain tolerance is useful because it can result in a higher thermal shock resistance for a given CTE. [0033] Based on composition studies such as outlined in Tables 1-18 above, a range of cordierite ceramic properties has been identified that is particularly well adapted for use in the manufacture of high porosity wall flow filter substrates. Cordierite ceramics within that range will have percent porosities in the range: 64% ≤ %porosity < 77%, and will have a median pore diameter (d₅₀) simultaneously satisfying the limitations: (i) 18 μm < dso ≤ 50 μm; (ii) dso > 158 - 2.0(%porosity); and (iii) d₅₀ < 210 - 2.5(%porosity). The median pore diameter will preferably fall below 30 μm in the higher porosity cordierite ceramics within that range. [0034] The field of porosity/median pore size within which these ceramics will fall is illustrated in Fig. 3 of the drawings, wherein compositions simultaneously satisfying the foregoing limits on porosity and pore size are located within the quadrilateral area A-B-C-D outlined in the drawing. Again providing lower median pore diameters in the higher porosity materials within the disclosed range enables higher MOR strengths for those ceramics than otherwise attainable. [0035] In yet another aspect of the invention, a field of cordierite ceramic design that includes many of the ceramics depicted in Fig. 3 of the drawings, plus some additional high MOR/high TSR materials lying outside of the design ranges covered by the A-B-C-D quadrilateral of Fig. 3, has been identified. Cordierite ceramics falling within those design limits will satisfy one of the following sets of requirements: (i) a median pore diameter in the range > 25 um and < 46 um with a porosity in the range > 64% and ≤ 67%, or (ii) a median pore diameter in the range > 21 um and < 42 um with a porosity in the range > 67% and < 68%, or (iii) a median pore diameter in the range ≥ 19 um and < 40 um with a porosity in the range > 68% and < 71%, or (iv) a median pore diameter in the range > 18 um and < 35 um with a porosity in the range ≥ 71% and < 73%, or (v) a median pore diameter in the range > 10 um and < 30 um with a porosity in the range ≥ 73% and < 75%. The preferred ceramics within that field of porosity design will have median pore diameters < 30μm. [0036] Fig 4 of the drawings plots median pore diameter (d50) in microns versus porosity in volume percent for a number of examples of cordierite ceramics simultaneously meeting one of the above requirements in accordance with the invention. Thus the plotted examples fall within one of the five rectangles superimposed on the field of the drawing that cover the five areas of pore design corresponding to the foregoing five sets of porosity and pore size limitations. [0037] In selecting a cordierite ceramic material design for a wall flow filter application from among the compositions described above and disclosed in Figs. 1-4 of the drawings, it is particularly preferred for best strength and thermal shock resistance that the porosity and median pore size (d₅o) fall within the ranges of: 65% < porosity < 75% and 15 ≤ d₅₀ ≤ 28 μm, especially 18 ≤ dso ≤ 25 μm. The mean coefficient of thermal expansion from 25 to 800⁰C, CTE(25-800), will desirably be ≤ 15x10^~7/°C, preferably < 10x10^"7V⁰C, more preferably < 8x10^'7/°C, and most preferably < 6x10^"7/°C.

[0038] The soot-loaded pressure drop of wall flow filters fabricated from these ceramics will depend to some degree on the distributions of pore sizes within the broader range of pore sizes present in the material. For wall flow filter applications employing these high porosity ceramics, it is preferred that the pore size distribution value (d₅o-dio)/d5o be ≤ 0.50, more preferably ≤ 0.40, and most preferably < 0.35. Further, the value of the pore size distribution parameter D_b, defined as (d₉o-dio)/d₅o and indicative of the breadth of the pore size distribution in the material, should be < 1.7, preferably < 1.4, more preferably < 1.2, and most preferably ≤ 1.0. Further, the value of dg₀ should be ≤ 60 μm, more preferably ≤ 50 μm, and most preferably < 40 μm, while the value of dio should be ≥ 10 μm, preferably > 12 μm, and most preferably ≥ 15 μm.

[0039] Within the family of high porosity (> 65% and < 80%) cordierite ceramics having narrow pore size distributions such that (dg_O-dio)/d₅o < 1.70, best thermal- mechanical properties are observed when the median pore diameter (d₅₀) is maintained in the range > 10 μm and < 25 μm at CTE(25-800) values of < 9.0x10^' ⁷/°C, or when the median pore diameter (dso) is maintained in the range > 25 μm and < 46 μm at CTE(25-800) values > 3.0x10^~7/°C and < 17.0x10^'7/°C. Fig. 5 of the drawings illustrates the above two ranges of porosity and CTE. The group exhibiting higher CTE values, indicative of less microcracking and therefore higher strength, exhibit good TSR at larger median pore sizes (d₅₀). All of the materials plotted have greater than 65% porosity and less than 80% porosity, and all have a Db value [(dgo- dio)/d_δo3 < 1.70. It is especially preferred that these bodies exhibit either a CTE(25- 800) ≥ 3.0x10^"7/°C and ≤ 9.0x10^"7/°C with a median pore diameter (d₅₀) in the range

> 10 μm and < 25 μm, or a CTE(25-800) > 5.0x10^'7/°C and < 15.0x10^"7/°C with a median pore diameter (d₅o) in the range > 25 μm and ≤ 36 μm

[0040] In a somewhat narrower range of high porosity materials with narrow pore size distributions, i.e. ceramics having porosities > 65% and < 75% and pore size distributions D_b [(d₉o-dio)/d_5O] < 1.70, pressure drop, TSR and MOR levels favor ceramics with d-io values ≥ 10 μm and either (i) median pore diameters of > 10 μm and < 30 μm with CTE(25-800) values < 15.0x10^~7/°C, or (ii) median pore diameters

> 30 μm and < 45 μm with CTE(25-800) values > 3.0x10^"7/°C and < 15.0x10^"7/°C. Fig. 6 of the drawings plots median pore sizes dso and mean CTE values (25 to 800⁰C, 10^"7/°C) for examples within the above ranges of median pore size and CTE. All examples within the outlined ranges of Fig. 6 have greater than 65% porosity and less than 75% porosity, all have narrow pore size distributions (D_b) satisfying [(d₉₀- dio)/d5o]< 1.70, and all have d™ values > 10 μm. It is preferred that such bodies have porosities > 65% and < 75%, pore size distributions D_b [(dgo-dio)/d₅o] < 1.70, dio values ≥ 10 μm, median pore diameters of ≥ 18 μm and ≤ 32 μm with CTE(25-800) values ≥ 5.0x10^"7/°C and ≤ 15.0x10^"7I⁰C Even more preferred are ceramics with CTEs < 9x10^"7/°C and median pores sizes dso in the range: 18 < d₅₀ ≤ 30 μm, and % porosities in the range 66% < %porosity < 73%. [0041] As noted above, the high porosity cordierite ceramics of the invention offer particular advantages for applications such as honeycomb wall flow filters for the removal of particulates from fuel combustion exhaust gases, especially exhaust gases from diesel engines. The most difficult of those applications involves the use of these ceramics in honeycomb configurations as combined filters/catalyst supports, wherein a catalyst or adsorber for the removal of nitrogen oxides (NOx) from the exhaust stream is disposed on the high porosity honeycombs. Particularly preferred in the latter case are cordierite ceramic honeycombs having a CTE < 10.0x10^"7/°C (or more preferably < 8.0x10^"7V⁰C), a median pore diameter dβo of ≥ 20 μm and ≤ 28 μm, a porosity of > 65% and < 75%, a value of dio > 11 μm, and a value of d_go < 50 μm. Honeycombs with these properties having Db values [(dgo-dioVdso] ≤ 1.5 and (d₅o-dio)/d₅o values ≤ 0.45 will be selected for best filtration performance.

Claims

We claim:

1. A cordierite ceramic article comprising a porosity of ≥ 64% and < 80% and a median pore diameter and average coefficient of thermal expansion from 25-800⁰C (CTE) falling within one of the following ranges:

(i) a CTE < 6.0x10^"7/°C at a median pore diameter (d₅₀) ≥ 10 μm and < 18 μm;

(ii) a CTE < 9.0x10^"7/°C at a median pore diameter (d₅₀) ≥ 18 μm and < 22 μm;

(iii) a CTE < 10.0x10^"7/°C at a median pore diameter (d₅o) ≥ 22 μm and ≤ 25 μm;

(iv) a CTE < 13.0x10^"7/°C at a median pore diameter (d₅o) > 25μm and <

29μm; or

(v) a CTE < 17.0x10^'7/°C and > 3.0x10^'7/°C at a median pore diameter (d₅₀) ≥

29 μm and ≤ 45 μm.

2. A cordierite ceramic body of claim 1 comprising a modulus of rupture MOR flexural strength of at least 500 psi as measured on a non-cellular rod or bar, or a ratio of modulus of rupture strength /closed frontal area MOR/CFA of at least 500 psi as measured on a cellular bar.

3. A cordierite ceramic article comprising at least 64% porosity and less than 80% porosity, a median pore diameter (d₅₀) of at least 10 μm and not more than 45 μm, and a mean CTE(25-800°C) in the axial direction wherein 0.5(d₅₀-24.0) < CTE(25- 800⁰C) < O.5(d₅o-5.O) wherein d₅o is expressed in micrometers and CTE(25-800°C) is expressed in units of 10^"7/°C.

4. A cordierite ceramic article comprising a porosity of ≥ 64% and < 80% and a combination of median pore diameter and CTE(25-800°C) selected from the group consisting of:

(i) a median pore diameter ≥ 10 μm and < 18 μm, and a CTE (25-800) < 6.0x10^'7/⁰C₁ or (ii) a median pore diameter > 18 μm and < 22 μm, and a CTE (25-800) <

9.0x10^'7/°C, or

(iii) a median pore diameter > 22 μm and < 29 μm, and a CTE (25-800) <

10.0x10-⁷/°C, or

(iv) a median pore diameter > 29 μm and ≤ 45 μm, and a CTE (25-800) <

17.0x10-⁷/°C and > 3.0x10T/°C.

5. A cordierite ceramic article comprising a % porosity in the range: 64% ≤ %porosity ≤ 77% and a median pore diameter (dso), in micrometers, wherein:

(i) 18 μm < d₅o ≤ 50 μm;

(ii) d₅o > 158 - 2.0(%porosity); and

(iii) d₅₀ < 210 - 2.5(%porosity).

6. A cordierite ceramic article comprising a % porosity and median pore diameter (dβo) selected from the group consisting of:

(i) a median pore diameter > 25 um and < 46 um, and a porosity > 64% and <

67%;

(ii) a median pore diameter is > 21 um and < 42 um, and the porosity > 67% and ≤ 68%;

(iii) a median pore diameter is ≥ 19 um and < 40 um, and the porosity > 68% and < 71%;

(iv) a median pore diameter is > 18 um and < 35 um, and the porosity ≥ 71% and < 73%; and

(v)a median pore diameter is > 10 um and < 30 um, and the porosity > 73% and < 75%.

7. A cordierite ceramic article comprising a % porosity > 65% and < 80% and pore size distribution wherein (dg₀-d-ιo)/d5o < 1 -70, wherein:

(i) the median pore diameter is > 10 μm and < 25 μm and the mean CTE(25- 800) is < 9.0x10-⁷V⁰C; or

(ii) the median pore diameter is > 25 μm and < 46 μm and mean CTE(25-800) is > 3.0x10-^"7⁰C and < 17.0x10-⁷/^oC.

8. A cordierite ceramic article comprising a % porosity > 65% and < 75%, and a pore size distribution such that (dgo-dioVdso < 1.70 and that dio ≥ 10 μm, wherein:

(i) the median pore diameter is > 10 μm and < 30 μm and the mean CTE(25- 800) is < 15.0x10-⁷/°C, or

(ii) the median pore diameter is ≥ 30 μm and < 45 μm and the mean CTE(25- 800) is > 3.0x10-⁷/°C and < 15.0x10-⁷/°C.

9. A cordierite ceramic honeycomb article comprising a mean CTE < 10.0x10^"7/°C, a median pore diameter > 20 μm and ≤ 28 μm, a porosity > 65% and < 75%, a value of dio > 11 μm, and a value of d₉₀ < 50 μm.

10. A cordierite ceramic article in accordance with claim 1 which is a honeycomb wall flow filter.

11. A cordierite ceramic article in accordance with claim 2 which has a strain tolerance (MOR/E) of at least 0.10%.

12. A cordierite ceramic article in accordance with claim 11 which has a strain tolerance ratio MOR/E of at least 0.12% and one of (i) a modulus of rupture MOR flexural strength of at least 600 psi as measured on a non-cellular rod or bar, or (ii) a modulus of rupture strength/closed frontal area ratio of MOR/CFA of at least 600 psi as measured on a cellular bar.

13. A cordierite ceramic article in accordance with claim 11 which has a strain tolerance ratio MOR/E of at least 0.14% and one of (i) a modulus of rupture MOR flexural strength of at least 700 psi as measured on a non-cellular rod or bar, or (ii) a ratio of modulus of rupture strength/closed frontal area MOR/CFA of at least 700 psi as measured on a cellular bar.