WO2012135106A2 - Ceramic particle and process for making the same - Google Patents
Ceramic particle and process for making the same Download PDFInfo
- Publication number
- WO2012135106A2 WO2012135106A2 PCT/US2012/030539 US2012030539W WO2012135106A2 WO 2012135106 A2 WO2012135106 A2 WO 2012135106A2 US 2012030539 W US2012030539 W US 2012030539W WO 2012135106 A2 WO2012135106 A2 WO 2012135106A2
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- particle
- ceramic material
- ceramic
- weight percent
- phase
- Prior art date
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C14/00—Glass compositions containing a non-glass component, e.g. compositions containing fibres, filaments, whiskers, platelets, or the like, dispersed in a glass matrix
- C03C14/006—Glass compositions containing a non-glass component, e.g. compositions containing fibres, filaments, whiskers, platelets, or the like, dispersed in a glass matrix the non-glass component being in the form of microcrystallites, e.g. of optically or electrically active material
-
- C—CHEMISTRY; METALLURGY
- C09—DYES; PAINTS; POLISHES; NATURAL RESINS; ADHESIVES; COMPOSITIONS NOT OTHERWISE PROVIDED FOR; APPLICATIONS OF MATERIALS NOT OTHERWISE PROVIDED FOR
- C09K—MATERIALS FOR MISCELLANEOUS APPLICATIONS, NOT PROVIDED FOR ELSEWHERE
- C09K8/00—Compositions for drilling of boreholes or wells; Compositions for treating boreholes or wells, e.g. for completion or for remedial operations
- C09K8/60—Compositions for stimulating production by acting on the underground formation
- C09K8/80—Compositions for reinforcing fractures, e.g. compositions of proppants used to keep the fractures open
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C10/00—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C14/00—Glass compositions containing a non-glass component, e.g. compositions containing fibres, filaments, whiskers, platelets, or the like, dispersed in a glass matrix
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C2214/00—Nature of the non-vitreous component
- C03C2214/20—Glass-ceramics matrix
Definitions
- Ceramic particles are produced for use in a wide variety of industrial applications. Some of these applications include using a plurality of ceramic particles: as a proppant to facilitate the removal of liquids and/or gases from wells that have been drilled into geological formations; as a media for scouring, grinding or polishing; as a bed support media in a chemical reactor; as a heat transfer media; as a filtration media; and as roofing granules when applied to asphalt shingles.
- the present invention is a sintered ceramic particle comprising at least two microstructural phases comprising an amorphous phase, representing between 30 volume percent and 70 volume percent of the particle, and a first substantially crystalline phase comprising a plurality of predominately crystalline regions distributed through the amorphous phase.
- the present invention is a process for producing a sintered ceramic particle. The process may comprise the following steps.
- Fig. 1 is a process flow chart.
- microstructural phase refers to a sintered ceramic particle's crystalline or amorphous phase(s) which are detectable using an X-ray diffractometer analytical device.
- a particle may have one or more microstructural phases.
- the microstructural phase is characterized by the physical arrangement of atoms which form repeating patterns in crystalline phases and do not form repeating patterns in an amorphous phase.
- the phrase "fluid conversion temperature” refers to the temperature at which a solid ceramic material begins to soften and thereafter becomes flowable due to an increase in its temperature.
- the phrase “crush resistance” refers to the particle's ability to withstand crushing. Crush resistance is commonly used to denote the strength of a ceramic particle, such as a proppant, and may be determined using ISO 13503-2:2006(E). A strong proppant generates a lower weight percent crush resistance than a weak proppant at the same closure stress. For example, a proppant that has a 2 weight percent crush resistance is considered to be a strong proppant and is preferred to a weak proppant that has a 10 weight percent crush resistance.
- Processes for manufacturing ceramic particles have been devised and used for many years to manufacture large quantities of ceramic particles such as proppants. Because proppants are used in a wide variety of geological formations, at different depths and exposed to extremes in temperature and pressure, the physical characteristics of the proppants may need to be customized in order to optimize the performance of the proppant in a particular environment. Some of the properties which may impact the performance of the proppant include:
- a first well known teaching for improving the proppant' s crush strength is to increase the percentage of AI2O 3 chemical content in the proppant.
- the AI2O 3 is calcined at a sufficiently high temperature, such as 1300°C, to convert the transitional crystalline phases to alpha alumina which is known to be strong and therefore highly resistant to crushing.
- raw materials that contain high concentrations of ⁇ 1 2 (3 ⁇ 4 chemical content are expensive and must be purchased in large quantities which can significantly increase the manufacturing cost of the proppant producer and is undesirable.
- a second well known technical teaching is that some amorphous ceramic materials, such as glass beads, tend to fracture at low stress and therefore has undesirably high crush resistance when used as an ingredient in a proppant.
- amorphous materials are relatively inexpensive and therefore desirable from a cost perspective.
- amorphous materials are problematic because they are known to have a fluid conversion temperature well below the minimum temperature needed to convert transitional alumina to alpha alumina. When an amorphous material begins to soften, it may become tacky and individual proppant particles may adhere to adjacent particles thereby forming large, loosely bound agglomerates made up of thousands of individual proppant particles.
- the proppants also tend to adhere to the inside surfaces of kilns and other equipment used to calcine the proppants. During the time the proppants reside in the kiln, such as a rotary kiln, the proppants may build up an increasingly thick layer of proppants on the inside surface of the kiln which ultimately results in the shut down of the kiln so that it can be cleaned and then restarted.
- some proppant manufacturers have elected to produce proppants having high alumina content, to achieve the desired crush resistance, and low amorphous material, to avoid the problems associated with proppant agglomeration and low crush resistance.
- a proppant wherein regions of predominately crystalline phase ceramic material and a matrix of a predominately amorphous phase ceramic material cooperate to form a proppant that has good resistance to crushing. More specifically, in a proppant of the present invention, predominately crystalline regions are surrounded by and embedded within a matrix of an amorphous ceramic material. The matrix forms a continuous phase through the proppant. The predominately crystalline regions collectively define a discontinuous phase. As described above, amorphous ceramic materials tend to fracture at low stress and therefore have undesirably high crush resistance when used as an ingredient in a proppant.
- the crystalline material and the amorphous material are selected so that a synergistic relationship is established between the materials which results in the creation of a beneficial stress, such as compressive stress, on the amorphous material.
- the compressive stress is believed to improve the particle's crush resistance by compressing the amorphous material thereby hindering crack origination and propagation through the amorphous phase.
- Hindering crack propagation effectively improves the crush resistance of the particle at a specified stress by requiring the exertion of a higher mechanical force to crush the particle.
- the compressive stress on the amorphous material may be created by selecting the crystalline and amorphous materials so that after forming, heating and cooling the proppant the crystalline material's coefficient of thermal expansion is greater than the amorphous material's coefficient of thermal expansion.
- the difference in coefficients of thermal expansion may cause the discreet crystalline material to attempt to shrink more than the adjacent amorphous material to which it has been bonded during the cooling step.
- the difference in the coefficients of thermal expansion is believed to cause the amorphous material to experience compressive stress as it resists the greater relative movement of the crystalline material.
- the coefficients of thermal expansion of the particle's ceramic materials may be determined using the procedure described below.
- the exact value of a material's coefficient of thermal expansion after heating of the particle may not be critical to the use of that material to manufacture a ceramic particle of this invention.
- the size of the difference between the coefficients of thermal expansion is the characteristic that may directly impact the creation of the compressive stress and the resulting resistance to crushing.
- a difference of at least 0.1 x 10 "6 /°C may be sufficient to exert a compressive stress. More preferably, the difference in coefficients of thermal expansion may be 0.2 or 0.3 x 10 "6 /°C.
- the coefficient of thermal expansion of the crystalline material may be greater than 6.0, more preferably, greater than 7.0 x 10 "6 /°C.
- the coefficient of thermal expansion of the amorphous material may be less than 6.0, more preferably, less than 5.0 x 10 "6 /°C.
- the quantity of the amorphous ceramic material in a porous ceramic particle of this invention may be between 30% and 70% based on the volume of the particle after heating and cooling of the same. If the amorphous material represents less than 30% of the particle's volume, the amorphous material may not form a continuous phase throughout the particle. The amorphous phase material may represent at least 40%, 45% or even 50% of the particle's volume. Examples of amorphous ceramic materials suitable for use in a porous ceramic particle of this invention include feldspar and nepheline syenite.
- the proppants' s microstructural phases, the chemical composition of those phases and the coefficient of thermal expansion of those phases should be determined.
- the identification of these physical characteristics may be determined using the following analytical procedures.
- an X-ray diffractometer such as an PANalytical® XRD, is used to detect the existence of one or more crystalline phases.
- the height of the lines on the X-ray diffraction pattern may be used to determine the relative quantities of each crystalline phase.
- the location of the lines on the X-ray diffraction pattern horizontal axis is indicative of a microstructural phase.
- an internal standard may facilitate the analysis of the X-ray diffraction pattern.
- the amount of amorphous phase material may be calculated as the amount of proppant that is not crystalline.
- the composition' s chemical elements may be determined using X-ray fluorescence (XRF).
- XRF X-ray fluorescence
- the coefficient of thermal expansion of each microstructural phase may be determined using an analytical technique known as dilatometry.
- a dilatometer such as a Unitherm 1161 from Anter Corporation, is an instrument capable of measuring the coefficient of thermal expansion (CTE) of a material. The dilatometer may be used to measure the change in length of a rectangular bar test sample as a function of temperature. The bar may be 40 mm long, 25 mm wide and 2 mm high.
- the CTE is obtained through recording the change in relative length of the rectangular bar upon cooling from below the fluid conversion temperature to 25°C. Commonly, the CTE is reported as units of 10 " 6 /°C, such as 5 x 10 "6 /°C, which represents a change of 0.0001 of the rectangular bar's length per every 1°C change in temperature.
- Test samples of each microstructure amorphous phase can be prepared using reagent grade raw materials, in a formulation equal to the determined chemical composition, which are then melted at high temperatures greater than the fluid conversion temperature. These melted samples of the amorphous phase are ground to a fine powder and formed in the shape, such as a rectangular bar which is suitable to dilatometry measurements, and sintered to high temperature.
- the same XRD and XRF techniques described above can be used to confirm the phase and chemical content of each crystalline and amorphous phase test sample.
- the quantity of crystalline alumina material in a porous ceramic particle of this invention may be between 30% and 70% of the particle's volume.
- the quantity of crystalline alumina material may be greater than 30%, 35% or even
- the crystalline material may be a single crystalline phase, such as alpha alumina.
- the crystalline alumina may be a mixture of transitional phases or a combination of alpha alumina and one or more transitional phases.
- Step 20 includes providing a first ceramic material and a second ceramic material.
- the first ceramic material has a fluid conversion temperature.
- the second ceramic material has a fluid conversion temperature that is less than the fluid conversion temperature of the first ceramic material.
- Step 22 includes mixing the first and second materials to form a mixture wherein the mixture comprises between 30 and 70 weight percent of the first ceramic material.
- Step 24 is directed to forming the mixture into a particle precursor.
- Step 26 includes heating the precursor to a maximum temperature that is no less than the first ceramic material's fluid conversion temperature and no greater than the second ceramic material's fluid conversion temperature wherein the first and second ceramic materials cooperate to form an amorphous phase that abuts and embeds predominately crystalline regions. During the heating step, the temperature of the precursor must at least equal and perhaps slightly exceed the first material's fluid conversion temperature.
- the heated precursor is cooled to ambient temperature thereby creating a sintered ceramic particle.
- the mixture may optionally include other materials such as binders and solvents.
- Suitable solvents include water and some alcohols.
- a binder may be one or more materials selected from organic starches, such as drilling starch, as well as gums or resins that are sold commercially for such purposes.
- a binder may also be an inorganic material such as clay or an acid.
- Binders are usually added in an amount less than 10 weight percent of the mixture and may be added dry or as a solution. While a binder may be responsible for some level of porosity in a ceramic particle, binders are not considered pore formers herein.
- the composition of the mixture may be limited to less than 0.1 weight percent of one or more pore formers selected from the list consisting of a transient pore former, an in-situ pore former, and combinations thereof.
- Transient pore formers may be limited to less than 0.05 weight percent of the mixture.
- In- situ pore formers may be limited to less than 0.01 weight percent of the mixture. In one embodiment, the mixture will not include any pore formers.
- a particle precursor is defined herein as a particle wherein the first and second ceramic materials are distributed therethrough and solvents, such as water, have been removed so that the precursor's loss on drying (LOD) after heating to between 110°C and 130°C for two hours is less than one percent of the precursor's starting weight.
- the precursor may or may not contain optional ingredients such as a binder.
- the precursor may include at least 30 weight percent of the first ceramic material and at least 30 weight percent of the second ceramic material. In some embodiments, the precursor may include between 60 weight percent and 70 weight percent of the first ceramic material and between 30 weight percent and 40 weight percent of the second ceramic material.
- Forming a particle precursor may be achieved by processing the mixture through a machine such as an Eirich R02 mixer, which is available from
- the action of the mixer causes the formation of a large number of small generally spherical balls of mix which may be referred to as particle precursors or greenware.
- the optional ingredients may be removed by drying the greenware in an oven to a sufficiently high temperature, such as 200°C or higher, to drive the optional ingredients from the greenware.
- the particle precursors may be processed through a screening apparatus that includes a No.8 ASTM sieve designation, which has 2.36 mm apertures, and a No. 70 ASTM sieve designation, which has 212 ⁇ sieve apertures.
- the precursors selected for heating in step 26 may flow through the No. 8 sieve and not flow through the No. 70 sieve.
- the precursor is heated to a maximum temperature which is below the fluid conversion temperature of the second ceramic material and above the fluid conversion temperature of the first ceramic material.
- the precursor may be heated to a maximum temperature which is above the melting temperature of the first ceramic material which is below the sintering temperature of the second ceramic material.
- the first ceramic material may convert from a solid material to a flowable material and then flow over the second ceramic material.
- both the first and second ceramic materials may be provided as powders which include a plurality of granules.
- granules may range from 1 to 10 microns, more specifically from 6 to 8 microns.
- the first and second ceramic materials may be selected so that the first ceramic material's coefficient of thermal expansion after heating and cooling as described above is at least 10% higher than the second ceramic material's coefficient of thermal expansion after experiencing the same heating and cooling regime. After heating and cooling, the coefficient of thermal expansion of the first ceramic material may be 20% or even 30% higher than the coefficient of thermal expansion of the second ceramic material. While the exact difference between the fluid conversion temperature of the first ceramic material and the fluid conversion temperature of the second ceramic material may not be critical, a difference of 50°C may be workable in particular embodiments.
- a suitable first ceramic material may be selected from the group consisting of bauxite, alumina, kaolin, clays, alumino-silicates, and magnesium silicates.
- a suitable second ceramic material may be selected from the group consisting of feldspar and nepheline syenite.
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- Life Sciences & Earth Sciences (AREA)
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- Ceramic Engineering (AREA)
- Dispersion Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General Chemical & Material Sciences (AREA)
- Geochemistry & Mineralogy (AREA)
- Crystallography & Structural Chemistry (AREA)
- General Life Sciences & Earth Sciences (AREA)
- Compositions Of Oxide Ceramics (AREA)
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Abstract
Description
Claims
Priority Applications (8)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
MX2013010886A MX2013010886A (en) | 2011-03-29 | 2012-03-26 | Ceramic particle and process for making the same. |
US14/005,278 US20140011658A1 (en) | 2011-03-29 | 2012-03-26 | Ceramic particle and process for making the same |
BR112013024350A BR112013024350A2 (en) | 2011-03-29 | 2012-03-26 | ceramic particle and process to produce the same |
CN2012800146267A CN103443051A (en) | 2011-03-29 | 2012-03-26 | Ceramic particle and process for making the same |
EP12764164.5A EP2691354A4 (en) | 2011-03-29 | 2012-03-26 | Ceramic particle and process for making the same |
CA2830795A CA2830795A1 (en) | 2011-03-29 | 2012-03-26 | Ceramic particle and process for making the same |
RU2013146848/03A RU2544209C1 (en) | 2011-03-29 | 2012-03-26 | Ceramic particle and method of obtaining thereof |
AU2012236861A AU2012236861A1 (en) | 2011-03-29 | 2012-03-26 | Ceramic particle and process for making the same |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US201161468773P | 2011-03-29 | 2011-03-29 | |
US61/468,773 | 2011-03-29 |
Publications (2)
Publication Number | Publication Date |
---|---|
WO2012135106A2 true WO2012135106A2 (en) | 2012-10-04 |
WO2012135106A3 WO2012135106A3 (en) | 2013-01-03 |
Family
ID=46932267
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/US2012/030539 WO2012135106A2 (en) | 2011-03-29 | 2012-03-26 | Ceramic particle and process for making the same |
Country Status (9)
Country | Link |
---|---|
US (1) | US20140011658A1 (en) |
EP (1) | EP2691354A4 (en) |
CN (1) | CN103443051A (en) |
AU (1) | AU2012236861A1 (en) |
BR (1) | BR112013024350A2 (en) |
CA (1) | CA2830795A1 (en) |
MX (1) | MX2013010886A (en) |
RU (1) | RU2544209C1 (en) |
WO (1) | WO2012135106A2 (en) |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
BRPI0923723A2 (en) * | 2008-12-31 | 2017-07-11 | Saint Gobain Ceramics | CERAMIC ARTICLE AND ITS PRODUCTION PROCESS |
BR112017001295A2 (en) * | 2014-07-23 | 2017-11-14 | Baker Hughes Inc | composite comprising well treatment agent and / or a beacon adhered to a calcined substrate of a metal oxide coated core and a method for using the same |
Family Cites Families (18)
Publication number | Priority date | Publication date | Assignee | Title |
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US2924533A (en) * | 1956-05-28 | 1960-02-09 | Carborundum Co | Spheroidal refractory material and method of making |
US3156545A (en) * | 1962-05-14 | 1964-11-10 | Wakefield Corp | Abrasive articles |
US3486706A (en) * | 1967-02-10 | 1969-12-30 | Minnesota Mining & Mfg | Ceramic grinding media |
FR2306327A1 (en) * | 1975-03-19 | 1976-10-29 | Inst Francais Du Petrole | PROCESS FOR SUPPORTING FRACTURES IN THE WALLS OF A WELL THROUGH GEOLOGICAL FORMATIONS |
US4073845A (en) * | 1976-01-29 | 1978-02-14 | Gte Sylvania Incorporated | High density high strength S13 N4 ceramics prepared by pressureless sintering of partly crystalline, partly amorphous S13 N4 powder |
US4944905A (en) * | 1984-01-18 | 1990-07-31 | Minnesota Mining And Manufacturing Company | Particulate ceramic useful as a proppant |
US4680230A (en) * | 1984-01-18 | 1987-07-14 | Minnesota Mining And Manufacturing Company | Particulate ceramic useful as a proppant |
US4921820A (en) * | 1989-01-17 | 1990-05-01 | Norton-Alcoa Proppants | Lightweight proppant for oil and gas wells and methods for making and using same |
DE3905271A1 (en) * | 1989-02-21 | 1990-08-23 | Hoechst Ag | SILICON NITRIDE CERAMICS AND METHOD FOR THEIR PRODUCTION |
JP2002544386A (en) * | 1999-04-30 | 2002-12-24 | カリフォルニア・インスティテュート・オブ・テクノロジー | In-situ formed ductile metal / bulk metallic glass matrix composite formed by concentration distribution |
RU2267010C1 (en) * | 2004-09-02 | 2005-12-27 | Открытое акционерное общество "Боровичский комбинат огнеупоров" | Proppant and a method for manufacturing thereof |
US7867613B2 (en) * | 2005-02-04 | 2011-01-11 | Oxane Materials, Inc. | Composition and method for making a proppant |
WO2008025320A1 (en) * | 2006-08-29 | 2008-03-06 | Fraunhofer-Gesellschaft zur Förderung der angewandten Forschung e.V. | Catalytically active component for thermal ionization detectors for the detection of halogen-containing compounds and process for producing an oxide-ceramic material for the component |
RU2344156C2 (en) * | 2007-02-28 | 2009-01-20 | Шлюмбергер Текнолоджи Б.В. | Proppant and method of well efficiency increase |
RU2336293C1 (en) * | 2007-09-24 | 2008-10-20 | Сергей Федорович Шмотьев | Methods of proppant fabrication from glass spheres |
BRPI0923723A2 (en) * | 2008-12-31 | 2017-07-11 | Saint Gobain Ceramics | CERAMIC ARTICLE AND ITS PRODUCTION PROCESS |
KR20120105536A (en) * | 2009-12-22 | 2012-09-25 | 옥세인 머티리얼스, 인크. | A proppant having a glass-ceramic material |
CN102781854B (en) * | 2009-12-31 | 2015-11-25 | 哈利伯顿能源服务公司 | There is ceramic particle and the manufacture method thereof of controlled hole and/or microballoon distribution and/or size |
-
2012
- 2012-03-26 RU RU2013146848/03A patent/RU2544209C1/en not_active IP Right Cessation
- 2012-03-26 CA CA2830795A patent/CA2830795A1/en not_active Abandoned
- 2012-03-26 WO PCT/US2012/030539 patent/WO2012135106A2/en active Application Filing
- 2012-03-26 MX MX2013010886A patent/MX2013010886A/en unknown
- 2012-03-26 CN CN2012800146267A patent/CN103443051A/en active Pending
- 2012-03-26 US US14/005,278 patent/US20140011658A1/en not_active Abandoned
- 2012-03-26 EP EP12764164.5A patent/EP2691354A4/en not_active Withdrawn
- 2012-03-26 BR BR112013024350A patent/BR112013024350A2/en not_active Application Discontinuation
- 2012-03-26 AU AU2012236861A patent/AU2012236861A1/en not_active Abandoned
Non-Patent Citations (1)
Title |
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See references of EP2691354A4 * |
Also Published As
Publication number | Publication date |
---|---|
AU2012236861A1 (en) | 2013-10-31 |
CA2830795A1 (en) | 2012-10-04 |
CN103443051A (en) | 2013-12-11 |
RU2544209C1 (en) | 2015-03-10 |
EP2691354A4 (en) | 2014-10-29 |
WO2012135106A3 (en) | 2013-01-03 |
BR112013024350A2 (en) | 2016-12-20 |
US20140011658A1 (en) | 2014-01-09 |
MX2013010886A (en) | 2014-04-14 |
EP2691354A2 (en) | 2014-02-05 |
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