Patent Application
20230202933
The present invention relates to sintered zirconia beads, to a process for manufacturing these beads, and to the use of these beads as grinding agents, agents for wet dispersion or for surface treatment.
The paint, ink, dye, magnetic lacquer and agrochemical industries use beads for the dispersion and homogenization of liquid and solid constituents.
The mineral industry uses beads for the fine grinding of materials that may have been pre-ground dry via conventional processes, notably for the fine grinding of calcium carbonate, titanium oxide, gypsum, kaolin and iron ore.
In the field of microgrinding, rounded particle sand, glass beads, metal beads and ceramic beads are known.
The beads are conventionally between 0.005 and 10 mm in size.
The following may be distinguished:
Unlike sintered beads, molten beads usually include a very abundant intergranular vitreous phase filling a network of crystalline grains. The problems encountered with sintered beads and fused beads in their respective applications, and the technical solutions adopted for solving them, are thus generally different. Moreover, due to the significant differences between manufacturing processes, a composition developed for manufacturing a fused bead is, in principle, unsuitable for manufacturing a sintered bead, and vice versa.
There is an ongoing need for sintered zirconia beads with improved wear resistance, in particular for grinding applications.
One aim of the invention is to address this need, at least partially.
The invention relates to a sintered bead, having:
the contents of Y2O3 and CeO2, as molar percentages on the basis of the sum of ZrO2, HfO2, Y2O3 and CeO2, being such that 1.8%≤Y2O3≤2.5% and 0.1%≤CeO2≤0.9%, and
As will be seen in greater detail in the rest of the description, the inventors have discovered that a low CeO2 content makes it possible, unexpectedly, to manufacture a sintered zirconia bead which has excellent resistance during grinding, irrespective of the Y2O3 content, provided that it remains between 1.8% and 2.5%.
The sintered zirconia beads according to the invention are thus particularly well suited to wet dispersion and microgrinding applications.
A sintered zirconia bead according to the invention may also have one or more of the following optional features:
The invention also relates to a bead powder comprising more than 90%, preferably more than 95%, preferably substantially 100%, as mass percentages, of beads according to the invention.
The invention also relates to a device chosen from a suspension, a grinder, and surface treatment apparatus, said device including a powder of beads according to the invention.
The invention also relates to a process for manufacturing sintered zirconia beads according to the invention, said process comprising the following successive steps:
A manufacturing process according to the invention may also have one or more of the following optional features:
The invention finally relates to the use of a bead powder according to the invention, in particular manufactured according to a process according to the invention, as agents for grinding, in particular wet grinding, as agents for wet dispersion, or for the treatment of surfaces.
However, hafnium oxide is not considered an impurity. It is considered that a total impurity content of less than 5% does not substantially modify the results obtained.
According to the present invention, HfO2 is not intentionally added to the starting feedstock. HfO2 thus refers only to trace amounts of hafnium oxide, as this oxide is always naturally present in zirconia sources in contents generally less than 2%.
AD-100/[(x/3.987)+(100−x)/ADz] (1)
where x is the alumina content, in mass percentages, and
ADz is the absolute density of the zirconia stabilized with Y2O3 and CeO2, calculated by dividing the mass of the unit cell of the zirconia by the volume of said unit cell, the zirconia being considered stabilized only in the quadratic phase. The volume of the unit cell is calculated by means of the cell parameters determined by X-ray diffraction. The mass of the unit cell is equal to the sum of the mass of the elements Zr, O, Y and Ce, present in the said unit cell, considering that all of the Y2O3 and CeO2 stabilizes the zirconia.
Sintered Zirconia Bead
The sintered zirconia bead according to the invention is noteworthy as regards its composition.
Surprisingly, and without being able to explain it theoretically, the inventors have discovered that the simultaneous presence of Y2O3 and CeO2, in the contents present in the invention, makes it possible to achieve an excellent compromise between resistance during grinding and resistance to hydrothermal aging.
A sintered zirconia bead according to the invention preferably consists of oxides for more than 98%, preferably for more than 99%, preferably for more than 99.5%, preferably for more than 99.9%, of its mass. Preferably, the sintered zirconia bead according to the invention consists substantially entirely of oxides.
Preferably, a sintered zirconia bead according to the invention has a Y2O3 content of greater than or equal to 1.9%, preferably greater than or equal to 2% and/or preferably less than or equal to 2.4%, preferably less than or equal to 2.2%, as molar percentages on the basis of the sum of ZrO2, HfO2, Y2O3 and CeO2.
Preferably, a sintered zirconia bead according to the invention has a CeO2 content greater than or equal to 0.2%, preferably greater than or equal to 0.3%, preferably greater than or equal to 0.4% and/or preferably less than 0.8%, preferably less than 0.7%, preferably less than 0.6%, as molar percentages on the basis of the sum of ZrO2, HfO2, Y2O3 and CeO2.
Preferably, a sintered zirconia bead according to the invention has a Y2O3 content greater than or equal to 1.9%, preferably greater than or equal to 2% and/or preferably less than or equal to 2.4%, preferably less than or equal to 2.2%, and a CeO2 content greater than or equal to 0.2%, preferably greater than or equal to 0.3%, preferably greater than or equal to 0.4% and less than 0.8%, preferably less than 0.7%, preferably less than 0.6%, as molar percentages on the basis of the sum of ZrO2, HfO2, Y2O3 and CeO2. Advantageously, the sintered zirconia bead has excellent wear resistance during grinding.
In a preferred embodiment, the sintered zirconia bead according to the invention has an Al2O3 content of greater than or equal to 0.2%, preferably greater than or equal to 0.25% and preferably less than or equal to 1.2%, preferably less than or equal to 1%, preferably less than or equal to 0.8%, as mass percentages on the basis of the oxides.
However, tests have shown that the presence of Al2O3 is not essential. In one embodiment, the sintered zirconia bead according to the invention has an Al2O3 content of less than 0.1%, less than 0.005%, less than 0.003%, less than 0.002%, or substantially zero, as a mass percentage on the basis of the oxides.
Preferably, the sintered bead according to the invention has a CaO content of less than 1.5%, preferably less than 1.0%, as mass percentages on the basis of the oxides.
In one embodiment, the sintered zirconia bead according to the invention has a CaO content of greater than 0.1%, preferably greater than 0.2%, preferably greater than 0.3%, as a mass percentage on the basis of the oxides.
Preferably, the sintered bead according to the invention has a total content of oxides other than ZrO2, HfO2, Y2O3, CeO2, Al2O3 and CaO of less than 4%, preferably less than 3%, preferably less than 2%, more preferably less than 1%, more preferably less than 0.8%, preferably less than 0.5%, as a mass percentage on the basis of the oxides.
Preferably, in the sintered zirconia bead according to the invention, the oxides other than ZrO2, HfO2, Y2O3, CeO2, Al2O3 and CaO are impurities.
Preferably, in the sintered zirconia bead according to the invention, any oxides other than ZrO2, HfO2, Y2O3, CeO2, Al2O3 and CaO are present in an amount of less than 2.0%, preferably less than 1.5%, preferably less than 1.0%, preferably less than 0.8%, preferably less than 0.5%, preferably less than 0.3%.
The sintered zirconia bead according to the invention preferably has a content of monoclinic zirconia, as a mass percentage on the basis of the total amount of crystalline phases, of less than 5%, preferably substantially zero.
The sintered zirconia bead according to the invention preferably has a total content of crystalline phases other than stabilized zirconia and monoclinic zirconia, as a mass percentage on the basis of the total amount of crystalline phases, of less than 6%, preferably less than 5% or even less than 4%.
In the sintered zirconia bead according to the invention, the zirconia is stabilized with Y2O3 and CeO2. Preferably, the stabilized zirconia is present substantially only in the form of quadratic zirconia.
Preferably, in the sintered bead of zirconia according to the invention, the mass amount of amorphous, i.e. vitreous, phase as a mass percentage relative to the mass of said bead is less than 7%, preferably less than 5%, preferably substantially zero.
The sintered zirconia bead according to the invention has an average grain size of less than 2 μm, preferably less than 1.5 μm, preferably less than 1 μm, preferably less than 0.9 μm, preferably less than 0.8 μm, preferably less than 0.6 μm, preferably less than 0.5 μm, and preferably greater than 0.1 μm, preferably greater than 0.2 μm. Advantageously, the resistance during grinding is improved.
Preferably, the sintered zirconia bead according to the invention has a grain size distribution with a standard deviation of less than 0.20 μm, preferably less than 0.15 μm, preferably less than 0.1 μm.
In a preferred embodiment, the sintered zirconia bead according to the invention has:
the Y2O3 and CeO2 contents, as molar percentages on the basis of the sum of ZrO2, HfO2, Y2O3 and CeO2, being such that the Y2O3 content is greater than or equal to 1.9%, preferably greater than or equal to 2% and/or preferably less than or equal to 2.4%, preferably less than or equal to 2.2%, and the CeO2 content is greater than or equal to 0.2%, preferably greater than or equal to 0.3%, preferably greater than or equal to 0.4% and less than 0.8%, preferably less than 0.7%, preferably less than 0.6%, and
In said preferred embodiment, the sintered zirconia bead preferably has an average grain size of less than 2 μm, preferably less than 1.5 μm, preferably less than 1 μm, preferably less than 0.9 μm, preferably less than 0.8 μm, preferably less than 0.6 μm, preferably less than 0.5 μm, and preferably greater than 0.1 μm, preferably greater than 0.2 μm, and a grain size distribution with a standard deviation of less than 0.20 μm, preferably less than 0.15 μm, preferably less than 0.1 μm.
Preferably, the sintered zirconia bead according to the invention has a relative density of greater than 99.5%, preferably greater than 99.6%, preferably greater than 99.7%, preferably greater than 99.8%, preferably greater than 99.9%, the absolute density being calculated according to the method described previously.
The sintered zirconia bead according to the invention preferably has a size of less than 10 mm, preferably less than 2.5 mm and/or greater than 0.005 mm, preferably greater than 0.01 mm, preferably greater than 0.02 mm, preferably greater than 0.03 mm.
A sintered zirconia bead according to the invention preferably has a sphericity of greater than 0.7, preferably greater than 0.8, preferably greater than 0.85, or even greater than 0.9.
A sintered zirconia bead according to the invention may be manufactured by means of a manufacturing process according to the invention.
To manufacture sintered zirconia beads according to the invention, steps a) to g) described above and detailed below may be performed.
In step a), a particle mixture with a median size of less than 2 μm is prepared. The composition of the particle mixture is also adapted, in a manner known per se, so that the sintered zirconia beads have a composition in accordance with the invention.
The starting material powders are intimately mixed.
The starting material powders may be ground individually or preferably co-milled so that the resulting particle mixture has a median size of less than 2 μm, preferably less than 1.5 μm, preferably less than 1 μm, preferably less than 0.8 μm, preferably less than 0.6 μm, preferably less than 0.5 μm, preferably less than 0.4 μm, preferably less than 0.3 μm, and/or preferably greater than 0.05 μm. This grinding may be wet grinding. Grinding or co-milling may also be used to obtain an intimate mixture.
Preferably, the particle mixture has a ratio (D90-D10)/D50 of less than 2, preferably less than 1.5, preferably less than 1.
Y2O3 and CeO2 are known stabilizers of zirconia. In the particle mixture, they may or may not stabilize the zirconia. According to the invention, the particle mixture should, however, lead to a sintered zirconia bead according to the invention.
In the particle mixture, the zirconia is preferably at least partially stabilized with Y2O3. Preferably then, a CeO2 ceria powder is used as the source of CeO2. In said embodiment, the zirconia powder is at least partially stabilized with Y2O3 and has a specific surface area, calculated via the BET method, of greater than 0.5 m2/g, preferably greater than 1 m2/g, preferably greater than 1.5 m2/g, and/or less than 20 m2/g, preferably less than 18 m2/g, preferably less than 15 m2/g. Advantageously, the optional grinding, generally in suspension, is thereby facilitated. Furthermore, the sintering temperature in step f) may be reduced. In said embodiment, in said zirconia powder at least partially stabilized with Y2O3, the zirconia is substantially only in the quadratic form.
A ceria and/or yttria and/or zirconia precursor may also be used in the particle mixture.
The ceria and/or the ceria precursor and/or the yttria and/or the yttria precursor may be incorporated, partially or totally, into the particle mixture in the form of a powder, i.e. in a form separate from the zirconia, so that, after sintering, the zirconia is at least partially stabilized. In this embodiment, the median size of the yttria powder and/or yttria precursor and/or ceria precursor and/or of the ceria precursor is preferably less than 1 μm, preferably less than 0.5 μm, more preferably less than 0.3 μm. The zirconia-stabilizing efficiency is thereby advantageously improved during the sintering.
In one embodiment, the particle mixture includes particles in which stabilized or nonstabilized zirconia and yttria and/or ceria are intimately mixed. Such an intimate mixture may be obtained, for example, by coprecipitation, thermal hydrolysis or atomization, and optionally consolidated by heat treatment. In a said particle mixture, yttria and/or ceria may be replaced with an equivalent amount of precursor(s).
Preferably, the particle mixture does not include any yttria precursor.
Preferably, the particle mixture does not include any ceria precursor.
Preferably, the particle mixture does not include any zirconia precursor.
Preferably, the particle mixture does not include any monoclinic zirconia powder.
Preferably, the Y2O3 content is greater than or equal to 1.9%, preferably greater than or equal to 2% and/or preferably less than or equal to 2.4%, preferably less than or equal to 2.2%, as molar percentages on the basis of the sum of ZrO2, HfO2, Y2O3 and CeO2 present in said particle mixture.
Preferably, the CeO2 content is greater than or equal to 0.2%, preferably greater than or equal to 0.3%, preferably greater than or equal to 0.4% and/or preferably less than 0.8%, preferably less than 0.7%, preferably less than 0.6%, as molar percentages on the basis of the sum of ZrO2, HfO2, Y2O3 and CeO2 present in said particle mixture.
Preferably the Y2O3 content is greater than or equal to 1.9%, preferably greater than or equal to 2% and/or preferably less than or equal to 2.4%, preferably less than or equal to 2.2%, and the CeO2 content is greater than or equal to 0.2%, preferably greater than or equal to 0.3%, preferably greater than or equal to 0.4% and less than 0.8%, preferably less than 0.7%, preferably less than 0.6%, as molar percentages on the basis of the sum of ZrO2, HfO2, Y2O3 and CeO2 present in said particle mixture. Advantageously, the sintered zirconia bead obtained from said particle mixture has excellent resistance during grinding.
In a preferred embodiment, the particle mixture comprises alumina powder in an amount of greater than or equal to 0.2%, preferably greater than or equal to 0.25% and preferably less than or equal to 1.2%, preferably less than or equal to 1%, preferably less than or equal to 0.8%, as mass percentages on the basis of the mass of the particle mixture. Advantageously, the sinterability of the particle mixture is thereby improved. The alumina may be replaced, totally or partly, with an equivalent amount of precursor. Preferably, the particle mixture does not include any alumina precursor. More preferably, the alumina is essentially present in the form of corundum, which preferably has a median size of less than 5 μm, preferably less than 3 μm, preferably less than 1 μm.
However, tests have shown that the presence of alumina is not essential. In one embodiment, the alumina content may in particular be less than 0.1%, less than 0.05%, less than 0.03%, less than 0.01%, or substantially zero, as mass percentages on the basis of the mass of the particle mixture.
In one embodiment, the particle mixture includes powders of
The powders providing the oxides are preferably chosen so that the total content of oxides other than ZrO2, HfO2, Y2O3, CeO2, Al2O3 and CaO is less than 5%, as a mass percentage on the basis of the oxides.
Preferably, no starting materials other than powders of zirconia at least partially stabilized with Y2O3, ceria and corundum are intentionally introduced into the particle mixture, the other oxides present being impurities.
Preferably, the powders used each have a median size of less than 5 μm, preferably less than 3 μm, preferably less than 2 μm, preferably less than 1 μm, preferably less than 0.7 μm, preferably less than 0.6 μm, preferably less than 0.5 μm, preferably less than 0.4 μm, or even less than 0.3 μm.
Irrespective of the embodiment, one or more of the powders of the particle mixture described above may be replaced, at least partially, with equivalent powders, i.e. with powders which, during the manufacture of a bead according to the invention, lead to the same constituents (same composition, same crystallographic phase) in said bead, in the same amounts.
In step b), which is optional, the particle mixture may be dried, for example in an oven or by atomization, in particular if it has been obtained by wet grinding or if at least one starting material powder has been obtained by wet grinding. Preferably, the temperature and/or duration of the drying step are adapted so that the residual moisture content of the particle mixture is less than 2%, or even less than 1.5%.
In step c), a starting feedstock is prepared, preferably at room temperature, including the particle mixture obtained at the end of step a) or at the end of step b) and, optionally, a solvent, preferably water, the amount of which is adapted to the forming method of step d).
As is well known to those skilled in the art, the starting feedstock is adapted to the forming process of step d).
In particular, the forming may result from a gelation process. To this end, a solvent, preferably water, is preferably added to the starting feedstock so as to produce a suspension.
The suspension preferably has a solids content by mass of between 50% and 70%.
The suspension may also include one or more of the following constituents:
Dispersants, surface tension modifiers and gelling agents are well known to those skilled in the art.
Examples that may be mentioned include:
The particle mixture is preferably added to a mixture of water and dispersants/deflocculants in a ball mill. After stirring, water in which a gelling agent has been previously dissolved is added to obtain a suspension.
If the forming is done by extrusion, thermoplastic polymers or thermosetting polymers may be added to the starting feedstock, which preferably does not contain any solvent.
In step d), any conventional forming process known for the manufacture of sintered beads may be performed.
Among these processes, mention may be made of:
In a gelling process, drops of the suspension described above are obtained by flowing the suspension through a calibrated orifice. The drops exiting the orifice fall into a bath of a gelling solution (electrolyte adapted to react with the gelling agent) where they harden after recovering a substantially spherical shape.
In step e), which is optional, the raw beads obtained in the previous step are washed, for example with water.
In step f), which is optional, the optionally washed raw beads are dried, for example in an oven.
In step g), the optionally washed and/or dried raw beads are sintered. Preferably, the sintering is performed in air, preferably in an electric furnace, preferably at atmospheric pressure.
The sintering in step g) is performed at a temperature preferably above 1330° C., preferably above 1350° C. and preferably below 1600° C., preferably below 1550° C., preferably below 1500° C., preferably below 1450° C.
The holding time at the temperature steady stage is preferably more than 1 hour and/or preferably less than 10 hours, preferably less than 7 hours, preferably less than 5 hours, preferably less than 3 hours. Preferably the sintering time is between 1 and 3 hours.
The sintered zirconia beads obtained preferably have a smallest diameter of greater than 0.005 mm, preferably greater than 0.1 mm, preferably greater than 0.15 mm and less than 10 mm, preferably less than 5 mm, preferably less than 2.5 mm.
The sintered zirconia beads according to the invention are particularly well suited as agents for grinding, notably for wet grinding, or as agents for wet dispersion. The invention thus also relates to the use of a powder of beads according to the invention, or of beads manufactured according to a process according to the invention, as agents for grinding, notably for wet grinding, or as agents for wet dispersion.
The properties of the sintered zirconia beads according to the invention, and also their ease of production, make them suitable for other applications, notably for the treatment of surfaces (in particular by spraying the sintered beads according to the invention).
The invention thus also relates to a device chosen from a suspension, a grinder and surface treatment apparatus, said device including a powder of beads according to the invention.
Measurement Protocols
The following methods may be used to determine properties of sintered beads or mixtures of sintered beads, in particular according to the invention.
To determine the sphericity of a bead, the smallest and largest Ferret diameters are measured on a Camsizer XT machine sold by the company Horba.
The quantification of the crystalline phases present in the sintered beads is performed directly on the beads, said beads being bonded to a self-adhesive carbon pellet, so that the surface of said pellet is covered with a maximum amount of beads.
The crystalline phases present in the sintered beads are measured by X-ray diffraction, for example using an X′Pert PRO diffractometer machine from the company Panalytical, equipped with a copper XD tube. The diffraction pattern is acquired using this equipment, over an angular range 29 of between 5° and 100°, with a step size of 0.017°, and a counting time of 150 s/step. The front optics include a fixed used ¼° programmable divergence slit, Soller slits of 0.04 rad, a mask equal to 10 mm and a fixed anti-scattering slit of ½°. The sample is rotated on itself so as to limit preferential orientations. The rear optics include a fixed used ¼° programmable anti-scattering slit, a 0.04 rad Soller slit and an Ni filter.
The diffraction patterns are then analyzed qualitatively using the EVA software and the ICDD2016 database.
Once the phases present are highlighted, the diffraction patterns are analyzed quantitatively with the High Score Plus software by Rietveld refinement according to the following strategy:
The amount of amorphous phase present in the sintered beads is measured by X-ray diffraction, for example using an X′Pert PRO diffractometer from the company Panalytical equipped with a copper XD tube. The diffraction pattern is acquired using this equipment, in the same way as for the determination of the crystalline phases present in the beads, the analyzed sample being in the form of a powder. The method applied consists in adding a known amount of a totally crystalline standard, in this case a zinc oxide ZnO powder, in an amount equal to 20%, based on the mass of zinc oxide and the sample of ground sintered beads. The maximum size of the zinc oxide powder is 1 μm and the sintered beads are ground so as to obtain a maximum powder size of less than 40 μm.
The maximum ZnO particle size is entered in the High Score Plus software so as to limit the microabsorption effects.
The content of amorphous phase, as a percentage, is calculated using the following formula, where QZnO is the amount of ZnO determined from the diffraction pattern:
Content of amorphous phase=100*(100/(100−20))*(1−(20/QZnO)).
For example, if QZnO is equal to 22%, then the content of amorphous phase is equal to 100*(100/(100−20))*(1−(20/22))=11.4%.
The bulk density of the sintered beads is measured by hydrostatic weighing.
The unit cell parameters required for calculating the absolute density of the at least partially stabilized zirconia are determined by X-ray diffraction on the surface of the sample to be characterized (the sample not being ground into a powder) using a Brüker D8 Endeavor machine. The parameters required for the acquisition of the diffraction pattern are identical to those used for the acquisition of the diffraction pattern required for the quantification of the crystalline phases.
The unit cell parameters a and c are determined after performing a refinement of the diffraction pattern using the Fullprof software available at https//www.ill.eu/sites/fullprof/, using a pseudo-Voigt profile (with npr=5), the refined parameters being as follows:
the space group of the partially substituted quadratic zirconia unit cell being P 42/n m c (137), considered identical to that of the unsubstituted quadratic zirconia unit cell.
The chemical analysis of the sintered beads is measured by Inductively Coupled Plasma (ICP) spectrometry for the elements whose content does not exceed 0.5%. To determine the content of the other elements, a drop of the sintered bead material to be analyzed is made by melting said material and chemical analysis is then performed by X-ray fluorescence.
The average grain size of the sintered beads is measured via the “Mean Linear Intercept” method. A method of this type is described in the standard ASTM E1382. According to this standard, analysis lines are drawn on images of the sintered beads and then, along each analysis line, the lengths, known as “intercepts”, between two consecutive grain boundaries intersecting said analysis line are measured.
The mean length “l” of the intercepts “I” is then determined.
The intercepts are measured on images obtained by scanning electron microscopy of sintered bead samples, said sections having been polished beforehand to mirror quality and then thermally etched, at a temperature 50° C. below the sintering temperature, to reveal the grain boundaries. The magnification used to take the images is chosen so as to visualize approximately 100 grains in one image. Five images per sintered bead are taken.
The average grain size “d” of a sintered bead is given by the relationship: d=1.56×l′. This formula is taken from formula (13) of the article “Average Grain Size in Polycrystalline Ceramics” M. I. Mendelson, J. Am. Ceram. Soc. Vol. 52, No. 8, pages 443-446.
The standard deviation of the grain size distribution is 1.56 times the standard deviation of the intercept distribution “I”.
The specific surface area of a powder or particle mixture is measured via the BET (Brunauer Emmett Teller) method described in the Journal of the American Chemical Society, 60 (1938), pages 309 to 316.
The 10, 50 and 90 percentiles of the powders and particle mixtures are conventionally measured using an LA950V2 model laser granulometer sold by the company Horba. To determine the “planetary wear”, 20 ml (volume measured using a graduated cylinder) of test beads with a size of between 0.9 and 1.1 mm are weighed out (mass m0) and introduced into one of the four bowls lined with dense sintered alumina, having a capacity of 125 ml, of a Retsch brand PM400 fast planetary mill. 2.2 g of Presi silicon carbide (with a median size D50 of 23 μm) and 40 ml of water are added to the same bowl already containing the beads. The bowl is closed and rotated (planetary motion) at 400 rpm with the direction of rotation reversed every minute for 1.5 hours. The contents of the bowl are then washed over a 100 μm sieve so as to remove the residual silicon carbide and any material removed by wear during the grinding. After screening on a 100 μm sieve, the beads are dried in an oven at 100° C. for 3 hours and then weighed (mass m1). Said beads (mass m1) are again introduced into one of the bowls with a suspension of SiC (same concentration and amount as before) and undergo a new grinding cycle, identical to the previous one. The contents of the bowl are then washed over a 100 μm sieve so as to remove the residual silicon carbide any material removed by wear during the grinding. After screening on a 100 μm sieve, the beads are dried in an oven at 100° C. for 3 hours and then weighed (mass m2). Said beads (mass m2) are again introduced into one of the bowls with a suspension of SIC (same concentration and amount as before) and undergo a new grinding cycle, identical to the previous one. The contents of the bowl are then washed over a 100 μm sieve so as to remove the residual silicon carbide and any material removed by wear during the grinding. After screening on a 100 μm sieve, the beads are dried in an oven at 100° C. for 3 hours and then weighed (mass m3).
The planetary wear (PW) is expressed as a percentage (%) and is equal to the loss of mass of the beads relative to the initial mass of the beads, i.e.: 100 (m2−m3)/(m2); the PW result is given in Table 2.
Manufacturing Protocol
Sintered beads were prepared using:
The Table 1 below summarizes the particle mixtures of the examples obtained in step
In step a), the various powders were mixed and then wet co-milled until a particle mixture with a median size of less than 0.3 μm was obtained.
In step b), the particle mixture was then dried.
In step c), for each example, a starting feedstock consisting of an aqueous suspension including, as mass percentages on the basis of the solids, 1% of a carboxylic acid ester dispersant, 3% of a carboxylic acid dispersant and 0.4% of a gelling agent, namely a polysaccharide of the alginate family, was then prepared from the dry particle mixture obtained on conclusion of step b). A ball mill was used for this preparation so as to obtain good homogeneity of the starting feedstock: A solution containing the gelling agent was first formed. The particle mixture and the dispersants were successively added to water. The solution containing the gelling agent was then added. The mixture thus obtained was stirred for 8 hours. The particle size was checked using an LA950V2 model laser granulometer sold by the company Horba (median size<0.3 μm), water was then added in a determined amount to obtain an aqueous suspension with a solids content of 68% and a viscosity, measured using a Brookfield viscometer with the LV3 spindle at a speed equal to 20 rpm, of less than 5000 centipoises. The pH of the suspension was then about 9 after optional adjustment with a strong base.
In step d), the suspension was forced through a calibrated hole and at a flow rate to obtain, after sintering, beads about 1 mm in size for these examples. The drops of suspension fell into a gelling bath based on an electrolyte (divalent cation salt), reacting with the gelling agent.
The raw beads were collected, washed with water in step e), and then dried at 80° C. in step f) to remove the moisture.
In step g), the beads were then transferred into a sintering furnace where they were sintered in the following cycle:
Results
The results obtained are collated in table 2 below.
The sintered beads of the examples consist substantially entirely of oxides and have an amount of amorphous phase of less than 5%/by mass.
The bead powders in the examples have an average sphericity of greater than 0.9.
Example 2, outside the invention, is representative of the prior art.
Example 1, outside the invention, is given to serve as a basis for comparison with Example 3 according to the invention, the total molar content of Y2O3+CeO2 of these two examples being substantially identical.
Comparison of Examples 1 and 2, outside the invention, and 3 according to the invention, shows that the beads according to Example 3 have 18.7% and 23.5% less planetary wear PW than that of Examples 1 and 2, respectively.
As now emerges clearly, the invention provides a sintered zirconia bead with noteworthy planetary wear PW.
The inventors also found that the beads according to the invention have high resistance to degradation in a hot liquid medium, in particular when they are in contact with water above 80° C., such conditions being referred to as “hydrothermal conditions”. They are thus particularly suitable for the use of beads as a medium for wet grinding, notably for the fine grinding of mineral, inorganic or organic materials. In this application, the beads are dispersed in an aqueous medium or a solvent, the temperature of which may exceed 80° C., while remaining preferably below 150° C., and undergo friction by contact with the material to be ground, by mutual contact and by contact with the members of the grinder.
Needless to say, the invention is not, however, limited to the isolated embodiments described previously.
| Number | Date | Country | Kind |
|---|---|---|---|
| FR2003340 | Apr 2020 | FR | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/EP2021/058816 | 4/2/2021 | WO |
