CN113105260A - Porous ceramic for low-thermal-conductivity high-porosity electronic cigarette atomization core and preparation method thereof - Google Patents
Porous ceramic for low-thermal-conductivity high-porosity electronic cigarette atomization core and preparation method thereof Download PDFInfo
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Abstract
The invention discloses porous ceramic for an electronic cigarette atomization core with low thermal conductivity and high porosity and a preparation method thereof, and particularly relates to the field of ceramic materials, wherein the used raw materials comprise, by mass, 1-15% of mullite, 40-60% of diatomite, 5-25% of alumina hollow spheres, 1-5% of foam carbon powder, 10-15% of a pore-forming agent, 1-8% of an inorganic binder and 0.1-0.5% of a retarder. According to the invention, the diatomite, the mullite and the foam dense carbon in the raw materials are in porous structures, the alumina hollow spheres are in hollow structures, the pore-forming agent can also make pores for the porous ceramic, meanwhile, the mullite can also play a role of aggregate, and the prepared porous ceramic atomizing core has lower thermal conductivity and higher apparent porosity by reasonable matching according to the proportion.
Description
Technical Field
The embodiment of the invention relates to the field of ceramic materials, in particular to porous ceramic for an electronic cigarette atomization core with low thermal conductivity and high porosity and a preparation method thereof.
Background
The porous ceramic has high porosity, good oil absorption and good liquid storage performance, and the ceramic itself is high temperature resistant and is not easy to generate scorch, so the porous ceramic is widely used in electronic cigarette atomizers. However, the ceramic core for electronic smoke in the current market is small in size, the ceramic atomizing core is long in heating time and short in time interval in the continuous smoking process, and the ceramic atomizing core in the current market still has the problem of core pasting due to overhigh heat conductivity coefficient of the atomizing core, so that the development of a porous ceramic material with high porosity and low heat conductivity is urgently needed, and the porous ceramic material has the characteristics of good oil absorption, low heat conductivity and the like, and can prevent the core pasting from improving the smoking taste.
Disclosure of Invention
Therefore, the embodiment of the invention provides the porous ceramic for the electronic cigarette atomization core with low thermal conductivity and high porosity and the preparation method thereof.
In order to achieve the above object, the embodiments of the present invention provide the following technical solutions: the porous ceramic for the electronic cigarette atomization core with low thermal conductivity and high porosity comprises, by mass, 1-15% of mullite, 40-60% of diatomite, 5-25% of alumina hollow spheres, 1-5% of foam carbon powder, 10-15% of pore-forming agent, 1-8% of inorganic binder and 0.1-0.5% of retarder.
Further, the raw material particle size distribution is as follows: 0.5-5 mu m of mullite D50, 1-20 mu m of diatomite D50, 60-120 mu m of alumina hollow sphere D50, 5-25 mu m of foam carbon D50, 0.1-10 mu m of pore-forming agent D50 and 0.5-5 mu m of inorganic binder D50.
Further, the inorganic binder comprises at least one of aluminum phosphate and silicate.
Further, the pore-forming agent comprises at least one of acrylic powder, phenolic resin powder and epoxy resin powder.
Further, the retarder comprises at least one of lignosulfonate and derivatives thereof, organic phosphonate and low molecular weight cellulose.
The invention also comprises a preparation method of the porous ceramic for the low-thermal-conductivity high-porosity electronic cigarette atomization core, which comprises the following specific steps:
step S1: mixing the raw materials into a standby material;
step S2: adding water into the standby materials and uniformly stirring;
step S3: preparing the uniformly stirred standby materials into a blank;
step S4: and sintering the green body in a sintering furnace for 1-5 hours to obtain porous ceramic, and then cutting the green body to obtain the porous ceramic atomizing core.
Further, the step of mixing the raw materials to form the spare material in step S1 includes: and uniformly mixing the raw materials to form ceramic powder with good consistency.
Further, the water used in step S2 is deionized water.
Further, the method of manufacturing the spare material into the blank is slip casting in step S3.
Further, the sintering temperature is 650 ℃ to 800 ℃ in step S4.
The embodiment of the invention has the following advantages:
in the raw materials of the invention, the diatomite, the mullite and the foam dense carbon are in porous structures, the alumina hollow spheres are in hollow structures, the pore-forming agent can also make pores for the porous ceramics, and the mullite can also play a role of aggregate. Dissolving the retarder in deionized water, adding the ceramic raw material, the inorganic binder and the pore-forming agent, slip casting, demolding, sintering in a sintering furnace, removing water in the blank during sintering, and obtaining high initial lightness of the blank. And (3) continuing heating to burn out the pore-forming agent and foam carbon, forming a large number of continuous through holes in the porous ceramic, and finally heating to the water loss temperature of the inorganic binder crystal water, so that the strength of the porous ceramic is further increased. The porous ceramic atomizing core prepared by the preparation method of the porous ceramic atomizing core has lower thermal conductivity and higher apparent porosity by reasonably matching according to the proportion.
Drawings
In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below. It should be apparent that the drawings in the following description are merely exemplary, and that other embodiments can be derived from the drawings provided by those of ordinary skill in the art without inventive effort.
The structures, ratios, sizes, and the like shown in the present specification are only used for matching with the contents disclosed in the specification, so as to be understood and read by those skilled in the art, and are not used to limit the conditions that the present invention can be implemented, so that the present invention has no technical significance, and any structural modifications, changes in the ratio relationship, or adjustments of the sizes, without affecting the effects and the achievable by the present invention, should still fall within the range that the technical contents disclosed in the present invention can cover.
FIG. 1 is a flow chart of the preparation process provided by the present invention;
Detailed Description
The present invention is described in terms of particular embodiments, other advantages and features of the invention will become apparent to those skilled in the art from the following disclosure, and it is to be understood that the described embodiments are merely exemplary of the invention and that it is not intended to limit the invention to the particular embodiments disclosed. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
As shown in fig. 1, the porous ceramic for the low-thermal-conductivity high-porosity electronic cigarette aerosol core of the embodiment comprises, by mass, 1% to 15% of mullite, 40% to 60% of diatomite, 5% to 25% of alumina hollow spheres, 1% to 5% of carbon foam, 10% to 15% of pore-forming agent, 1% to 8% of inorganic binder, and 0.1% to 0.5% of retarder.
The preparation method of the porous ceramic for the electronic cigarette atomization core with low thermal conductivity and high porosity comprises the following specific steps:
step S1: mixing the raw materials into a standby material.
Specifically, the process of mixing the raw materials into the standby materials comprises the following steps: mullite, diatomite, foam carbon, alumina hollow spheres, inorganic binder, pore-forming agent and retarder are mixed into raw materials with good consistency.
Specifically, the mixing method adopts one or more of dry ball milling mixing, double-motion mixer mixing, three-dimensional mixer mixing, V-shaped mixer mixing and the like.
Specifically, the mixing time is 1-3 hours.
Wherein the raw materials comprise the following components in percentage by mass: 1 to 15 percent of mullite, 40 to 60 percent of diatomite, 5 to 25 percent of alumina hollow spheres, 1 to 5 percent of foam carbon powder, 10 to 15 percent of pore-forming agent, 1 to 8 percent of inorganic binder and 0.1 to 0.5 percent of retarder.
The inorganic binder comprises at least one of aluminum phosphate and silicate; the pore-forming agent comprises at least one of acrylic powder, phenolic resin powder and epoxy resin powder; the retarder comprises at least one of lignosulfonate and derivatives thereof, organic phosphonate and low molecular weight cellulose.
Further, the inorganic binder D50 was 0.5 to 5 μm. The inorganic binder with a lower particle size is more suitable for uniform mixing and the performance of the binding action of the formed hydrated slurry, so that the strength of the whole ceramic atomizing core is more uniform.
The diatomite, the foam carbon and the mullite are all porous structural substances, wherein the diatomite and the mullite are used as main body structures of the ceramic atomizing core, so that the ceramic presents a porous structure. The foam carbon has larger pore diameter, absorbs other raw materials into the pores during hydration, the foam carbon is oxidized and burned off during subsequent sintering, and the ceramic raw materials in the pores are reserved to form a through-hole structure. The diatomite, the mullite and the foam carbon with reasonable particle size matching can ensure that the porous ceramic atomizing core has more uniform apparent porosity and higher strength.
The alumina hollow sphere is a common refractory material raw material and has the advantages of high temperature resistance, low thermal conductivity and the like, the alumina hollow sphere D50 is 60-120 mu m, and the alumina hollow sphere with larger particle size not only plays a role in supporting a porous ceramic framework, but also can provide more particle gaps, so that the strength of the ceramic atomization core is improved, and the thermal conductivity of the porous ceramic is reduced.
Pore formers can expand in volume during low temperature sintering and then be removed by oxidation during continued sintering. Specifically. The pore-forming agent is selected from one or more of acrylic powder, phenolic resin powder and epoxy resin powder. Further, the pore-forming agent D50 was 0.1 to 10 μm. Pore-forming agent with proper particle size can not only make the porous
The ceramic atomization core is provided with the holes with proper sizes and shapes, so that the porous ceramic atomization core is favorable for reducing the thermal conductivity of the porous ceramic while having higher apparent porosity, the oil guide performance of the atomization core is increased, and the problem that the pore diameter of the porous ceramic in the diatomite is small can be solved.
Step S2: and adding water into the mixture, stirring, and performing grouting forming.
Specifically, the method for manufacturing the mixture into the green body is slip casting.
Further, deionized water is used for the preparation of the grouting slurry.
Step S3: and sintering the green body in a sintering furnace.
Specifically, the sintering temperature rise process is as follows: heating to 240-300 ℃ at the rate of 30-60 ℃/h, keeping the temperature for 0.5-1h, continuously heating to 450-800 ℃ at the rate of 25-50 ℃/h, keeping the temperature for 0-2h, and heating to 650-800 ℃ at the rate of 100-150 ℃/h, keeping the temperature for 1-5 h.
Specifically, the maximum sintering temperature was 650-.
Specifically, the high-temperature sintering heat preservation time is 1-5 h.
The porous ceramic is dried at low temperature, the pore-forming agent and the carbon foam are burnt at medium temperature, and the inorganic binder crystal water is removed at high temperature, so that the porous ceramic has high strength, low thermal conductivity and high porosity after the sintering process.
The preparation method of the porous ceramic atomizing core has at least the following advantages:
(1) according to the preparation method of the porous ceramic, the diatomite and the mullite in the raw materials are in a porous structure, the pore-forming agent and the foam carbon can be used for making pores for the porous ceramic, and meanwhile, the porous ceramic atomizing core prepared by the method has high strength and low thermal conductivity by reasonable matching according to the proportion.
(2) The inorganic binder has quick-drying performance, so that the slip casting blank can quickly obtain initial strength, a high-temperature sintering step can be omitted for the ceramic atomizing core, higher overall strength can be obtained by sintering at lower temperature, and the sintering period is greatly shortened.
(3) The alumina hollow sphere is a common refractory material raw material and has the advantages of high temperature resistance, low thermal conductivity and the like, the alumina hollow sphere D50 is 60-120 mu m, and the alumina hollow sphere with larger particle size not only plays a role in supporting a porous ceramic framework, but also can provide more particle gaps, so that the strength of the ceramic atomization core is improved, and the thermal conductivity of the porous ceramic is reduced.
(4) By controlling the distribution of the components D50 to distribute the particle sizes of the components, the ceramic atomizing core has holes with proper sizes and good multi-structure, which is beneficial to improving the strength and the apparent porosity of the ceramic atomizing core and reducing the thermal conductivity of the atomizing core.
The porous ceramic prepared by the method enables the porous ceramic atomizing core to have high strength and low thermal conductivity.
Example 1
The preparation process of the porous ceramic atomizing core of the embodiment is as follows:
(1) according to the table 1, the raw materials are obtained by weighing the components according to the mass percentage (abbreviated as content in the table). Wherein, the mullite D50 is 2 μm; diatomaceous earth D50 was 15 μm; the alumina hollow ball D50 is 80 μm; the foam carbon D50 is 15 μm, the pore-forming agent D50 is 8 μm, and the inorganic binder D50 is 1.5 μm. Adding into a ball mill or other mixing equipment for dry mixing for 2 hours.
(2) And uniformly mixing and stirring the mixed raw materials according to the liquid-solid ratio of 1.2:1 to obtain the ceramic slurry.
(3) And (3) performing grouting forming on the ceramic slurry to obtain a square block-shaped porous ceramic blank.
(4) And sintering the ceramic blank in a sintering furnace to obtain a porous ceramic atomizing core product. Specifically, the drying temperature is 260 ℃, the pore-forming agent and foam carbon burning-off temperature is 480 ℃, and the sintering temperature is 750 ℃.
Example 2
The preparation process of the porous ceramic atomizing core of the embodiment is as follows:
(1) according to the table 1, the raw materials are obtained by weighing the components according to the mass percentage. Wherein, the mullite D50 is 4 μm; diatomaceous earth D50 was 10 μm; the alumina hollow ball D50 is 100 μm; 10 μm for carbon foam D50, 6 μm for pore former D50, and 3 μm for inorganic binder D50. Adding into a ball mill or other mixing equipment for dry mixing for 0.5 hour.
(2) And uniformly mixing and stirring the mixed raw materials according to the liquid-solid ratio of 1:1 to obtain the ceramic slurry.
(3) And (3) performing grouting forming on the ceramic slurry to obtain a square block-shaped porous ceramic blank.
(4) And sintering the ceramic blank in a sintering furnace to obtain a porous ceramic atomizing core product. Specifically, the drying temperature is 240 ℃, the pore-forming agent and foam carbon burning-off temperature is 500 ℃, and the sintering temperature is 700 ℃.
Example 3
The preparation process of the porous ceramic atomizing core of the embodiment is as follows:
(1) according to the table 1, the raw materials are obtained by weighing the components according to the mass percentage. Wherein, the mullite D50 is 5 μm; diatomaceous earth D50 was 20 μm; the alumina hollow ball D50 is 120 μm; 20 μm for foamed carbon D50, 5 μm for pore former D50, and 5 μm for inorganic binder D50. Adding into a ball mill or other mixing equipment for dry mixing for 2 hours.
(2) And uniformly mixing and stirring the mixed raw materials according to the liquid-solid ratio of 1:1 to obtain the ceramic slurry.
(3) And (3) performing grouting forming on the ceramic slurry to obtain a square block-shaped porous ceramic blank.
(4) And sintering the ceramic blank in a sintering furnace to obtain a porous ceramic atomizing core product. Specifically, the drying temperature is 280 ℃, the pore-forming agent and foam carbon burning-off temperature is 450 ℃, and the sintering temperature is 800 ℃.
Comparative example 1
The preparation process of the porous ceramic of comparative example 1 is substantially the same as that of example 1, except that the composition of the raw materials in step (1) is different, the porous ceramic does not contain alumina hollow spheres, and the raw materials of comparative example 3 are, in terms of mass percentage: 9% of mullite, 65% of diatomite, 5% of foam carbon powder, 15% of pore-forming agent, 8% of inorganic binder and 0.4% of retarder.
Comparative example 2
The preparation process of the porous ceramic of comparative example 2 is substantially the same as that of example 1, except that the composition of the raw materials in step (1) is different, the porous ceramic does not contain carbon foam and alumina hollow spheres, and the raw materials of comparative example 1 are as follows by mass percent: 10% of mullite, 70% of diatomite, 13% of pore-forming agent, 7% of inorganic binder and 0.4% of retarder.
TABLE 1 ingredient content of each component
Testing
The apparent porosity of the porous ceramics of examples 1 to 3 and comparative examples 1 to 2 was respectively tested according to the GBT1966-1996 porous ceramic apparent porosity and volume-weight test method; the heat conductivity coefficients of the porous ceramics of examples 1-3 and comparative examples 1-2 were respectively tested according to the experimental method for heat conductivity coefficient of GB/T17911.8-2002 refractory ceramic fiber products. The apparent porosity and thermal conductivity of the porous ceramics of examples 1 to 3 and comparative examples 1 to 2 are shown in Table 2.
As can be seen from Table 2, the porous ceramics of examples 1 to 3 have an apparent porosity of at least 54%, a thermal conductivity of at most 225W/(m.K), and excellent overall properties, because the alumina hollow spheres have excellent heat insulating properties, and the apparent porosity of the porous ceramics is significantly increased and the thermal conductivity is reduced by forming through holes after firing with additional carbon foam.
The technical features of the embodiments described above may be arbitrarily combined, and for the sake of brevity, all possible combinations of the technical features in the embodiments described above are not described, but should be considered as being within the scope of the present specification as long as there is no contradiction between the combinations of the technical features.
The above-mentioned embodiments only express several embodiments of the present invention, and the description thereof is more specific and detailed, but not construed as limiting the scope of the invention. It should be noted that, for a person skilled in the art, several variations and modifications can be made without departing from the inventive concept, which falls within the scope of the present invention. Therefore, the protection scope of the present patent shall be subject to the appended claims.
Claims (10)
1. The porous ceramic for the electronic cigarette atomization core with low thermal conductivity and high porosity is characterized in that the used raw materials comprise, by mass, 1-15% of mullite, 40-60% of diatomite, 5-25% of alumina hollow spheres, 1-5% of foam carbon powder, 10-15% of pore-forming agent, 1-8% of inorganic binder and 0.1-0.5% of retarder.
2. The porous ceramic for the low thermal conductivity high porosity electronic aerosolization core of claim 1, wherein the feedstock particle size distribution is as follows: 0.5-5 mu m of mullite D50, 1-20 mu m of diatomite D50, 60-120 mu m of alumina hollow sphere D50, 5-25 mu m of foam carbon D50, 0.1-10 mu m of pore-forming agent D50 and 0.5-5 mu m of inorganic binder D50.
3. The porous ceramic for a low thermal conductivity high porosity electronic aerosolization core of claim 1 wherein the inorganic binder comprises at least one of an aluminophosphate, a silicate.
4. The porous ceramic for the low-thermal-conductivity high-porosity electronic aerosolization core of claim 1, wherein the pore-forming agent comprises at least one of an acrylic powder, a phenolic resin powder, and an epoxy resin powder.
5. The porous ceramic for the low thermal conductivity high porosity electronic aerosolization core of claim 1, wherein the set retarder comprises at least one of lignosulfonate and derivatives thereof, organophosphonate, low molecular weight cellulose.
6. The porous ceramic for the low-thermal-conductivity high-porosity electronic aerosolization core according to any one of claims 1-5, further comprising a preparation method of the porous ceramic for the low-thermal-conductivity high-porosity electronic aerosolization core, comprising the following specific steps:
step S1: mixing the raw materials into a standby material;
step S2: adding water into the standby materials and uniformly stirring;
step S3: preparing the uniformly stirred standby materials into a blank;
step S4: and sintering the green body in a sintering furnace for 1-5 hours to obtain porous ceramic, and then cutting the green body to obtain the porous ceramic atomizing core.
7. The method of preparing a porous ceramic for a low thermal conductivity high porosity electronic aerosolization core of claim 6, wherein the step of mixing the raw materials to form a stock in step S1 comprises: and uniformly mixing the raw materials to form ceramic powder with good consistency.
8. The method of preparing a porous ceramic for a low thermal conductivity high porosity electronic aerosolization core of claim 6, wherein the water used in step S2 is deionized water.
9. The method for preparing a porous ceramic for a low thermal conductivity and high porosity electronic aerosolization core according to claim 6, wherein the method of forming the stock into a green body is slip casting in step S3.
10. The method of preparing a porous ceramic for a low thermal conductivity high porosity electronic aerosolization core of claim 6, wherein the sintering temperature is 650-800 ℃ in step S4.
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