Ceramic material and preparation method thereof, ceramic heating core and liquid heating device

Abstract

The invention belongs to the technical field of materials, and particularly relates to a ceramic material and a preparation method thereof, a ceramic heating core and a liquid heating device. The preparation method of the ceramic material comprises the following steps: preparing a titanium source, an aluminum source and a magnesium source into mixed powder; wherein the titanium source comprises TiO2, and the magnesium source comprises Mg (OH) 2, 4MgCO3. Mg (OH) 2. 6H2O, MgCl2. 6H2O and MgO; and pressing the mixed powder into a green body, drying the green body, and calcining the green body at the temperature of 1000-1500 DEG C for 1.1-3 hours to obtain the ceramic material with a porous structure. The raw materials do not contain heavy metal, and the porosity, mechanical strength, high temperature resistance and the like of the ceramic material are improved through compounding use of multiple raw materials and specific calcination conditions. The heavy metal migration risk of the ceramic material is reduced, and the high-temperature tolerance performance and the safety performance of the ceramic material are improved.

Description

Technical Field

[0001] This application belongs to the field of materials technology, and in particular relates to a ceramic material and its preparation method, as well as a ceramic heating core and a liquid heating device. Background Technology

[0002] Traditional ceramic heating cores, in pursuit of specific physical properties (such as strength, toughness, and temperature resistance), often fail to adequately consider the biocompatibility of raw materials, neglecting to eliminate substances potentially harmful to human health. They may use compounds or additives containing heavy metals, such as specific heavy metal oxides as calcination aids, stabilizers, or reinforcing phases. During high-temperature heating, these heavy metal elements may migrate from the ceramic matrix, posing a risk of heavy metal ions migrating into aerosols and being inhaled, thus posing a potential threat to user health. Furthermore, some ceramic heating core materials are prone to high-temperature intolerance issues such as high-temperature deformation and structural creep under long-term thermal cycling loads. This leads to changes in the microporous structure of the ceramic heating core, poor contact with the metal electrodes, and consequently affects heating efficiency, taste consistency, and product lifespan.

[0003] Therefore, it is urgent to solve the safety problems caused by the high-temperature insensitivity and heavy metal migration of existing ceramic heating elements. Summary of the Invention

[0004] The purpose of this application is to provide a ceramic material and its preparation method, as well as a ceramic heating core and a liquid heating device, which aim to solve to some extent the safety problems of high temperature intolerance and heavy metal migration of existing ceramic heating cores.

[0005] To achieve the above-mentioned objectives, the technical solution adopted in this application is as follows: In a first aspect, this application provides a method for preparing a ceramic material, comprising the following steps: Titanium source, aluminum source and magnesium source are made into mixed powder; wherein, the titanium source includes TiO2, and the magnesium source includes Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, MgCl2·6H2O and MgO; The mixed powder is pressed into a green body, which is then dried and calcined at 1000℃~1500℃ for 1.1h~3h to obtain a porous ceramic material.

[0006] In some possible implementations, the titanium source includes anatase titanium dioxide.

[0007] In some possible implementations, the aluminum source includes at least one of Al(NO3)3·6H2O, Al(OCH(CH3)2)3, Al2O3, and Al2(SO4)3.

[0008] In some possible implementations, the aluminum source includes Al(NO3)3·6H2O.

[0009] In some possible implementations, the molar ratio of the titanium source, the aluminum source and the magnesium source is (85~95):(2~5):(5~10).

[0010] In some possible implementations, the molar ratio of Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, MgCl2·6H2O and MgO in the magnesium source is (0.8~1.2):(0.8~1.2):(0.8~1.2):(0.8~1.2).

[0011] In some possible implementations, the pressure used to press the mixed powder into a green body is 50 MPa to 60 MPa.

[0012] In some possible implementations, the drying process includes drying at a temperature of 50°C to 80°C for 4 to 8 hours, followed by drying at a temperature of 100°C to 130°C for 12 to 24 hours.

[0013] In some possible implementations, the heating rate step of the calcination treatment includes: heating to 1000°C at a rate of 5°C / min to 8°C / min, and then adjusting the heating rate to 2°C / min to 4°C / min.

[0014] In some possible implementations, the calcination temperature is 1200℃~1500℃ and the calcination time is 1.5h~3h.

[0015] Secondly, this application provides a ceramic material, which is prepared by the above-described preparation method.

[0016] In some possible implementations, the main crystalline phase of the ceramic material includes TiO2, and the auxiliary crystalline phase includes at least one of aluminum titanate, magnesium aluminate, and magnesium titanate.

[0017] In some possible implementations, the apparent porosity of the ceramic material is 30% to 45%.

[0018] In some possible implementations, the bulk density of the ceramic material is 1.95 g / cm³. 3 ~2.5g / cm 3 .

[0019] In some possible implementations, the cold fracture strength of the ceramic material is 27 MPa to 50 MPa.

[0020] In some possible implementations, the apparent porosity of the ceramic material is 30% to 40%; the bulk density of the ceramic material is 2.4 g / cm³. 3 ~2.5g / cm 3 The cold crushing strength of the ceramic material is 40MPa~50MPa.

[0021] Thirdly, this application provides a ceramic heating core, which includes ceramic materials prepared by the above method and / or the above-mentioned ceramic materials.

[0022] In some possible implementations, the ceramic heating core is made of the ceramic material.

[0023] Fourthly, this application provides a liquid heating device, which includes the aforementioned ceramic heating core.

[0024] The method for preparing ceramic materials provided in the first aspect of this application uses titanium, aluminum, and magnesium sources as raw materials. All selected raw materials are free of heavy metals, eliminating the introduction of harmful elements at the source and effectively solving the risk of heavy metal migration that may exist in traditional ceramic heating cores, significantly improving the product's biosafety. The method also includes magnesium sources such as Mg(OH)₂, 4MgCO₃·Mg(OH)₂·6H₂O, MgCl₂·6H₂O, and MgO. By using multiple magnesium compounds as magnesium sources, their differences in thermal decomposition behavior and chemical properties allow them to exert synergistic effects at different stages of the calcination process. The decomposition of Mg(OH)₂ and 4MgCO₃·Mg(OH)₂·6H₂O occurs in a relay fashion over time, MgCl₂·6H₂O improves processability, and MgO provides high-temperature stability. This combination ensures that gases are released in stages and in a relay manner during calcination. This synergistic effect is beneficial for forming a uniform, interconnected, and more controllable three-dimensional porous network within the ceramic body. Meanwhile, the aluminum source, acting as a calcination aid and stabilizer, decomposes at high temperatures, and the resulting active components react with the titanium and magnesium components in a solid-phase reaction, promoting the formation of highly thermally stable phases such as spinel. This helps strengthen the ceramic framework, improve the structural stability of the ceramic material, and enhance its high-temperature resistance. The mixed powder is pressed into a green body, dried, and then calcined at 1000℃~1500℃ for 1.1h~3h. Under these conditions, the raw materials can be ensured to react fully and form a stable crystalline phase, while avoiding excessive pore closure or abnormal grain growth caused by excessively high temperatures or prolonged calcination. This ensures that the final ceramic material possesses sufficient mechanical strength while maintaining an appropriate apparent porosity, thereby improving the high-temperature resistance of the ceramic material.

[0025] The ceramic material provided in the second aspect of this application is prepared by the method described in the first aspect, and therefore inherits and embodies all the microstructural features and macroscopic performance advantages brought about by this preparation method. This ceramic material does not contain harmful metallic substances, reducing the risk of migration of harmful substances at high temperatures and ensuring the safety of the material. Thanks to the synergistic and phased decomposition of various magnesium compounds during heat treatment, and the sintering-aiding and stabilizing effect of the aluminum source, a uniform, interconnected, and more controllable three-dimensional porous network is formed inside the ceramic material, ensuring its liquid conductivity. Furthermore, thanks to sufficient sintering and the formation of reinforcing phases, the ceramic material possesses both sufficient mechanical strength and maintains suitable apparent porosity, exhibiting good high-temperature resistance and resistance to deformation.

[0026] The ceramic heating core provided in this application contains the aforementioned ceramic material, which is free of heavy metals, has high porosity, and is resistant to high temperatures and is not easily deformed. Therefore, it not only ensures the liquid conductivity of the ceramic heating core, but also significantly reduces the risk of heavy metal migration caused by high-temperature heating, thereby improving safety and reliability.

[0027] The liquid heating device provided in this application improves the performance of the liquid heating device in terms of safety, heating stability and reliability by using a ceramic heating core with the characteristics of good structural stability, no heavy metals, high porosity and good high temperature resistance. Attached Figure Description

[0028] To more clearly illustrate the technical solutions in the embodiments of this application, the drawings used in the description of the embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are only some embodiments of this application. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0029] Figure 1 This is a schematic flowchart of the method for preparing ceramic materials provided in the embodiments of this application; Figure 2 This is an electron microscope image of the ceramic material provided in Embodiment 1 of this application; Figure 3 This is an electron microscope image of the ceramic material provided in Embodiment 2 of this application; Figure 4 This is an electron microscope image of the ceramic material provided in Embodiment 3 of this application; Figure 5 This is an electron microscope image of the ceramic material provided in Embodiment 4 of this application; Figure 6 This is an electron microscope image of the ceramic material provided in Embodiment 5 of this application; Figure 7 This is an electron microscope image of the ceramic material provided in Embodiment 6 of this application; Figure 8 This is an electron microscope image of the ceramic material provided in Embodiment 7 of this application; Figure 9 This is an electron microscope image of the ceramic material provided in Embodiment 8 of this application; Figure 10 This is an electron microscope image of the ceramic material provided in Comparative Example 1 of this application; Figure 11 This is an electron microscope image of the ceramic material provided in Comparative Example 2 of this application; Figure 12 This is an electron microscope image of the ceramic material provided in Comparative Example 3 of this application; Figure 13 This is an electron microscope image of the ceramic material provided in Comparative Example 4 of this application; Figure 14 This is an electron microscope image of the ceramic material provided in Comparative Example 8 of this application; Figure 15 This is an electron microscope image of the ceramic material provided in Comparative Example 14 of this application. Detailed Implementation

[0030] To make the technical problems, technical solutions, and beneficial effects of this application clearer, the following detailed description is provided in conjunction with embodiments. It should be understood that the specific embodiments described herein are merely illustrative and not intended to limit the scope of this application.

[0031] In this application, the term "and / or" describes the relationship between related objects, indicating that three relationships can exist. For example, A and / or B can represent: A existing alone, A and B existing simultaneously, or B existing alone. A and B can be singular or plural. The character " / " generally indicates that the preceding and following related objects have an "or" relationship.

[0032] In this application, "at least one" means one or more, and "more than one" means two or more. "At least one of the following" or similar expressions refer to any combination of these items, including any combination of single or multiple items. For example, "at least one of a, b or c", or "at least one of a, b and c", can both mean: a, b, c, ab (i.e., a and b), ac, bc, or abc, where a, b, and c can be single or multiple.

[0033] It should be understood that in the various embodiments of this application, the order of the above processes does not imply the order of execution. Some or all steps may be executed in parallel or sequentially. The execution order of each process should be determined by its function and internal logic, and should not constitute any limitation on the implementation process of the embodiments of this application.

[0034] The terminology used in the embodiments of this application is for the purpose of describing particular embodiments only and is not intended to be limiting of this application. The singular forms "a" and "the" as used in the embodiments of this application and the appended claims are also intended to include the plural forms, unless the context clearly indicates otherwise.

[0035] The weights of the relevant components mentioned in the embodiments of this application can refer not only to the specific content of each component, but also to the proportional relationship between the weights of the components. Therefore, any scaling up or down of the content of the relevant components according to the embodiments of this application is within the scope disclosed in the embodiments of this application. Specifically, the mass described in the embodiments of this application can be a mass unit known in the chemical industry, such as µg, mg, g, or kg.

[0036] The terms "first" and "second" are used for descriptive purposes only, to distinguish objects, such as substances, from one another, and should not be construed as indicating or implying relative importance or implicitly specifying the number of technical features indicated. For example, without departing from the scope of the embodiments of this application, "first XX" may also be referred to as "second XX," and similarly, "second XX" may also be referred to as "first XX." Thus, features defined with "first" and "second" may explicitly or implicitly include one or more of that feature.

[0037] The term "apparent porosity," abbreviated as AP, refers to the percentage of the volume of open pores in a material to its total volume.

[0038] The term "bulk density," abbreviated as BD, refers to the ratio of a material's mass to its total volume (including solids, open pores, and closed pores).

[0039] The term "cold crushing strength" (CCS) refers to the maximum compressive stress a material can withstand at room temperature until it breaks.

[0040] In the field of liquid heating devices, porous ceramic heating cores are widely used due to their excellent liquid conductivity and stable heating performance. However, existing ceramic heating cores and their manufacturing technologies still have many shortcomings that urgently need to be addressed: Regarding material safety: To meet the mechanical strength and temperature resistance requirements of ceramic heating elements, compounds or additives containing heavy metals may be used in their raw materials. For example, specific metal oxides may be used as calcination aids, stabilizers, or reinforcing phases. This leads to a risk that heavy metal ions may migrate into aerosols and be inhaled by the human body during high-temperature heating, posing a potential threat to the user's health.

[0041] Regarding material properties: Ceramic heating cores need to withstand repeated cycles of instantaneous high temperatures and cooling during operation, which places extremely high demands on the thermal stability of the materials. Some existing ceramic heating core materials may experience softening, deformation, or slight plastic flow (creep) under long-term high temperatures, leading to changes in the microstructure of the ceramic heating core and affecting heating efficiency and lifespan. Furthermore, high-temperature deformation may cause poor contact between the ceramic heating core and the metal electrode, or cracking of the ceramic body, affecting the reliability and consistency of the product.

[0042] In terms of manufacturing: traditional manufacturing processes rely on raw materials that may be expensive or have limited availability, and the manufacturing process is often quite complex, involving energy-intensive and precisely controlled processes such as high-temperature calcination. This not only increases production costs but also burdens the environment, while also hindering improvements in production efficiency and product yield.

[0043] Therefore, developing a ceramic heating core that can balance safety, high-temperature stability, and simple and cost-effective manufacturing process has become an urgent technical challenge to be solved in this field.

[0044] Based on the above considerations, the first aspect of this application provides a method for preparing a ceramic material, as shown in the attached figure. Figure 1 As shown, it includes the following steps: S10. Prepare a mixed powder from titanium source, aluminum source and magnesium source; wherein the titanium source includes TiO2 and the magnesium source includes Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, MgCl2·6H2O and MgO; S20. Press the mixed powder into a green body, dry the green body, and then calcine it at a temperature of 1000℃~1500℃ for 1.1h~3h to obtain a porous ceramic material.

[0045] The method for preparing ceramic materials provided in the first aspect of this application uses titanium, aluminum, and magnesium sources as raw materials. These raw materials are all free of heavy metals, eliminating the introduction of harmful elements at the source and effectively solving the risk of heavy metal migration that may exist in traditional ceramic heating cores, significantly improving the product's biosafety. The magnesium source includes Mg(OH)₂, 4MgCO₃·Mg(OH)₂·6H₂O, MgCl₂·6H₂O, and MgO. Mg(OH)₂ has a low decomposition temperature (~350℃), decomposing to produce MgO and H₂O. Mg(OH)₂ is used to enhance pore formation and reactivity at low temperatures; its early decomposition provides initial pores for the green body and generates highly active MgO, participating in the solid-phase reaction earlier. 4MgCO₃·Mg(OH)₂·6H₂O is a complex basic salt that also contains OH⁻. - and CO3² -MgCl2·6H2O is a functional complex of Mg(OH)2 and pure magnesium carbonate. Its decomposition process is complex and gradual (from 100℃ to over 500℃), continuously releasing H2O and CO2. This gradual decomposition helps form uniform, fine pores over a wide temperature range and avoids cracking of the green body caused by a sudden large release of gas. MgCl2·6H2O is hygroscopic and promotes the wetting and uniform distribution of other powders during mixing. Its decomposition products contain HCl gas, which may have a slight corrosive and activating effect on local calcination. MgO, as a direct raw material, does not require decomposition and directly participates in the high-temperature calcination reaction, providing high-temperature stability. This application uses multiple magnesium compounds as magnesium sources, utilizing their differences in thermal decomposition behavior and chemical properties to exert synergistic effects at different stages of the calcination process. Specifically, the synergistic effects are: the decomposition of Mg(OH)2 and 4MgCO3·Mg(OH)2·6H2O occurs in succession over time; MgCl2·6H2O improves processability; and MgO provides high-temperature stability. This combination ensures the phased, relay-like release of gases during calcination. This synergistic effect facilitates the formation of a uniform, interconnected, and more controllable three-dimensional porous network within the ceramic body. Simultaneously, the aluminum source, acting as a calcination aid and stabilizer, decomposes at high temperatures, and the resulting active components react with the titanium and magnesium components in a solid-state reaction, promoting the formation of highly thermally stable phases such as spinel. This helps strengthen the ceramic framework, improve the structural stability of the ceramic material, and enhance its high-temperature resistance.

[0046] In addition, in this embodiment, the mixed powder is pressed into a green body, dried, and then calcined at 1000℃~1500℃ for 1.1h~3h. Under these conditions, the raw materials can be ensured to react fully and form a stable crystalline phase, while avoiding excessive pore closure or abnormal grain growth caused by excessively high temperature or time. This ensures that the final ceramic material has sufficient mechanical strength and maintains a suitable apparent porosity, improving the high-temperature resistance of the ceramic material. If the calcination temperature is below 1000℃, it will lead to insufficient calcination, incomplete solid-phase reaction, a large amount of raw powder in the product, weak interparticle bonding, extremely low cold crushing strength (CCS), loose structure, and easy powder shedding. If the calcination temperature is above 1500℃, it will lead to over-calcination, abnormal grain growth, rapid shrinkage, closure, or even disappearance of pores, resulting in excessively low apparent porosity (AP), poor liquid conductivity, and increased brittleness of the material. If the calcination time is less than 1.1 hours, the calcination time is insufficient, the reaction is incomplete, and the material density and strength do not reach the optimal values. If the calcination time is longer than 3 hours, it will lead to energy waste and may cause effects similar to "overheating," such as grain coarsening and pore coarsening. Although the strength may still be high, the porosity will further decrease, affecting the liquid conductivity and resulting in poor economic efficiency.

[0047] The method for preparing the ceramic material in this application has advantages such as readily available raw materials, low hazard to human health, and simple preparation method. The ceramic material prepared in this application is die-cast to form a ceramic heating core. Because this ceramic material does not contain heavy metals, is resistant to high temperatures and is not easily deformed, the risk of heavy metal migration from the ceramic heating core due to high-temperature heating can be significantly reduced.

[0048] In step S10 above: In some possible implementations, the titanium source includes anatase titanium dioxide. The anatase structure is a tetragonal crystal with titanium dioxide (TiO2) as its main component. Its basic unit is formed by covalently linked titanium-oxygen octahedra, exhibiting high symmetry and metastable characteristics. The reasons for favoring the anatase structure include: firstly, anatase titanium dioxide has high calcination activity: the anatase phase begins to transform into the rutile phase when heated to approximately 600-800℃. This phase transformation process is accompanied by volume changes and high lattice energy. Within the calcination temperature range (1000℃~1500℃) of this application embodiment, it promotes diffusion and densification, making it easier to form a calcined body with high strength and stable structure. Secondly, the pore structure of anatase titanium dioxide is easily controlled: its specific crystal structure and transformation behavior are conducive to forming a uniform, interconnected porous structure.

[0049] In some possible implementations, the aluminum source includes at least one of Al(NO3)3·6H2O, Al(OCH(CH3)2)3, Al2O3, and Al2(SO4)3. In the embodiments of this application, the aluminum source acts as a calcination aid, decomposing at high temperature to generate highly active Al2O3, which reacts with TiO2 and magnesium compounds to form a composite oxide phase (such as magnesium aluminate), lowering the calcination temperature and promoting densification. Simultaneously, the incorporated Al... 3+ Ions may dissolve into the TiO2 lattice, inhibiting excessive grain growth, refining the microstructure, and improving structural stability and strength.

[0050] In some possible implementations, the aluminum source includes Al(NO3)3·6H2O. Nitrates have advantages such as moderate decomposition temperature and no residual anion contamination. Hexahydrate is preferred because it provides a certain amount of water of crystallization during the mixing and pressing stages, which helps to uniformly mix the raw materials and forms a more uniform initial porous structure through the slow removal of moisture during the drying and initial calcination stages. If anhydrous Al(NO3)3 is used, its decomposition is too rapid, which may lead to localized compositional inhomogeneity and structural defects.

[0051] In some possible implementations, the molar ratio of titanium, aluminum, and magnesium sources is (85~95):(2~5):(5~10). This ratio achieves an optimal balance between porosity, strength, and calcination activity. The titanium source constitutes the main body of the ceramic material's framework, and its content is crucial for ensuring the framework's strength. The aluminum source, acting as a calcination aid and stabilizer, ensures both effective calcination and the formation of an appropriate amount of spinel phase in the ceramic material, thus maintaining its porous structure and porosity. The magnesium source primarily forms the spinel phase with the aluminum source and participates in pore formation; its content ensures both the porosity and strength of the ceramic material.

[0052] For example, the molar ratio of the titanium source, aluminum source and magnesium source can be any typical but non-limiting point value or an interval value between any two point values, such as 90:3:6, 85:5:10, 86:5:9, 88:4:8, 89:3:8, 91:2:7, 92:3:5, 93:2:5.

[0053] In some possible implementations, the molar ratio of Mg(OH)₂, 4MgCO₃·Mg(OH)₂·6H₂O, MgCl₂·6H₂O, and MgO in the magnesium source is (0.8~1.2):(0.8~1.2):(0.8~1.2):(0.8~1.2). In this case, the differences in their thermal decomposition behavior and chemical properties can be better utilized to achieve synergistic effects at different stages of the calcination process. This ensures the phased, relay-like release of gases during calcination, and this synergistic effect is beneficial for forming a uniform, interconnected, and more controllable three-dimensional porous network within the ceramic body.

[0054] In some embodiments, the molar ratio of Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, MgCl2·6H2O and MgO in the magnesium source can be any typical but non-limiting point value or an interval value between any two point values, such as 1:1:1:1, 0.8:1:1, 0.9:1.1:1.1, 1:0.8:1, 1:0.9:0.9, 1.1:1:1, 1.2:1:1, 1:1.2:1, 1:1:1.2, etc.

[0055] In step S20 above: In some possible implementations, the pressure used to press the mixed powder into green bodies is 50 MPa to 60 MPa. In this case, this pressure is key to balancing the green body density and calcination shrinkage. If the pressure is too low, the green body strength will decrease, resulting in excessively large and uneven porosity; if the pressure is too high, the green body will be too dense, which is not conducive to the subsequent formation of interconnected porous structures.

[0056] For example, the pressure used to press the mixed powder into a green body can be any typical but non-limiting point value or a range between any two point values, such as 50MPa, 51MPa, 52MPa, 53MPa, 54MPa, 55MPa, 56MPa, 57MPa, 58MPa, 59MPa, 60MPa.

[0057] In some possible implementations, the drying process includes drying at 50℃~80℃ for 4h~8h, followed by drying at 100℃~130℃ for 12h~24h. In this case, a two-stage drying process is used to safely and uniformly remove physically adsorbed water and water of crystallization from the raw material. First, drying at 50℃~80℃ for 4h~8h primarily removes surface adsorbed water and some water of crystallization, preventing rapid temperature increases that could lead to excessive vaporization and cracking of the green body. Then, drying at 100℃~130℃ for 12h~24h completely removes most of the water of crystallization in this higher-temperature stage, preparing the material for subsequent high-temperature calcination.

[0058] For example, the temperature of the first stage drying process can be any typical but non-limiting point value or a range between any two points, such as 50℃, 55℃, 60℃, 65℃, 70℃, 75℃, and 80℃, and the drying time can be any typical but non-limiting point value or a range between any two points, such as 4h, 5h, 6h, 7h, and 8h. The temperature of the second stage drying process can be any typical but non-limiting point value or a range between any two points, such as 100℃, 105℃, 110℃, 115℃, 120℃, 125℃, and 130℃, and the drying time can be any typical but non-limiting point value or a range between any two points, such as 12h, 16h, 18h, 20h, and 24h.

[0059] In some possible implementations, the heating rate steps of the calcination process include: heating to 1000°C at a rate of 5°C / min to 8°C / min, then adjusting the heating rate to 2°C / min to 4°C / min. In this case, controlling the heating rate ensures uniform heating of the green body, avoids cracking due to thermal stress, and controls the crystallization and phase transformation process. Heating to 1000°C at a rate of 5°C / min to 8°C / min involves solvent evaporation, hydrate decomposition, organic combustion, and preliminary crystallization; the slower rate ensures these processes proceed smoothly and gases are expelled efficiently. If further heating is required after reaching 1000°C, such as from 1000°C to 1500°C, this is a critical sintering stage involving intense grain growth and solid-state reactions. Using a slower heating rate of 2°C / min to 4°C / min is beneficial for obtaining a uniform microstructure and a controllable densification process, avoiding the risk of overheating or localized densification.

[0060] For example, the heating rate to 1000℃ can be any typical but non-limiting point value or an interval between any two point values, such as 5℃ / min, 6℃ / min, 7℃ / min, 8℃ / min, and the heating rate after reaching 1000℃ can be any typical but non-limiting point value or an interval between any two point values, such as 2℃ / min, 3℃ / min, 4℃ / min.

[0061] For example, the calcination temperature can be any typical but non-limiting point value or a range between any two points, such as 1000℃, 1050℃, 1100℃, 1150℃, 1200℃, 1250℃, 1300℃, 1350℃, 1400℃, 1450℃, 1500℃, etc., and the calcination time can be any typical but non-limiting point value or a range between any two points, such as 1.1h, 1.2h, 1.3h, 1.4h, 1.5h, 1.8h, 2h, 2.2h, 2.4h, 2.5h, 2.6h, 2.8h, 3h, etc.

[0062] In some possible implementations, the calcination temperature is 1200℃~1500℃, and the calcination time is 1.5h~3h. Under these conditions, the ceramic materials prepared by calcination have greater apparent porosity (AP) and bulk density (BD), as well as cold crushing strength, resulting in superior overall performance.

[0063] Secondly, embodiments of this application provide a ceramic material, which is prepared using the above-described preparation method.

[0064] The ceramic material provided in the second aspect of this application is prepared by the method described in the first aspect, and therefore inherits and embodies all the microstructural features and macroscopic performance advantages brought about by this preparation method. This ceramic material does not contain harmful metallic substances, reducing the risk of harmful substance migration at high temperatures and ensuring material safety. Thanks to the synergistic and phased decomposition of various magnesium compounds during heat treatment, and the sintering-aiding and stabilizing effects of the aluminum source, a uniform, interconnected, and more controllable three-dimensional porous network is formed inside the ceramic material, ensuring its liquid conductivity. Furthermore, thanks to sufficient sintering and the formation of reinforcing phases, the ceramic material possesses both sufficient mechanical strength and maintains suitable apparent porosity, exhibiting good high-temperature resistance and resistance to deformation.

[0065] In some possible implementations, the main crystalline phase in the ceramic material includes TiO2, and the auxiliary crystalline phase includes at least one of aluminum titanate, magnesium aluminate, and magnesium titanate. The aluminum and magnesium sources ultimately exist in the ceramic matrix in a combined state (such as a spinel phase) and a solid solution. Exemplarily, the main crystalline phase includes unreacted anatase or rutile TiO2 (depending on the calcination temperature). The auxiliary crystalline phase includes compounds formed by the reaction of Al2O3, MgO, and TiO2, such as aluminum titanate (Al2TiO5) and magnesium aluminate (MgAl2O4, spinel), which are key to imparting high refractoriness and thermal stability to the material. Additionally, the ceramic material may also contain small amounts of amorphous phases (i.e., glassy phases) formed by impurities or component segregation.

[0066] In some possible implementations, the apparent porosity of the ceramic material is 30% to 45%; this range of apparent porosity ensures that the ceramic material has sufficient and interconnected channels, providing an ideal structural basis for achieving efficient and uniform liquid transport (fluid conduction).

[0067] For example, the apparent porosity of ceramic materials can be any typical but non-limiting point value or an interval between any two point values, such as 30%, 31%, 32%, 33%, 34%, 35%, 36%, 37%, 38%, 39%, 40%, 41%, 42%, 43%, 44%, 45%.

[0068] In some possible implementations, the bulk density of the ceramic material is 1.95 g / cm³. 3 ~2.5g / cm 3 This density range reflects that the ceramic material, while possessing a porous structure, also achieves good sintering densification and skeletal strength.

[0069] For example, the bulk density of the ceramic material can be 1.95 g / cm³. 3 1.96g / cm 3 1.97g / cm 3 1.98g / cm 3 2g / cm 3 2.1g / cm 3 2.2g / cm 3 2.3g / cm 3 2.4g / cm 3 2.5g / cm 3 Typical but not restrictive arbitrary point values ​​or interval values ​​between any two point values.

[0070] In some possible implementations, the cold fracture strength of ceramic materials ranges from 27 MPa to 50 MPa. This demonstrates the excellent mechanical integrity and fracture resistance of ceramic materials, sufficient to withstand assembly stresses and long-term mechanical loads in practical applications.

[0071] For example, the cold fracture strength of ceramic materials can be any point value or an interval between any two point values, such as 27MPa, 30MPa, 35MPa, 40MPa, 45MPa, 50MPa, etc.

[0072] In some possible implementations, the apparent porosity of the ceramic material is 30%–40%; the bulk density of the ceramic material is 2.4 g / cm³. 3 ~2.5g / cm 3 The cold crushing strength of the ceramic material is 40 MPa to 50 MPa. Under these conditions, the high bulk density and cold crushing strength jointly confirm that the ceramic skeleton has achieved a high degree of sintering densification and excellent interparticle bonding. This gives the material outstanding mechanical strength, effectively resisting physical impacts, wear, and structural creep under long-term high temperatures during use, fundamentally solving the problems of powder shedding and structural failure. Simultaneously, maintaining an apparent porosity of 30% to 40% means that a uniform and interconnected open-pore network has been successfully preserved and controlled during the process of achieving high strengthening and densification.

[0073] The apparent porosity (AP) and bulk density (BD) of the ceramic material in this application embodiment are determined according to Archimedes' principle in GB / T 2997–2015, including the following steps: First, the weighed and dried sample is placed in a container, then placed in a vacuum device, and vacuumed until the pressure is less than 2.5 kPa, and the vacuum is maintained for 15 minutes. Second, pure water is poured into the container containing the sample through a pipe until the sample is completely submerged in water within 3 minutes. The sample is kept in water for 30 minutes until the water completely enters the open pores of the sample. Third, the sample is removed from the water, and excess water on the sample surface is removed. AP and BD are calculated according to the following formula: AP = (m3-m1) / (m3-m2) × 100%; BD = m1 / (m3-m2); Where m1 is the mass of the dried sample, m2 is the mass of the water-saturated sample suspended in water, and m3 is the mass of the water-saturated sample.

[0074] The cold fracture strength (CCS) of the ceramic material in this application embodiment was measured according to GB / T 5072-2023. The sample was mounted in the center of the testing machine, and pressure was continuously and uniformly applied at a loading rate of 0.1 MPa / s until the sample fractured. The CCS was calculated according to the following formula: CCS=F max / A0; Among them, F max A0 is the maximum load force, and A0 is the area of ​​the sample under pressure.

[0075] Thirdly, embodiments of this application provide a ceramic heating core, which includes ceramic materials prepared by the above method and / or the above-described ceramic materials.

[0076] The ceramic heating core provided in this application embodiment contains the aforementioned ceramic material, which is free of heavy metals, has high porosity, and is resistant to high temperatures and is not easily deformed. Therefore, it can ensure the liquid conductivity of the ceramic heating core and significantly reduce the risk of heavy metal migration caused by high-temperature heating, thereby improving safety and reliability.

[0077] In some possible implementations, the ceramic heating core is made of ceramic material. The ceramic material prepared in the embodiments of this application is directly die-cast to form the ceramic heating core.

[0078] Fourthly, embodiments of this application provide a liquid heating device, which includes the aforementioned ceramic heating core.

[0079] The liquid heating device provided in this application improves the performance of the liquid heating device in terms of safety, heating stability and reliability by using a ceramic heating core with the characteristics of good structural stability, no heavy metals, high porosity and good high temperature resistance.

[0080] To enable those skilled in the art to clearly understand the above-described implementation details and operations, and to highlight the significant advancements in the ceramic materials and preparation methods of the embodiments of this application, the following examples illustrate the above technical solutions.

[0081] Example 1 A ceramic material, the preparation of which includes the following steps: 1. Porous titanium oxide ceramics were prepared using 90 mol of anatase TiO2 powder as the main raw material, 3 mol of Al(NO3)3·6H2O, and 2 mol of different magnesium compounds (Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, 2 mol of MgCl2·6H2O, and 2 mol of MgO) as stabilizer precursors. Among them, anatase TiO2 was labeled as MT, Al(NO3)3·6H2O was labeled as AL, and Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, MgCl2·6H2O, and MgO were labeled as AM1, AM2, AM3, and AM4, respectively.

[0082] 2. The above raw materials were uniformly mixed and pressed into cylindrical samples with a diameter of Φ20 mm × 20 mm under 55 MPa. The samples were first dried at 60℃ for 6 h, then dried at 110℃ for 18 h, and then calcined at 1166.7℃ for 1.33 h. The calcination rate of the dried samples from room temperature to 1000℃ was 5℃ / min, and the calcination rate from 1000℃ to 1500℃ was 3℃ / min.

[0083] Example 2 A ceramic material, the preparation of which includes the following steps: 1. Porous titanium dioxide ceramics were prepared using 90 mol of anatase TiO2 powder as the main raw material, 3 mol of Al(NO3)3·6H2O, and different magnesium compounds 2 mol of Mg(OH)2, 2 mol of 4MgCO3·Mg(OH)2·6H2O, 2 mol of MgCl2·6H2O, and 2 mol of MgO as stabilizer precursors. Among them, 90 mol of anatase TiO2 was labeled as MT, Al(NO3)3·6H2O was labeled as AL, and Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, MgCl2·6H2O, and MgO were labeled as AM1, AM2, AM3, and AM4, respectively.

[0084] 2. The above raw materials were uniformly mixed and pressed into cylindrical samples with a diameter of Φ20 mm × 20 mm under 55 MPa. The samples were first dried at 60℃ for 6 h, then dried at 110℃ for 18 h, and then calcined at 1222.2℃ for 1.61 h. The calcination rate of the dried samples from room temperature to 1000℃ was 5℃ / min, and the calcination rate from 1000℃ to 1500℃ was 3℃ / min.

[0085] Examples 3-8 Examples 3 to 8 of this application provide a ceramic material. Except for the reaction temperature and calcination time, the operation steps in the preparation process are the same, as shown in Table 1 below.

[0086] Comparative Example 1 A ceramic material, the preparation of which includes the following steps: 1. Porous titanium dioxide ceramics were prepared using 90 mol of anatase TiO2 powder as the main raw material, 3 mol of Al(NO3)3·6H2O, and 2 mol of different magnesium compounds (Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, 2 mol of MgCl2·6H2O, and 2 mol of MgO) as stabilizer precursors. Among them, anatase TiO2 was labeled as MT, Al(NO3)3·6H2O was labeled as AL, and Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, MgCl2·6H2O, and MgO were labeled as AM1, AM2, AM3, and AM4, respectively.

[0087] 2. The above raw materials were uniformly mixed and pressed into cylindrical samples with a diameter of Φ20 mm × 20 mm under 55 MPa. The samples were first dried at 60℃ for 6 h, then dried at 110℃ for 18 h, and then calcined at 1500℃ for 0.50 h. The calcination rate of the dried samples from room temperature to 1000℃ was 5℃ / min, and the calcination rate from 1000℃ to 1500℃ was 3℃ / min.

[0088] Comparative Examples 2-7 Comparative Examples 2 to 7 of this application each provide a ceramic material. Except for the reaction temperature and calcination time, the operation steps in the preparation process are the same, as shown in Table 1 below.

[0089] Comparative Example 8 A ceramic material, the preparation of which includes the following steps: 1. Porous titanium oxide ceramics were prepared using 3 mol Al(NO3)3·6H2O and 2 mol Mg(OH)2, 2 mol 4MgCO3·Mg(OH)2·6H2O, 2 mol MgCl2·6H2O, and 2 mol MgO as stabilizer precursors. Al(NO3)3·6H2O was labeled as AL, and Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, MgCl2·6H2O, and MgO were labeled as AM1, AM2, AM3, and AM4, respectively.

[0090] 2. The above raw materials were uniformly mixed and pressed into cylindrical samples with a diameter of Φ20 mm × 20 mm under 55 MPa. The samples were first dried at 60℃ for 6 h, then dried at 110℃ for 18 h, and then calcined at 1500℃ for 0.50 h. The calcination rate of the dried samples from room temperature to 1000℃ was 5℃ / min, and the calcination rate from 1000℃ to 1500℃ was 3℃ / min.

[0091] Comparative Example 9 A ceramic material, the preparation of which includes the following steps: 1. Porous titanium oxide ceramics were prepared using 90 mol of anatase TiO2 powder as the main raw material and 2 mol of different magnesium compounds, namely Mg(OH)2, 2 mol of 4MgCO3·Mg(OH)2·6H2O, 2 mol of MgCl2·6H2O, and 2 mol of MgO, as stabilizer precursors. Among them, anatase TiO2 was labeled as MT, and Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, MgCl2·6H2O, and MgO were labeled as AM1, AM2, AM3, and AM4, respectively.

[0092] 2. The above raw materials were uniformly mixed and pressed into cylindrical samples with a diameter of Φ20 mm × 20 mm under 55 MPa. The samples were first dried at 60℃ for 6 h, then dried at 110℃ for 18 h, and then calcined at 1500℃ for 0.50 h. The calcination rate of the dried samples from room temperature to 1000℃ was 5℃ / min, and the calcination rate from 1000℃ to 1500℃ was 3℃ / min.

[0093] Comparative Example 10 A ceramic material, the preparation of which includes the following steps: 1. The main raw materials are 90 mol of anatase TiO2 powder and 3 mol of Al(NO3)3·6H2O. The anatase TiO2 is labeled as MT and the Al(NO3)3·6H2O is labeled as AL.

[0094] 2. The above raw materials were uniformly mixed and pressed into cylindrical samples with a diameter of Φ20 mm × 20 mm under 55 MPa. The samples were first dried at 60℃ for 6 h, then dried at 110℃ for 18 h, and then calcined at 1500℃ for 0.50 h. The calcination rate of the dried samples from room temperature to 1000℃ was 5℃ / min, and the calcination rate from 1000℃ to 1500℃ was 3℃ / min.

[0095] Comparative Example 11 A ceramic material, the preparation of which includes the following steps: 1. Porous titanium oxide ceramics were prepared using 90 mol of anatase TiO2 powder as the main raw material, 3 mol of Al(NO3)3·6H2O, 4 mol of Mg(OH)2, and 4 mol of 4MgCO3·Mg(OH)2·6H2O as stabilizer precursors. Among them, anatase TiO2 was labeled as MT, Al(NO3)3·6H2O was labeled as AL, and Mg(OH)2 and 4MgCO3·Mg(OH)2·6H2O were labeled as AM1 and AM2, respectively.

[0096] 2. The above raw materials were uniformly mixed and pressed into cylindrical samples with a diameter of Φ20 mm × 20 mm under 55 MPa. The samples were first dried at 60℃ for 6 h, then dried at 110℃ for 18 h, and then calcined at 1500℃ for 0.50 h. The calcination rate of the dried samples from room temperature to 1000℃ was 5℃ / min, and the calcination rate from 1000℃ to 1500℃ was 3℃ / min.

[0097] Comparative Example 12 A ceramic material, the preparation of which includes the following steps: 1. Porous titanium oxide ceramics were prepared using 90 mol of anatase TiO2 powder as the main raw material, 3 mol of Al(NO3)3·6H2O and 4 mol of different magnesium compounds, MgCl2·6H2O and MgO as stabilizer precursors. Among them, anatase TiO2 was labeled as MT, Al(NO3)3·6H2O was labeled as AL, and 8 mol of MgCl2·6H2O and MgO were labeled as AM3 and AM4, respectively.

[0098] 2. The above raw materials were uniformly mixed and pressed into cylindrical samples with a diameter of Φ20 mm × 20 mm under 55 MPa. The samples were first dried at 60℃ for 6 h, then dried at 110℃ for 18 h, and then calcined at 1500℃ for 0.50 h. The calcination rate of the dried samples from room temperature to 1000℃ was 5℃ / min, and the calcination rate from 1000℃ to 1500℃ was 3℃ / min.

[0099] Comparative Example 13 A ceramic material, the preparation of which includes the following steps: 1. Porous titanium dioxide ceramics were prepared using 90 mol of anatase TiO2 powder as the main raw material, 3 mol of Al(NO3)3·6H2O and 4 mol of different magnesium compounds Mg(OH)2 and 4 mol of MgCl2·6H2O as stabilizer precursors. Among them, 90 mol of anatase TiO2 was labeled as MT, Al(NO3)3·6H2O was labeled as AL, and Mg(OH)2 and MgCl2·6H2O were labeled as AM1 and AM3, respectively.

[0100] 2. The above raw materials were uniformly mixed and pressed into cylindrical samples with a diameter of Φ20 mm × 20 mm under 55 MPa. The samples were first dried at 60℃ for 6 h, then dried at 110℃ for 18 h, and then calcined at 1500℃ for 0.50 h. The calcination rate of the dried samples from room temperature to 1000℃ was 5℃ / min, and the calcination rate from 1000℃ to 1500℃ was 3℃ / min.

[0101] Comparative Example 14 A ceramic material, the preparation of which includes the following steps: 1. Porous titanium oxide ceramics were prepared using 90 mol of anatase TiO2 powder as the main raw material, 3 mol of Al(NO3)3·6H2O and 4 mol of different magnesium compounds, 4 mol of 4MgCO3·Mg(OH)2·6H2O and 4 mol of MgO as stabilizer precursors. Among them, anatase TiO2 was labeled as MT, Al(NO3)3·6H2O was labeled as AL, and 4MgCO3·Mg(OH)2·6H2O and MgO were labeled as AM2 and AM4, respectively.

[0102] 2. The above raw materials were uniformly mixed and pressed into cylindrical samples with a diameter of Φ20 mm × 20 mm under 55 MPa. The samples were first dried at 60℃ for 6 h, then dried at 110℃ for 18 h, and then calcined at 1500℃ for 0.50 h. The calcination rate of the dried samples from room temperature to 1000℃ was 5℃ / min, and the calcination rate from 1000℃ to 1500℃ was 3℃ / min.

[0103] The reaction raw material components and calcination conditions of the above embodiments and comparative examples are shown in Table 1 below: Table 1

[0104] To verify the progressiveness of the embodiments of this application, the following performance tests were performed on the above embodiments and comparative examples: 1. The apparent porosity (AP) and bulk density (BD) of ceramic materials were determined according to Archimedes' principle in GB / T 2997–2015. The procedure included: First, the weighed, dried sample was placed in a container and then placed in a vacuum apparatus. A vacuum was drawn until the pressure was less than 2.5 kPa, and this vacuuming was maintained for 15 minutes. Second, pure water was poured into the container containing the sample through a pipe until the sample was completely submerged within 3 minutes. The sample was then kept in the water for 30 minutes until the water completely entered the open pores of the sample. Third, the sample was removed from the water, and excess moisture on the sample surface was removed. AP and BD were calculated using the following formula: AP = (m3-m1) / (m3-m2) × 100%; BD = m1 / (m3-m2); Where m1 is the mass of the dried sample, m2 is the mass of the water-saturated sample suspended in water, and m3 is the mass of the water-saturated sample.

[0105] 2. The cold fracture strength (CCS) of ceramic materials is tested according to GB / T 5072-2023. The sample is mounted in the center of the testing machine, and pressure is continuously and uniformly applied at a loading rate of 0.1 MPa / s until the sample breaks. The CCS is calculated using the following formula: CCS=F max / A0; Among them, F max A0 is the maximum load force, and A0 is the area of ​​the sample under pressure.

[0106] The test results are shown in Table 2 below: Table 2

[0107] As shown in Table 2 above, the ceramic materials prepared in Examples 1-8 of this application do not contain heavy metals, thus avoiding the risk of heavy metal migration at the source. The apparent porosity of the ceramic materials is 30%~45%, and the bulk density is 1.95 g / cm³. 3 ~2.5g / cm 3 The cold crushing strength is 27 MPa to 50 MPa. The apparent porosity of the ceramic material is 30% to 45%, indicating a uniform and continuous pore structure, which is beneficial for the uniform liquid conduction and aerosolization of the aerosol matrix. The bulk density is 1.95 g / cm³. 3 ~2.5g / cm 3 The dense structure and surface integrity of the ceramic heating core prepared from ceramic materials ensure that it is not prone to powdering or wear during use, thus improving product life and safety. The cold crushing strength is 27MPa~50MPa, indicating that the ceramic heating core prepared from ceramic materials has high hardness, demonstrating excellent mechanical strength and resistance to breakage. Specifically, the ceramic material prepared in Example 7 achieved a cold crushing strength of 50MPa, an apparent porosity of 30.0%, and a bulk density of 2.50 g / cm³. 3 It also has excellent structural density and surface integrity, is not easy to shed powder or wear, as well as high mechanical strength and anti-breakage ability, and excellent high temperature resistance.

[0108] Comparative Examples 1 to 4 showed that due to the calcination time being less than 1.1 hours and insufficient sintering time, the reaction was incomplete, resulting in a significant reduction in the bulk density and cold crushing strength of the ceramic materials.

[0109] Comparative Example 5: Due to the calcination temperature being below 1000℃, the sintering was insufficient and the solid-phase reaction was not completed, resulting in a large amount of raw powder in the product and weak interparticle bonding, leading to excessively high apparent porosity of the ceramic material and reduced cold crushing strength and bulk density.

[0110] Comparative Example 6 shows that due to the calcination time being longer than 3 hours, the material was over-burned, resulting in grain coarsening and pore coarsening, thus reducing the apparent porosity of the ceramic material.

[0111] Comparative Example 7 shows that due to the calcination temperature being higher than 1500℃, excessive sintering occurred, resulting in abnormal grain growth and rapid shrinkage and closure of pores, leading to a decrease in the apparent porosity of the ceramic material.

[0112] Comparative Examples 8 to 14 showed a significant decrease in the cold crushing strength of the prepared ceramic materials (5.0 to 26.0 MPa) due to the absence or improper combination of the reactant components.

[0113] 3. The morphology of the ceramic materials prepared in Examples 1-8, Comparative Examples 1-4, and Comparative Examples 8 and 14 was observed. The electron micrograph of the ceramic material in Example 1 is attached. Figure 2 As shown; the electron microscope image of the ceramic material in Example 2 is attached. Figure 3 As shown; the electron microscope image of the ceramic material in Example 3 is attached. Figure 4 As shown; the electron microscope image of the ceramic material in Example 4 is attached. Figure 5 As shown; the electron microscope image of the ceramic material in Example 5 is attached. Figure 6 As shown; the electron microscope image of the ceramic material in Example 6 is attached. Figure 7 As shown; the electron microscope image of the ceramic material in Example 7 is attached. Figure 8 As shown; the electron microscope image of the ceramic material in Example 8 is attached. Figure 9 As shown; the electron microscope image of the ceramic material in Comparative Example 1 is attached. Figure 10 As shown; the electron microscope image of the ceramic material in Comparative Example 2 is attached. Figure 11 As shown; the electron microscope image of the ceramic material in Comparative Example 3 is attached. Figure 12 As shown; the electron microscope image of the ceramic material in Comparative Example 4 is attached. Figure 13 As shown; the electron microscope image of the ceramic material in Comparative Example 8 is attached. Figure 14 As shown; electron micrograph of the ceramic material in Comparative Example 14 is attached. Figure 15 As shown in the attached figures, the test results indicate that the ceramic materials prepared in Examples 1-8 of this application have a uniform and continuous pore structure, which is beneficial for the uniform liquid conduction and aerosolization of the aerosol matrix. In contrast, the ceramic materials prepared in the comparative examples have poor pore uniformity and poor pore continuity, resulting in poor liquid conduction performance.

[0114] The above description is merely a preferred embodiment of this application and is not intended to limit this application. Any modifications, equivalent substitutions, and improvements made within the spirit and principles of this application should be included within the protection scope of this application.

Claims

1. A method for preparing a ceramic material, characterized in that, Includes the following steps: Titanium source, aluminum source and magnesium source are made into mixed powder; wherein, the titanium source includes TiO2, and the magnesium source includes Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, MgCl2·6H2O and MgO; The mixed powder is pressed into a green body, which is then dried and calcined at 1000℃~1500℃ for 1.1h~3h to obtain a porous ceramic material.

2. The method for preparing the ceramic material as described in claim 1, characterized in that, The titanium source includes anatase titanium dioxide; And / or, the aluminum source includes at least one of Al(NO3)3·6H2O, Al(OCH(CH3)2)3, Al2O3, and Al2(SO4)3.

3. The method for preparing the ceramic material as described in claim 2, characterized in that, The aluminum source includes Al(NO3)3·6H2O.

4. The method for preparing the ceramic material according to any one of claims 1 to 3, characterized in that, The molar ratio of the titanium source, the aluminum source and the magnesium source is (85~95):(2~5):(5~10).

5. The method for preparing the ceramic material as described in claim 4, characterized in that, In the magnesium source, the molar ratio of Mg(OH)2, 4MgCO3·Mg(OH)2·6H2O, MgCl2·6H2O and MgO is (0.8~1.2):(0.8~1.2):(0.8~1.2):(0.8~1.2).

6. The method for preparing the ceramic material according to any one of claims 1 to 3 or 5, characterized in that, The pressure used to press the mixed powder into a green body is 50MPa~60MPa; And / or, the drying process includes: drying at a temperature of 50℃~80℃ for 4h~8h, followed by drying at a temperature of 100℃~130℃ for 12h~24h.

7. The method for preparing the ceramic material as described in claim 6, characterized in that, The heating rate step of the calcination treatment includes: heating to 1000℃ at a rate of 5℃ / min to 8℃ / min, and then adjusting the heating rate to 2℃ / min to 4℃ / min. And / or, the calcination temperature is 1200℃~1500℃, and the calcination time is 1.5h~3h.

8. A ceramic material, characterized in that, The ceramic material is prepared by the preparation method described in any one of claims 1 to 7.

9. The ceramic material as described in claim 8, characterized in that, The ceramic material has a main crystalline phase including TiO2 and an auxiliary crystalline phase including at least one of aluminum titanate, magnesium aluminate, and magnesium titanate.

10. The ceramic material as described in claim 8 or 9, characterized in that, The apparent porosity of the ceramic material is 30%~45%; and / or the ceramic material has a bulk density of 1.95 g / cm3 3 2.5 g / cm3 3 ; And / or, the cold crushing strength of the ceramic material is 27MPa~50MPa.

11. The ceramic material as described in claim 10, characterized in that, The apparent porosity of the ceramic material is 30%~40%; the bulk density of the ceramic material is 2.4 g / cm³. 3 ~2.5g / cm 3 The cold crushing strength of the ceramic material is 40MPa~50MPa.

12. A ceramic heating core, characterized in that, The ceramic heating core includes ceramic materials prepared by the method described in any one of claims 1 to 7 and / or ceramic materials described in any one of claims 8 to 11.

13. The ceramic heating core as described in claim 12, characterized in that, The ceramic heating core is made of the ceramic material.

14. A liquid heating device, characterized in that, The liquid heating device includes a ceramic heating core as described in any one of claims 12 to 13.

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