High magnetic heating susceptor and cartridge

Abstract

The utility model provides a kind of high magnetic heating susceptor and cartridge, by using a large number of magnetic element component, multilayer structure design and doping rare earth element etc. Configuration, so that the magnetic heating susceptor whole has stronger magnetism and respectively strengthens temperature mark and eddy current heating function;Adopt the intermediate metal layer of larger ductility, so that the deformation amount increases in processing process, it is favorable to enhance interface bonding strength and keep the stability of overall magnetism. And the extrusion type cartridge containing the magnetic heating susceptor, the sheet-shaped magnetic heating susceptor in smoke body is tightly combined with extrusion paste body, has good manufacturability.

Description

Technical Field

[0001] This utility model relates to the field of novel tobacco heating technology, specifically a high magnetic heating sensor and a tobacco cartridge. Background Technology

[0002] Heated non-combustible (HNB) technology has become an important development direction in the field of new tobacco products. The heating element is usually configured by embedding a magnetic heating sensor in an aerosol matrix, which generates eddy current heating in a high-frequency magnetic field of 1-30MHz. As a core functional component of the tobacco cartridge, the magnetic heating sensor must meet the requirements of high magnetic permeability, strong eddy current effect, and mechanical compatibility.

[0003] Currently, aerosol matrices are mainly classified into granular and sheet types. For granular types, thick-sheet magnetic heating sensors are typically used, assembled by cutting and then inserting them. These sensors need to withstand significant resistance during insertion into the aerosol matrix to maintain their shape, requiring high mechanical strength from the material. For sheet types, the mainstream approach is to first wind a thin strip of magnetic heating sensor material together with tobacco sheets, then cut it into small segments for generating smoke. However, existing materials are usually in a fully rigid or semi-rigid state, easily cutting the tobacco sheets during winding and causing them to break. Moreover, these fully rigid or semi-rigid materials have weak magnetism, requiring very high magnetic field strength and frequency from the smoking device, which is often difficult to match.

[0004] The industry-leading extrusion-type aerosol matrix uses an emerging process to extrude the paste into strip-shaped smoke generators. This makes it possible to co-mold and extrude magnetic heating sensors with the paste, and to construct a new type of electromagnetic cigarette cartridge structure.

[0005] Against this background, this application proposes an electromagnetic heating solution, particularly a magnetic heating sensor solution that is applicable to extruded cigarette cartridges and has high magnetic properties, soft mechanical properties, and easy processing. Utility Model Content

[0006] To address the aforementioned problems in the prior art, this utility model provides a high magnetic heating sensor, characterized in that it comprises a first magnetic metal layer and a second magnetic metal layer, wherein the thickness of the first magnetic metal layer is less than or equal to the thickness of the second magnetic metal layer; wherein the first magnetic metal layer contains iron and nickel, with the iron content ranging from 5-50 wt% and the nickel content ranging from 35-90 wt%; the second magnetic metal layer contains iron, wherein the iron content is greater than 65 wt%, and the total content of iron and nickel in the high magnetic heating sensor is greater than 75 wt%.

[0007] Furthermore, the first magnetic metal layer and / or the second magnetic metal layer contain cobalt, with a content ranging from 2 to 25 wt%.

[0008] Furthermore, the first magnetic metal layer and / or the second magnetic metal layer contain rare earth elements, with a total content ranging from 0.1 to 5 wt%.

[0009] Furthermore, it also includes an intermediate metal layer, which contains at least one of the elements gold, silver, copper, iron, nickel, and aluminum.

[0010] Furthermore, the ductility of the intermediate metal layer material is greater than that of the first magnetic metal layer material and the second magnetic metal layer material.

[0011] Furthermore, the equivalent average thickness of the high magnetic heating sensor is 0.03-0.085 mm.

[0012] Furthermore, the permeability of the high-magnetic heating sensor is no higher than 70,000 H / m.

[0013] Furthermore, the rigidity of the first magnetic metal layer is greater than that of the second magnetic metal layer.

[0014] Furthermore, it is configured as a sheet or a curved shape.

[0015] A cigarette cartridge is also provided, including the aforementioned high magnetic heating sensor.

[0016] Compared with existing technologies, the beneficial effects of this utility model are as follows: It proposes a magnetic heating sensor, which, through the use of a large number of magnetic elements, a multi-layer structure design, and rare-earth element doping, gives the magnetic heating sensor strong overall magnetism and enhances both temperature marking and eddy current heating functions. The use of a highly ductile intermediate metal layer increases the deformation during processing, which is beneficial for strengthening the interfacial bonding strength and maintaining the overall magnetic stability. Furthermore, the extruded cigarette cartridge containing the aforementioned magnetic heating sensor exhibits good manufacturability, as the sheet-like magnetic heating sensor is tightly integrated with the extruded paste within the smoke-generating body. Attached Figure Description

[0017] Figure 1 This is a schematic diagram of the structural composition of an electromagnetically heated smoke cartridge.

[0018] Figure 2 This is a schematic diagram of a high-magnetic heating sensor structure with an intermediate metal layer.

[0019] Figure 3 This is a schematic diagram of a three-section electromagnetic heating cigarette cartridge. Detailed Implementation

[0020] The technical solutions of the present utility model will be clearly and completely described below with reference to the accompanying drawings of the embodiments. Obviously, the described embodiments are only some embodiments of the present utility model, and not all embodiments. Based on the embodiments of the present utility model, all other embodiments obtained by those of ordinary skill in the art without creative effort are within the protection scope of the present utility model.

[0021] like Figure 1 As shown, the heated tobacco cartridge 300 has an internal storage space for accommodating various components, and the smoke-generating element can be housed within this space. When heated, the smoke-generating element produces an aerosol for the user to inhale. The smoke-generating element mainly includes a smoke-generating section 200 and a heating sensor 100. The smoke-generating section 200 is primarily composed of plant materials (including tobacco and tobacco leaves), and produces an aerosol when heated to a certain temperature. The heating sensor 100 is embedded inside the smoke-generating section 200; in other words, the heating sensor 100 is not visible from the outside and is entirely housed within the smoke-generating section 200. The heating sensor 100 is primarily made of ferromagnetic or ferrimagnetic alloy material, possessing high permeability at room temperature.

[0022] Its heating theory is based on Faraday's law of electromagnetic induction and Ohm's law. When a conductor moves in an electromagnetic field or when the direction of the electromagnetic field changes at a high frequency, eddy currents are generated inside the conductor. These eddy currents generate energy loss and thus heat. In the application of electromagnetic induction heating non-combustible tobacco cartridges, a commonly used model is a sheet conductor (magnetic heating sensor) located at the central axis of a solenoid coil. Based on this configuration, when a sinusoidal alternating magnetic flux passes through the magnetic heating sensor, the eddy current loss P per unit volume of the magnetic heating sensor can be expressed by the following formula:

[0023] P = K * f 2 *B 2 *d 2 *μ

[0024] Where K is a constant, f is the magnetic field frequency, and B is the magnetic field strength; these three are parameters related to the smoking device. μ is the permeability of the magnetic heating sensor, and d is the thickness of the magnetic heating sensor; these two are parameters related to the magnetic heating sensor. Therefore, it can be seen that the eddy current effect is proportional to the square of the magnetic field frequency, the square of the magnetic field strength, the square of the thickness of the magnetic heating sensor, and the permeability of the magnetic heating sensor.

[0025] In practical applications, manufacturers of tobacco cartridges typically use smaller weight aerosol matrixes to reduce costs (e.g., related to nicotine content). This trend leads to limitations in the size of the magnetic heating sensor. To reduce the space occupied by the magnetic heating sensor and control the compression deformation of the aerosol matrix, the thickness and width of the magnetic heating sensor are further reduced, for example, its thickness is reduced to a thinner dimension, such as 0.085 mm, or even an ultra-thin dimension, such as 0.03 mm. Based on the above formula, the eddy current loss P, which is the power ultimately applied to the magnetic heating sensor by the system, contributes little to improving the size of the magnetic heating sensor itself in order to achieve the expected heating power or further increase the heating power. Therefore, increasing the magnetic permeability (μ) becomes a compensatory approach to enhance the eddy current heating effect of electromagnetic induction.

[0026] This application selects high-permeability materials as high-magnetic-sensors to generate strong eddy currents in alternating magnetic fields. Ferromagnetic materials such as iron, nickel, cobalt and their alloys, as well as magnetic soft steel, exhibit high permeability in the 1-30MHz frequency range and are therefore chosen as suitable candidate materials. Based on experimental data and relevant literature, the overall permeability of the sensor is set within the range of 5-70000 H / m to ensure sufficient eddy current effect in the target frequency range, thereby achieving continuous and complete carbonization of the aerosol-generating matrix.

[0027] Example 1

[0028] The magnetic heating sensor is composed of a metal containing a large amount of magnetic elements. The high permeability of these magnetic elements (such as iron, nickel, and cobalt) and their alloys stems from the magnetic domain orientation and low coercivity of their crystal lattice structure. In an alternating magnetic field, the rapid flipping of magnetic domains and the narrowing of the hysteresis loop can significantly enhance the eddy current effect. Therefore, the magnetic heating sensor material design in this invention employs a large amount of magnetic elements, setting the total content of iron and nickel to above 75 wt%. Through the synergistic effect of these two elements, a high magnetic sensor is generated, thereby achieving a high overall permeability.

[0029] In one feasible approach, the magnetic heating sensor uses an iron-nickel permalloy (with a nickel content between 35-90 wt%) as the base alloy and is optimized in multiple ways, including alloying modification and structural modification.

[0030] The strong magnetism of permalloy stems from the synergistic effect of iron and nickel, achieved through compositional control and optimization of magnetocrystalline anisotropy. When the nickel content is approximately 80 wt%, the alloy forms a face-centered cubic (FCC) crystal structure. Its high symmetry reduces the magnetocrystalline anisotropy constant (K1), making it easier for magnetic domains to rearrange under an external magnetic field. This results in high permeability (μ up to 70,000 or even higher) and low coercivity (H). c<1A / m). The key mechanism is that in this face-centered cubic structure, the difference in magnetic anisotropy between crystal orientations is small, the resistance to magnetic domain wall movement is reduced, and the magnetization process is easier to complete.

[0031] As shown in Table 1 below, in this embodiment, a new soft magnetic nickel-based alloy was formed by adjusting the composition of a permalloy with a nickel content of about 80 wt%, which serves as the first magnetic metal layer material in the magnetic heating sensor, with a thickness of 0.04 mm.

[0032] Table 1: Composition of a magnetic metal layer material in Example 1

[0033] wt% margin 80.2 5.5 0.8 0.8 0.25 0.3 3.1 Less than 0.1

[0034] Wherein, wt% is the weight percentage, which means that the raw material elements of the base alloy can be accurately identified and calculated using various technical means such as chemical composition analysis, spectral analysis, mass spectrometry, chromatographic analysis, X-ray atomic spectroscopy, etc.

[0035] In this embodiment, nickel is the dominant element in the alloy, imparting high magnetic permeability and low coercivity to the alloy material, while also enhancing its high-temperature resistance and oxidation resistance. Iron, as the matrix element, provides a certain degree of basic magnetism and promotes structural stability and optimizes mechanical properties.

[0036] The remaining alloying elements produce a synergistic effect, significantly enhancing magnetism. Molybdenum suppresses the formation of the Ni3Fe ordered phase, reduces magnetocrystalline anisotropy, and increases initial permeability. Copper enhances the cold working properties of the alloy and reduces the magnetic sensitivity to forces. Chromium, silicon, and manganese refine the grains, reduce the hindrance of grain boundaries to magnetic domain movement, and reduce magnetocrystalline anisotropy to improve magnetic properties. Cobalt is used to enhance the magnetism of the material and increase the Curie temperature of the alloy to compensate for the negative impact of alloying elements such as molybdenum, copper, chromium, silicon, and manganese on the Curie temperature, preventing a sharp drop in permeability at high temperatures. In this embodiment, the Curie temperature of cobalt itself is approximately 1151°C. By replacing a certain amount of iron, it is desired to control the Curie temperature to around 430°C. To obtain a suitable Curie temperature, the cobalt content in the magnetic heating sensor is controlled at 2-25 wt%.

[0037] Other elements are impurities, mainly carbon, phosphorus, and sulfur. Their total content is strictly controlled to be less than 0.1% by wt% to reduce their negative impact on magnetic properties.

[0038] The magnetization process of this alloy in electromagnetic induction heating non-combustible applications may involve three scenarios:

[0039] ① Reversible domain wall movement: Under a weak magnetic field, the domain walls detach from the grain boundaries and impurity pinning points, resulting in reversible displacement, which corresponds to high initial permeability.

[0040] ② Irreversible domain wall movement: Under a strong magnetic field, the domain walls completely detach from the pinning, forming an irreversible displacement, and the magnetic permeability reaches its peak.

[0041] ③ Domain rotation: Under an extremely strong magnetic field (exceeding the saturation critical value), the direction of the magnetic moment is aligned with the external field, reaching the saturation magnetic induction intensity. Movement of the domain walls can no longer further increase the magnetization intensity. At this point, the magnetic moment within the domain needs to be rotated to align with the direction of the external field.

[0042] In summary, the magnetic metal layer constructs a core material for a high-performance magnetic heating sensor through the innovative design of a high-nickel content iron-nickel-based soft magnetic alloy. Based on a face-centered cubic (FCC) crystal structure, this material achieves high permeability and the expected Curie temperature through the synergistic control of multi-element alloying.

[0043] Example 2

[0044] The magnetic heating sensor consists of a multi-layered composite structure. A key characteristic of the aforementioned permalloy and modified soft magnetic alloys is their high permeability. However, the permeability fluctuates significantly with temperature. If this type of alloy is used alone as the magnetic heating sensor, the permeability will fluctuate greatly when the temperature rises from room temperature to 350°C or even higher, such as 420°C, during the smoking process. This reduces the coupling stability with the magnetic field and makes input power control very difficult. Furthermore, soft magnetic alloys have low magnetocrystalline anisotropy, low magnetostriction coefficient, and high resistivity. These factors result in low high-frequency losses, making them unsuitable for heating.

[0045] Based on this, a multi-layered composite structure is adopted in this second embodiment. A second magnetic metal layer is added to the magnetic heating sensor. This layer is made of ferromagnetic or ferrimagnetic metal with a high Curie temperature. Its magnetism does not change significantly within the range of room temperature to 420°C. This magnetism serves as the basic magnetism, ensuring that the magnetic heating sensor maintains stable coupling with the magnetic field at all times. In this configuration, the first magnetic metal layer provides temperature signal feedback to the aerosol generation device through significant magnetic fluctuations generated with temperature changes, and is defined as the temperature marking layer. The second magnetic metal layer, by maintaining relatively stable magnetism throughout the suction application and coupling with the magnetic field, continuously generates a large amount of eddy current effect, and is defined as the heating layer.

[0046] In this second embodiment, since the thickness of the first magnetic metal layer is no greater than that of the second magnetic metal layer, setting the rigidity of the first magnetic metal layer to be greater than that of the second magnetic metal layer helps to counteract the bending force when inserting the cartridge and prevents it from easily bending. The mechanical strength of the sensor characterizes its ability to resist external forces without deformation. During production and use, the sensor may interact mechanically with the aerosol generating matrix and may also collide with some production fixtures and human tools (such as tweezers).

[0047] In one feasible embodiment, the material of the second magnetic metal layer is T. c Iron, cobalt, iron-cobalt alloys, iron-silicon alloys, iron-silicon-aluminum alloys, iron-chromium-aluminum alloys, and various magnetic stainless steels, etc., exceeding 550℃. Theoretically, the magnetic permeability of magnetic metals will not decrease significantly before reaching 100℃ from the Curie temperature, that is, the second magnetic metal layer will not experience a significant decrease in magnetism before reaching 450℃.

[0048] In this second embodiment, the magnetic metal layer described in the first embodiment is used as the first magnetic metal layer as the temperature marking layer, with a thickness of 0.04 mm. The iron-chromium-aluminum alloy with the composition in Table 2 is used as the second magnetic metal layer as the heating layer, with a thickness of 0.043 mm.

[0049] Table 2: Material composition of the second magnetic metal layer in Example 2

[0050] wt% margin 12.2 5.5 2.2 0.1 0.2 Less than 0.1

[0051] The second magnetic metal layer, an iron-silicon-aluminum alloy, can achieve stable magnetism and efficient eddy current heating within a temperature range from room temperature to 420°C. The main mechanism is as follows:

[0052] Firstly, high-temperature magnetic stability is achieved through Curie temperature control and dynamic optimization of magnetic domains.

[0053] An iron matrix constructs a body-centered cubic (BCC) crystal structure, providing high saturation magnetization and forming a strongly ferromagnetically ordered state through 3d electron spin coupling. A substitutional solid solution is formed in the iron matrix (79.7 wt%) by introducing (12.2 wt%) and aluminum (5.5 wt%) atoms. The solid solution of chromium atoms (atomic radius 0.128 nm) and aluminum atoms (0.143 nm) results in approximately 1.3% lattice distortion (atomic radius difference) in the iron lattice (BCC structure, atomic radius 0.126 nm). According to the Heisenberg exchange interaction model, the lattice distortion enhances the overlap of 3d electron orbitals between adjacent atoms, increasing the exchange integral constant J to 4.8 x 10⁻⁶. -21 J (pure iron is 3.5 x 10) -21 According to the mean-field theory of ferromagnetic phase transitions within the framework of quantum mechanics, the Curie temperature (T) of this iron-silicon-aluminum alloy is... c The temperature can be calculated to be approximately 580℃ using the following formula.

[0054]

[0055] Where J is the exchange integral constant, the larger J is, the stronger the interaction between adjacent spins, and T cThe higher the coordination number, the stronger the overall magnetic order; z is the coordination number (number of adjacent atoms), which is an integer, for example, z=8 in the BCC structure. Increasing the coordination number enhances the overall magnetic order; S is the spin quantum number, which is a half-integer or an integer, such as Fe. 3+ With S = 5 / 2, the larger the spin quantum number, the larger the magnetic moment, and T c The higher; K B is the Boltzmann constant, with a value of 1.38 x 10⁻⁶. -23 J / K, serving as a bridge between temperature and energy, K B Fixed and unchanging.

[0056] During alloying, aluminum preferentially oxidizes to form a continuous aluminum oxide thin film (approximately 50 nm thick), which reduces surface leakage flux and stabilizes the 180° Bloch wall structure through a pinning effect. The addition of chromium suppresses the α→γ phase transformation, allowing the alloy to maintain its BCC structure (lattice constant a = 0.287 nm) at high temperatures, with the cubic magnetocrystalline anisotropy constant K1 remaining at 4.8 x 10⁻⁶. 3 J / m 3 (At 400℃), ensure the stability of the easy axis orientation of the magnetization vector.

[0057] Secondly, the eddy current heating dynamics mechanism is further optimized through the coordinated control of resistivity and dynamic permeability response.

[0058] Copper (2.2 wt%) can be decomposed by amplitude modulation to form a nanoscale copper-rich precipitate (3-8 nm in size). Combined with chromium / aluminum solid solution atomic scattering, the resistivity ρ can be increased to 1.5 μΩ·m at room temperature (approximately 15 times that of pure iron). According to the modified skin effect formula below, at high frequencies of 1-30 MHz, the skin depth of iron-chromium-aluminum alloy is significantly increased compared to pure iron, thus achieving a bulk heating-dominated mode.

[0059]

[0060] Furthermore, based on the Landau-Lifshitz equation, it can be determined that the magnetization response time of this alloy can be shortened, and a smaller eddy current hysteresis angle and a larger power factor can be obtained in the high-frequency state of 1-30MHz, thereby promoting eddy current heating.

[0061] It is worth mentioning that the addition of copper, aluminum and manganese improves the mechanical properties of the material, including reducing hardness and increasing elongation, which is beneficial for processing and manufacturing, while the addition of chromium and aluminum can significantly reduce the oxidation rate and improve oxidation resistance.

[0062] Thirdly, the multi-layered composite structure can form a gradient magnetic permeability distribution. The intensity distribution of the high-frequency magnetic field generated by the smoking device in space usually exhibits a certain gradient. The magnetic composition gradient of the magnetic heating sensor itself (the difference in nickel and iron content along the thickness direction) constructs a magnetic permeability gradient distribution inside. To a certain extent, by matching the magnetic field distribution gradient, magnetic flux leakage can be reduced and energy utilization can be improved.

[0063] In summary, the second magnetic alloy layer in this embodiment achieves magnetothermal stability, high eddy current efficiency, and long-term service reliability through the synergistic design of multi-element alloying, and can better meet the dual response requirements of the heating layer in the aerosol generation device to dynamic temperature field and static magnetic field.

[0064] Example 3

[0065] Adding a small amount of rare earth element R to the magnetic heating sensor e To further optimize the overall magnetic properties of the magnetic heating sensor, a small amount (0.1-5 wt%) of rare earth elements, including one or more of yttrium, scandium, and lanthanides, can be added during material preparation, with the total content controlled within the range of 0.1-5 wt%. There are 15 lanthanides, including lanthanum (La), cerium (Ce), praseodymium (Pr), neodymium (Nd), promethium (Pm), samarium (Sm), europium (Eu), gadolinium (Gd), terbium (Tb), dysprosium (Dy), holmium (Ho), erbium (Er), thulium (Tm), ytterbium (Yb), and lutetium (Lu).

[0066] In some reference examples, heavy rare earth doping, such as dysprosium or terbium, can be used to enhance magnetocrystalline anisotropy. For example, adding 0.5-1.5 wt% dysprosium can improve the magnetocrystalline anisotropy field of iron-based alloys, suppress magnetic domain flipping hysteresis at high frequencies, and significantly improve the effective permeability at high frequencies.

[0067] In some reference examples, heavy rare earth doping, such as dysprosium, can be used to improve the thermal stability of the material and slow down the rate of magnetic permeability decay. For example, the addition of dysprosium can raise the Curie temperature of iron to 800°C and prevent high-temperature demagnetization.

[0068] In some reference examples, light rare earth composite doping, such as cerium or lanthanum, can be used to modify grain boundaries. For example, the addition of lanthanum / cerium composite (total ≤3%) can refine the grain size of the material to the submicron level (<500 nm), reducing coercivity (H) through the grain boundary pinning effect. c <10A / m), improving low-frequency permeability.

[0069] In some reference examples, light rare-earth composite doping with cerium can be used to compensate for magnetic dilution. For example, adding 1 wt% cerium to an Fe-Si-B alloy can form a cerium-rich grain boundary phase (CeFe2B2), utilizing its high resistivity (ρ≈10).-4 To suppress grain boundary eddy current losses, Ω·m is used, while maintaining the high permeability of the main phase.

[0070] In some reference examples, the rare earth-transition metal synergy can be employed, for example, by depositing a samarium-cobalt nanolayer (50-100 nm thick) on an iron substrate, utilizing its high magnetocrystalline anisotropy (K2). u ≈3×10 6 J / m 3 It guides the orientation of the main phase magnetic domains, thereby significantly improving the overall permeability.

[0071] In this third embodiment, rare earth lanthanum and cerium metals were added to the first magnetic metal layer, replacing silicon and manganese respectively. The specific composition is shown in Table 3 below. The thickness of the magnetic metal layer is 0.04 mm.

[0072] Table 3: Material composition of the first magnetic metal layer in Example 3

[0073] wt% 8.95 80.2 5.5 0.8 0.8 0.25 0.3 3.1 0.1％

[0074] According to the experiment, by comparing the magnetization of the alloys in Example 1 and Example 3, it can be found that the composite doping of lanthanum / cerium can significantly improve the magnetic permeability of the material, thereby further enhancing the overall magnetism of the magnetic heating sensor.

[0075] In general, the addition of rare earth elements has two main benefits: first, it can control grain size and purify grain boundaries, thereby reducing the resistance to magnetic domain wall movement; second, it can enhance the 4f electrons (0f...) of lanthanum. 0 ) and cerium 4f 1 Electrons participate in localized electronic hybridization, altering the overlap of iron-3d / nickel-3d orbitals, thus increasing the magnetocrystalline anisotropy constant K1 from approximately 100 J / m in traditional permalloys. 3 Further reduction is possible, down to less than 50 J / m 3 Furthermore, at high frequencies, the grain boundary pinning of lanthanum / cerium reduces the domain wall resonance frequency shift, thereby further improving the effective permeability; thirdly, it enhances the sensitivity of permeability to temperature changes, thus improving the sensitivity of its temperature marking function.

[0076] Example 4

[0077] As in the aforementioned embodiments, each layer of the magnetic heating sensor has a high yield strength and low elongation in its hard state. This state makes it difficult to produce the desired large deformation during extrusion or rolling bonding, which is not conducive to composite processing. Repeated annealing and softening treatment of the material can easily lead to surface oxidation and damage to its magnetic properties. Based on this, in order to improve manufacturability, this fourth embodiment adopts a scheme of applying a thin intermediate metal layer in the structural design of the magnetic heating sensor, which serves to bond the first and second magnetic metal layers.

[0078] The design logic for the intermediate metal layer follows the principle of having a lower hardness and higher ductility than the bonded metal layer. Considering the highest temperature conditions of the application, suitable intermediate metal layer materials include soft metals containing one or more of the elements gold, silver, copper, iron, nickel, and aluminum.

[0079] The application sequence of the intermediate metal layer can be divided into three types: (1) Before the first and second magnetic metal layers are bonded, an intermediate metal layer material is applied to one or more surfaces of one of the materials, or an intermediate metal layer material is applied to one or more surfaces of the two materials, and then the first and second magnetic metal layers are finally bonded. (2) The first and / or second magnetic metal layers are first initially bonded with the intermediate metal layer material, and then the final bonding is further implemented. (3) An intermediate metal layer material is placed between the first and second magnetic metal layers, and then a multilayer simultaneous final bonding process is implemented.

[0080] The intermediate metal layer can be applied using appropriate methods, such as electroplating, electroless plating, cladding, sputtering, lamination, thermal spraying, coating, spraying, application, and sintering.

[0081] like Figure 2 As shown, in this fourth embodiment, an intermediate metal layer 103 is introduced into the magnetic heating sensor strip, with a final thickness of 0.01 mm. The first magnetic metal layer 101 is a 1J30 iron-nickel soft magnetic alloy (Ni30Fe70) with a thickness of 0.03 mm, and the second magnetic metal layer 102 is a special iron-cobalt alloy (Fe30Co70) with a thickness of 0.04 mm. This configuration increases the mechanical interlocking between the interlayer interfaces in the early stage of composite bonding and the interatomic metallurgical bonding in the later stage of processing. It also allows the intermediate metal layer to preferentially undergo plastic flow during subsequent stamping of the composite plate, reducing the risk of interlayer delamination. This results in better manufacturability, processability, and the ability to maintain stable magnetic properties of the material.

[0082] The introduction of the intermediate metal layer serves two main purposes. First, it can absorb the majority of the plastic deformation during the composite process, forming an atomic mechanical bond with the first and second magnetic metal layers. This effectively improves the manufacturability of the bond between the first and second magnetic metal layers and reduces the probability of delamination failure during subsequent multi-pass rolling. Second, the intermediate metal layer and the magnetic metal layer can form a gradient diffusion interface during thermomechanical processing, resulting in a stronger metallurgical bond. This is achieved by controlling the extrusion or rolling temperature and the maximum heat treatment temperature to 0.4T. m Below the melting point of the metal, limited atomic diffusion (diffusion depth of about 5-10 nm) can be achieved, which ensures the interlayer metallurgical bonding and avoids magnetic degradation caused by excessive interdiffusion of elements; thirdly, the intermediate metal layer adopts a high stacking fault energy metal (such as aluminum, whose stacking fault energy is about 200 mJ / m). 2It can absorb deformation energy through dislocation slip mechanism. When the composite plate undergoes 50% cold rolling deformation, the intermediate layer undergoes dynamic recovery and forms a subcrystalline structure (e.g., grain size of about 500 nm), while the magnetic layer maintains the deformation texture. The overall lattice mismatch stress is reduced. This differential deformation behavior allows the overall structure to maintain magnetic anisotropy while having a large rolling elongation.

[0083] After obtaining the above-mentioned series of magnetic heating sensor strips, they can be further applied to electromagnetic induction heating cartridges, that is, integrated with sheet-type or extruded cartridges. Before being assembled into the aerosol matrix, the cartridges are in the form of long strip rolls. During the cartridge forming process, the magnetic heating sensor strips and the aerosol matrix strips are cut into small segments at the same time, thus forming individual magnetic heating sensors.

[0084] The magnetic heating sensor is ultimately configured in the cartridge in a sheet-like or roughly sheet-like form to facilitate assembly and to achieve a strong and stable coupling with the magnetic field.

[0085] Considering the size of the cartridge and the coupling characteristics required, the equivalent average thickness of the magnetic heating sensor is defined as 0.03-0.085 mm, the equivalent average width or unfolded width is 1-6 mm, and the equivalent average length is 5-20 mm.

[0086] Example 5

[0087] like Figure 3 As shown in this embodiment, Example 5 illustrates a three-section extruded electromagnetic cigarette cartridge with an outer diameter of 7 mm and a total length of 43 mm. It consists of a smoke-generating section 400, a cooling section 500, and a filter section 600, with corresponding lengths of 15 mm, 15 mm, and 13 mm, respectively. It also includes an outer cigarette paper 700. The smoke-generating section 400 is prepared by co-molding extrusion and drying of a magnetic heating sensor strip and an aerosol matrix paste, ultimately forming a composite core structure. This is then cut into small segments and finally rolled into the inside of the cartridge, where the extruded aerosol matrix 402 and the magnetic heating sensor 401 are tightly bonded together.

[0088] In this embodiment, the magnetic heating sensor 401 is shaped as a strip with a certain degree of curvature, such as a sheet with a semi-circular cross-section. This is a pretreatment measure taken to increase the bonding strength at the contact point with the paste and to mitigate the risk of separation during drying and cutting. Alternative pretreatment methods include roughening the surface of the magnetic heating sensor strip, for example, by using processes such as sandblasting, wire drawing, embossing, or scratching to increase its surface roughness.

[0089] In the description of this utility model, it should be understood that the terms "center", "longitudinal", "lateral", "length", "width", "thickness", "upper", "lower", "front", "rear", "left", "right", "vertical", "horizontal", "top", "bottom", "inner", "outer", "clockwise", "counterclockwise", etc., indicating the orientation or positional relationship are based on the orientation or positional relationship shown in the accompanying drawings, and are only for the convenience of describing this utility model and simplifying the description, and are not intended to indicate or imply that the device or component referred to must have a specific orientation, or be constructed and operated in a specific orientation, and therefore should not be construed as a limitation of this utility model.

[0090] The foregoing has shown and described the basic principles, main features, and advantages of this utility model. Those skilled in the art should understand that this utility model is not limited to the above embodiments. The embodiments and descriptions in the specification are merely preferred examples and are not intended to limit the utility model. Various changes and modifications can be made to this utility model without departing from its spirit and scope, and all such changes and modifications fall within the scope of the claimed utility model. The scope of protection of this utility model is defined by the appended claims and their equivalents.

Claims

1. A high-magnetic heating sensor, characterized in that, It includes a first magnetic metal layer and a second magnetic metal layer, the thickness of the first magnetic metal layer being less than or equal to the thickness of the second magnetic metal layer; wherein the first magnetic metal layer contains iron and nickel, and the second magnetic metal layer contains iron; the equivalent average thickness of the high magnetic heating sensor is 0.03-0.085 mm, and the magnetic permeability is 5-70000 H / m.

2. The high magnetic heating sensor according to claim 1, characterized in that, It also includes a metal interlayer, the ductility of which is greater than that of the first magnetic metal layer and the second magnetic metal layer.

3. The high magnetic heating sensor according to claim 1, characterized in that, The rigidity of the first magnetic metal layer is greater than that of the second magnetic metal layer.

4. The high magnetic heating sensor according to claim 1, characterized in that, It is configured as a sheet or a curved shape.

5. A type of e-cigarette cartridge, characterized in that, Includes the high magnetic heating sensor as described in any one of claims 1 to 4.

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