Aerosol generating product

Abstract

The application discloses an aerosol generating product, including an aerosol generation substrate segment, the substrate segment includes an aerosol generation substrate and a susceptor assembly; the susceptor assembly inductively heats the aerosol generation substrate under the influence of an alternating magnetic field, and the susceptor assembly is made of a soft magnetic alloy, and the soft magnetic alloy has a single layer with an uniform distribution of elements; the soft magnetic alloy has an average grain size of 50-70 µm, and a grain size number of 5.5-4.5. This micro-structured susceptor assembly meets the requirements for aerosol generator susceptor regarding magnetic properties and Curie temperature, ensuring that the temperature rises rapidly in the preheating stage, and ferromagnetic-paramagnetic transition occurs before reaching 400°C and completely loses its magnetism. It can be used in the field of heated cigarettes using an electromagnetic heating process with automatic temperature control based on the non-contact radio transmission concept, considerably lowering the risk of heating cigarettes in this mode.

Description

Technical field

[0001] The present application relates to the technical field of heat-not-burn tobacco, in particular to an aerosol generating product.Background

[0002] In the field of heat-not-burn tobacco, the aerosol generation system includes an aerosol generation device and an aerosol generating product. The Magnetic Coupling Resonance Wireless Power Transfer (MCR-WPT) system offers excellent energy conversion efficiency and non-contact heating, making it capable of efficiently heating tobacco products while also improving the robustness of heating system. It is a preferred solution to develop an aerosol generation device based on MCR-WPT principle. The susceptor is arranged in the aerosol generation device or in the aerosol generating product, and it heats the aerosol generating product via the resonant wireless power transfer technique.

[0003] The material of the susceptor is expected to have the appropriate high-frequency permeability, resistivity and material size to match the specific coil parameters and external circuit characteristics, so as to maintain the resonance state in the basic constant temperature stage and achieve the purpose of heating non-combustible cigarettes. The heating procedure of aerosol products using the susceptor includes two stages: preheating and basic constant temperature. To achieve the desired user experience, the temperature is usually raised quickly during the preheating stage in order to efficiently release volatile smoke substances. According to the characteristics of automatic temperature control of soft magnetic core materials, during the preheating stage, the temperature of the core materials can continuously rise to the Curie point, after which the core materials lose their magnetism and cool down because they can no longer absorb energy from the external magnetic field. During inhalation and exhalation, the temperature of core material drops significantly due to the inflow of cold air, and the magnetic properties of the material recover, thus developing a cycle of heating-cooling and achieving the purpose of automatic temperature control.

[0004] However, when the temperature exceeds 400°C, it is likely to increase the risk of harmful release and tobacco burning. In order to avoid the release of harmful components and reduce the potential burning risk, it is necessary to reduce the magnetothermal conversion ability and Curie temperature of the susceptor material during electromagnetic induction, but this will lead to the situation that the use temperature of cigarettes cannot be reached. Therefore, a susceptor material must be provided that takes into account the application size, permeability, saturation magnetic induction intensity, coercivity, resistivity, and Curie temperature in order to meet its application in the field of heat-not-burn products and alleviate the problem of insufficient or excessive heating of the aerosol generation substrate by the heater.Summary

[0005] In view of this, the application provides an aerosol generating product and a preparation method thereof, which meet the requirements of the susceptor of the aerosol generation device for magnetic properties and Curie temperature, ensure the rapid temperature rise in the preheating stage, and realize ferromagnetic-paramagnetic transformation and complete demagnetization before reaching 400°C, thereby reducing the risk of the aerosol generation substrate being overheated by the heater.

[0006] In order to achieve the above technical objectives, the application adopts the following technical solutions.

[0007] In a first aspect, the application provides a heated aerosol generating product for generating an inhalable aerosol, which includes an aerosol generation substrate segment, the aerosol generation substrate segment includes an aerosol generation substrate and a susceptor assembly; the susceptor assembly inductively heats the aerosol generation substrate under the influence of an alternating magnetic field, and the susceptor assembly is made of a soft magnetic alloy, and the soft magnetic alloy has a single layer with an uniform distribution of elements; the soft magnetic alloy has an average grain size of 50-70 µm, and a grain size number of 5.5-4.5.

[0008] The soft magnetic alloy includes components of iron, molybdenum and nickel, with molybdenum accounting for 3.5%-6% and nickel accounting for 77%-81% of the total mass of the soft magnetic alloy.

[0009] Preferably, the soft magnetic alloy further includes chromium, accounting for 0.2-0.5% of the total mass of the soft magnetic alloy.

[0010] Preferably, the soft magnetic alloy further includes manganese, accounting for 0.1%-0.5% of the total mass of the soft magnetic alloy.

[0011] Preferably, the soft magnetic alloy further includes components of silicon and aluminum, with silicon accounting for 0.1%-0.4% and aluminum accounting for 0.15%-0.7% of the total mass of the soft magnetic alloy.

[0012] Preferably, the soft magnetic alloy includes the following components in parts by mass: 77-81 parts of nickel, 3.5-6.0 parts of molybdenum, 0.2-0.5 part of chromium, 0.1-0.5 part of manganese, 0.1-0.4 part of silicon, 0.15-0.7 part of aluminum and 11-18 parts of iron.

[0013] Preferably, the aerosol generation substrate segment susceptor assembly has a thickness of 0.03-0.18 mm, a width of 1.5-4.5 mm and a length of 9-18 mm.

[0014] Preferably, the heated aerosol generating product for generating an inhalable aerosol further includes a filter segment and a cooling segment, and the cooling segment is located between the aerosol generation substrate segment and the filter segment; the aerosol generation substrate is made of tobacco materials or non-tobacco materials and distributed in a filiform, flaky or granular manner, and the susceptor assembly is wrapped by the aerosol generation substrate.

[0015] The preparation method of the susceptor assembly includes the following steps. S1. weighing an alloy raw material and coke according to parts by mass, and sequentially performing smelting, remelting, hot forging and cogging, hot rolling and cold rolling processes to obtain a cold-rolled material; and S2. placing the cold-rolled material and a mixed powder in a vacuum hydrogen annealing furnace for annealing process, and a annealing process temperature is 1000-1200°C, a heat preservation period is 70-120 min, a cooling speed is 150-220°C / h, and after lowering the temperature to 580-630°C, performing air cooling or furnace cooling to reach 100-200°C.

[0016] Preferably, the mixed powder is 100-300 mesh mixed powder, including a mixture of Fe, MnO, SiO 2 , Al 2 O 3 and C powders; and a volume ratio of the mixed powder to the cold-rolled material is 0.05: 100.

[0017] The beneficial effects of the application are as follows.

[0018] The application provides a heated aerosol generating product for generating an inhalable aerosol, which includes an aerosol generation substrate segment, the aerosol generation substrate segment includes an aerosol generation substrate and a susceptor assembly; the susceptor assembly inductively heats the homogeneous tobacco material of the aerosol generation substrate under the influence of an alternating magnetic field to generate aerosol for users to inhale. The susceptor assembly is a soft magnetic alloy with a single-layer homogenous structure, allowing for application in the field of heating non-combustible tobacco. The soft magnetic alloy can achieve non-contact heating of the aerosol generation substrate using the resonant wireless power transfer technique, and the soft magnetic alloy with a single-layer homogenous structure has a stable Curie temperature range. Controlling the average grain size of the soft magnetic alloy to 50-70m and the grain size number to 5.5-4.5 greatly influences the saturation magnetic induction intensity. For magnetic domain rotation, the larger the grain size of the susceptor assembly, the greater the saturation magnetic induction intensity. The appropriate magnetic permeability, lower coercivity and appropriate resistivity at high frequency can ensure the rapid temperature rise in the preheating stage. In this way, the susceptor assembly can completely lose magnetism before reaching 400°C, which will stop heating the aerosol generation substrate and improve user satisfaction, reduce the risk of users using aerosol products, and alleviate the heater's overheating of the aerosol generation substrate.Brief description of drawings

[0019] Fig. 1 is a metallographic examination diagram of the soft magnetic alloy assembly 100X. Fig. 2 is a metallographic examination diagram of the soft magnetic alloy assembly 200X. Fig. 3 is an examination diagram of a field emission scanning electron microscope of a typical area of the soft magnetic alloy assembly. Fig. 4 is an energy spectrum diagram of elemental analysis of point defects in Area A of Fig. 3. Fig. 5 is an energy spectrum diagram of elemental analysis of point defects in Area B of Fig. 3. Fig. 6 is an energy spectrum diagram of elemental analysis of point defects in Area C of Fig. 3. Fig. 7 is an examination diagram of a field emission scanning electron microscope of a typical area of the soft magnetic alloy assembly. Fig. 8 is a hysteresis B-H graph of the soft magnetic alloy assembly. Fig. 9 is a hysteresis B-H graph of the soft magnetic alloy assembly. Fig. 10 is a schematic gray scale diagram of the cross-section of the soft magnetic alloy. Fig. 11 is a schematic diagram of magnetization-temperature curve and derivative curve of the soft magnetic alloy. Fig. 12 is a schematic diagram of magnetization-temperature curve and derivative curve of the soft magnetic alloy. Fig. 13 shows a ternary structure aerosol generating product. Fig. 14 shows a quaternary structure aerosol generating product. Fig. 15 is a schematic diagram of the time-temperature curve of the soft magnetic alloy in the aerosol generation device.

[0020] The reference signs in the drawings are as follows. 1. Aerosol generation substrate segment; 2. Cooling segment; 3. Filter segment; 4. Anti-permeation segment.Detailed description of embodiments

[0021] In order to make the objectives, technical solutions and beneficial effects of the present application clearer, the present application will be described in further detail below with embodiments. It should be understood that the specific embodiments described he re are only used to illustrate the application, rather than to limit the application.

[0022] In the field of heat-not-burn products, the aerosol generator has the characteristics of automatic temperature control based on the soft magnetic core material. In the preheating process, the susceptor material continues to heat until it reaches Curie point, after which it loses magnetism. During inhalation and exhalation, air enters the cigarette core to contact the susceptor material, so that the temperature of the susceptor material drops, and the magnetic conductivity is restored, thus developing a heating-cooling cycle and achieving the purpose of automatic temperature control. However, in the field of heat-not-burn tobacco products, the existing alloy technology can not meet the design requirements for magnetic properties, Curie temperature and magnetic permeability, and the prepared alloy materials are all multilayer materials. Because the Curie temperature points of two- or more-layered susceptor materials are different, the heating temperature of aerosol products may surpass 400°C, which significantly increases the release of harmful components and the risk of combustion. In view of this, the present application provides a homogeneous tobacco core material with a single-layer structure, which realizes non-contact heating of aerosol generating products based on the resonant wireless power transfer principle. The preheating stage involves rapid heating. Followed by a ferromagnetic-paramagnetic transition before reaching 400°C and complete demagnetization, and then stop heating, which is beneficial to improve the user experience and effectively reduce the release of harmful substances and combustion risks of aerosol products.

[0023] The application provides a heated aerosol generating product used for generating an inhalable aerosol, which includes an aerosol generation substrate segment, the substrate segment includes an aerosol generation substrate and a susceptor assembly; the susceptor assembly inductively heats the aerosol generation substrate to generate a substrate under the influence of an alternating magnetic field, and the susceptor assembly is made of a soft magnetic alloy, the soft magnetic alloy has a single-layer structure; the soft magnetic alloy has an average grain size of 50-70 µm, and a grain size number of 5.5-4.5

[0024] The soft magnetic alloy meets the requirements of aerosol generator susceptor on magnetic properties and Curie temperature, ensuring that the temperature rises rapidly in the preheating stage, and ferromagnetic-paramagnetic transition occurs before reaching 400°C and completely loses its magnetism. It can be used in the field of heated cigarettes using an electromagnetic heating process with automatic temperature control based on the non-contact radio transmission concept, considerably lowering the risk of heating cigarettes in this mode. The grain size of the soft magnetic alloy affects the saturation magnetic induction intensity of the susceptor. For the mode that the magnetization mode is mainly domain rotation, the larger the grain size of the soft magnetic alloy is, the greater the saturation magnetic induction intensity is.

[0025] The single-layer structure defined in the application meets the following two conditions: the manufacturing process of soft magnetic alloy only includes melting, remelting, hot forging and cogging, hot rolling, cold rolling and annealing, and does not include any of the following processes: electroplating, coating, welding and coating. In the gray scale image of soft magnetic alloy captured by scanning electron microscope, the contrast of the whole image is basically uniform within the range of 100-3000 times, visible to the naked eye. The color area with the widest area in the main part of soft magnetic alloy accounts for at least 95% of the area value of all areas of soft magnetic alloy.

[0026] The soft magnetic alloy includes components molybdenum and nickel, with molybdenum accounting for 3.5%-6% and nickel accounting for 77%-81% of the total mass of the soft magnetic alloy, and the balance being iron. The mass ratio of nickel to molybdenum is 15.2-16.5: 1.

[0027] The soft magnetic alloy in this application includes not only iron, nickel and molybdenum, but also one or more of Al, Cr, Mn and Cu, and other metals or nonmetals that can be used for alloying. The elements that can be mixed include but are not limited to Si, C, O, S and P. In some embodiments, the surface of the soft magnetic alloy in this solution is locally treated to form defects.

[0028] The Curie temperature of a soft magnetic alloy is mainly related to the spatial arrangement structure of magnetic atoms and non-magnetic atoms. The soft magnetic alloy in this solution controls the composition ratio of nickel and molybdenum, and adding a certain proportion of molybdenum to reduce the relative content of nickel is beneficial to increase the initial permeability and resistivity of the alloy. Furthermore, molybdenum is a paramagnetic element, and a solid solution is formed with paramagnetic molybdenum element and ferromagnetic Ni and Fe elements. Because of molybdenum's solid solution characteristic, electrons in the outer layer of molybdenum atom are transported to ferromagnetic atoms, and the spin is reversely filled, reducing the magnetic exchange effect of ferromagnetic atoms. At the same time, the solid solution behavior increases the crystal lattice of ferromagnetic materials, increases the distance between ferromagnetic elements, and weakens the magnetic exchange effect of ferromagnetic atoms, reducing the remanence and coercivity of materials and improving the initial permeability. Molybdenum is added in one of two ways: at the start of batching or later in the refining process. Proper Ni-Mo ratio is beneficial to control the Curie temperature of soft magnetic alloys and keep it between 350-400°C.

[0029] The soft magnetic alloy further includes chromium, accounting for 0.2-0.5% of the total mass of the soft magnetic alloy. When the relative content of nickel is reduced, the initial magnetic permeability is improved, the oxidation resistance of the alloy is improved, and the coercivity is effectively reduced.

[0030] The soft magnetic alloy further includes manganese, accounting for 0.1%-0.5% of the total mass of the soft magnetic alloy, which can be added in the refining process to achieve the purpose of alloying. At the same time, Mn element is easy to combine with S element, which prevents element Fe and element S from generating FeS to increase the thermal brittleness of the alloy.

[0031] The soft magnetic alloy further includes components of silicon and aluminum, with silicon accounting for 0.1%-0.4% and aluminum accounting for 0.15%-0.7% of the total mass of the soft magnetic alloy. Preferably, the mass ratio of manganese to silicon is 0.9-2.95: 1. The elements manganese, silicon, and aluminum efficiently lower the high proportion of oxides in the alloy, effectively reduce its coercivity, and counteract the increase of coercivity of soft magnetic alloy caused by introducing some oxides in annealing process.

[0032] Furthermore, the addition of a small amount of element Al might create lattice distortion of metal atom arrangement, improving the solid solution behavior of element Mo to ferromagnetic elements Ni and Fe. Strengthening solid solution behavior increases the lattice of ferromagnetic crystal and the distance between ferromagnetic elements, weakens the magnetic exchange effect of ferromagnetic atoms, reduces material remanence and coercivity, and improving initial permeability. The increase of initial magnetic permeability is beneficial to maintain good magnetic properties after introducing surface oxidation in the late annealing stage.

[0033] The mass ratio of nickel to iron in the soft magnetic alloy is 4.5-5:1, which is beneficial to form the best short-range ordered structure around Ni 3 Fe. And at this point, it has the smallest magnetocrystalline anisotropy constant and saturated magnetostrictive coefficient.

[0034] The soft magnetic alloy includes the following components in parts by mass: 77-81 parts of nickel, 3.5-6.0 parts of molybdenum, 0.2-0.5 part of chromium, 0.1-0.5 part of manganese, 0.1-0.4 part of silicon, 0.15-0.7 part of aluminum and the balance of about 11-18 parts of iron.

[0035] The thickness of the susceptor assembly is 0.03-0.18 mm, the width is 1.5-4.5 mm, the length is 9-18 mm. Preferably, the thickness is 0.105-0.15 mm. Preferably, the width is 2-4 mm. Preferably, the length of the material is 10-14 mm.

[0036] The Curie temperature of the soft magnetic alloy is 350-400°C, preferably 380-395°C. When the soft magnetic alloy assembly approaches the Curie temperature, the magnetic permeability of the soft magnetic alloy assembly will be significantly lowered to near-zero levels, and the loss power of the soft magnetic alloy assembly will be significantly reduced to near-zero levels. A Curie temperature of no more than 400°C can prevent the release of hazardous components and lower potential combustion risks.

[0037] Under the condition that the soft magnetic alloy has a thickness of 0.1-0.18 mm and a magnetic field frequency of 60Hz, the saturation magnetic induction intensity between 0.4-20Oe is 7000-10000Gs, preferably 7000-9000Gs, more preferably 7000-8500Gs. The saturation magnetic induction intensity of this solution is employed to satisfy the rapid temperature increase process in the preheating stage of the aerosol generation substrate segment, which greatly improves the magnetic flux value in the coil.

[0038] According to the ASTM A772 / A772M magnetic permeability test standard, the soft magnetic alloy has a thickness of 0.1-0.18 mm. Under the condition that the magnetic field frequency is 60Hz, the maximum magnetic permeability is 120-275 MH / m, preferably 150-220 MH / m, more preferably 190-200 Mh / m. A certain skin depth can be ensured within the maximum magnetic permeability range of this solution, so as to ensure that eddy current loss of a certain size can be effectively converted into heat energy and absorbed by aerosol generation substrate to generate aerosol.

[0039] Under the condition that the thickness of the soft magnetic alloy is 0.1-0.18 mm and the magnetic field frequency is 60Hz, the coercivity of the soft magnetic alloy is 0.1-4A / m, more preferably 0.1-2A / m, and even more preferably 0.1-1.5A / m. The magnetic stability of the soft magnetic alloy assembly is high within this range.

[0040] Under the condition that the thickness of the soft magnetic alloy is 0.1-0.18 mm and the magnetic field frequency is 60Hz, the room temperature resistivity of the soft magnetic alloy is 40-100µΩcm, preferably 40-80µΩcm, more preferably 40-70µΩcm.

[0041] As shown in Figs. 14 and 15, the application provides an aerosol generating product, further including a filter segment 3 and a cooling segment 2, the cooling segment 2 is located between the aerosol generation substrate segment 1 and the filter segment 3. The aerosol generation substrate is made of tobacco materials or non-tobacco materials and distributed in a filiform, flaky or granular manner, and the susceptor assembly is wrapped by the aerosol generation substrate. Specifically, the iliform, flaky tobacco or non-tobacco material surrounds the susceptor assembly, and the granular tobacco or non-tobacco material buries the susceptor assembly in a stacked manner. Fig. 14 is an aerosol generating product with ternary structure, including a filter segment 3, a cooling segment 2 and an aerosol generation substrate segment 1. Fig. 15 is a aerosol generating product with quaternary structure, including a filter segment 3, a cooling segment 2, an aerosol generation substrate segment 1 and an anti-permeation segment 4. The aerosol generation substrate segment 1 includes an aerosol generation substrate and the above-mentioned soft magnetic alloy assembly. The soft magnetic alloy heats the aerosol generation substrate based on the electromagnetic induction heating principle. The aerosol generation substrate may be tobacco flakes, cut tobacco, shred tobacco, expanded cut tobacco, expanded shred tobacco and tobacco particles. It contains smoking substances such as glycerol and propylene glycol, nicotine and cannabis substances. Flavors and scents can also be added. Volatile smoke, nicotine, cannabis, and flavorings are released when the aerosol generation substrate is heated, producing steam that is cooled throughout the inhalation and exhalation process. Droplets are formed when steam condenses as a result of the nucleation mechanism. Aerosol droplets with big particle sizes are formed when the temperature drops low enough and there are enough droplets to condense with one another. The cooling segment 2 reduces the temperature of flue gas, which aids in the cooling of volatile substances from the aerosol generation substrate segment, resulting in the formation of aerosols. It typically features a smooth air passage for transporting vapor substances or aerosols, and its cooling mechanism is convection heat exchange or phase change of cooling materials. A filter segment is arranged away from the aerosol generation substrate segment, which is in contact with the oral cavity to support lung aspiration and filter harmful substances at the same time. The filter segment is often made of fiber bundles, and dense fiber bundles can effectively intercept harmful substances in smoke. Furthermore, at another end of the aerosol generation substrate segment, an anti-permeation segment 4 is provided. It can prevent aerosols or vapor substances from escaping in all directions, preventing pollution and keeping the aerosol generation device clean.

[0042] The preparation method of the susceptor assembly includes the following steps. S1. weighing an alloy raw material and coke according to parts by mass, and sequentially performing smelting, remelting, hot forging and cogging, hot rolling and cold rolling processes to obtain a cold-rolled material; and S2. placing the cold-rolled material and a mixed powder in a vacuum hydrogen annealing furnace for annealing process, and a annealing process temperature is 1000-1200°C, a heat preservation period is 70-120 min, a cooling speed is 150-220°C / h. The mixed powder includes a mixture of Fe, MnO, SiO 2 , Al 2 O 3 and C powders.

[0043] The annealing process significantly affects the magnetic properties of the soft magnetic alloys, such as magnetic permeability and saturation magnetic induction intensity. The purity and grain size of the soft magnetic alloy increase with higher annealing temperature and longer heat preservation period. This leads to an increase in saturation magnetic induction intensity and maximum magnetic permeability. The above mentioned annealing temperature and heat preservation period are beneficial to properly adjust the maximum magnetic permeability and saturation magnetic induction intensity. By controlling the cooling speed, especially the cooling speed of secondary cooling at the beginning of about 600°C, the initial magnetic permeability of the alloy can be significantly increased, but only the maximum relative magnetic permeability is slightly increased, and finally a slightly higher saturation magnetic induction intensity and appropriate maximum magnetic permeability can be realized.

[0044] The mixed powder's function is to oxidize the alloy surface, and the oxidation process on the alloy surface will greatly reduce the maximum permeability of the material, enhance coercivity, and reduce resistivity. Controlling the addition and preparation of the mixed powder not only stabilizes the production process but also effectively controls the inclusions on the alloy surface, which is necessary to achieve the invention's goal of producing the material with the largest reduction in magnetic permeability.

[0045] After 30-50 parts of Fe powder, 25-30 parts of SiO 2 , 10-15 parts of C powder, 15-19 parts of Al 2 O 3 , 1-5 parts of MnO are mixed, elements with inclusions may be introduced into the alloy, including but not limited to Al, Si, C, O, Mn, S and P. These elements with inclusions mainly exist in the form of metal oxides or sulfides. The nonmetallic inclusions will increase the grain size of the alloy, create pinning effect, increase and complicate the magnetic domains, decrease the magnetic permeability of the alloy, slightly increase the saturation magnetic induction intensity and increase the coercivity.

[0046] On the basis of controlling the grain size and nickel-molybdenum ratio of soft magnetic alloy, special surface oxidation treatment is adopted in the annealing process, so that the Curie temperature, saturation magnetic induction intensity, coercivity and resistivity of soft magnetic alloy do not change significantly. Moreover, the magnetic permeability of soft magnetic alloy is reduced, making it suitable for the application in the field of heated cigarettes in the electromagnetic heating process for automatic temperature control based on the non-contact radio transmission principle.

[0047] The alloy raw material used in step S1 include but are not limited to iron, nickel, molybdenum, chromium, manganese and silicon. Iron and nickel are added in the smelting step, and nickel or other alloy raw materials are added in the smelting and / or remelting step.

[0048] In some embodiments, the smelting process of step S1 is as follows.

[0049] Weighing iron, nickel and molybdenum according to the requirements of the total components in the finished soft magnetic alloy and the calculation of the purity of the raw material, meanwhile, adding coke which is half of the total mass of the iron, nickel and molybdenum, placing the coke in a feeding area, adding the coke into a vacuum induction melting furnace from the feeding area, vacuumizing, and then smelting in a mixed furnace, the smelting temperature is 1500-1600°C and the smelting period is 60-100 min. The refining process continues after melting. In the refining process, 0.5 part of manganese ore with 25% manganese content is added to achieve the purpose of alloying. The refining period is 0.5-1.5h and the refining temperature is 1550-1650°C. Following refinement, casting is performed at 1400-1500°C. Demoulding and furnace numbering are then done to produce ingots. Other alloys include, but are not limited to, molybdenum, chromium, manganese, and silicon, which meet the total composition requirements of the finished soft magnetic alloy. In some embodiments, the mass ratio of iron, nickel, and molybdenum in step S1 is 2-3: 9-10: 0.5-1, and other components can be supplemented or adjusted in the later remelting step.

[0050] In some embodiments, the remelting process of step S1 is as follows.

[0051] Cutting the ingot into small pieces of blocks of 5*5*5 mm and polishing the small pieces to remove oil stains and rust on the surface. A graphite crucible is lined in a magnesia crucible, the bottom of the graphite crucible is padded with 0.8-1.5 wt% electrolytic nickel plate, and then a piece of ingot block is placed, with 0-0.1 wt% fused magnesia filling the gap between the ingots. Then it is added into a vacuum induction melting furnace and vacuumized. Then smelting in a mixed furnace, 10KW power supply is used for melting, the smelting temperature is 1500-1600°C, and the smelting period is 50-80 min. 0.06-0.2 wt% of graphite carbon powder and 0.03-0.07 wt% of Si-Ca-Ba powder with particle size less than 1.0 mm are added with a ratio of 2:1 for three times. The interval between the first and second addition is 5-10 min, and 0-0.1 wt% of molybdenum bar is added for the third time. After the raw materials are added, the refining period is 20 - 40 minutes, with the heating power adjusted to 2KW. After the heating is finished, when the temperature is dropped to 300°C, the circuit is closed, the vacuum degree is maintained, and the sample is cooled in the furnace to achieve the remelted ingot.

[0052] After the alloy is smelted and refined by vacuum induction furnace for the first time (that is, the smelting process), cleaning its surface and performing secondary remelting. This step is beneficial to the removal of P, S, and other elements in the alloy, as well as reducing the proportion of non-metallic elements in the alloy to stabilize the composition of the alloy and the stability of subsequent processing technology. The proportion of nonmetal and metal elements in an alloy can be effectively controlled during remelting by adding materials or modifying the process, and the alloy composition can be adjusted twice. At this stage, the alloy composition is sampled and analyzed to confirm that it falls within a preset range. The soft magnetic alloy was then made into a material with a thickness of 0.03-0.18 mm by hot forging, cogging, hot binding, and cold binding. The cold-rolled material was sampled to determine its magnetic properties, Curie temperature, and resistivity. The specifics are as follows.

[0053] The types and amounts of raw materials used in the aforementioned smelting and remelting steps might be added in stages. In some embodiments, the soft magnetic alloy assembly consists of 77-81 parts nickel, 11-18 parts iron, 3.5-6.0 parts molybdenum, 0.2-0.5 parts chromium, 0.1-0.5 parts manganese, and 0.1-0.4 parts silicon.

[0054] In some embodiments, the hot forging and cogging process of step S1 is as follows.

[0055] Depressurizing the smelting furnace, taking out the crucible and the remelt ingot, placing the remelted ingot in a chamber furnace, raising the temperature in the furnace to 1250-1300°C in 50-70 min, performing hot-forging under the action of a 2-ton steam hammer for 5-15 min, and grinding with a surface grinding wheel to obtain a billet.

[0056] In some embodiments, the hot rolling process of step S1 is as follows.

[0057] After heating the billet to 1150-1250°C, adopting a Four-Roll Reversible Hot Rolling Mill, performing heat preservation for three times for 30-60 min, 20-40 min and 15-30-60min. The thickness after three times of hot rolling is 15-20 mm, 8-15 mm and 3-8 mm. The deformation temperature range of the hot rolling processing is 900-1200°C, and further it may be 1000-1200°C. The surface temperature of hot-rolled plate is tested by infrared thermometer, and hot rolling is stopped when the temperature is lower than 1000°C, preferably 900°C, to obtain a hot-rolled material.

[0058] In some embodiments, the cold rolling process of step S1 is as follows.

[0059] Performing cold rolling on the hot-rolled material with a Four-Roll Reversible Hot Rolling Mill to a thickness of 1-1.5 mm, and further rolling the cold-rolled material to a thickness of 0.03-0.18 mm with the Four-Roll Reversible Hot Rolling Mill to obtain a cold-rolled material.

[0060] Before the final annealing process, it is necessary to obtain stable semi-finished materials and cold-rolled material with expected material properties. The semi-finished material is then annealed, which helps to eliminate impurities and internal stress from the alloy, and the alloy is recrystallized to obtain a disordered and uniform crystal structure.

[0061] In some embodiments, the annealing process of step S2 is as follows.

[0062] Performing annealing process on the cold-rolled material, preparing a mixed powder with 100-300 meshes, putting it in a vacuum hydrogen annealing furnace together with the cold-rolled material, raising the temperature in the furnace to 1000-1200°C for 60-120 min, keeping the temperature for 70-120 min, then cooling to 580-630°C according to the cooling speed of 150-220°C / h, and then cooling by air or with the furnace to 100-200°C and discharging. For the cooling mode with the furnace, the temperature is reduced from 600°C to 300°C for 30-60min, and the cooling rate is 300 - 600°C / h. For air cooling, the temperature is reduced from 600°C to 300°C for 8-20 min, and the cooling rate is 900-2250°C / h. During this annealing process, the alloy surface is oxidized to some extent, and proper surface oxidation can make the magnetic properties of the material meet the requirements. The annealing temperature, heat preservation period, cooling speed and air cooling mode adopted in the annealing process of this solution are beneficial to control the average grain size of 50-70 mm and the grain size number of 5.5-4.5. The grain size of the soft magnetic alloy affects the saturation magnetic induction intensity of the material. For the mode that the magnetization mode is mainly domain rotation, the larger the grain size of the soft magnetic alloy is, the greater the saturation magnetic induction intensity is.

[0063] In the smelting process of the alloy, due to the influence of the purity of raw materials, the deoxidation of some metals in the smelting process and the presence of pollutants on the furnace wall, there will be a certain proportion of oxides in the alloy composition. In the preparation process of soft magnetic alloys, the genereal oxides include MnO, SiO 2 and Al 2 O 3 . The magnetization modes of soft magnetic alloys mainly include reversible domain rotation and irreversible domain-wall motion. Because the magnetic field intensity is generally not higher than 50Oe in the application of magnetothermal conversion in the field of heat-not-burn tobacco, the magnetic domain rotation and relatively few domain-wall motion mainly occur in soft magnetic alloys. The presence of more oxides causes the soft magnetic alloy to do two things: first, when it is magnetized, a demagnetization field is created, creating a magnetic domain structure inside the alloy; second, the oxide causes a pinning effect within the alloy, increasing coercivity and hysteresis loss, making it harder to magnetize and requiring more external force to move the domain wall. The magnetization of soft magnetic alloys is typically hampered by the presence of oxides during the preparation process, which can result in an increase in coercivity and a decrease in maximum magnetic permeability.

[0064] The soft magnetic alloy of the application has large grain size, high saturation magnetic induction intensity and low magnetic permeability, and cooperates with the component ratio of molybdenum and nickel to jointly improve the magnetic properties of the soft magnetic alloy. The particle size and particle size number of the soft magnetic alloy are controlled by adjusting various parameters of the annealing process, so that the magnetic permeability of the susceptor assembly is low, the saturation magnetic induction intensity is high, and the average particle size is controlled to be 50-70m, and the particle size number is 5.5-4.5, thereby achieving the most optimal properties.

[0065] The mixed powder includes the following components in parts by mass: 30-50 parts of Fe powder, 25-30 parts of SiO 2 , 10-15 parts of C powder, 15-19 parts of Al 2 O 3 and 1-5 parts of MnO. Preferably, the particle size of the mixed powder is 100-300 meshes.

[0066] Preferably, the volume ratio of the mixed powder to the cold-rolled material is 0.05-0.15: 100.

[0067] The Curie temperature of the soft magnetic alloy obtained by the above process steps as an aerosol generation substrate segment for induction heating is 350-400°C. Under the condition that the soft magnetic alloy has a thickness of 0.1-0.18 mm and a magnetic field frequency of 60Hz, the saturation magnetic induction intensity between 0.4-20Oe is 7000-10000Gs. The maximum magnetic permeability of soft magnetic alloy is 120-275 MH / m when the thickness is 0.1-0.18 mm and the magnetic field frequency is 60Hz. The coercivity of soft magnetic alloy is 0 - 4 A / m when the thickness is 0.1-0.18 mm and the magnetic field frequency is 60Hz. The room temperature resistivity of soft magnetic alloy is 40-100 µω •cm when the thickness is 0.1-0.18 mm and the magnetic frequency is 60Hz.

[0068] This solution will be further explained by specific embodiments.Eembodiment 1

[0069] A heated aerosol generating product for generating an inhalable aerosol is provided, which includes an aerosol generation substrate segment, the substrate segment includes an aerosol generation substrate and a susceptor assembly; the susceptor assembly is used for inductively heating the aerosol to form a substrate under the influence of an alternating magnetic field, and the susceptor assembly is made of a soft magnetic alloy, the soft magnetic alloy has a single layer with an uniform distribution of elements; the soft magnetic alloy has an average grain size of 50-70 µm, and a grain size number of 5.5-4.5. The components of the soft magnetic alloy are shown in Table 1, and the preparation method of the susceptor assembly is as follows. S1. weighing an alloy raw material and coke according to parts by mass, and sequentially performing smelting, remelting, hot forging and cogging, hot rolling and cold rolling processes to obtain a cold-rolled material; and The melting process is as follows.

[0070] Weighing iron, nickel, molybdenum and aluminum in the mass ratio of 2:9.5:0.6:0.025 according to the requirements of the total components in the finished soft magnetic alloy, adding coke equal to half of the total mass of the iron, nickel, molybdenum and aluminum, placing the coke in a feeding area, adding the coke into a vacuum induction melting furnace from the feeding area, vacuumizing, and then smelting in a mixed furnace, the smelting temperature is 1500°C and the smelting period is 70 min. The refining process continues after melting. In the refining process, 2.8wt% manganese ore and 0.5wt% low-carbon ferrochrome of raw nickel are added to achieve the purpose of alloying. The manganese content in manganese ore is 25%, and the chromium content in low-carbon ferrochrome is 55%. After refining, performing casting at 1450°C, and then demoulding and numbering the furnace to obtain ingots.

[0071] The remelting process is as follows.

[0072] Cutting the ingot into small pieces of blocks of 5*5*5 mm and polishing the small pieces to remove oil stains and rust on the surface. A graphite crucible is lined in a magnesia crucible, the bottom of the graphite crucible is padded with 1wt% electrolytic nickel plate, and then a piece of ingot block is placed, with 0.5wt% fused magnesia filling the gap between the ingots. Then it is added into a vacuum induction melting furnace and vacuumized. Then smelting in a mixed furnace, 10KW power supply is used for melting, the smelting temperature is 1560°C, and the smelting period is 60 min. 0.1wt% graphite carbon powder and 0.05wt% Si-Ca-Ba powder with particle size less than 1.0 mm are added in the ratio of 2:1 for three times, with the interval between the two additions being 8 min, and 0.05wt% molybdenum bar is added with the last addition. After all the raw materials are added, the refining time is 20 min, and the power is adjusted to 2KW. When the temperature is reduced to 300°C, the circuit is closed, the vacuum degree is maintained, and the sample is cooled with the furnace to obtain the remelted ingot.

[0073] The hot forging and cogging process is as follows.

[0074] Depressurizing the smelting furnace, taking out the crucible and the remelt ingot, placing the remelted ingot in a chamber furnace, raising the temperature in the furnace to 1270°C in 60 min, performing hot-forging under the action of a 2-ton steam hammer for 10 min, and grinding with a surface grinding wheel to obtain a billet.

[0075] The hot rolling process is as follows.

[0076] After heating the billet to 1150-1250°C, adopting a Four-Roll Reversible Hot Rolling Mill, performing heat preservation for 40 min, 30 min and 20 min. The thickness after three times of hot rolling is 15 mm, 10 mm and 4 mm. The deformation temperature range of the hot rolling processing is 1000-1200°C. The surface temperature of hot-rolled plate is tested by infrared thermometer, and hot rolling is stopped when the temperature is lower than 1000°C to obtain a hot-rolled material.

[0077] The cold rolling process is as follows. Performing cold rolling on the hot-rolled material with a Four-Roll Reversible Hot Rolling Mill to a thickness of 1.2 mm, and further rolling the cold-rolled material to a thickness of 0.1 mm with the Four-Roll Reversible Hot Rolling Mill to obtain a cold-rolled material.

[0078] Placing the cold-rolled material and a mixed powder in a vacuum hydrogen annealing furnace for annealing process. The annealing process is as follows: performing annealing process on the cold-rolled material, preparing a mixed powder with 100 meshes, putting it in a vacuum hydrogen annealing furnace together with the cold-rolled material, raising the temperature in the furnace to 1030°C for 100 min, keeping the temperature for 90 min, then cooling to 600°C according to the cooling speed of 200°C / h, and then cooling by air or with the furnace to 150°C according to the cooling speed of 1800°C / h and discharging. The mixed powder includes the following components in parts by mass: 45 parts of Fe powder, 20 parts of SiO 2 , 13 parts of C powder, 16 parts of Al 2 O 3 and 6 parts of MnO, and the volume ratio of the mixed powder to the cold-rolled material is 0.05:100. The mixed powder and hydrogen form a powder airflow, which causes local oxidation on the alloy surface during annealing. The elements in the mixed powder have limited atomic exchange with the elements on the alloy surface. Since the atomic diameter is 0.1 nm, the influence of this local oxidation on the alloy composition can be neglected.Embodiment 2

[0079] A heated aerosol generating product for generating an inhalable aerosol is provided, which is essentially the same as Embodiment 1, except that the mass ratio of iron, nickel, molybdenum and aluminum in the melting process is controlled to be 2:10.5:0.65:0.025 for the preparation of the susceptor assembly.Embodiment 3

[0080] A heated aerosol generating product for generating an inhalable aerosol is provided, which is essentially the same as Embodiment 1, except that the mass ratio of iron, nickel, molybdenum and aluminum in the melting process is controlled to be 2:8.5:0.5:0.025 for the preparation of the susceptor assembly.Embodiment 4

[0081] A heated aerosol generating product for generating an inhalable aerosol is provided, which is essentially the same as Embodiment 1, except that the annealing temperature is 1300°C for the preparation of the susceptor assembly.Embodiment 5

[0082] A heated aerosol generating product for generating an inhalable aerosol is provided, which is essentially the same as Embodiment 1, except that for the preparation of the susceptor assembly, the secondary cooling is performed at 400°C / h with the furnace cooling to 150°C.Embodiment 6

[0083] A heated aerosol generating product for generating an inhalable aerosol is provided, which is essentially the same as Embodiment 1, except that the annealing condition is that the heat preservation period is 200 min for the preparation of susceptor assembly.Embodiment 7

[0084] A heated aerosol generating product for generating an inhalable aerosol is provided, which is essentially the same as Embodiment 1, except that no mixed powder is added during annealing for the preparation of susceptor assembly.Comparative example 1

[0085] A heated aerosol generating product for generating an inhalable aerosol is provided, which is essentially the same as Embodiment 1, except that the susceptor assembly is a commercially available alloy material, and its international brand is Hymu 80 alloy.Comparative example 2

[0086] A heated aerosol generating product for generating an inhalable aerosol is provided, which is essentially the same as Embodiment 1, except that the susceptor assembly is a commercially available alloy material, and its international brand is 1J77 alloy.Comparative example 3

[0087] A heated aerosol generating product for generating an inhalable aerosol is provided, which is essentially the same as Embodiment 1, except that the susceptor assembly is a commercially available alloy material, and its international brand is 1J79 alloy.Comparative example 4

[0088] A heated aerosol generating product for generating an inhalable aerosol is provided, which is essentially the same as Embodiment 1, except that the susceptor assembly is a commercially available alloy material, and its international brand is 1J85 alloy.Comparative example 5

[0089] A heated aerosol generating product for generating an inhalable aerosol is provided, which is essentially the same as Embodiment 1, except that the susceptor assembly is a multilayer susceptor, which is composed of Hymu80 alloy and Fe-Cr alloy.

[0090] After the element content analysis, the compositions of the alloy is determined using inductively coupled plasma mass spectrometry and a sulfur-carbon analyzer. The compositions of the susceptor assemblies obtained according to the above procedures are shown in Table 1. Table 1 Proportion of Components in Soft Magnetic AlloyElementNiFeSiMoCMnCrCuAlPSEmbodiment 179.0balance0.355.00.030.490.20.020.20.0030.005Embodiment 281.0balance0.355.00.030.490.20.020.20.0030.005Embodiment 377.0balance0.355.00.030.490.20.020.20.0030.005Embodiment 479.0balance0.355.00.030.490.20.020.20.0030.005Embodiment 579.0balance0.355.00.030.490.20.020.20.0030.005Embodiment 679.0balance0.355.00.030.490.20.020.20.0030.005Embodiment 779.0balance0.355.00.030.490.20.020.20.0030.005Comparative example 177.0balance0.254.20.030.40 / 5.5 / 0.020.02Comparative example 279.0balance0.205.00.030.70 / 0.2 / 0.020.02Comparative example 380.0balance0.354.90.010.490.10.02 / 0.0150.003Comparative example 481.0balance0.305.00.030.45 / 0.2 / 0.020.02Comparative example 5 (Fe-Cr)0.6079.461.00.50.070.8017.5 / / 0.030.04 Table 2 Physical properties of soft magnetic alloy Key performanceCurie temperature -°CSaturation magnetic induction intensity at 60Hz -GsMaximum magnetic permeability at 60Hz -mH / mcoercivity at 60Hz -A / mResistivity at 60Hz -mW·cmEmbodiment 138579201941.2058.4Embodiment 240078004051.1061.2Embodiment 336072501801.1556.4Embodiment 438577202551.3058.0Embodiment 538576801851.2557.8Embodiment 638576902601.3258.2Embodiment 738575503100.9055.2Comparative example 139075902430.9657.6Comparative example 245076003300.9854.6Comparative example 335068001751.9052.0Comparative example 441079004500.8058.2Comparative example 5 (Fe-Cr)660125002.272.060.0

[0091] The surface of the soft magnetic alloy (susceptor assembly) prepared in Embodiment 1 was tested and inspected using a metallographic microscope. The schematic diagrams are shown in Figure 1(100X) and Figure 2(200X). According to the GB-T-6394-2017 metal average grain size determination technique, the alloy grain size number in Embodiment 1 was calculated to be 5.3, with an average grain diameter of 50.2m.

[0092] As illustrated in Figure 3, the surface morphology was assessed using a field emission scanning electron microscope, and the local characteristic spots were examined using an energy spectrometer. In Embodiments 1-6, the prepared soft magnetic alloys were scanned over a wide area of the surface, and the multi-type and multi-component defects on the surface of the materials were easily identified. Cluster-like defects can be seen in Area 1, and the elemental compositions of the four defects are basically the same. Figure 4 shows the elemental analysis. The main inclusion components are Fe, C, and O, and the oxide that can be generated is Fe 3 O 4 . Triangular defects are shown in Area 2 of Figure. 3, and the elemental analysis is presented in Figure 5. The key inclusion elements are C, Al, O and Si, and the oxides that can be generated are Al 2 O 3; and SiO 2 . Figure 6 depicts the elemental analysis of a circular defect that appears in Area 3 of Figure. 3. The main inclusion elements are C, O, Mn, and S, which form Mn compounds. On the one hand, local inclusions on the surface of the alloy make it harder to magnetize when the soft magnetic alloy is magnetized, resulting in demagnetization field and magnetic domain structure within the material. Second, the inclusion oxide causes a pinning effect in the alloy, increasing hysteresis loss and coercivity, requiring more external force for domain-wall motion and making it difficult to magnetize. The presence of oxides during the preparation process usually makes magnetization of materials harder, such as reducing maximum magnetic permeability and increasing coercivity. In Example 7, the alloy surface was oxidized without using mixed powder. There were no multi-type or multi-component defects discovered while scanning a wide area of the surface, as in Example 1. Figure 7 shows a typical diagram of the test results.

[0093] The magnetic properties of the soft magnetic alloy of Embodiment 1 were examined in accordance with the A772 / A772M testing standard, as seen in Figure . 8. At a magnetic field frequency of 60Hz, it reached saturation magnetic induction intensity near 0.7Oe, with a value of 7920Gs, and the maximum relative permeability was 154059 and the absolute permeability was 194mH / m at 0.028Oe. As shown in Figure. 9, the magnetic performance test data in Comparative Example 1, at the magnetic field frequency of 60Hz, reached the saturation magnetic induction intensity around 0.5Oe, with the value of 7590Gs. The maximum relative permeability is 192573 and the absolute permeability is 243mH / m at 0.022Oe. There is a significant difference in magnetic permeability between Embodiment 1 and Comparative example 1, with the maximum magnetic permeability in Embodiment 1 decreasing by approximately 50 MH / m. However, there is little difference in saturation magnetic induction intensity between the two, and the saturation magnetic induction intensity of Embodiment 1 is slightly higher than that of Comparative example 1 by about 330Gs.

[0094] Fig. 10 is a typical cross-sectional gray image of the soft magnetic materials prepared in Embodiments 1-7. It is obvious from the image that when the metal materials are embedded with epoxy resin, black areas appear on the upper and lower sides of the image, and the middle part of the upper and lower black areas represents the part of alloy material. Furthermore, referring to the schematic gray scale diagram of the cross-section, Figure 10, the image's contrast is essentially uniform with naked eyes, and the color area with the widest area in the main part of the soft magnetic alloy accounts for at least 95% of the area value of all areas of the soft magnetic alloy, and the material is a homogeneous layer.

[0095] As shown in Figures. 11 and 12, the Curie temperature of the soft magnetic alloy assembly of Embodiment 1 and a commercially available multilayer susceptor were tested. The results showed that the Curie temperature of the multilayer susceptor was 402°C and the magnetization of the corresponding material was 61 emu / g. In contrast, the Curie temperature of single-layer iron core material is 385°C, and the magnetization of the corresponding material is 10 emu / g. This means that the demagnetization phenomenon of single-layer iron core material is more visible near Curie temperature, which can help to prevent the aerosol generation substrate from overheating.

[0096] As shown in Figure. 15, the soft magnetic alloy assemblies of Embodiment 1 and Comparative example 5 were installed with aerosol generating products with a thickness of 0.1 mm, a width of 4 mm and a length of 12 mm. The length of aerosol generation substrate segment is 12 mm, and the aerosol generation substrate is a tobacco sheet made by the thick slurry method. Then, the aerosol generating product was put into a specific Magnetic Coupling Resonance Wireless Power Transfer system (MCR-WPT), and the heating temperature of the surface of the soft magnetic alloy assembly in this application was tested, and it was found that the maximum temperature was 397°C. In comparison to the multilayer susceptor material, the maximum temperature in the same aerosol generating product is 384°C. The maximum temperature decreased by 13°C.

[0097] The foregoing are only preferred embodiments of the present application; however, the protection scope of the present application is not limited to these, and any changes or substitutions that can be easily anticipated by those skilled in the art within the technical scope disclosed by the present application shall be included in the protection scope of the present application.

Claims

1. A heated aerosol generating product for generating an inhalable aerosol, comprising an aerosol generation substrate segment, wherein the substrate segment comprises an aerosol generation substrate and a susceptor assembly; the susceptor assembly inductively heats the aerosol generation substrate under the influence of an alternating magnetic field, and the susceptor assembly is made of a soft magnetic alloy, and is characterized in that the soft magnetic alloy has a single layer with an uniform distribution of elements; the soft magnetic alloy has an average grain size of 50-70 µm, and a grain size number of 5.5-4.5.

2. The heated aerosol generating product for generating an inhalable aerosol of claim 1, wherein the soft magnetic alloy comprises components of iron, molybdenum and nickel, with molybdenum accounting for 3.5%-6% and nickel accounting for 77%-81% of the total mass of the soft magnetic alloy.

3. The heated aerosol generating product for generating an inhalable aerosol of claim 1, wherein the soft magnetic alloy further comprises chromium, accounting for 0.2-0.5% of the total mass of the soft magnetic alloy.

4. The heated aerosol generating product for generating an inhalable aerosol of claim 1, wherein the soft magnetic alloy further comprises manganese, accounting for 0.1%-0.5% of the total mass of the soft magnetic alloy.

5. The heated aerosol generating product for generating an inhalable aerosol of claim 4, wherein the soft magnetic alloy further comprises components of silicon and aluminum, with silicon accounting for 0.1%-0.4% and aluminum accounting for 0.15%-0.7% of the total mass of the soft magnetic alloy.

6. The heated aerosol generating product for generating an inhalable aerosol of claim 1, wherein the soft magnetic alloy comprises the following components in parts by mass: 77-81 parts of nickel, 3.5-6.0 parts of molybdenum, 0.2-0.5 part of chromium, 0.1-0.5 part of manganese, 0.1-0.4 part of silicon, 0.15-0.7 part of aluminum and 11-18 parts of iron.

7. The heated aerosol generating product for generating an inhalable aerosol of claim 1, wherein the susceptor assembly has a thickness of 0.03-0.18 mm, a width of 1.5-4.5 mm and a length of 9-18 mm.

8. The heated aerosol generating product for generating an inhalable aerosol of claim 1, further comprising a filter segment and a cooling segment, wherein the cooling segment is located between the aerosol generation substrate segment and the filter segment; the aerosol generation substrate is made of tobacco materials or non-tobacco materials and distributed in a filiform, flaky or granular manner, and the susceptor assembly is wrapped by the aerosol generation substrate.

9. The heated aerosol generating product for generating an inhalable aerosol of claim 1, wherein a preparation method of the susceptor assembly comprises the following steps: S1. weighing an alloy raw material and coke according to parts by mass, and sequentially performing smelting, remelting, hot forging and cogging, hot rolling and cold rolling processes to obtain a cold-rolled material; and S2. placing the cold-rolled material and a mixed powder in a vacuum hydrogen annealing furnace for annealing process, wherein a annealing process temperature is 1000-1200°C, a heat preservation period is 70-120 min, a cooling speed is 150-220°C / h, and after lowering the temperature to 580-630°C, performing air cooling or furnace cooling to reach 100-200°C.

10. The method of claim 9, wherein the mixed powder is 100-300 mesh mixed powder, comprising a mixture of Fe, MnO, SiO2, Al2O3 and C powders; and a volume ratio of the mixed powder to the cold-rolled material is 0.05:100.

Images