Battery cell, battery device, power-consuming device and energy storage device

Abstract

Battery cell characterized in that it comprises a stacked electrical core, wherein the stacked electrical core comprises a cathode foil and an anode foil, wherein the cathode foil comprises a cathode collector and a cathode film layer provided on at least one side of the cathode collector, wherein the cathode film layer comprises lithium-containing transition metal phosphate particles provided with a carbon material on at least part of a surface; wherein a median C50 of the degree of graphitization in the cumulative distribution curve for the graphitization C value of the cathode film layer, obtained in the area-scanning mode of the laser microconfocal Raman spectrometer, is 0.95–1.20; wherein the graphitization C value is IG / ID, where IG is the intensity of the G-peak of the Raman spectrum at 1580 ± 100 cm⁻¹ and IG is the intensity of the D-peak. of the Raman spectrum at 1350±100cm-1;where the density of the cathode foil when the battery cell is in a fully discharged state is 2.3 g / cm3-2.6 g / cm3;

Description

TECHNICAL AREA The present application relates to the technical field of lithium-ion secondary battery cells, in particular a battery cell, a battery device, a power-consuming device and an energy storage device. STATE OF THE ART In recent years, lithium-ion secondary battery cells have been used in a wide variety of fields, such as energy storage systems for hydroelectric, thermal, wind and solar power plants, as well as power tools, electric bicycles, electric motorcycles, electric vehicles, military equipment and aerospace. With the doubling of market demand for battery range and lifespan, the requirements for battery capacity and cycle life have also increased. However, achieving simultaneous improvements in these performance areas with current technology is difficult, making it a technical problem that urgently needs to be addressed. DISCLOSURE OF REGISTRATION The present application is made in view of the aforementioned subject matter with the aim of providing a battery cell with both high capacity and good cycle performance. A first aspect of the present application provides a battery cell comprising a stacked electrical core, wherein the stacked electrical core comprises a cathode foil and an anode foil, wherein the cathode foil comprises a cathode collector and a cathode film layer provided on at least one side of the cathode collector, wherein the cathode film layer comprises lithium-containing transition metal phosphate particles provided with a carbon material on at least part of a surface; wherein a median C50 of the graphitization degree in the cumulative distribution curve for the graphitization C value of the cathode film layer, obtained in the area-scanning mode of the laser microconfocal Raman spectrometer, is 0.95-1.20;wherein the graphitization C-value IG / ID is, where IG represents the intensity of the G-peak of the Raman spectrum at 1580±100cm-1 and ID represents the intensity of the D-peak of the Raman spectrum at 1350±100cm-1; wherein the density of the cathode foil when the battery cell is in a fully discharged state is 2.3 g / cm3-2.6 g / cm3; The present application uses a stacked electrical core and improves the compression density of the cathode film to reduce the ineffective space within the battery cell, improve the space utilization rate, and then increase the volumetric energy density and capacity of the battery cell; at the same time, the present application regulates the median C50 of the graphitization degree (which reflects the order degree of the carbon coating material), reduces the frictional resistance between the particles, improves the sliding ability of the particles in the cathode film layer, reduces the stress concentration in the cathode film layer, and reduces the risk of the film layer detaching during the cycling process, ultimately achieving an effective balance between high capacity and good cycle performance of the battery. In each embodiment, the median C50 of the graphitization degree in the cumulative distribution curve for the graphitization C value of the cathode film layer obtained in the area scanning mode of the laser microconfocal Raman spectrometer is 1.01-1.13. The degree of graphitization of the cathode film layer is within the above range, which helps to further improve the sliding ability of the particles in the cathode film layer, reduce the stress concentration in the cathode film layer and decrease the risk of the film layer falling off during the cycle process, thus further improving the cycle life of the battery cell. In each embodiment, based on the total area of ​​the particles in the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, the percentage area fraction of the particles with a particle size R1 of R1 ≥1000 nm is 12%-50%, optionally 12%-40%. The area fraction of particles with a particle size R1 of R1>1000 nm in the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil is in the range of 12%-50% and further in the range of 12%-40%, which is able to improve the pressing density of the electrode foil without increasing the probability of the film layer delaminating, thereby improving the energy density of the battery cell and at the same time mitigating the problem of capacity degradation, taking into account the cycle life of the battery. In each embodiment, in the cumulative distribution curve of the sphericity area of ​​the particles with a particle size R1 of R1≥1000 nm in a cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, the median LR1A150 of the sphericity is 0.6-0.8, optionally 0.65-0.75, further optionally 0.67-0.75. In the cumulative distribution curve of the sphericity area of ​​particles with a particle size R1 of R1≥1000 nm in the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, LR1A50 lies in the range of 0.65-0.75 and further in the range of 0.67-0.75, which helps to further reduce the voltage concentration at the large particles in the cathode film layer of the stacked electric core, thereby reducing the probability of film layer degradation and improving the cycle life of the battery. In each embodiment, the median B50 of the coating value in the cumulative distribution curve for the coating value-B of the cathode film layer obtained in the area scanning mode of the laser microconfocal Raman spectrometer is 0.30-0.60; where the coating value-B is IP / ID, where IP represents the intensity of the P-peak of the Raman spectrum at 948±100cm-1 and ID represents the intensity of the D-peak of the Raman spectrum at 1350±100cm-1. The median B50 value of the cathode film layer lies within the above range, indicating that the carbon coating material of the active cathode material is relatively dense and uniform. This improves the uniformity of cathode film layer slippage during roller pressing and reduces the phenomenon of stress concentration within the cathode film layer. Furthermore, the dense and uniform carbon material layer facilitates the slippage of large particles within the cathode film layer during the pressing process. This reduces stress concentration on these particles, decreases the likelihood of film layer delamination, improves battery capacity degradation, and extends battery cycle life. In each embodiment, the lithium-containing transition metal phosphate particles comprise a component with the general formula shown below: Formula I: LimFexPyOjQq where Q comprises one or more of Al, Na, K, Mg, Cu, Mn, Cr, Zn, Pb, Ca, Co, Ni, Sr, Nb, V, Ti, B, S, Si, N, F, Cl, Br, and where 0.8≤m≤1.15, 0.9≤x≤1, 0.95≤y≤1, 3.5≤j≤4, 0≤q≤0.1. In each embodiment, the lithium-containing transition metal phosphate particles in the cathode film layer comprise one or more of the following materials: lithium iron phosphate, lithium manganese phosphate, lithium fluorine-substituted vanadium phosphate, lithium ferromanganese phosphate and their modified materials. In each embodiment, the lithium-containing transition metal phosphate particles in the cathode film layer comprise one or more of the following materials: lithium iron phosphate and its doped modified materials, as well as modified coating materials. In each embodiment, the iron dissolution rate of the active cathode material is 658 ppm-1921 ppm, optionally 658 ppm-1485 ppm. In each embodiment, the mass content of titanium is 500 ppm-8000 ppm, optionally 1000 ppm-3000 ppm, based on the total mass of the lithium-containing transition metal phosphate particles. In the embodiments of the present application, the reactivity of the synthetic raw material of the active cathode material can be reduced by adding a high proportion of titanium to the lithium-containing transition metal phosphate particles, so that the active cathode material has a high degree of graphitization and at the same time achieves control of the proportion of large particles, which reduces the stress concentration of the cathode film layer and decreases the probability of the film layer deteriorating, thereby improving the energy density of the battery and taking into account the reliability of the battery. In each embodiment, the mass content of vanadium is 500 ppm-5000 ppm, optionally 500 ppm-3000 ppm, based on the total mass of the lithium-containing transition metal phosphate particles in the cathode film layer. The vanadium element in the cathode film layer can exist in different valence states. +5-valent vanadium (V5+) can be doped with phosphorus sites, leading to lattice distortions due to its larger radius. This enlarges the lithium-ion diffusion channels and thus improves the ionic conductivity of the active cathode material, thereby enhancing the battery's kinetic performance. +3-valent vanadium (V3+) can be doped with transition metal sites, creating lithium gaps through charge compensation, which improves the electronic conductivity of the active cathode material.Furthermore, the increased uniformity of the vanadium element in the lithium-containing transition metal phosphate particles contributes to a further improvement in the kinetic performance of the cathode film layer and the uniformity of the reaction of the cathode film layer, thus further improving the kinetic performance and the cycle performance of the battery cell. In each embodiment, the porosity of the cathode film layer is 14%-28%. The porosity of the cathode film layer lies within the range mentioned above, and the cathode film layer exhibits a good electrolyte infiltration rate and good tortuosity, which promotes the diffusion of lithium ions in the liquid and solid phases, reduces the concentration polarization of the thick electrode foil, and improves the kinetic performance of the battery. Simultaneously, it helps to reduce the volume expansion of the cathode foil during the cycling process, decrease the mechanical stress on the film layer, and mitigate the phenomenon of stress concentration, thereby reducing the risk of film layer delamination. In each embodiment, the specific resistance of the cathode film layer is 10 Ω·cm to 35 Ω·cm. The specific resistance of the cathode film layer is in the above range, which contributes to reducing the impedance of electron transfer, reducing charge / discharge polarization, and improving the multiplication performance and cycle performance of the battery. In each embodiment, a one-sided thickness of the cathode film layer is designated as H, where H is 70 µm-120 µm. In each embodiment, a one-sided thickness of the cathode film layer is designated as H, where H is 90 µm-120 µm. The one-sided thickness of the cathode film layer is within the above range, which helps to increase the charge of the active cathode material in the battery and improve the battery's capacity, while reducing the risk of the film layer detaching during the cycling process. In each embodiment, a one-sided thickness of the cathode film layer is designated as H, where H is 100 µm-120 µm. Increasing the thickness of the cathode film layer helps to increase the charge capacity of the active cathode material and thus the battery's capacity. However, the applicant found that when the one-sided thickness of the cathode film layer is greater than or equal to 100 µm, the volume expansion of the cathode film layer during the battery's cycling process is more significant, generating a higher voltage. This also increases the phenomenon of voltage concentration within the cathode film layer and raises the risk of film delamination, ultimately impairing the battery's cycling performance.The embodiments of the present application increase the battery capacity by increasing the thickness of the cathode film layer, and simultaneously control the median C50 of the graphitization degree in the cumulative distribution curve for the graphitization C value of the cathode film layer, which is obtained in the area scanning mode of the laser microconfocal Raman spectrometer, in order to increase the sliding ability between the particles in the cathode film layer, which reduces the phenomenon of stress concentration in the film layer and the risk of film layer delamination, and then improves the cycle life of the battery. In each embodiment, the cathode film layer is provided with a lower coating layer at a lower region facing the cathode collector, the lower coating layer comprising a conductive agent and a binder, wherein the conductive agent comprises carbon nanotubes and conductive carbon black, and wherein the binder comprises a vinylidene fluoride polymer. In each embodiment, the thickness of the lower coating layer is 0.5 µm-5 µm. The lower coating layer provided in the embodiments of the present application contributes to improving the adhesion between the cathode film layer and the cathode collector and to reducing the phenomenon of voltage concentration at the large particles, thereby decreasing the probability of cathode film layer delamination and improving the cycle stability of the battery. At the same time, compared to direct contact between the cathode collector and the cathode film layer, the contact area between the lower coating layer and the cathode film layer is increased, which contributes to increasing the electron transfer area between the collector and the cathode film layer, thereby reducing the internal resistance of the electrode foil and improving the kinetic performance of the battery. In each embodiment, the cathode film layer further comprises a dispersing agent, wherein the dispersing agent comprises hydrogenated nitrile butadiene rubber (HNBR). When HNBR is adsorbed onto the surface of particles in the slurry, its long-chain molecules form a physical barrier around the particles, preventing them from approaching and aggregating. This allows the particles to remain relatively independent and dispersed within the system. Simultaneously, HNBR can reduce the surface tension between the dispersion medium and the dispersed particles, making it easier for the particles to be moistened by the medium and thus promoting their dispersion. It can also reduce the interfacial energy between the particles, particularly mitigating the aggregation phenomenon of the conductive medium caused by interfacial energy reduction.Furthermore, when the slurry is dried to form a film, the elastic network structure of HNBR can buffer the shrinkage stress generated by solvent evaporation, regroup the conductive agent in the process due to capillary action, and reduce the area fraction of the conductive agent agglomeration region, thereby improving the kinetic performance and cycle life of the battery. In each embodiment, the mass content of the conductive medium is 0.5%-2%, based on the mass of the cathode film layer. The mass fraction of the dispersant is within the above range, which allows for a uniform dispersion of the particles in the cathode film layer, while maintaining a high charge capacity in the cathode film layer. This reduces the voltage concentration in the cathode film layer, effectively alleviates the problem of battery capacity degradation, and improves the battery's cycle performance. In each embodiment, the cathode film layer further comprises a conductive agent, wherein, with respect to a total area of ​​the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, the area fraction of an agglomeration region of the conductive agent is 0.5%-2.5%, optionally 1.5%-2.5%. Based on the total area of ​​the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, the area fraction of the agglomeration region of the conductive medium lies in the above range, indicating that the conductive medium is uniformly dispersed in the cathode film layer and that it is easy to form a homogeneous conductive network. This particularly helps to reduce the problem of reduced kinetics in a film layer due to the increase in ion transfer paths, to reduce local polarization or even lithium precipitation of the battery during the cycling process, and thus improves the battery's cycle life. In each embodiment, the conductive means comprises carbon nanotubes, wherein the carbon nanotubes comprise one or more of cin-walled carbon nanotubes, thin-walled carbon nanotubes, or multi-walled carbon nanotubes. Since carbon nanotubes have a one-dimensional structure, they can form a network structure in the cathode film layer. On the one hand, due to the high elastic modulus of carbon nanotubes, the network structure not only serves as a bridge for the propagation of voltages, but also has a binding effect on the cathode film layer, which inhibits the rebound of lithium-containing transition metal phosphate particles. This effectively reduces the voltage concentration and the risk of the film layer deteriorating, which in turn improves the problem of battery capacity degradation.On the other hand, the excellent electrical conductivity of carbon nanotubes makes their network structure a highly efficient electron transfer channel, and even if there is local drop-off of the film layer, the thick electrode foil can still maintain a high electron transfer efficiency in the plane direction and in the thickness direction, thus slowing down the problem of capacity drop-off and further improving the kinetic performance and cycle life of the battery. In each embodiment, the conductive medium further comprises conductive carbon black. Conductive carbon black has a high specific surface area and therefore good liquid retention capacity. The expansion force of the thick electrode foil during the cycling process is high, which allows the electrolyte solution to be easily extruded. The distribution of conductive carbon black in the cathode film layer contributes to improving the liquid retention capacity of the thick electrode foil, further mitigating the phenomenon of capacity loss during the battery's cycling process and improving the battery's cycle life. In each embodiment, the mass fraction C1 of the carbon nanotubes, relative to the mass of the cathode film layer, is 0. <C1≤2,5% und der Massengehalt C2 des leitfähigen Rußes 0<C1≤2,5%. The mass content of carbon nanotubes and conductive carbon black within the above range can effectively reduce the agglomeration phenomenon of carbon nanotubes and form a good conductive network structure, thereby effectively reducing the voltage concentration of the cathode film layer and improving the retention rate of electrolyte solution of the cathode foil during long cycles, further reducing the risk of electrode foil film layer deterioration and the degree of polarization, thus increasing the kinetic performance of the battery and improving the battery cycle life, while addressing the problem of capacity degradation. In each embodiment, the battery cell comprises a housing, wherein at least one stacked electrical core is received in the housing, wherein the housing has a dimension of L0 in a longitudinal direction, wherein the housing has a dimension of W0 in a width direction, wherein the housing has a dimension of H0 in a thickness direction, wherein 450 mm ≤ L0 ≤ 1300 mm, 100 mm ≤ W0 ≤ 150 mm, and 14 mm ≤ H0 ≤ 22 mm. In each embodiment, the dimension L0 of the housing in the longitudinal direction satisfies the following condition: 450 mm ≤ L0 ≤ 650 mm. If the length dimension L1 of the casing meets the criteria of 450 mm ≤ L0 ≤ 650 mm, the battery cell length is shorter. This helps to shorten the current diffusion path and reduce the internal resistance of the electrodes, thereby reducing heat generation in the battery and improving its kinetic performance. Furthermore, the shorter casing length contributes to shortening the electrolyte diffusion path during infiltration, improving the infiltration rate and electrolyte uniformity, further promoting the uniformity of lithium ion disembedding during the cycling process, mitigating voltage concentration, reducing the risk of film degradation, and improving the cycle stability of the battery cell. In each embodiment, the dimension L0 of the housing in the longitudinal direction fulfills the following condition: 900mm ≤ L0 ≤ 1300mm. If the length dimension L0 of the casing meets the following condition: 900 mm ≤ L0 ≤ 1300 mm, the longer battery cell size helps to reduce the volume fraction of the casing within the battery cell and improve the load-bearing capacity of the active material. Simultaneously, a longer battery cell can reduce the number of batteries required in the battery module, simplify the structural design of the battery module, decrease the number and complexity of structural components within the module, and thereby improve the space utilization rate of the battery pack, which in turn contributes to improving the volume energy density of the battery cell. In each embodiment, the housing material is a soft packing material, wherein the soft packing material comprises an aluminum-plastic composite film, optionally comprising one or more of aluminum, polypropylene (PP), polybutylene terephthalate (PBT), polybutylene succinate (PBS), nylon, polyethylene terephthalate (PET), polyethylene (PE). In each embodiment, the housing comprises a first sealing zone, wherein the first sealing zone is provided at at least one end extending in the width direction of the stacked electrical core; wherein the first sealing zone comprises a folded edge structure extending in the length direction, wherein the folded edge structure is provided with an encapsulating adhesive, wherein the encapsulating adhesive is provided successively along the length direction and secures the folded edge structure. In each embodiment, the housing comprises at least one second sealing zone, wherein the second sealing zone is provided at at least one end of the stacked electrical core along the longitudinal direction of the housing, and wherein the second sealing zone is provided on one side of the electrode tab of the stacked electrical core. In each embodiment, a plurality of adhesive rings circumferentially arranged in the width direction are provided around an outer circumference of the stacked electrical core, wherein the adhesive rings circumferentially arranged in the width direction are provided at intervals along the length direction. The spaced arrangement of the adhesive rings in the longitudinal direction, which surround the electrical core along the width direction, is beneficial for fixing the position between the electrode foils in the electrical core and reducing the probability of displacement of the electrical core when the battery is shaken. This is particularly suitable for long batteries, which can effectively reduce displacement between the electrode foils in the longitudinal direction and lead to the phenomenon of lithium precipitation. It is also beneficial for keeping the internal spatial structure of the battery stable, so that it does not affect the normal operation of the battery. In each embodiment, the battery cell capacity at 25°C is 105 Ah-190 Ah, optionally 150 Ah-190 Ah. A second aspect of the present application provides a battery device comprising a battery cell according to the first aspect of the present application. A third aspect of the present application provides a power-consuming device, wherein the power-consuming device comprises a battery device according to the second aspect of the present application, wherein the battery device is used to provide electrical energy. A fourth aspect of the present application provides an energy storage device, the energy storage device comprising a battery device according to the second aspect of the present application, wherein the battery device is used for storing electrical energy. PRESENTATION OF THE REGISTRATION Fig. 1 is a schematic representation of a separator in an embodiment of the present application; Fig. 2 shows a schematic representation of a separator in the prior art; Fig. 3 is a schematic representation of a surface morphology of a binder layer of an embodiment of the present application; Fig. 4 shows a schematic representation of a stacked soft-pack battery of the present application; Fig. 5 shows a schematic representation of a current-consuming device in an embodiment of the present application. Reference symbol list: 5 Battery cell; 50 Housing; 20 Separator; 201 Base film; 202 Ceramic layer; 203 Bonding layer; X Longitudinal direction; Y Width direction; Z Thickness direction. SPECIFIC EXECUTION FORMS The following sections disclose in detail embodiments of the battery cell, battery device, power-consuming device, and energy storage device of the present application with corresponding reference to the accompanying drawings. However, there will be instances where an unnecessarily detailed description is omitted. For example, detailed descriptions of things that are already well known and repeated descriptions of the same structure will be left out. This is to avoid making the following description unnecessarily long and to facilitate understanding by those skilled in the art. Furthermore, the accompanying drawings and the following description serve to provide those skilled in the art with a complete understanding of the present application and are not intended to limit the subject matter specified in the claims. The "range" disclosed here is defined in terms of a lower bound and an upper bound, with a particular range being defined by selecting a lower bound and an upper bound that establish the limits of that range. Ranges defined in this way can include or exclude end values ​​and can be combined in any way; that is, any lower bound can be combined with any upper bound to form a range. For example, if a range of 60-120 and 80-110 is specified for a particular parameter, then a range of 60-110 and 80-120 is also to be expected. Furthermore, if the minimum values ​​of 1 and 2 and the maximum values ​​of 3, 4, and 5 are specified, then the following ranges can be expected: 1-3, 1-4, 1-5, 2-3, 2-4, and 2-5.Unless otherwise specified, the range "ab" denotes any combination of real numbers between a and b, where both a and b are real numbers. For example, the range "0-5" means that all real numbers between 0 and 5 are listed here, and 0-5 is simply a shorthand representation of the combination of these values. Furthermore, stating that a parameter is an integer ≥ 2 is equivalent to stating that the parameter is, for example, an integer 2, 3, 4, 5, 6, 7, 8, 9, 10, 11, 12, and so on. Unless expressly stated otherwise, all embodiments and optional embodiments of the present application may be combined to form new technical solutions, and such a technical solution should be considered to be covered by the disclosure of the present application. Unless expressly stated otherwise, all technical features of the present application, as well as optional technical features, may be combined to form a new technical solution, and such a technical solution should be considered to be covered by the disclosure of the present application. Unless expressly stated otherwise, all steps of the present application may be carried out sequentially or randomly, preferably sequentially. For example, the method includes steps (a) and (b), which means that the method may include steps (a) and (b) carried out one after the other, or that it may include steps (b) and (a) carried out one after the other. The indication that the method may also include step (c) means, for example, that step (c) may be added to the method in any order; e.g., the method may include steps (a), (b), and (c), or it may include steps (a), (c), and (b), or it may include steps (c), (a), and (b). In the present application, the terms "plural" and "multiple" refer to two or more. Unless otherwise stated, the terms used in this application have the known meanings as generally understood by those skilled in the art. Unless otherwise specified, the values ​​of the parameters mentioned in this application can be determined by various test methods commonly used in practice, e.g., according to the test methods specified in the embodiments of this application. Unless otherwise specified, the test temperature for each parameter is 25°C. The battery devices in the embodiments of the present application can comprise one or more battery cells to provide a voltage and capacity. The battery cell assembly can comprise a plurality of soft-pack battery cells, wherein the plurality of soft-pack battery cells are connected in series, parallel, or in a mixed configuration by a converging element. For example, the battery cell assembly is typically formed by arranging a plurality of soft-pack battery cells; the battery cell assembly can be a battery module, wherein the battery module comprises a plurality of soft-pack battery cells arranged and secured to form a single module. For example, the battery module can be formed by bonding the multiple battery cells together. The battery device can be a battery pack comprising a housing and one or more battery cell assemblies, with the battery cell assemblies being contained within the housing. The battery cell assembly can be a battery module, and the battery cell assembly can be contained within the housing by securing the battery module within the housing; the battery cell assembly can also be contained within the housing by directly securing a plurality of soft-packed battery cells within the housing. In the embodiments of the present application, the box can comprise a first box and a second box. The first box and the second box are attached to one another in such a way that an enclosed space is formed inside the box, which accommodates the battery cell assembly. "Enclosed" here means covered or sealed, and this space may be sealed or unsealed. The first box can be a top cover or a bottom plate. For example, the box can comprise a top cover, a frame, and a bottom plate. The top cover and the bottom plate are each connected to the frame, so that an enclosed space is formed inside the box, which accommodates the battery cell assembly. In the embodiments of the present application, the box can be part of a chassis structure of the vehicle. For example, parts of the box can be at least part of a floor of the vehicle, or parts of the box can be at least part of a cross member and a longitudinal member of the vehicle. In the embodiments of the present application, the battery cell can be a secondary battery, i.e., a battery cell that can be recharged after it has been discharged, so that the active material can be reactivated and reused; the battery cell can be a lithium-ion battery. The battery cell can be flat. The batteries mentioned in the embodiments of the present application can comprise one or more battery cells to achieve a higher voltage and capacity. The batteries mentioned in the present application can be, for example, battery cells, battery modules, or battery packs. The battery cell is the smallest unit that makes up the battery and is alone capable of performing the functions of charging and discharging. In the case of multiple battery cells, the multiple battery cells are connected in series, parallel, or a mixed configuration via a sink component. In some embodiments, the battery can be a battery module; in the case of multiple batteries, the multiple battery cells are arranged and secured to form a battery module. In some embodiments, the battery can be a battery pack comprising a housing and a battery cell, with the battery cell or battery module being contained within the housing. In some embodiments, the housing can be part of a vehicle's chassis structure. For example, parts of the housing can be at least part of the vehicle's chassis, or parts of the housing can be at least part of a crossmember and a longitudinal member of the vehicle. In some embodiments, the battery can be an energy storage device. Energy storage devices include energy storage containers, energy storage cabinets, and the like. In some embodiments, the battery cells can be assembled into a battery module, and the number of battery cells contained in the battery module can be a plurality, with the exact number being adjustable depending on the application and capacity of the battery module. In some embodiments, the battery modules described above can also be assembled into a battery pack, with the number of battery modules contained in the battery pack being adjustable depending on the application and capacity of the battery pack. The battery cell comprises an electrode component and an electrolyte. The electrode component typically comprises a cathode foil and an anode foil, the anode foil being the electrode where the reaction of uptake or lithiation of lithium ions during charging and release or delthiation of lithium during discharging takes place, and the cathode foil being the electrode where the reaction of release or delthiation of lithium ions during charging and uptake or lithiation of lithium during discharging takes place. Although lithium-containing transition metal phosphate particles offer a significant advantage in terms of cycle stability as an active cathode material, their intrinsic gram capacity is considerably lower than that of ternary materials. The applicant found that the disadvantages in terms of capacity and energy density can be compensated for by increasing the packing density of the lithium-containing transition metal phosphate particle material and combining it with a stacked electrical core structure. However, this process optimization also introduces new technical challenges: Compared to ternary materials, lithium-containing transition metal phosphate particles have a more stable structure and are less prone to fracturing under high pressure. Therefore, the lithium-containing transition metal phosphate particles are often subjected to higher pressures during the electrode foil packing process to achieve a higher packing density.If the material's slip resistance is insufficient under high pressing density conditions, local stress concentrations can easily occur during the roll pressing of the electrode foil. Secondly, the stacked electric core has a high energy density compared to the wound electric core because it lacks the corner bonding of the wound core. This results in lower pressure on the cathode film layer inside the stacked electric core compared to the wound electric core, making it easier to exacerbate the demolding of the cathode film layer. The shedding of the film layer not only leads to an immediate reduction in the active substances involved in the electrochemical reaction but also to an "island effect," i.e.,This leads to the formation of isolated areas between the particles or between the particles and the conductive medium, preventing good electrical contact and thus participation in the charging and discharging process, resulting in a decrease in battery capacity. Furthermore, the deposition of active substances impedes the ion transfer pathway, increases the battery's internal resistance, leads to local overheating, and even increases the risk of thermal runaway, significantly impacting the battery's lifespan and safety. Therefore, a first aspect of the present application provides a battery cell comprising a stacked electrical core, wherein the stacked electrical core comprises a cathode foil and an anode foil, wherein the cathode foil comprises a cathode collector and a cathode film layer provided on at least one side of the cathode collector, wherein the cathode film layer comprises lithium-containing transition metal phosphate particles provided with a carbon material on at least part of a surface; wherein a median C50 of the graphitization degree in the cumulative distribution curve for the graphitization C value of the cathode film layer, obtained in the area-scanning mode of the laser microconfocal Raman spectrometer, is 0.95-1.20; where the graphitization C-value is IG / ID, where IG represents the intensity of the G-peak of the Raman spectrum at 1580±100em-1 and ID represents the intensity of the D-peak of the Raman spectrum at 1350±100cm-1;where the density of the cathode foil when the battery cell is in a fully discharged state is 2.3 g / cm3-2.6 g / cm3; The present application provides a battery cell, and the battery cell of the present application improves the problem of capacity degradation while achieving a high capacity, taking into account the cycle life of the battery. Without being bound to any specific theory, this can be attributed to the fact that: the use of a stacked electrical core structure reduces the presence of ineffective space within the battery cell, effectively eliminates the corner gaps and interlayer gaps that are unavoidable in the winding process, and makes the overall battery cell structure more compact, thereby improving the space utilization rate, enhancing the volumetric energy density of the battery cell, and increasing the battery's capacity; furthermore, the regularity of the stacked structure also creates favorable conditions for improving the process for achieving a high electrode foil density. For the same volume, the stacked electrical core can accommodate more electrode foils, which, together with the high electrode foil density, further improves the battery's energy density and capacity performance.Simultaneously, the applicant controls the median C50 of the graphitization degree in the cumulative distribution curve for the graphitization-C of the cathode film layer, obtained in the area-scanning mode of the laser microconfocal Raman spectrometer, thus achieving a balance between battery capacity and cycle performance. The median C50 of the graphitization degree of the cathode film layer, obtained in the area-scanning mode of the laser microconfocal Raman spectrometer, can reflect the graphitization degree of the carbon coating material on the surface of the lithium-containing transition metal phosphate, i.e., the degree of order of the carbon coating material on the surface of the lithium-containing transition metal phosphate particles. The higher the graphitization degree of the lithium-containing transition metal phosphate particles, the more ordered the carbon atoms are, forming a near-ideal graphite layer structure.This structure can effectively reduce friction between the particles, which promotes the relative sliding of the particles along the interlayer when subjected to a force, and exhibits better sliding properties, which helps to mitigate the phenomenon of stress concentration in the film layer, reduce the risk of film layer delamination, and thus improve the cycle life of the battery. In the present application, the stacked electrical core refers to an electrical core formed by stacking a cathode foil, a separator and an anode foil. In the present application, the cathode film layer comprises lithium-containing transition metal phosphate particles, but the cathode film layer does not refer only to the active cathode material layer, and other film layers associated with the active cathode material layer and difficult to distinguish from it, such as the sublayer, the liquid-retaining layer and the like, are collectively referred to as the cathode film layer. In the present application, the lithium-containing transition metal phosphate particles refer to a phosphate material comprising lithium and a transition metal element and can be detected by any known method in this field. It can be detected, for example, by a combination of an X-ray diffractometer (XRD). In the present application, the carbon coating material located on at least a portion of the surface of the lithium-containing transition metal phosphate particles can be detected in any manner known in the art. For example, the carbon coating material arranged on at least a portion of the surface of the lithium-containing transition metal phosphate particles can be observed by characterizing the lithium-containing transition metal phosphate particles using a combination of transmission electron microscopy and an energy spectrum analyzer. In the present application, a fully discharged state means: storing the battery at 25°C for 2 hours, waiting until the temperature of the battery is maintained at 25°C, and discharging the battery with a constant current of 1 / 3 C to 2.5 V and then discharging the battery with a constant current of 0.1 C to 2.0 V. The density of the cathode foil can be tested according to known methods in this technical field.As an example, the battery is placed in an oven environment at 25°C and stored for 2 hours. While the battery temperature is maintained at 25°C, it is discharged to 2.5 V at a constant current of 1 / 3 C and then to 2.0 V at a constant current of 0.1 C. The battery is then disassembled to obtain a cathode foil. The remaining electrolyte solution is treated using the solvent dimethyl carbonate. The electrode foil is dried and cut into a small round disc with area S to obtain the mass W1. Using a micrometer, the thickness T1 of the cathode foil is measured. The cathode film layer is then wiped off the weighed electrode foil. The mass of the collector is weighed and recorded as W2. The thickness T2 of the collector is measured using a micrometer. The density PD of the cathode foil is then determined. =(W1-W2) / [(T1-T2)×S]. In some embodiments, the pressed density of the cathode foil when the battery cell is in a fully discharged state is optionally 2.3 g / cm3, 2.31 g / cm3, 2.32 g / cm3, 2.33 g / cm3, 2.34 g / cm3, 2.35 g / cm3, 2.36 g / cm3, 2.37 g / cm3, 2.38 g / cm3, 2.39 g / cm3, 2.40 g / cm3, 2.41 g / cm3, 2.42 g / cm3, 2.43 g / cm3, 2.44 g / cm3, 2.45 g / cm3, 2.46 g / cm3, 2.47 g / cm3, 2.48 g / cm3, 2.49 g / cm3, 2.50 g / cm3, 2.55 g / cm3, 2.60 g / cm3 or any value in a range between two of these values. In the present application, the cumulative distribution curve of graphitization degree-C value is the curve obtained when at least 100 C values ​​are arranged in order from smallest to largest, using the graphitization degree as the horizontal axis and the cumulative number fraction as the vertical axis. C50 is the C value when the cumulative number fraction on the vertical axis of the cumulative distribution curve of graphitization degree-C value is 50%. The median C50 of the graphitization degree can, compared to a point value, reflect the graphitization degree of the particles in the cathode film layer, i.e., the degree of particle slippage; and, compared to a mean value, it can reduce the influence of extreme values ​​in the test process and improve the reliability of the test results. The graphitization C-value can be obtained using an area-scanning mode of a laser microconfocal Raman spectrometer. Specifically, a laser microconfocal Raman spectrometer (a high-precision Renishaw laser microconfocal Raman spectrometer) is used as an example. An excitation wavelength of 532 nm is selected, and a suitable amount of the cathode film layer is taken for area scanning of the surface or a cross-sectional area along the thickness direction of the electrode foil. The scanning area is 45 µm × 45 µm, subdivided into 10 × 10 grids, with the grid vertex serving as the test point. The step size is 5 µm, and the total number of scan points is 100 to obtain the C-values ​​at various locations and the cumulative distribution curve of the C-values ​​in the area scan.The cathode film layer in the present application can be either a freshly produced cathode film layer or a cathode film layer obtained by dismantling a battery. The surface of the cathode film layer obtained by dismantling the battery inevitably contains residues of electrolyte salt particles, and to improve the accuracy of the test, an area scan of a cross-sectional area of ​​the cathode film layer is preferably performed along the thickness direction of the electrode foil to characterize the degree of graphitization of the cathode film layer. The graphitization C-value of the cathode film layer is obtained from the peak intensity ratio of the G-peak (G-band) and D-peak (D-band) of the Raman spectra. The G-peak is located at 1580 ± 100 cm⁻¹ and characterizes the sp² hybrid structure of the carbon, while the D-peak is located at 1350 ± 100 cm⁻¹ and characterizes the disordered structure. Disorder means that there is no regular arrangement between the carbon atoms in the structure. In graphite crystals, the carbon atoms in the same layer are sp² hybridized and form covalent bonds. Van der Waals forces act between the layers, allowing for easy sliding of the carbon within the graphite structure. Therefore, the C-value can characterize the degree of graphitization of the cathode film layer.It is understood that the degree of graphitization in the cathode film layer originates primarily from the graphitized carbon material within the cathode film layer, i.e., the carbon coating material of the active cathode material. Although conductive elements such as carbon nanotubes rich in sp²-hybridized structures also exhibit relatively high IG / ID values, their incorporation into the cathode film layer proves to be an extreme case in the Raman area scanning test of the cathode film layer due to their low additive content and small tube diameters, and they do not influence the C50in graphitization degree of the cathode film layer. Therefore, the graphitization degree of the cathode film layer can also characterize the graphitization degree of the active cathode material. A person skilled in the art can regulate the degree of graphitization of the active material particles using any known method. For example, the degree of graphitization of the active material particles can be adjusted by regulating the carbon source, the sintering temperature, the sintering time, the sintering pressure, and the sintering atmosphere. The higher the degree of graphitization of the carbon on the surface of the active cathode material, the higher the proportion of graphitic structural carbon in the cathode film layer, and the more easily the particles can slide in the coating layer with the help of the highly graphited carbon structure to reduce the stress concentration in the electrode foil, thereby reducing the demolding phenomenon and improving the cycle performance of the battery. In some embodiments, the median C50 of the graphitization degree in the cumulative distribution curve for the graphitization C value of the cathode film layer is optionally 0.95, 0.96, 0.97, 0.98, 0.99, 1.00, 1.01, 1.02, 1.03, 1.04, 1.05, 1.06, 1.07, 1.08, 1.09, 1.10, 1.11, 1.12, 1.13, 1.14, 1.15, 1.16, 1.17, 1.18, 1.19, 1.20 or any value in a range between any two of these values. In each embodiment, the median C50 of the graphitization degree in the cumulative distribution curve for the graphitization C value of the cathode film layer obtained in the area scanning mode of the laser microconfocal Raman spectrometer is 1.01-1.13. Furthermore, the degree of graphitization of the cathode film layer is within the above range, which helps to further improve the sliding ability of the particles in the cathode film layer, reduce the stress concentration in the cathode film layer and thereby further improve the long-term cycle stability of the battery cell. In some embodiments, the concentration level (C90-C10) / C50 of the C value in the cumulative distribution curve for the graphitization C value of the cathode film layer obtained in the area scanning mode of the laser microconfocal Raman spectrometer is 0.01-0.05. With reference to the above, analogously, C90 is the C-value when the cumulative number fraction of the vertical axis in the curve of the cumulative distribution of graphitization grade-C-value is 90%, and C10 is the C-value when the cumulative number fraction of the vertical axis in the curve of the cumulative distribution of graphitization grade-C-value is 10%. The concentration of the C-value is represented as (C90-C10) / C50. (C90-C10) / C50 can not only reflect the magnitude of most C-values ​​but also be unaffected by extreme values ​​and can also reflect the width of the particle graphitation distribution in the cathode film layer. A low concentration of the C-value in the cathode film layer indicates that the particle graphitation distribution in the cathode film layer is narrow and well concentrated. In some embodiments, the concentration level (C90-C10) / C50 of the C value in the cumulative distribution curve for the graphitization C value of the cathode film layer is optionally 0.01, 0.02, 0.023, 0.025, 0.03, 0.035, 0.036, 0.039, 0.04, 0.045, 0.05 or any value in a range between two of these values. The concentration of the C value of the cathode film layer is 0.01-0.05, which indicates that the graphitization of the particles in the cathode film layer is very uniform, meaning that the active cathode material has good uniformity and consistency of the coating, which can reduce the slip resistance caused by the unevenness of the graphitization of the particles in the active cathode material as well as the local stress concentration and reduce the risk of demolding, thus increasing the long-term cycle stability of the battery cell. In some embodiments, the concentration level (C90-C10) / C50 of the C value in the cumulative distribution curve for the graphitization C value of the cathode film layer obtained in the area scanning mode of the laser microconfocal Raman spectrometer is 0.02-0.04. The median C50 of the graphitization degree of the cathode film layer lies within the above range, which leads to a further improvement in the sliding ability between the particles, a further reduction in the local stress concentration and a reduction in the risk of demolding, while maintaining the high kinetic performance of the battery, thus achieving a balance between battery power and energy density. In some embodiments, the percentage area fraction of particles with a particle size R1 of R1≥1000 nm is 12%-50%, based on the total area of ​​the particles in a cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil. In the present application, the term "particle" refers to particles in the field of view of the cathode film layer at a specific magnification, e.g., 10,000x, with discernible complete boundaries, whereby defects and scratches may be present within the particles, but no complete boundaries sufficient for subdivision of the particles are discernible within the particles. The cathode film layer in the present application can be either a newly produced cathode film layer or a cathode film layer obtained by disassembling a battery. The particle identification procedure is as follows: the cathode film layer is cut by the argon ion beam along the thickness direction of the electrode foil (for example, optional: instrument model: Leica EMTIC3XCP, operating voltage: 6 kV, operating time: 6 h), and after exposing the cut surface, a scanning electron microscope is used (for example, optional: instrument model: Hitachi SU8230, operating voltage: 3 kV, beam current: high, probe model: U (LA100), working distance <5 mm) to observe the cut surface of the cathode film layer along the thickness direction of the electrode foil. The images are acquired with the field emission scanning electron microscope (FESEM) in the non-marginal position of the cut surface of the cathode film layer (after observing the edge of the electrode foil under the scanning electron microscope, the field of view is adjusted to the central part of the sample) in secondary electron mode.The electropherograms are acquired at 10k magnification, and the particles in the electropherograms are analyzed using ImageJ software (1.46r, Win64 version). The ImageJ software is used as follows: loading the SEM image to be analyzed; identifying the particles using the Cellpose plug-in software and manually correcting them based on this identification; reading and counting the data using ImageJ. The specific procedure for using the Cellpose plug-in software to identify the particles is as follows: setting the segmentation diameter parameter (diameter in the segmentation module) to 15 pixels, clicking "runcyto3" to identify the particles; the particles in the image that are not identified, not fully identified, or incorrectly identified by the software are manually marked. The particles in the image that are not identified, not fully identified, or incorrectly identified by the software are...The most common reasons for misidentification are: 1. The particles are too large or have scratches on their surface, preventing or incomplete identification; 2. Scratches occur on the particle surface during the argon ion beam sectioning process, and the software may misinterpret these scratches as particle boundaries during identification, leading to an identification error; 3. The particles are too small and therefore cannot be successfully identified; 4. The particles are located at the edge of the electron microscope's field of view, and the edge penetrates the particle's interior, resulting in an incomplete morphology and the identification of only a localized portion instead of the entire particle, leading to an identification error. The aforementioned unidentified or incorrectly identified particles are calibrated manually.and the specific process is as follows: Delete the particles that are located at the edges of the scanning electron microscope environment and are not fully displayed; assess whether or not there is a slit scratch within the other unidentified or misidentified particles, and if there is no slit scratch within a particle, it is assessed as a single particle, and it is manually marked according to the manually observed boundaries of the particles; in response to the presence of a slit scratch within the particle, it is assessed whether the slit scratch runs through the particle, and if it does not run through the particle, it is assessed that it is a single particle, and it is manually marked; in response to the slit scratch running through the particle, it is assessed whether the slit scratch is linear or irregular; in response to the slit scratch being irregular,It is judged to be a boundary between the particles, and the particles are divided along the boundary; in response to the fact that the slit scratch is linear, a contrast comparison is performed; in response to the fact that the contrast comparison is not obvious and there is no cracking effect, the slit scratch is judged to be a scratch, and it is marked as one particle; in response to the fact that the contrast comparison is strong and there is a cracking effect, the slit scratch is judged to be a boundary between the particles, and it is marked as two particles. After manual marking, the information that is not related to the particles in the automatic processing of the image is deleted, i.e., the assessment and marking of the particles in the image is complete. It is understood that the particles in a cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, in particular the particles of 50 nm or more, originate mainly from the active cathode material. Therefore, the embodiment of the present application can accurately and objectively reflect the distribution of the lithium-containing transition metal phosphate particles in the cathode film layer by observing and counting the particle area of ​​the particles in a cross-sectional area of ​​the cathode foil along the thickness direction of the electrode foil. In the prior art, the particle size of the active cathode material is usually determined using a laser particle size analyzer based on the Malvern laser diffraction method. However, the applicant's research shows that, because the lithium-containing transition metal phosphate particles readily agglomerate, the test results obtained using the Malvern laser diffraction method based on the laser scattering principle often measure the particle size of the particle agglomerates. This does not accurately reflect the particle size of the particles in the active cathode material, and even less so the dispersion of the active cathode material in the film layer, since the dispersion of the active cathode material in the film layer increases during the roller pressing process for film formation.The test results obtained by the Malvern laser diffraction method are influenced by the particle size, the specific surface area, and the degree of agglomeration of the active cathode material, and the number of large particles obtained by this test is lower than the actual value, and the number of small particles is higher than the actual value, compared to the real dispersion in the electrode foil, so that the particle size obtained by the Malvern laser diffraction method cannot be equivalent or analogous to the particle size obtained by the embodiment of the present application. The counting method for the area fraction of particles with a particle size R1 ≥ 1000 nm in the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil was carried out as follows: The particles in the cathode film layer are detected with reference to the above method of the present application; the image of particle determination and identification is imported into the ImageJ software for analysis, and the scale is set according to the scanning electron microscope image; the particle size, area, sphericity, and roughness of the particles in the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil are statistically analyzed using the analysis functions "Feret Diameter," "Area," "Round," and "Solidity." According to the software manual (ImageJUserGuideIJ 1.46r) The “Feret” parameter obtained from the analysis represents the maximum distance between all parallel lines in the two-dimensional projection of the particles, which is used to characterize the particle size; and the “Area” parameter obtained from the analysis represents the pixel size of the particles. Since particles with a size of less than 50 nm are difficult to identify accurately due to large errors in the statistical process, and since the particle size of the conductive medium is generally less than 50 nm, which can cause large errors in the statistical results, particles with a size of less than 50 nm are therefore not counted in the particle size statistical process of the present application, and the “NaN” corresponding statistical data displayed for AR, Round, or Solidity are deleted.The sum of the area parameters of particles with a particle size R1 ≥ 1000 nm and the sum of the area parameters of all particles were calculated as the area of ​​particles with a particle size R1 ≥ 1000 nm and the total area of ​​the counted particles, respectively. The sum of the areas of particles with a particle size R1 ≥ 1000 nm, divided by the total area of ​​the counted particles, is considered the percentage of the area occupied by particles with a particle size R1 ≥ 1000 nm in a cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil. In some embodiments, the percentage area fraction of particles with a particle size R1 of R1≥1000 nm, based on the total area of ​​the particles in a cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, is optionally 12%, 13%, 14%, 15%, 16%, 17%, 18%, 19%, 20%, 21%, 22%, 23%, 24%, 25%, 26%, 27%, 28%, 29%, 30%, 31%, 32%, 33%, 34%, 35%, 36%, 37%, 38%, 39%, 40%, 41%, 42%, 43%, 44%, 45%, 46%, 47%, 48%. 49%, 50% or any value in a range between two of these values. In some embodiments, the percentage area fraction of particles with a particle size R1 of R1≥1000 nm is 12%-40%, based on the total area of ​​the particles in a cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil. Large particles with a particle size R1 of R1 ≥ 1000 nm help to improve the compression density of the cathode film and thus increase the volumetric energy density of the battery cell; however, the researchers found that these large particles tend to cause a stress concentration on the large particles, thereby increasing the risk of cathode film delamination.Therefore, the area fraction of particles with a particle size R1 of R1≥1000 nm in the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil is in the range of 12%-50% and further in the range of 12%-40%, which is able to improve the pressing density of the electrode foil without making the probability of the film layer falling off too high, thereby improving the energy density of the densely coated batteries with lithium-containing transition metal phosphates and at the same time mitigating the problem of capacity degradation, taking into account the cycle life of the battery. In some embodiments, the cumulative distribution curve of the sphericity area of ​​particles with a particle size R1 of R1≥1000 nm is LRIA500.6-0.8. In the present application, where the cross-sectional area of ​​the cathode film layer is obtained along the thickness direction of the cathode foil, the test procedure for the sphericity of the particles with a particle size R1 of R1 ≥ 1000 nm is as follows: The particles in the cross-sectional area of ​​the cathode film layer are identified according to the procedure described above in the present application, and the morphology of the particles in the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil is analyzed using the "Shape-Description" analysis function in ImageJ. According to the software manual (ImageJ User Guide IJ 1.46r), the parameter "Round" obtained from the analysis represents the ratio of the pixel area of ​​the particle to the area of ​​the circle with the adjusted longitudinal diameter as the diameter, and can characterize the sphericity of the particles.The closer a particle is to a sphere, the closer the ratio of its pixel area to the area of ​​a circle with a modified longitudinal diameter (its diameter) is to 1. Therefore, the particle's "round" parameter, obtained from the analysis, is used to characterize its sphericity. To achieve a statistically significant number of samples, at least 10 scanning electron microscope images with non-overlapping fields of view were acquired for each electrode foil. The sphericities of the resulting 1000 particles are arranged in order from smallest to largest, and the cumulative distribution curve of the particle sphericity in the cathode film layer is obtained by using the sphericity as the horizontal axis and the cumulative area fraction as the vertical axis.LA50 is a sphericity L-value of the particles if, in the cumulative distribution curve of the sphericity L-value, the cumulative area fraction of the vertical axis is 50%. In some embodiments, LR1A50 in the cumulative distribution curve of the sphericity area of ​​the particles R1 of R1≥1000 nm in the cross-sectional area of ​​the cathode film layer along the thickness direction of the cathode foil is optionally 0.60, 0.61, 0.62, 0.63, 0.64, 0.65, 0.66, 0.67, 0.68, 0.69, 0.70, 0.705, 0.71, 0.72, 0.73, 0.74, 0.75, 0.76, 0.77, 0.78, 0.79, 0.80 or any value in a range between two of these values. A person skilled in the art can achieve control of the particle sphericity by any known method. The adjustment of particle sphericity can be achieved, for example, by processes such as comminution, polishing, chemical etching, mechanical mixing, extrusion, coating, granulation, addition of surfactants, etc., as well as by adjusting the parameters of the respective processes. In some embodiments, the cumulative distribution curve of the sphericity area of ​​the particles with a particle size R1 of R1≥1000 nm in the cross-sectional area of ​​the cathode film layer along the thickness direction of the cathode foil is LR1A500.65-0.75. In some embodiments, the cumulative distribution curve of the sphericity area of ​​the particles with a particle size R1 of R1≥1000 nm in the cross-sectional area of ​​the cathode film layer along the thickness direction of the cathode foil is LR1A500.67-0.75. In the cumulative distribution curve of the sphericity area of ​​particles with a particle size R1 of R1≥1000 nm in the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, LR1A50 lies in the range of 0.65-0.75 and further in the range of 0.67-0.75, which helps to further reduce the voltage concentration at the large particles in the cathode film layer of the thickly coated stacked electric core, thereby reducing the probability of film layer degradation and improving the cycle life of the battery. In some embodiments, the median B50 of the coating value in the cumulative distribution curve for the coating value-B of the cathode film layer obtained in the area scanning mode of the laser microconfocal Raman spectrometer is 0.30-0.60; where the coating value-B is IP / ID, where IP represents the intensity of the P-peak of the Raman spectrum at 948±100cm-1 and ID represents the intensity of the D-peak of the Raman spectrum at 1350±100cm-1. The cumulative distribution curve of coating value B is the curve obtained when at least 100 B values ​​are arranged in order from smallest to largest, using the coating value as the horizontal axis and the cumulative number fraction as the vertical axis. To reduce the influence of the extreme coating value due to the non-particle-like region in the cathode film layer on the test results, the median B50 of the coating value was used to assess the degree of density of the carbon coating material on the active cathode material. B50 is the B value when the cumulative number fraction on the vertical axis of the cumulative distribution curve of coating value B is 50%. In the present application, the coating value B can be obtained by an area-scanning mode of the laser microconfocal Raman spectrometer. As an example, a laser microconfocal Raman spectrometer (a high-precision Renishaw laser microconfocal Raman spectrometer) is used, an excitation wavelength of 532 nm is selected, and a suitable amount of the cathode film layer is taken for area scanning of the surface or a cross-sectional area along the thickness direction of the electrode foil. The scanning area is 45 µm × 45 µm, subdivided into 10 × 10 grids, with the vertex of the grid serving as the test point. The step size is 5 µm, and the total number of scan points is 100 to obtain the B values ​​at various locations and the cumulative distribution curve of the B values ​​in the area-scanning area.The cathode film layer in the present application can be either a freshly produced cathode film layer or a cathode film layer obtained by dismantling a battery. The surface of the cathode film layer obtained by dismantling the battery inevitably contains residues of electrolyte salt particles, and to improve the accuracy of the test, an area scan of a cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil is preferably carried out to characterize the coating value of the cathode film layer. The coating value B of the cathode film layer is obtained from the peak intensity ratio of the P-peak (P-band) and D-peak (D-band) of the Raman spectra, where the P-peak is located at 948 ± 100 cm⁻¹ and characterizes the phosphate PO₄³⁻ structure, and the D-peak is located at 1350 ± 100 cm⁻¹ and characterizes the disordered structure, where disorder means that there is no regular arrangement between the carbon atoms in the structure. The excitation wavelength of 532 nm is selected during the test, and the test depth is shallow. Consequently, the carbon structure peaks show a higher intensity than the phosphate structure peaks in the cathode film layer test results obtained in the area-scanning mode of the laser microconfocal Raman spectrometer. A person skilled in the art can regulate the coating value of the active material particles using any known method. For example, the coating value of the active material particles can be adjusted by regulating the type of carbon source, the amount of carbon source added, the sintering temperature, the sintering time, the sintering pressure, and the sintering atmosphere. The coating value B can reflect the degree of density of the carbon coating material on the surface of the lithium-containing transition metal phosphate particles. The denser the carbon coating, the relatively lower the intensity of the phosphate structure detected in the Raman spectrum, and the lower the coating value B of the cathode film layer. In some embodiments, the cathode film layer further comprises a coating layer that is applied to at least a portion of the surface of the lithium-containing transition metal phosphate particles, the median B50 of the coating value in the cumulative distribution curve for the coating value-B of the cathode film layer optionally being 0.3, 0.31, 0.32, 0.33, 0.34, 0.35, 0.36, 0.37, 0.38, 0.39, 0.4, 0.41, 0.42, 0.43, 0.44, 0.45, 0.46, 0.47, 0.48, 0.49, 0.5, 0.51, 0.52, 0.53, 0.54, 0.55, 0.56, 0.57, 0.58. 0.59, 0.6 or any value in a range between any two of these values. The median B50 value of the cathode film layer lies within the above range, indicating that the carbon coating material of the active cathode material is relatively dense and uniform. This improves the uniformity of cathode film layer slippage during roller pressing and reduces the phenomenon of stress concentration in the thickly coated cathode film layer. Furthermore, the dense and uniform carbon material layer facilitates the slippage of large particles in the cathode film layer during the pressing process. This reduces stress concentration on these particles, decreases the likelihood of cathode film layer delamination, improves battery capacity degradation, and extends battery cycle life. In some embodiments, the one-sided thickness H of the cathode film layer is 70 µm-120 µm. In some embodiments, the one-sided thickness H of the cathode film layer is 90 µm-120 µm. The thickness of the cathode film layer can be tested according to any known methods in this technical field. As an example, the thickness of the cathode film layer in the cross-sectional area of ​​the cathode foil was measured along the thickness direction using a scanning electron microscope. In some embodiments, the one-sided thickness H of the cathode film layer is optionally 70 µm, 71 µm, 71.53 µm, 72 µm, 73 µm, 74 µm, 75 µm, 76 µm, 77 µm, 78 µm, 79 µm, 80 µm, 81 µm, 82 µm, 83 µm, 84 µm, 85 µm, 86 µm, 87 µm, 88 µm, 89 µm, 90 µm, 91 µm, 92 µm, 93 µm, 94 µm, 95 µm, 96 µm, 97 µm, 98 µm, 99 µm, 100 µm, 101 µm, 102 µm, 103 µm, 104 µm, 105 µm, 105.64 µm, 105.89 µm, 106 µm, 106.66 µm, 106.79 µm, 107 µm, 108 µm, 109 µm, 110 µm, 111 µm, 112 µm, 113 µm, 114 µm, 115 µm, 116 µm, 117 µm, 118 µm, 119 µm, 119.12 µm, 120 µm oder einen beliebigen Wert in einem Bereich zwischen zwei dieser Werte. During the long-term battery cycle, the high thickness of the cathode film layer leads to significant volume expansion, resulting in an increase in internal stresses. This increases the risk of the film layer detaching from the electrode foil at the end of the cycle. The one-sided thickness of the cathode film layer is within the aforementioned range, which further increases the charge of the active cathode material in the battery and improves the battery's capacity, while simultaneously reducing the risk of film detachment and thus improving the battery's cycle performance. In some embodiments, the one-sided thickness H of the cathode film layer is 100 µm-120 µm. Increasing the thickness of the cathode film layer helps to increase the charge capacity of the active cathode material and thus the battery's capacity. However, the applicant found that when the one-sided thickness of the cathode film layer is greater than or equal to 100 µm, the volume expansion of the cathode film layer during the battery's cycling process is more significant, generating a higher voltage. This also increases the phenomenon of voltage concentration within the cathode film layer and raises the risk of film delamination, ultimately impairing the battery's cycling performance.The embodiments of the present application increase the battery capacity by increasing the thickness of the cathode film layer, and simultaneously control the median C50 of the graphitization degree in the cumulative distribution curve for the graphitization C value of the cathode film layer, which is obtained in the area scanning mode of the laser microconfocal Raman spectrometer, in order to increase the sliding ability between the particles in the cathode film layer, which supports the phenomenon of stress concentration in the film layer and reduces the risk of film layer degradation, thereby improving the cycle life of the battery. In some embodiments, the lithium-containing transition metal phosphate particles in the cathode film layer comprise a component with the following formula: Formula I: LimFexPyOjQq where Q comprises one or more of Al, Na, K, Mg, Cu, Mn, Cr, Zn, Pb, Ca, Co, Ni, Sr, Nb, V, Ti, B, S, Si, N, F, Cl, Br, and where 0.8≤m≤1.15, 0.9≤x≤1, 0.95≤y≤1, 3.5≤j≤4, 0≤q≤0.1. In some embodiments, m is optionally 0.8, 0.85, 0.9, 0.95, 0.98, 1.00, 1.03, 1.05, 1.08, 1.10, 1.13, 1.15 or any value in a range between any two of these values; x is optionally 0.9, 0.91, 0.92, 0.93, 0.94, 0.95, 0.96, 0.97, 0.98, 0.99, 1.0 or any value in a range between any two of these values; y is optionally 0.95, 0.96, 0.97, 0.98, 0.99, 1.00 or any value in a range between any two of these values; j is optionally 3.5, 3.6, 3.7, 3.8, 3.9, 4 or any value in a range between any two of these values; q is optionally 0, 0.01, 0.02, 0.03, 0.04, 0.05, 0.06, 0.07, 0.08, 0.09, 0.1 or any value in a range between any two of these values. In some embodiments, the lithium-containing transition metal phosphate particles in the cathode film layer comprise one or more of the following materials: lithium iron phosphate, lithium manganese phosphate, lithium fluoro-substituted vanadium phosphate, lithium ferromanganese phosphate and their modified materials. In some embodiments, the lithium-containing transition metal phosphate particles in the cathode film layer comprise one or more of the following materials: lithium iron phosphate and its doped modified materials, as well as modified coating materials. In some embodiments, the iron dissolution rate of the cathode material is 658 ppm-1921 ppm. The iron dissolution rate of the cathode material can be tested using methods known in the technical field. For example, 7.5 g of cathode material powder, obtained by scraping powder from a sample of the cathode film layer, are weighed out and added to 100.3 g of a 0.3% mass concentration ascorbic acid solution (the solvent being high-purity water). The solution is stirred at 500 revolutions per minute for 305 minutes, then rapidly aspirated with a 5 mL syringe and filtered into a test tube using a 0.45 µm orifice filter head. One mL of the supernatant is aspirated with a pipette gun and placed in a glass volumetric flask for 50-fold dilution. The iron dissolution rate is then tested using an inductively coupled plasma mass spectrometer (ICP-OES).to obtain the concentration of iron element in the solution using the following formula: [(ICP test concentration of iron element × volume of solution / mass of solution used for analysis) × 100.3 g / mass of cathode material powder], where the volume of the solution is 50 mL and the mass of the solution used for analysis is 1 g, and the iron dissolution rate of the cathode material is calculated. In some embodiments, the iron dissolution rate of the cathode material is optionally 658 ppm, 700 ppm, 800 ppm, 890 ppm, 900 ppm, 1000 ppm, 1058 ppm, 1076 ppm, 1100 ppm, 1143 ppm, 1200 ppm, 1236 ppm, 1300 ppm, 1311 ppm, 1384 ppm, 1349 ppm, 1400 ppm, 1485 ppm, 1500 ppm, 1531 ppm, 1600 ppm, 1700 ppm, 1800 ppm, 1921 ppm, or any value in a range between any two of these values. In some embodiments, the iron dissolution rate of the cathode material is 658 ppm-1485 ppm. The iron dissolved in the cathode material originates primarily from the lithium-containing transition metal phosphate particles of the active cathode material. The iron dissolution rate depends on the number of lattice defects in the lithium-containing transition metal phosphate and on the completeness and density of the carbon coating on the surface of the active cathode material. The lower the iron dissolution rate, the fewer the lattice defects in the lithium-containing transition metal phosphate, thus reducing lattice corrosion in the weakly acidic environment. Conversely, the more complete and dense the carbon coating on the surface of the active cathode material is, thus inhibiting the dissolution of iron ions in the weakly acidic environment.The cathode material with an iron dissolution rate within the above range exhibits relatively few lattice defects, and the carbon coating material is complete and dense, which is conducive to improving the compression resistance and the degree of easy particle slippage in the cathode film layer under high roller pressure, increasing the compression density of the cathode film layer and reducing the stress concentration in the cathode film layer, thus improving the energy density of the battery while addressing the problem of battery capacity degradation. In some embodiments, the mass content of titanium is 500 ppm-8000 ppm, based on the total mass of the lithium-containing transition metal phosphate particles in the cathode film layer. Both the type and the content of the elements in the lithium-containing transition metal phosphate particles in the cathode film layer can be tested according to any known methods in the relevant technical field. For example, the titanium content is tested using inductively coupled plasma emission spectrometry with reference to Annex C of GB / T 33822-2017. In some embodiments, the mass content of titanium, based on the total mass of the lithium-containing transition metal phosphate particles in the cathode film layer, is optionally 500 ppm, 600 ppm, 700 ppm, 800 ppm, 900 ppm, 1000 ppm, 1100 ppm, 1200 ppm, 1400 ppm, 1500 ppm, 1600 ppm, 1700 ppm, 1800 ppm, 1900 ppm, 2000 ppm, 2100 ppm, 2200 ppm, 2300 ppm, 2400 ppm, 2500 ppm, 2600 ppm, 2700 ppm, 2800 ppm, 2900 ppm, 3000 ppm, 3500 ppm, 4000 ppm, 4500 ppm. 5000ppm, 5500ppm, 6000ppm, 6500ppm, 7000ppm, 7500ppm, 8000ppm or any value in a range between any two of these values. In some embodiments, the mass content of titanium is 1000 ppm-3000 ppm, based on the total mass of the lithium-containing transition metal phosphate particles in the cathode film layer. The introduction of titanium into lithium-containing transition metal phosphate particles requires the addition of a titanium source during the fabrication of the active cathode material. This titanium source is often an inert material that adheres to the surface of the lithium-containing transition metal phosphate particles to reduce reactivity and particle size growth. Increasing the degree of graphitization of the active cathode material often necessitates a higher sintering temperature or a longer sintering time, which, however, also increases the particle size in the cathode film layer, increases the stress concentration in the cathode film layer, and triggers the phenomenon of cathode film delamination.In the embodiments of the present application, the reactivity of the synthetic raw material of the active cathode material can be reduced by adding a high proportion of titanium to the lithium-containing transition metal phosphate particles, so that the active cathode material has a high degree of graphitization and at the same time achieves control of the proportion of large particles, which reduces the stress concentration of the cathode film layer and decreases the probability of the cathode film layer deteriorating, thereby improving the energy density of the battery and taking into account the reliability of the battery. Simultaneously, the doping of titanium in the active cathode material leads to lattice distortion, reduces the Li-O bond energy, increases the lithium ion diffusion rate, and improves the battery's kinetic performance. The uneven diffusion of lithium ions in the thick-coated film layer is often accompanied by significant lithium ion concentration gradients, and the embodiments of the present application improve the solid-state transfer rate of the active cathode material by adding a high titanium content to the lithium-containing transition metal phosphate particles, thereby improving the kinetics of the battery with a thick electrode film. In some embodiments, the mass content of vanadium is 500 ppm-5000 ppm, based on the total mass of the lithium-containing transition metal phosphate particles in the cathode film layer. Both the type and the content of the elements in the lithium-containing transition metal phosphate particles in the cathode film layer can be tested according to any known methods in the relevant technical field. For example, the vanadium and its content are tested using inductively coupled plasma emission spectrometry with reference to Annex C of GB / T 33822-2017. In some embodiments, the vanadium mass content, based on the total mass of the lithium-containing transition metal phosphate particles in the cathode film layer, is optionally 500 ppm, 600 ppm, 700 ppm, 800 ppm, 900 ppm, 1000 ppm, 1100 ppm, 1200 ppm, 1400 ppm, 1500 ppm, 1600 ppm, 1700 ppm, 1800 ppm, 1900 ppm, 2000 ppm, 2100 ppm, 2200 ppm, 2300 ppm, 2400 ppm, 2500 ppm, 2600 ppm, 2700 ppm, 2800 ppm, 2900 ppm, 3000 ppm, 3500 ppm, 4000 ppm, 4500 ppm. 5000ppm or any value in a range between two of these values. In some embodiments, the mass content of vanadium is 500 ppm-3000 ppm, based on the total mass of the lithium-containing transition metal phosphate particles in the cathode film layer. The vanadium element in the cathode film layer can exist in different valence states. +5-valent vanadium (V5+) can be doped with phosphorus sites, leading to lattice distortions due to its larger radius. This enlarges the lithium-ion diffusion channels and thus improves the ionic conductivity of the active cathode material, thereby enhancing the battery's kinetic performance. +3-valent vanadium (V3+) can be doped with transition metal sites, creating lithium gaps through charge compensation, which improves the electronic conductivity of the active cathode material.Furthermore, the increased uniformity of the vanadium element in the lithium-containing transition metal phosphate particles contributes to a further improvement in the kinetic performance of the cathode film layer and the uniformity of the reaction of the cathode film layer, thus further improving the kinetic performance and the cycle performance of the battery cell. The vanadium content in the above area contributes to improving the kinetic performance of the cathode foil and the kinetic performance of the thick-coated lithium-containing transition metal phosphate battery. Simultaneously, the synergistic action of the titanium element, the vanadium element, and the carbon nanotubes in the cathode film layer helps to form a good three-dimensional network, further improving the electronic and ionic conductivity of the cathode film layer, thereby further enhancing the kinetic performance of the thick-coated lithium-containing transition metal phosphate battery. In some embodiments, the porosity of the cathode film layer is 14%-28%. In the present application, the porosity of the cathode film layer can be tested using the following procedure: Import the scanning electron micrograph of the cross-sectional area of ​​the cathode film layer, obtained using the above method, along the thickness direction of the electrode foil into the ImageJ software, select the straight line tool, use a straight line to mark the length of the scale in the image, click on "Analyze Set Scale" and adjust the scale parameters in the software according to the length of the scale in the image.Select the rectangle tool, select the portion of the image outside the scale range, use "Image Duplicate" to duplicate the selected area, use "Image Type 8 bit" to adjust the image format; select "Analyze Set Measurements" and select the following five options: "Area", "Mean gray value", "Area Fraction", "Limit to threshold", "Feret's diameter", selecting 3 for "Decimal places", and successively selecting "Image" - "Adjust" - "Threshold", and successively setting the "Threshold" position to 0 and 100, thereby enabling the "Analyze-Measure" function to export the pore data in the scanning electron microscope image of the section.Use “Image” - “Overlay” - “Flatten” to export and obtain the pore image; click “Apply” in “Threshold”, then click “Analyze” - “Analyze Particles”, checking the four columns on the left to obtain the pore statistics. It is understood that, in an embodiment of the present application, the "pores" in the cut surface of the cathode film layer are identified by the color difference and the threshold value of the image. The "pore" is not the porosity data obtained in the exhaust gas test, but is primarily used to characterize the distances between the particles in the cut surface of the cathode film layer. This method is superior to the exhaust gas method because the porosity obtained by the exhaust gas method is related to the pores between the particles, and also to the pores in the carbon coating material on the surface, and therefore the pores between the particles cannot be objectively represented. In some embodiments, the porosity of the cathode film layer is optionally 14%, 15%, 16%, 17%, 18%, 19%, 20%, 21%, 22%, 23%, 24%, 25%, 26%, 27%, 28% or any value in a range between two of these values. The porosity of the cathode film layer lies within the range mentioned above, and the cathode film layer exhibits a good electrolyte infiltration rate and good tortuosity, which promotes the diffusion of lithium ions in the liquid and solid phases, reduces the concentration polarization of the thick electrode foil, and improves the battery's kinetic performance. Simultaneously, it helps to reduce the volume expansion of the thick-coated electrode foil during the cycling process, decrease the mechanical stress on the film layer, and mitigate the phenomenon of voltage concentration, thereby reducing the risk of the thick-coated electrode foil delamination. In particular, in a thick-coated soft-pack battery, the gap between the casing and the electrode foil is small, the volume coverage of the film layer is large, the absorption volume of the electrolyte solution is reduced, and the porosity of the cathode film layer is within the above range, which helps to improve the liquid retention rate of the electrical core and the kinetic performance of the battery. In some embodiments, the specific resistance of the cathode film layer is 10 Ω·cm to 35 Ω·cm. In some embodiments, the specific resistance of the cathode film layer is optionally 10 Ω·cm, 12 Ω·cm, 14 Ω·cm, 16 Ω·cm, 18 Ω·cm, 20 Ω·cm, 22 Ω·cm, 22 Ω·cm, 24 Ω·cm, 26 Ω·cm, 28 Ω·cm, 30 Ω·cm, 32 Ω·cm, 35 Ω·cm or any value in a range between two of these values. The specific resistance of the cathode film layer is in the above range, which contributes to reducing the impedance of electron transfer, reducing charge / discharge polarization, and improving the multiplication performance and cycle performance of the battery. In some embodiments, the cathode film layer further comprises a dispersing agent, wherein the dispersing agent comprises hydrogenated nitrile butadiene rubber (HNBR). HNBR is obtained from nitrile rubber by hydrogenation of saturated double bonds, and its highly saturated main-chain structure gives it excellent oil resistance, heat resistance, and aging resistance, among other properties. This makes it stable in various environments and systems when used as a dispersant, and it does not degrade or degrade easily, allowing it to effectively fulfill the role of a dispersion agent. The HNBR molecular chain contains both polar nitrile groups and nonpolar hydrocarbon chain segments. Polar nitrile groups can interact with some polar substances or particle surfaces, for example...through adsorption on the surface of the dispersed particles by hydrogen bonds, electrostatic interaction, and so on; The nonpolar hydrocarbon chain segments have good lipophilicity, which allows them to be well stretched and dispersed in nonpolar or weakly polar media, so that the particles are uniformly dispersed in the media. When HNBR is adsorbed onto the surface of particles in the slurry, its long-chain molecules form a physical barrier around the particles, preventing them from approaching and aggregating. This allows the particles to remain relatively independent and dispersed within the system. Simultaneously, HNBR can reduce the surface tension between the dispersion medium and the dispersed particles, making it easier for the particles to be moistened by the medium and thus promoting their dispersion. It can also reduce the interfacial energy between the particles, particularly mitigating the aggregation phenomenon of the conductive medium caused by interfacial energy reduction.Furthermore, when the slurry is dried to form a film, the elastic network structure of HNBR can buffer the shrinkage stress generated by solvent evaporation, regroup the conductive agent in the process due to capillary action, and reduce the area fraction of the conductive agent agglomeration region, thereby improving the kinetic performance and cycle life of the battery. In some embodiments, the mass content of the dispersant is 0.5%-2%, based on the mass of the cathode film layer. In some embodiments, the mass fraction of the dispersing agent relative to that of the cathode film layer is optionally 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1%, 1.5%, 2% or any value in a range between two of these values. The mass content of the dispersant is within the above range, which allows for a uniform dispersion of the particles in the cathode film layer, while maintaining a high charge capacity in the cathode film layer. This reduces the voltage concentration in the thickly coated lithium-containing transition metal phosphate cathode film layer, effectively alleviating the problem of battery capacity loss. In some embodiments, the cathode film layer further comprises a conductive agent, where, based on the total area of ​​the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, the area fraction of an agglomeration region of the conductive agent is 0.5%-2.5%. In the present application, the area fraction of the conductive agglomeration region can be tested by the following method, based on the total area of ​​the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil. The area of ​​the conductive agglomeration region in this scanning electron microscope image is measured at a magnification of 3k by scanning the cross-sectional area of ​​the cathode film layer using a scanning electron microscope according to a similar method described above. Since the conductive material is generally carbon-based, such as conductive carbon black, carbon nanotubes, etc., the agglomerated conductive material is visible at high magnification, and the conductive agglomeration region tends to show a black agglomeration compared to other areas in the cathode film layer.Using image analysis software, the conductive agglomeration area is the black area where the conductive material is clearly aggregated in the scanning electron microscopy image. Specifically, the scanning electron microscopy image is imported into ImageJ at a magnification of 3k, the black agglomeration areas of the conductive material with a feret of 2 µm or more are filtered out, and the sum of the areas of the filtered-out areas is statistically recorded as the area of ​​the conductive agglomeration area. The area fraction of the conductive agglomeration area is the ratio of the area of ​​the conductive agglomeration area to the total area of ​​the imported scanning electron microscopy image.Three scanning electron microscope images with non-overlapping areas are taken at random, the average value of the area fractions of the agglomeration area of ​​the conductive medium is calculated and averaged as "the area fraction of the agglomeration area of ​​the conductive medium relative to the total area of ​​the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil". In some embodiments, the cathode film layer further comprises a conductive agent. Based on the total area of ​​the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, the area fraction of an agglomeration region of the conductive agent is optionally 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2%, 2.1%, 2.2%, 2.3%, 2.4%, 2.5%, or any value in a range between two of these values. Based on the total area of ​​the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, the area fraction of the agglomeration region of the conductive medium lies in the above range, indicating that the conductive medium is uniformly dispersed in the cathode film layer and that it is easy to form a homogeneous conductive network. This particularly helps to reduce the problem of reduced kinetics in a thick-coated film layer due to the increase in ion transfer paths, to reduce local polarization or even lithium precipitation of the battery during the cycling process, and thus improves the battery's cycle life. At the same time, research has shown that the first particles, being large in size, are easily rebounded by the lithium-containing transition metal phosphate particles. The agglomeration area of ​​the conductive agent in the above region can inhibit the rebound of the lithium-containing transition metal phosphate particles by means of the uniform distribution of the conductive agent, in order to form a mechanical bond between the particles and even the film layer, improve the cohesion of the film layer, reduce powder fallout and film layer deterioration, and extend the battery's lifespan. In some embodiments, the cathode film layer further comprises a conductive agent, where, based on the total area of ​​the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, the area fraction of an agglomeration region of the conductive agent is 1.5%-2.5%. In the embodiments of the present application, the area fraction of the agglomeration region of the conductive agent lies further within the above range, indicating that the conductive agent is distributed more uniformly in the cathode film layer and that the content of the conductive agent is lower, which improves the kinetic performance of the cathode film layer and at the same time helps to reduce the occupancy of the space of the active cathode material due to the excess of conductive agent, thus further improving the volume energy density of the battery and simultaneously increasing the kinetic performance of the battery. In some embodiments, the conductive medium comprises carbon nanotubes, wherein the carbon nanotubes comprise one or more of single-walled carbon nanotubes, thin-walled carbon nanotubes, or multi-walled carbon nanotubes. In this application, the term "carbon nanotube" refers to a nanomaterial with several to ten layers of coaxial hollow tubes formed by coiling graphene sheets with carbon atoms bonded by sp² hybridization. The diameters are typically in the range of a few to several dozen nanometers, and the lengths can vary from micrometers to centimeters, exhibiting a high length-to-diameter ratio. Carbon nanotubes can be classified according to the number of graphene layers: single-walled carbon nanotubes (SWCNTs), few-walled carbon nanotubes (FWCNTs), and multi-walled carbon nanotubes (MWCNTs). Carbon nanotubes have excellent electrical conductivity and a high elastic modulus. Since carbon nanotubes have a one-dimensional structure, they can form a network structure in the cathode film layer. On the one hand, due to the high elastic modulus of carbon nanotubes, the network structure not only serves as a bridge for the propagation of voltages, but also has a binding effect on the densely coated cathode film layer, which inhibits the rebound of lithium-containing transition metal phosphate particles. This effectively reduces the voltage concentration and the risk of the film layer deteriorating, which in turn improves the problem of battery capacity degradation.On the other hand, the excellent electrical conductivity of carbon nanotubes makes their network structure a highly efficient electron transfer channel, and even if there is local drop-off of the film layer, the thick electrode foil can still maintain a high electron transfer efficiency in the plane direction and in the thickness direction, thus slowing down the problem of capacity drop-off and further improving the kinetic performance and cycle life of the battery. In some embodiments, the conductive medium also comprises conductive carbon black. Conductive carbon black has a high specific surface area and therefore good liquid retention capacity. The expansion force of the thick electrode foil during the cycling process is high, which allows the electrolyte solution to be easily extruded. The distribution of conductive carbon black in the cathode film layer contributes to improving the liquid retention capacity of the thick electrode foil, further mitigating the phenomenon of capacity loss during the battery's cycling process and improving the battery's cycle life. In some embodiments, the agglomeration area of ​​the conductive agent comprises carbon nanotubes and conductive carbon black. The researchers found that carbon nanotubes, due to their high surface energy, tend to agglomerate, leading to an uneven distribution in the cathode film layer and preventing the formation of an effective network structure. Conductive carbon black, with a surface energy close to that of carbon nanotubes, can be adsorbed onto their surface to form a physical barrier. This increases resistance to agglomeration, reduces direct contact between the nanotubes, and thus inhibits the agglomeration phenomenon. The uniformity of carbon nanotube distribution within the cathode film layer is thereby improved.On the one hand, this helps to improve the electrical conductivity of the thick-coated cathode film layer and the kinetic performance of the battery; on the other hand, it helps to exert the binding effect of the carbon nanotubes on the cathode film layer, reducing the risk of the thick-coated cathode film layer delaminating and further improving the kinetic performance and lifetime of the battery. Furthermore, the agglomeration of carbon nanotubes in the agglomeration region of the conductive agent also leads to the blocking of the local ion transfer pathway in this region, and the collocation of conductive carbon black can improve the lithium-ion transfer capacity in this region, reduce local polarization, and further improve the cycle stability of the battery.In some embodiments, the mass fraction C1 of the carbon nanotubes fulfills 0 with respect to the mass of the cathode film layer. <C1≤2,5% und der Massengehalt C2 des leitfähigen Rußes 0<C1≤2,5%. In some embodiments, the mass fraction C1 of the carbon nanotubes, based on the mass of the cathode film layer, is optionally 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%, 2.1%, 2.2%, 2.3%, 2.4%, 2.5%, or any value in a range between any two of these values. In some embodiments, the mass fraction C2 of the conductive carbon black, based on the mass of the cathode film layer, is optionally 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1%, 1.1%, 1.2%, 1.3%, 1.4%, 1.5%, 1.6%, 1.7%, 1.8%, 1.9%, 2.0%, 2.1%, 2.2%, 2.3%, 2.4%, 2.5%, or any value in a range between any two of these values. The mass content of carbon nanotubes and conductive carbon black within the above range can effectively reduce the agglomeration phenomenon of carbon nanotubes and form a good conductive network structure, thereby effectively reducing the voltage concentration of the cathode film layer and improving the retention rate of electrolyte solution of the cathode foil during long cycles, further reducing the risk of electrode foil film layer deterioration and the degree of polarization, thus increasing the kinetic performance of the battery and improving the battery cycle life, while addressing the problem of capacity degradation. In some embodiments, the battery cell further comprises a separator 20 provided between the cathode foil and the anode foil, wherein the separator 20 comprises a base film 201 and a ceramic layer 202 provided on at least one side of the base film 201, and a binder layer 203 provided on a side of the ceramic layer 202 facing away from the base film 201, wherein the binder layer 203 is a continuous layer with a porous structure, and wherein the binder layer 203 comprises a vinylidene fluoride polymer. In some embodiments, the battery cell further comprises a separator provided between the cathode foil and the anode foil, wherein the separator comprises a base film, a ceramic layer provided on both sides of the base film, and a bonding layer provided on at least one side of the ceramic layer facing away from the base film. The ceramic layer is applied to both sides of the base film to improve the rigidity of the soft-pack battery and reduce local stress concentration. In some embodiments, the battery cell further comprises a separator provided between the cathode foil and the anode foil, wherein the separator comprises a base film, a ceramic layer provided on both sides of the base film, and a bonding layer provided on both sides of the ceramic layer facing away from the base film. In some embodiments, the vinylidene fluoride polymer comprises one or more of the following materials: polyvinylidene fluoride (PVDF), polyvinylidene fluoride-hexafluoropropylene copolymer (PVDF-HFP). In some embodiments, the vinylidene fluoride polymer comprises polyvinylidene fluoride (PVDF). According to the prior art, aqueous PVDF is generally used for the separator bonding layer, which tends to form an island-like structure in the separator, as shown in Fig. 2. This helps to create a gap for the expansion of the electrical core and is easy to manufacture; however, such a separator bonding layer has a smaller contact area with the electrode foil and a weak bonding force. The separator provided by the embodiments of the present application has a continuous layer with a porous structure as a bonding layer, as shown in Fig. 1 and Fig. 3, which has a larger bonding area with the electrode foil compared to the bonding layer in the prior art, thereby making the bond between the separator and the electrode foil stronger and more uniform; furthermore, if the cathode film layer detaches, it is advantageous to maintain the interfacial contact between the separator and the cathode film layer, thereby reducing the probability of the film layer detaching. It is understood that the continuous layer may be broken and deformed into a block shape due to contact with the cathode foil or the anode foil, or due to extrusion by force during the manufacturing or cycling process of the electrode foil. The continuous layer referred to in the present application does not require the bonding layer to be continuous throughout the entire battery. The continuous structure in the present application is shown at the microscopic level; as can be seen under a scanning electron microscope or a light microscope, the separator bonding layer is continuous. To obtain feedback on the actual morphology of the separator, sampling preferably involves sampling the separator in an area of ​​the battery where there is no bond between the separator bonding layer and the cathode foil or the anode foil.For example, by sampling the separator at a point extending beyond the cathode and anode foils, or by sampling the separator near the surface of the electrode assembly. This type of separator exhibits less bonding between the sampling area and the cathode or anode foil, providing better feedback on the actual condition of the separator. Compared to a wound electrical core, the extrusion between the separator and the electrode film in a stacked electrical core is small, and the separator and electrode film tend to shift relative to each other, which disturbs the film layer and causes it to pulverize or detach. Furthermore, it can lead to the cathode and anode being superimposed, which may increase the risk of an internal short circuit in the electrical core. Therefore, the separator provided by the embodiments of the present application is particularly suitable for stacked electrical cores.Increasing the bonding force between the porous bonding layer and the electrode foil helps to improve the bonding force between the separator and the electrode foil and to reduce the relative displacement between the separator and the electrode foil, which not only helps to reduce disturbance of the cathode film layer and decrease the likelihood of the film layer detaching, but also helps to reduce the risk of the cathode and anode colliding and thereby causing a short circuit in the electrical core. In summary, selecting the fluorinated vinylidene fluoride polymer from the materials described above for the bonding layer of the embodiments of the present application helps to form a continuous and uniform porous bonding layer. Firstly, the bonding strength between the bonding layer and the electrode foil is improved and evenly distributed, which helps to reduce the phenomenon of voltage concentration in the thickly coated cathode film layer of lithium-containing transition metal phosphate and decrease the risk of film delamination, thereby further improving the cycle life of the battery.Secondly, the bonding layer is stably bonded to the cathode foil or the anode foil, which helps to reduce direct contact between the cathode foil and the anode foil due to the relative displacement of the cathode foil and the separator, thus reducing the risk of an internal short circuit and contributing to improved battery safety; Thirdly, the porous bonding layer helps to maintain the porosity of the separator, thereby reserving space for the expansion of the electrical core and further improving the cycle life of the battery. In some embodiments, the base film material may include, but is not limited to, one or more of the following materials: fiberglass, nonwoven fabric, polyethylene (PE), polypropylene (PP). In some embodiments, the ceramic layer comprises one or more of the following materials: aluminum oxide (Al2O3), zirconium oxide (ZrO2), titanium oxide (TiO2), silicon oxide (SiO2), boron nitride (BN). Ceramic particles are highly flame-resistant, exhibit high hardness, and are not easily deformed by heat, resulting in excellent dimensional stability. The low thermal conductivity of ceramic materials can also prevent specific points of thermal runaway within the battery from developing into a full-blown thermal runaway, thus improving the battery cell's safety performance. In some embodiments, the thickness of the base film in the separator is 7-9 µm. In some embodiments, the thickness of the base film in the separator is 7 µm, 7.5 µm, 8 µm, 8.5 µm, 9 µm or any value in a range between two of these values. In some embodiments, the thickness of the ceramic layer on one side of the separator is 2-4 µm. In some embodiments, the one-sided thickness of the ceramic layer in the separator is 2 µm, 2.5 µm, 3 µm, 3.5 µm, 4 µm or any value in a range between two of these values. In some embodiments, the thickness of the bonding layer on one side of the separator is 1-5 µm. In some embodiments, the one-sided thickness of the bonding layer in the separator is 1 µm, 1.5 µm, 2 µm, 2.5 µm, 3 µm, 3.5 µm, 4 µm, 4.5 µm, 5 µm or any value in a range between two of these values. In the present application, "thickness" has a meaning known in the art and can be measured using methods and instruments known in the art. For example, a high-precision micrometer (e.g., a Mitutoyo 293-100 with an accuracy of 0.1 µm) can be used for the test. If the thickness of the bonding layer is too small, the space for the gaps in the separator is limited, and the bonding force between the separator and the electrode foil is weak. On the one hand, this increases the probability of elevated voltage after film expansion and delamination, impacting the battery's lifetime; on the other hand, it increases the probability of a short circuit during negative cathode overlap, negatively impacting the battery's safety performance. Conversely, if the bonding layer thickness is too large and the battery's volumetric energy density is high, it negatively affects the battery's volumetric energy density. In the embodiments of the present application, the bonding layer thickness is within the aforementioned range, thus balancing the battery's cycle life, safety performance, and volumetric energy density. In some embodiments, the cathode film layer is provided with a lower coating layer at a lower area facing the cathode collector, the lower coating layer comprising a conductive agent and a binder, wherein the conductive agent comprises carbon nanotubes and conductive carbon black, and the binder comprises a polyvinylidene fluoride (PVDF). In some embodiments, the thickness of the lower coating layer is 0.5 µm-5 µm. In some embodiments, the thickness of the lower coating layer is 0.5 µm, 1 µm, 1.5 µm, 2 µm, 2.5 µm, 3 µm, 3.5 µm, 4 µm, 4.5 µm, 5 µm or any value in a range between two of these values. The lower coating layer provided in the embodiments of the present application contributes to improving the adhesion between the cathode film layer and the cathode collector and to reducing the phenomenon of voltage concentration at the large particles, thereby decreasing the probability of cathode film layer delamination and improving the cycle stability of the battery. At the same time, compared to direct contact between the cathode collector and the cathode film layer, the contact area between the lower coating layer and the cathode film layer is increased, which contributes to increasing the electron transfer area between the collector and the cathode film layer, thereby reducing the internal resistance of the electrode foil and improving the kinetic performance of the battery. In some embodiments, as shown in Fig. 4, the battery cell 5 comprises a housing 50, wherein the stacked electrical core is received in the housing 50, wherein the housing 50 has a dimension of L0 in a longitudinal direction X, wherein the housing has a dimension of W0 in a width direction Y, wherein the housing has a dimension of H0 in a thickness direction Z, wherein 480 mm ≤ L0 ≤ 720 mm, 100 mm ≤ W0 ≤ 150 mm, and 14 mm ≤ H0 ≤ 22 mm. In some embodiments, L0 is optionally 480 mm, 490 mm, 500 mm, 510 mm, 520 mm, 530 mm, 540 mm, 550 mm, 560 mm, 570 mm, 580 mm, 590 mm, 600 mm, 610 mm, 620 mm, 630 mm, 640 mm, 650 mm, 660 mm, 670 mm, 680 mm, 690 mm, 700 mm, 710 mm, 720 mm, 750 mm, 800 mm, 850 mm, 900 mm, 950 mm, 1000 mm, 1050 mm, 1100 mm, 1150 mm, 1200 mm, 1250 mm, 1300 mm, or any value in a range between any two of these Values. In some embodiments, W0 is optionally 100 mm, 110 mm, 120 mm, 130 mm, 140 mm, 150 mm or any value in a range between any two of these values. In some embodiments, H0 is 14 mm, 15 mm, 16 mm, 17 mm, 18 mm, 19 mm, 20 mm, 21 mm, 22 mm or any value in a range between any two of these values. In some embodiments, the dimension of the housing in the longitudinal direction L0 is 450 mm ≤ L0 ≤ 650 mm. If the length dimension L0 of the casing meets the criteria of 450 mm ≤ L0 ≤ 650 mm, the battery cell length is shorter. This helps to shorten the current diffusion path and reduce the internal resistance of the electrodes, thereby reducing heat generation in the battery and improving its kinetic performance. Furthermore, the shorter casing length contributes to shortening the electrolyte diffusion path during infiltration, improving the infiltration rate and electrolyte uniformity, further promoting the uniformity of lithium ion disembedding during the cycling process, mitigating voltage concentration, reducing the risk of film degradation, and improving the cycle stability of the battery cell. In some embodiments, the dimension of the housing in the longitudinal direction L0 is 900 mm ≤ L0 ≤ 1300 mm. If the length dimension L0 of the casing meets the following condition: 900 mm ≤ L0 ≤ 1300 mm, the longer battery cell size helps to reduce the volume fraction of the casing within the battery cell and improve the load-bearing capacity of the active material. Simultaneously, a longer battery cell can reduce the number of batteries required in the battery module, simplify the structural design of the battery module, decrease the number and complexity of structural components within the module, and thereby improve the space utilization rate of the battery pack, which in turn contributes to improving the volume energy density of the battery cell. In some embodiments, as shown in Fig. 4, the material of the housing 50 is a soft packaging material, wherein the soft packaging material comprises an aluminum-plastic composite film, optionally a composite film formed from one or more of polypropylene (PP), polybutylene terephthalate (PBT), polybutylene succinate (PBS), nylon, polyethylene terephthalate (PET), polyethylene (PE) with aluminum. The applicant found that the soft packing materials are lighter than hard shell materials such as aluminum and steel shells, which contributes to a further improvement in the energy density of lithium-containing transition metal phosphate batteries. Furthermore, the soft packing material has high ductility, allowing for a thinner and softer casing, which helps to improve the space utilization of the battery cell and thus increase its energy density. In addition, the high barrier properties of aluminum effectively reduce the ingress of water and oxygen into the battery interior, thereby reducing electrolyte degradation and electrode material oxidation, and thus extending the battery's lifespan. In some embodiments, as shown in Fig. 4, the housing 50 comprises a first sealing zone 51, wherein the first sealing zone 51 is provided at at least one laterally extending end of the stacked electrical core; wherein the first sealing zone 51 comprises a longitudinally extending folded edge structure, wherein the folded edge structure is provided with an encapsulating adhesive, wherein the encapsulating adhesive is provided successively along the longitudinal direction and secures the folded edge structure; The folded edge structure is a reinforcement structure formed by an unlimited number of folds of the encapsulation area, e.g., a singly folded edge structure that is folded once, or a doubly folded edge structure that is folded on both sides. The SEI film in the cathode film layer thickens during the electrode foil's cycling process, leading to strong rebound and gas production during long cycles. The sealing zone of the soft-packed electrical core serves to seal the electrode assembly, but this zone has limited strength and is easily washed away by the strong rebound and high gas production in the film layer. The embodiments of the present application further improve the sealing strength of the first sealing zone by incorporating a folded edge structure extending along the longitudinal direction within the first sealing zone. The encapsulation adhesive is continuously applied along the longitudinal direction and secures the folded edge structure, in contrast to discontinuous application of the encapsulation adhesive along the longitudinal direction. This further improves the encapsulation strength, achieves continuous reinforcement of the sealing zone in the longitudinal direction, and reduces the likelihood of the thick-coated electrode film popping out of the packaging's sealing zone during the cycle process. In some embodiments, the housing 50 comprises at least one second sealing zone 52, wherein the second sealing zone 52 is provided at at least one end of the stacked electrical core along the longitudinal direction of the housing 50, wherein the second sealing zone 52 is provided on one side of the electrode tab of the stacked electrical core. It goes without saying that the cathode tab and the anode tab can be provided on the same side of the stacked electrical core, as shown in Fig. 1, or that they can be provided on opposite sides of the stacked electrical core. In some embodiments, the battery cell 5 further comprises a lead element 53 which is connected to the electrode tabs of the battery cell; for example, the lead element 53 may be welded to the electrode tabs, wherein the lead element 53 is a conductive element; at least a part of the lead element 53 is located outside the housing 50; the lead element 53 acts as an electrode lead end of the battery cell 5; the lead element 53 is used to facilitate the electrical connection of the battery cell 5 to other battery cells 5 or other components. The lead element 53 may, for example, have the form of a sheet. Accordingly, the supply element 53 also includes a cathode supply element and an anode supply element, wherein the cathode supply element is connected to the cathode tab and the anode supply element is connected to the anode tab. In some embodiments, the second sealing zone is located on the side of the electrode tab, the electrode tab must be connected to a lead element, and the connection strength of the lead element and the housing material is relatively weak, so that the gas can easily be flushed out of the second sealing zone, which contributes to achieving directed pressure relief of the battery, reducing the effects of thermal runaway on the adjacent electrical core, and improving the overall lifespan of the battery. In some embodiments, a plurality of adhesive rings circumferentially in the width direction are provided around an outer circumference of the stacked electrical core, wherein the adhesive rings circumferentially in the width direction are provided at intervals along the length direction. The spaced arrangement of the adhesive rings in the longitudinal direction, which surround the electrical core along the width direction, is beneficial for fixing the position between the electrode foils in the electrical core and reducing the probability of displacement of the electrical core when the battery is shaken. This is particularly suitable for long batteries, which can effectively reduce displacement between the electrode foils in the longitudinal direction and lead to the phenomenon of lithium precipitation. It is also beneficial for keeping the internal spatial structure of the battery stable, so that it does not affect the normal operation of the battery. In some embodiments, the battery cell capacity at 25°C is 95 Ah-300 Ah. In some embodiments, the battery cell capacity at 25°C is 150 Ah-180 Ah. In the present application, the capacity of the battery cell has a meaning known in the art and can be tested by methods known in the art. For example, the battery is charged at 25 °C with a charging rate of 0.5C of the nominal capacity of the battery to 3.65 V, then charged with a constant voltage of 3.65 V to 0.05 C and left to stand for 10 minutes, then discharged with a discharge rate of 1C to 2.5 V and left to stand for 10 minutes, and the capacity C in units of Ah is calculated during the discharge process according to the formula C=I*t. In some embodiments, the battery cell capacity at 25°C is optionally 95Ah, 100Ah, 105Ah, 107Ah, 110Ah, 115Ah, 120Ah, 125Ah, 130Ah, 135Ah, 140Ah, 145Ah, 150Ah, 155Ah, 160Ah, 161Ah, 162Ah, 163Ah, 164Ah, 165Ah, 170Ah, 175Ah, 180Ah, 182Ah, 185Ah, 190Ah, 200Ah, 210Ah, 220Ah, 230Ah, 240Ah, 250Ah. 270Ah, 280Ah, 290Ah, 300Ah or any value in a range between any two of these values. In some embodiments, the cathode collector can be a metal foil or a composite collector. For example, an aluminum foil can be used as the metal foil. The composite collector can comprise a base layer of polymeric material and a metal layer formed on at least one surface of the polymeric base layer. The composite collector can be formed by depositing metallic material (aluminum, aluminum alloys, nickel, nickel alloys, titanium, titanium alloys, silver, and silver alloys, etc.) onto a polymer substrate (such as polypropylene (PP), polyethylene terephthalate (PET), polybutylene terephthalate (PBT), polystyrene (PS), polyethylene (PE), etc.). In some embodiments, the anode collector can be a metal foil or a composite collector. For example, a copper foil can be used as the metal foil. The composite collector can comprise a base layer of polymeric material and a metal layer formed on at least one surface of the polymeric base layer. The composite collector can be formed by depositing metallic material (copper, copper alloys, nickel, nickel alloys, titanium, titanium alloys, silver, and silver alloys, etc.) onto a polymer substrate (such as a substrate made of polypropylene (PP), polyethylene terephthalate (PET), polybutylene terephthalate (PBT), polystyrene (PS), polyethylene (PE), etc.). In some embodiments, the anode film layer comprises an active anode material. The active anode material may, for example, comprise at least one of the following materials: synthetic graphite, natural graphite, soft carbon, or hard carbon. However, the present application is not limited to these materials, and other conventional materials suitable for use as active anode materials in batteries may also be used. It is possible to use only one of these active anode materials or to use more than two in combination. In some embodiments, the anode film layer optionally comprises a binder. This binder may be at least one of styrene-butadiene rubber (SBR), polyacrylic acid (PAA), sodium polyacrylate (PAAS), polyacrylamide (PAM), polyvinyl alcohol (PVA), sodium alginate (SA), polymethacrylic acid (PMAA), and carboxymethyl chitosan (CMCS). In some embodiments, the anode film layer optionally includes further additives, such as thickening agents (e.g. sodium carboxymethylcellulose (CMC-Na)), etc. In some embodiments, the anode foil can be produced as follows: Dispersing the components described above for the production of the anode foil, such as the active anode material, the conductive agent, the binder and other components, in a solvent (e.g. deionized water) to form an anode slurry; applying the anode slurry to the anode collector and obtaining the anode foil after drying, cold pressing and other processes. A second aspect of the present application provides a battery device comprising a battery cell according to the first aspect of the present application. The battery devices disclosed in the embodiments of this application can be used in power-consuming devices that use the battery devices as a power source, or in various energy storage systems that use the battery devices as an energy storage element. The battery devices can be used, among other things, for mobile phones, tablets, laptops, electric toys, power tools, electric bicycles, electric vehicles, ships, spacecraft, and the like, as well as for vehicles. Electric toys can include stationary or mobile electric toys, such as game consoles, electric vehicle toys, electric boat toys, and electric airplane toys, etc., and spacecraft can include airplanes, rockets, space shuttles, and spacecraft, etc. A third aspect of the present application provides a power-consuming device that uses the battery device as a power source, wherein the power-consuming device comprises at least one of the battery cells of the present application, a battery module, and a battery pack. The battery cell, battery module, or battery pack can be used as a power source for the power-consuming device or as an energy storage unit for the power-consuming device. The power-consuming device can be selected as a battery cell, battery module, or battery pack, depending on requirements. Fig. 5 shows an example of the power-consuming device. The power-consuming device disclosed in the embodiments of the present application can be a fuel oil vehicle, a gas vehicle, or a new energy vehicle, and the new energy vehicle can be a pure electric vehicle, a hybrid vehicle, a supercharged vehicle, and the like. The vehicle is provided internally with a battery device. The battery device can be located on the underside, at the front, or at the rear of the vehicle. The battery device can be used to supply power to the vehicle; for example, the battery device can be used as an operating power source for the vehicle. The vehicle can further comprise a control unit and a motor, the control unit serving to control the battery device in order to supply power to the motor, for example, to meet the vehicle's operating energy requirements for starting, navigating, and driving.In some embodiments of the present application, the battery device can be used not only as an operating energy source for the vehicle, but also as a propulsion energy source for the vehicle, instead of or partially instead of heating oil or natural gas to provide propulsion energy for the vehicle. A fourth aspect of the present application further provides an energy storage device which uses a battery device as a power source, wherein the energy storage device may be, but is not limited to, an energy storage container, an energy storage cabinet, an energy storage power plant, an energy storage battery pack or a portable energy storage system. Example of implementation The following describes exemplary embodiments of the present application. The embodiments described below are exemplary, serve to explain the present application, and cannot be construed as limiting the present application. Unless specific techniques or conditions are indicated in the exemplary embodiments, they correspond to the techniques or conditions described in the relevant literature or to the information in the product specification. The reagents or instruments used without manufacturer identification are all commercially available products. Example 1 (1) Production of the active cathode material Lithium dihydrogen phosphate, iron(II) oxalate, a carbon source, titanium dioxide, and vanadium pentoxide are homogeneously mixed in methanol and milled to obtain a mixed raw material. The ratio of lithium dihydrogen phosphate to iron oxalate is determined such that the molar ratio of lithium to iron is 1.025:1.0. The carbon source comprises a polyethylene glycol with a weight-average molecular weight of 500, a weight-average molecular weight of 2000, and a weight-average molecular weight of 4000 in a mass ratio of 2:6:2. The iron(II) oxalate has a particle size D10 of 6.5 µm, a particle size D50 of 62 µm and a particle size D90 of 108 µm, and the mass content of elemental Fe in the iron(II) oxalate is 30.5%, and the mass content of elemental trivalent iron is 0.03%. The mixed raw material was milled several times in a ball mill and demagnetized to obtain a mixed slurry. The number of milling passes and the milling process are controlled, and the particle size Dv50 of the mixed slurry after milling is 3.15 µm. The mixed slurry was spray-dried to obtain a dry precursor powder material, and the appearance of the dried precursor powder material was light yellow with a uniform color. The precursor powder material is placed in a sintering furnace and heated from 25°C to 360°C at 2°C / min under a nitrogen atmosphere and held at this temperature for 3.5 hours. It is then heated a second time to 785°C at 5°C / min and held at this temperature for 10 hours, after which it is cooled. The total mass of the active cathode material contains 1050 ppm titanium and 950 ppm volatile matter. The material obtained was crushed by an airflow crushing process with a classification frequency of 21Hz and a crushing air pressure of 0.54 MPa to obtain a carbon-coated active lithium iron phosphate cathode material. The D10, D50, D90 and Dv50 above refer to data obtained through the Malvern laser scattering test. (2) Production of the cathode foil The above active cathode material, the conductive agent, and the binder polyvinylidene fluoride are mixed in the solvent N-methylpyrrolidone according to a mass ratio of 94.1:1.9:3. A dispersing agent HNBR is then added at a mass fraction of 1%, and the mixture is thoroughly mixed, stirred, and dispersed in a mixing vessel to produce the cathode slurry. After completion of the stirring process, the cathode slurry is transferred to a coating process. The conductive agent comprises conductive carbon black and multi-walled carbon nanotubes in a mass fraction of 0.9:1, wherein the conductive carbon black has a specific surface area of ​​80 m² / g and an oil absorption value of 180 ml / 100 g, and the carbon nanotubes have an average length of 20 µm and a specific surface area of ​​280 m² / g. The cathode slurry is extruded onto an aluminum foil for drying, and after cold pressing, a cathode foil with a thickness (H) of 105.64 µm and a density of 2.36 g / cm³ is obtained. The density here refers to the density when the battery cell is fully discharged. The cathode foil is cut into strips and punched into a predetermined shape, and the punched cathode foil is sorted by weight in a weighing and sorting machine and stacked in a stacking machine. The median LR1A50 of the sphericity in the cumulative distribution curve of the sphericity area of ​​particles with a particle size R1 of R1 ≥ 1000 nm in the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil is 0.72; the median C50 of the graphitization degree of the cathode film layer is 1.12; a concentration degree (C90-C10) / C50 of the graphitization C value is 0.025, based on the total area of ​​the particles in the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, the percentage area fraction of particles with a particle size R1 of R1 ≥ 1000 nm is 35.28%, and the median B50 of the coating value B of the cathode film layer is 0.441; the iron dissolution rate of the cathode material is 976 ppm; The area fraction of the agglomeration zone of the conductive medium is 1.91%, based on the total area of ​​the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil;and the porosity of the cathode film layer is 15.06%; a specific resistance of the cathode film layer is 31.0 Ω·cm.; (2) Production of the anode foil A mixture of artificial graphite and natural graphite (mass ratio 1:1), conductive agent of conductive carbon black, binder of styrene-butadiene rubber (SBR) and thickener of sodium carboxymethylcellulose (CMC) are mixed uniformly according to the weight percentage of 96:0.5:2.0:1.5 and deionized water is added and then stirred and dispersed to obtain the anode slurry, and the anode slurry is applied to the copper foil of the base material, and then the anode foil is obtained after drying, cold pressing, cutting and stacking. The anode foil is cut into strips and punched into a predetermined shape, and the punched anode foil is sorted by weight in a weighing and sorting machine and stacked in a stacking machine. (3) Separator Polyvinylidene fluoride (PVDF) was dissolved in N-methylpyrrolidone (NMP), stirred thoroughly, and then polyethylene glycol (PEG) was added as a pore-forming agent. The mixture was stirred and mixed sufficiently to obtain the binder layer solution. This binder layer solution was applied to the aforementioned base film with a double-sided ceramic coating. The PEG was dissolved by pre-evaporation at 80°C and drying at 110°C after immersion in deionized water to obtain a separator with a porous binder layer structure. The thickness of the base film is 8 µm, the thickness of the ceramic layer on one side is 3 µm, and the thickness of the bonding layer on one side is 1 µm. (4) Electrolyte solution The organic solvents dimethyl carbonate (DMC), ethyl methyl carbonate (EMC) and ethylene carbonate (EC) were thoroughly mixed in a glove box with an argon atmosphere (H2O<0.1 ppm, O2<0.1 ppm). Lithium hexafluorophosphate was then added to dissolve the lithium hexafluorophosphate in the organic solvent, so that the concentration of lithium hexafluorophosphate is 1.05 mol / L, and vinylidene carbonate (VC) is added and stirred homogeneously to obtain the electrolyte solution of embodiment 1. In this, based on the total mass of the electrolyte solution, the mass content of dimethyl carbonate is 26%, the mass content of methyl ethyl carbonate is 43.3%, the mass content of vinyl carbonate is 17.3% and the mass content of vinylidene carbonate is 0.9%. 5. Battery production The stacking machine is used to stack the cathode foil, separator, and anode foil sequentially. The separator should be able to insulate the cathode and anode foils to form the stacked electrical core. The stacked electrical core is then coated with adhesive, which tightly encases it. After the adhesive is applied, the stacked electrical core is placed in the outer packaging, which is a flexible aluminum-plastic film. The aluminum-plastic film consists of an inner polypropylene layer, an intermediate layer of aluminum foil, and an outer layer of nylon composite. The aluminum-plastic film outer packaging is formed and cut to the desired shape and size using a forming machine. The aluminum-plastic film is then thermally encapsulated to achieve an encapsulation tensile strength of >25 N / 8 mm.The batteries are vacuum-baked, rested, injected with electrolyte solution, and encapsulated. The soft-pack batteries then undergo hot and cold pressing. Hot pressing occurs at a temperature of 45°C, a time of 2 minutes, and a pressure of 90 kg / cm², while cold pressing occurs at a temperature of 25°C, a time of 2 minutes, and a pressure of 90 kg / cm². Finally, the battery cell is obtained after forming, vacuum extraction, and edge trimming. The battery cell has dimensions of 600 mm in length, 125 mm in width, and 20 mm in thickness. The manufacturing process of embodiments 2 to 10 is essentially the same as that of embodiment 1, with the difference that the manufacturing process for the active cathode material is adapted as follows: Example 2 The manufacturing process of embodiment 2 is essentially the same as that of embodiment 1, with the difference that the second temperature is set to 765 °C during the production of the active cathode material. Example 3 The manufacturing process of embodiment 3 is essentially the same as that of embodiment 1, with the difference that the second temperature is set to 735°C during the production of the active cathode material. Example 4 The manufacturing process of embodiment 4 is essentially the same as that of embodiment 1, with the difference that in the production of the active cathode material the carbon source is replaced by a polyethylene glycol with a weight-average molecular weight of 500 and a weight-average molecular weight of 2000 in a mass ratio of 2:8. Example 5 The manufacturing process of embodiment 5 is essentially the same as that of embodiment 1, with the difference that in the production of the active cathode material the carbon source is replaced by a polyethylene glycol with a weight-average molecular weight of 500. Example 6 The manufacturing process of embodiment 6 is essentially the same as that of embodiment 1, with the difference that in the production of the active cathode material the carbon source is replaced by a polyethylene glycol with a weight-average molecular weight of 2000. Example 7 The manufacturing process of embodiment 7 is essentially the same as that of embodiment 3, with the difference that in the production of the active cathode material the carbon source is replaced by polyethylene glycol with a weight-average molecular weight of 500 and glucose in a mass ratio of 2:8. Example 8 The manufacturing process of embodiment 8 is essentially the same as that of embodiment 1, with the difference that during the production of the cathode foil the coating weight is set and parameters such as the hot rolling pressure, the hot rolling temperature, the transfer rate of the coating and the heating temperature are adaptively adjusted before the first entry into the hot rolling press in order to adjust the pressing density of the cathode foil. Example 9 The manufacturing process of embodiment 9 is essentially the same as that of embodiment 1, with the difference that in the manufacture of the cathode foil the coating weight is adjusted so that the one-sided thickness H of the cathode film layer obtained by cold pressing is 119.12 µm; and the thickness of the battery is adjusted appropriately, keeping the number of cathode foils, separator and anode foils constant. Example 10 The manufacturing process of embodiment 10 is essentially the same as that of embodiment 1, with the difference that in the manufacture of the cathode foil the coating weight is adjusted so that the one-sided thickness H of the cathode film layer obtained by cold pressing is 71.53 µm; and the thickness of the battery is adjusted appropriately, keeping the number of cathode foils, separator and anode foils constant. Comparative example 1 The manufacturing process of Comparative Example 1 is essentially the same as that of Exemplary Example 7, with the difference that the carbon source is replaced by glucose in the production of the active cathode material. Test procedure: 1. Capacity of the lithium-ion secondary battery cell The battery is charged at 25°C with a charging rate of 0.5 C of the battery's nominal capacity to 3.65 V, then charged with a constant voltage of 3.65 V to 0.05 C and left to stand for 10 minutes, then discharged with a discharge rate of 1 C to 2.5 V and left to stand for 10 minutes, and the capacity C in units of Ah is calculated during the discharge process according to the formula C=I*t. 2. Number of cycles corresponds to a drop in capacity to 80% The battery is charged at 25°C with a charging rate of 0.5C of the battery's nominal capacity to 3.65V, then charged with a constant voltage of 3.65V to 0.05C and left to stand for 10 minutes. The above single charge / discharge is one cycle until the battery capacity drops to 80% of the nominal capacity to end the test, which is recorded as the cycle count at @80% SOH. Test result The test results for the above-mentioned embodiments and the comparative examples are shown in Table 1. Table 1: Manufacturing parameters in the embodiments and comparative examples Example of implementation 1105,642,361,110,0250,722107160 Exemplary embodiment 2105,892,361,020,0390,702040159 Execution-105,892,361,010,0390,672018158 example 3 Exemplary embodiment 4106,662,361,070,0350,722097161 Example of execution 5106,792,361,030,0350,722075160 Exemplary embodiment 6106,792,361,060,0360,722089160 Example of implementation 7106,792,360,960,0450,671998160 Example of execution 8105,652,521,130,0240,722095170 Exemplary embodiment 9119,122,361,130,0230,722090178 Exemplary embodiment 1071,532,361,110,0250,72211895 Comparative example 1105,642,360,930,0530,671953158 As can be seen from the comparison between embodiments 1-10 and comparative example 1, the battery cell comprises a stacked electrical core, wherein the stacked electrical core comprises a cathode foil and an anode foil, wherein the cathode foil comprises a cathode collector and a cathode film layer provided on at least one side of the cathode collector, wherein the cathode film layer comprises lithium-containing transition metal phosphate particles provided with a carbon material on at least part of a surface; wherein a median C50 of the graphitization degree in the cumulative distribution curve for the graphitization C value of the cathode film layer, obtained in the area-scanning mode of the laser microconfocal Raman spectrometer, is 0.95-1.20;where the graphitization C-value is IG / ID, where IG represents the intensity of the G-peak of the Raman spectrum at 1580±100cm-1 and ID represents the intensity of the D-peak of the Raman spectrum at 1350±100cm-1; where the cathode foil density when the battery cell is in a fully discharged state is 2.3 g / cm3-2.6 g / cm3; The battery cell contributes to improving the battery's cycle life during long-cycle operation while maintaining good capacity. As can be seen from the comparison between embodiment 1, embodiments 4-6 and embodiment 7, the median C50 of the graphitization degree in the cumulative distribution curve for the graphitization C value of the cathode film layer obtained in the area scanning mode of the laser microconfocal Raman spectrometer is further optionally 1.01-1.13, which helps to further improve the cycle life of the battery cell during a long cycle. As can be seen from the comparison between embodiments 1-10 and comparative example 1, the concentration level (C90-C10) / C50 of the C value in the cumulative distribution curve for the graphitization C value of the cathode film layer obtained in the area scanning mode of the laser microconfocal Raman spectrometer is 0.01-0.05, which helps to further improve the cycle life of the battery cell during a long cycle. As can be seen from embodiments 1-3, in the cumulative distribution curve of the sphericity area of ​​the particles with a particle size R1 of R1≥1000 nm in the cross-sectional area of ​​the cathode film layer along the thickness direction of the cathode foil LRIA50in is 0.67-0.75, which gives the battery cell a good cycle life during a long cycle. As can be seen from embodiments 1-9, the thickness H of one side of the cathode film layer is in the range of 70 µm-120 µm, and the battery cell contributes to improving the cycle life of the battery during the long cycle process, while maintaining good capacity. It should be noted that the present application is not limited to the embodiments mentioned above. The embodiments mentioned above are only examples, and embodiments within the scope of the technical solution of the present application that have essentially the same composition as the technical idea and have the same effect are included in the technical scope of the present application. Furthermore, within the scope of the present application, other possibilities for constructing the embodiments by combining some of the constituent elements of the embodiments and applying various deformations to the embodiments that a person skilled in the art can imagine without departing from the subject matter of the present application are also included. QUOTES INCLUDED IN THE DESCRIPTION This list of documents cited by the applicant was automatically generated and is included solely for the reader's convenience. The list is not part of the German patent or utility model application. The DPMA accepts no liability for any errors or omissions. Cited non-patent literature GB / T 33822-2017 [0148, 0154]

Claims

Battery cell characterized in that it comprises a stacked electrical core, wherein the stacked electrical core comprises a cathode foil and an anode foil, wherein the cathode foil comprises a cathode collector and a cathode film layer provided on at least one side of the cathode collector, wherein the cathode film layer comprises lithium-containing transition metal phosphate particles provided with a carbon material on at least part of a surface; wherein a median C50 of the degree of graphitization in the cumulative distribution curve for the graphitization C value of the cathode film layer obtained in the area-scanning mode of the laser microconfocal Raman spectrometer is 0.95–1.20; wherein the graphitization C value is IG / ID, where IG is the intensity of the G-peak of the Raman spectrum at 1580 ± 100 cm⁻¹ and IG is the intensity of the D-peaks of the Raman spectrum at 1350±100cm-1 stands;where the density of the cathode foil when the battery cell is in a fully discharged state is 2.3 g / cm3-2.6 g / cm3; Battery cell according to claim 1, characterized in that the median C50 of the graphitization degree in the cumulative distribution curve for the graphitization C value of the cathode film layer obtained in the area scanning mode of the laser microconfocal Raman spectrometer is 1.01-1.

13. Battery cell according to claim 1 or 2, characterized in that a concentration level (C90-C10) / C50 of the C value in the cumulative distribution curve for the graphitization C value of the cathode film layer, obtained in the area scanning mode of the laser microconfocal Raman spectrometer, is 0.01-0.05, optionally 0.02-0.

04. Battery cell according to one of claims 1 to 3, characterized in that, with reference to the total area of ​​the particles in the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, the percentage area fraction of the particles with a particle size R1 of R1≥1000 nm is 12%-50%, optionally 12%-40%. Battery cell according to one of claims 1 to 4, characterized in that in a cumulative distribution curve of the sphericity area of ​​the particles with a particle size R1 of R1≥1000 nm in the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil the median LR1A150 of the sphericity is 0.6-0.8, optionally 0.65-0.75, further optionally 0.67-0.

75. A battery cell according to any one of claims 1 to 5, characterized in that the median B50 of the coating value in the cumulative distribution curve for the coating value-B of the cathode film layer, obtained in the area-scanning mode of the laser microconfocal Raman spectrometer, is 0.30-0.60, wherein the coating value-B is IP / ID, where IP represents the intensity of the P-peak of the Raman spectrum at 948±100cm-1 and ID represents the intensity of the D-peak of the Raman spectrum at 1350±100cm-1. Battery cell according to one of claims 1 to 6, characterized in that the lithium-containing transition metal phosphate particles comprise a component with a general formula as follows: Formula I: LimFexPyOjQq where Q comprises one or more of Al, Na, K, Mg, Cu, Mn, Cr, Zn, Pb, Ca, Co, Ni, Sr, Nb, V, Ti, B, S, Si, N, F, Cl, Br, and where 0.8≤m≤1.15, 0.9≤x≤1, 0.95≤y≤1, 3.5≤j≤4, 0≤q≤0.

1. Battery cell of claims 1 to 7, characterized in that the iron dissolution rate of the active cathode material is 658 ppm-1921 ppm, optionally 658 ppm-1485 ppm. Battery cell according to one of claims 1 to 8, characterized in that, based on the total mass of the lithium-containing transition metal phosphate particles, the mass content of titanium is 500 ppm-8000 ppm, optionally 1000 ppm-3000 ppm. Battery cell according to one of claims 1 to 9, characterized in that, based on the total mass of the lithium-containing transition metal phosphate particles in the cathode film layer, the mass content of vanadium is 500 ppm-5000 ppm, optionally 500 ppm-3000 ppm. Battery cell according to one of claims 1 to 10, characterized in that the porosity of the cathode film layer is 14%-28%. Battery cell according to one of claims 1 to 11, characterized in that a specific resistance of the cathode film layer is 10 Ω·cm-35 Ω·cm. Battery cell according to one of claims 1 to 12, characterized in that a one-sided thickness of the cathode film layer is designated as H, wherein H is 70 µm-120 µm, optionally 90 µm-120 µm, further optionally 100 µm-120 µm. Battery cell according to one of claims 1 to 13, characterized in that the cathode film layer is provided with a lower coating layer in a lower region facing the cathode collector, wherein the lower coating layer fulfills at least one of the following conditions: (1) the lower coating layer comprises a conductive agent and a binder, wherein the conductive agent comprises carbon nanotubes and conductive carbon black, and wherein the binder comprises a vinylidene fluoride polymer; (2) the thickness of the lower coating layer is 0.5 µm-5 µm. Battery cell according to one of claims 1 to 14, characterized in that the cathode film layer further comprises a dispersing agent, wherein the dispersing agent comprises hydrogenated nitrile butadiene rubber (HNBR). Battery cell according to one of claims 1 to 15, characterized in that the mass content of the dispersing agent is 0.5%-2% in relation to the mass of the cathode film layer. Battery cell according to one of claims 1 to 16, characterized in that the cathode film layer further comprises a conductive means, wherein, with respect to a total area of ​​the cross-sectional area of ​​the cathode film layer along the thickness direction of the electrode foil, the area fraction of an agglomeration region of the conductive means is 0.5%-2.5%, optionally 1.5%-2.5%. Battery cell according to claim 17, characterized in that the conductive means comprises carbon nanotubes, wherein the carbon nanotubes comprise one or more of single-walled carbon nanotubes, thin-walled carbon nanotubes, multi-walled carbon nanotubes, wherein the conductive means further optionally comprises conductive carbon black. Battery cell according to claim 17 or 18, characterized in that the agglomeration area of ​​the conductive agent comprises carbon nanotubes and conductive carbon black. Battery cell according to claim 18 or 19, characterized in that, with respect to the mass of the cathode film layer, the mass content C1 of the carbon nanotubes is 0 <C1≤2,5% und der Massengehalt C2 des leitfähigen Rußes 0<C1<2,5% erfüllt. Battery cell according to one of claims 1 to 20, characterized in that the battery cell further comprises a separator arranged between the cathode foil and the anode foil, wherein the separator comprises a base film and a ceramic layer arranged on both sides of the base film, and a bonding layer arranged on at least one side of the ceramic layer facing away from the base film, wherein the bonding layer is a continuous layer with a porous structure, and wherein the bonding layer comprises a vinylidene fluoride polymer. Battery cell according to claim 21, characterized in that the separator meets at least one of the following conditions: (1) the thickness of the base film is 7-9 µm; (2) the one-sided thickness of the ceramic layer is 2-4 µm; (3) the one-sided thickness of the bonding layer is 1-5 µm. Battery cell according to one of claims 1 to 22, characterized in that the battery cell comprises a housing, wherein the at least one stacked electrical core is received in the housing, wherein the housing has a dimension of L0 in a longitudinal direction, wherein the housing has a dimension of W0 in a width direction, wherein the housing has a dimension of H0 in a thickness direction, wherein 450 mm ≤ L0 ≤ 1300 mm, 100 mm ≤ W0 ≤ 150 mm, and 14 mm ≤ H0 ≤ 22 mm. Battery cell according to claim 23, characterized in that the dimension L0 of the housing in the longitudinal direction satisfies the following condition: 450 mm ≤ L0 ≤ 650 mm. Battery cell according to claim 23 or 24, characterized in that the dimension L0 of the housing in the longitudinal direction satisfies the following condition: 900mm ≤ L0 ≤ 1300mm. Battery cell according to claim 25, characterized in that (1) the housing material is a soft packaging material, wherein the soft packaging material comprises an aluminum-plastic composite film, optionally comprising at least one or more of aluminum, polypropylene (PP), polybutylene terephthalate (PBT), polybutylene succinate (PBS), nylon, polyethylene terephthalate (PET), polyethylene (PE); (2) the housing comprises a first sealing zone, wherein the first sealing zone is provided at at least one laterally extending end of the stacked electrical core; wherein the first sealing zone comprises a longitudinally extending folded edge structure, wherein the folded edge structure is provided with an encapsulating adhesive, the encapsulating adhesive being applied successively along the longitudinal direction and securing the folded edge structure;(3) The housing comprises at least one second sealing zone, the second sealing zone being provided at at least one end of the stacked electrical core along the longitudinal direction of the housing, the second sealing zone being provided on one side of the electrode tab of the stacked electrical core. Battery cell according to one of claims 1 to 26, characterized in that a plurality of adhesive rings circumferentially in the width direction are provided around an outer circumference of the stacked electrical core, wherein the adhesive rings circumferentially in the width direction are provided at intervals along the length direction. Battery cell according to one of claims 1 to 27, characterized in that the capacity of the battery cell at 25°C is 105 Ah-190 Ah, optionally 150 Ah-190 Ah. Battery device, characterized in that it comprises a battery cell according to any one of claims 1 to 28. Power-consuming device, characterized in that the power-consuming device comprises a battery device according to claim 29, wherein the battery device is used to provide electrical energy. Energy storage device characterized in that the energy storage device comprises a battery device according to claim 30, wherein the battery device is used for storing electrical energy.

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