Patent Application
20240421296
The present disclosure relates to the technical field of sodium-ion batteries, and particularly, to a sodium-ion cathode material, a preparation method and use thereof, a sodium-ion battery, a sodium-ion battery pack, and a device.
With an explosive development of new energy vehicles and large-scale energy storage markets, sales of lithium-ion batteries have increased sharply, which poses a serious challenge to global supply of lithium resources. Compared with the lithium resources, sodium resources are widely distributed in the crustal structure, with a content up to 2.4 wt %, which is much higher than a content of the lithium resources of 0.0065 wt %. Therefore, in recent years, the sodium-ion batteries have become a key energy storage system undergoing intense development in a new energy industry.
A cathode material is a very important key material in the sodium-ion batteries, mainly including systems such as metal oxides, polyanionic compounds, Prussian blue materials, and organic materials. The cathode material of metal oxide systems has the advantages of high voltage platform, high discharge capacity, and high powder compaction, and is a type of battery material with great development potential. A charging and discharging process of metal oxide cathode materials is a deintercalation reaction. Due to a greater radius, a sodium ion has a great change of expansion and contraction in volume during the charging and discharging process, resulting in poor cycle performance and an adverse effect on safety performance of the battery.
Therefore, it is urgent to provide a new composite cathode material for the sodium-ion batteries.
In a first aspect, the present disclosure provides a sodium-ion cathode material. The cathode material includes a matrix and a coating layer coated on the matrix. The matrix has a composition represented by formula I: Na1−x[NiyMnzMu]TivO2 (formula I), where −0.4≤x≤0.4, 0.2≤y≤0.6, 0.1≤z≤0.5, 0.1≤u≤0.5, 0≤v≤0.02, y+z+u+v=1; and M is selected from at least one of Fe, Mg, Al, Cu, Zn, Zr, Nb, Co, Y, V, Sc, Cr, W, La, Mo, Os, Pr, Re, Ru, Sr, Sm, and Ta. The coating layer has a composition represented by formula II: Na2−βTi6−αM′αO13 (formula II), where 0≤α<0.6, −2≤β<1; and M′ is selected from at least one of Li, Mg, Fe, Al, Ga, In, Ge, Y, Sc, and Zr.
In a second aspect, the present disclosure provides a preparation method of a sodium-ion cathode material. The preparation method includes: (1) performing a first mixing on a first sodium source, an optional M′ source, a titanium source with a solvent to obtain a first slurry; sequentially performing a first drying and a first sintering on the first slurry to obtain a first sintered product; and sequentially crushing and drying the first sintered product to obtain a coating layer; wherein the coating layer has a composition represented by formula II: Na2−βTi6−αM′αO13 (formula II), where 0≤α<0.6, −2≤β<1; and M′ is selected from at least one of Li, Mg, Fe, Al, Ga, In, Ge, Y, Sc, and Zr; (2) performing a second mixing on a second sodium source, a nickel source, a manganese source, an M source, and an optional titanium source, and sequentially performing a second drying and a second sintering on the obtained second mixture to obtain a matrix; wherein the matrix has a composition represented by formula I: Na1−x[NiyMnzMu]TivO2 (formula I), where −0.4≤x≤0.4, 0.2≤y≤0.6, 0.1≤z≤0.5, 0.1≤u≤0.5, 0≤v≤0.02, y+z+u+v=1; and M is selected from at least one of Fe, Mg, Al, Cu, Zn, Zr, Nb, Co, Y, V, Sc, Cr, W, La, Mo, Os, Pr, Re, Ru, Sr, Sm, and Ta; and (3) performing a third mixing on the coating layer and the matrix, and performing a heat treatment on the obtained third mixture to obtain the sodium-ion cathode material. The first sintering is performed in a non-oxidizing gas.
In a third aspect, the present disclosure provides a sodium-ion battery. The sodium-ion battery includes a positive electrode pole piece prepared by the sodium-ion cathode material according to the first aspect.
The endpoints and any value of the ranges disclosed herein shall not limited to the exact range or value, and those ranges or values should be understood to include values close to those ranges or values. For numerical ranges, endpoints of each range, an endpoint of each range and an individual point value, and individual point values may be combined with each other to obtain one or more new numerical ranges, which should be deemed to be specifically disclosed herein.
In the present disclosure, unless otherwise specified, the term “first”, “second”, and “third”, instead of indicating a sequence of precedence or a limitation on each material or step, are only used to distinguish that these materials or steps are not the same material or step. For example, the term “first” and “second” in “first sodium source” and “second sodium source” are only used to distinguish that the sodium sources are not the same sodium source; and the term “first”, “second”, and “third” in “first mixing”, “second mixing”, and “third mixing” are only used to distinguish that said mixings are not the same mixing.
An object of the present disclosure is to overcome problems existing in a cathode material of a sodium-ion battery in the related art, such as low ionic conductivity, poor structural stability, and poor chemical stability. The present disclosure provides a sodium-ion cathode material, a preparation method and use thereof, a sodium-ion battery, a sodium-ion battery pack, and a device. The sodium-ion cathode material has the characteristics such as high ionic and electronic conductivity, strong structural stability, and strong chemical stability. At the same time, by applying the composite cathode material to the sodium-ion batteries, an electrochemical performance of the batteries can be effectively improved.
To achieve the above-mentioned object, in a first aspect, the present disclosure provides a sodium-ion cathode material. The cathode material includes a matrix and a coating layer coated on the matrix. The matrix has a composition represented by formula I: Na1−x[NiyMnzMu]TivO2 (formula I), where −0.4≤x≤0.4, 0.2≤y≤0.6, 0.1≤z≤0.5, 0.1≤u≤0.5, 0≤v≤0.02, y+z+u+v=1; and M is selected from at least one of Fe, Mg, Al, Cu, Zn, Zr, Nb, Co, Y, V, Sc, Cr, W, La, Mo, Os, Pr, Re, Ru, Sr, Sm, and Ta. The coating layer has a composition represented by formula II: Na2−βTi6−αM′αO13 (formula II), where 0≤α≤0.6, −2≤β≤1; and M′ is selected from at least one of Li, Mg, Fe, Al, Ga, In, Ge, Y, Sc, and Zr.
In the present disclosure, the sodium-ion cathode material includes a coating layer Na2−βTi6−αM′αO13 having a specific composition. The coating layer and the matrix both partially contain the same Na2Ti6O13 phase, and the Na2Ti6O13 phase in the coating layer has the same crystal structure as the Na2Ti6O13 phase in the matrix. The Na—Ti—O chemical bonds existing in both the coating layer and the matrix may be organically bonded to achieve an object of tight coating. In this way, the sodium-ion cathode material including the matrix and the Na2−βTi6−αM′αO13 coating layer coated on the matrix can have a high ionic and electronic conductivity, and excellent structural and chemical stability.
In a specific embodiment of the present disclosure, in formula I, −0.25≤x≤0.4, 0.2≤y≤0.5, 0.2≤z≤0.5, 0.2≤u≤0.5, 0.01≤v≤0.02, y+z+u+v=1; and M is selected from at least one of Fe, Cu, Nb, Co, V, and Cr.
In a preferred embodiment of the present disclosure, in formula I, 0≤x≤0.35, 0.3≤y≤0.4, 0.2≤z≤0.4, 0.2≤u≤0.4, 0.01≤v≤0.02, y+z++v=1; and M is selected from at least one of Fe, Cu, Nb, Co, and V.
In a specific embodiment of the present disclosure, in formula II, 0<α<0.5, −2≤β<1; and M′ is selected from at least one of Mg, Fe, Al, Y, and Zr.
In a preferred embodiment of the present disclosure, in formula II, 0.01≤α<0.3, −2≤β<0.5; and M′is selected from at least one of Fe, Mg, and Al.
In the present disclosure, in formula II, a value of β depends on a change in valence state of respective ions in formula II to ensure charge balance of the coating layer material.
According to the present disclosure, in a direction from a center of the matrix to a surface of the matrix, element Ti is distributed in a gradient, and preferably, in an increasing gradient.
In the present disclosure, element Ti is controlled to be distributed in a gradient, and preferably in an increasing gradient, along the direction from the center of the matrix to the surface of the matrix, to be distributed in an increasing gradient. That is, a content of element Ti on the surface of the matrix is relatively high. In this way, it can be ensured that element Ti in the matrix can easily form a chemical bond Na—Ti—O with the Na2Ti6O13 phase contained in the coating layer, thereby further reducing the interface impedance under the premise of achieving tight coating of the coating layer.
Further, in the direction from the center of the matrix to the surface of the matrix, element Ti is increased with a rate ranging from 0.001 mol %/μm to 0.3 mol %/μm, preferably, from 0.001 mol %/μm to 0.2 mol %/μm, and more preferably, from 0.001 mol %/μm to 0.1 mol %/μm.
In some embodiments of the present disclosure, preferably, a weight ratio of the matrix to the coating layer is 100:(0.01 to 5), for example, 100:0.01, 100:0.05, 100:0.1, 100:0.5, 100:1, 100:3, 100:5, or any value in a range consisting of any two of the above-mentioned values, and preferably, 100:(0.05 to 3). With the preferred weight ratio, the coating layer can form a uniform coating on the matrix with a relatively high coating density, which can effectively inhibit side reactions between the matrix and the electrolyte. At the same time, the coating layer is not too thick to affect exertion of the capacity and rate performance of the cathode material.
In some embodiments of the present disclosure, preferably, the coating layer has a thickness ranging from 10 nm to 200 nm, preferably, from 10 nm to 100 nm, and more preferably, from 50 nm to 100 nm.
In some embodiments of the present disclosure, preferably, the sodium-ion cathode material has an average particle size D50 ranging from 2 μm to 30 μm, and preferably, from 4 μm to 12 μm.
In the present disclosure, unless otherwise specified, parameters of the average particle diameter D50 are measured by a laser particle size analyzer; and parameters of the thickness are measured by a transmission electron microscope.
In some embodiments of the present disclosure, preferably, the sodium-ion cathode material has an ionic conductivity ranging from 10−4 S/cm to 10−3 S/cm, and preferably, from 5×10−4 S/cm to 10−3 S/cm.
In some embodiments of the present disclosure, preferably, the sodium-ion cathode material has an ionic conductivity ranging from 10−7 S/cm to 10−6 S/cm, and preferably, from 5×10−7 S/cm to 10−6 S/cm.
In the present disclosure, unless otherwise specified, the ionic conductivity of the sodium-ion cathode material is measured using an electrochemical workstation, and the electronic conductivity of the sodium-ion cathode material is measured using a powder resistance tester.
In the present disclosure, the coating layer of the sodium-ion cathode material is subjected to a heat treatment in a non-oxidizing gas, allowing the coating layer and the matrix to be more closely bonded, thereby improving the electrochemical performance of the sodium-ion battery prepared by the sodium-ion cathode material.
In a second aspect, the present disclosure provides a preparation method of a sodium-ion cathode material. The preparation method includes: (1) performing a first mixing on a first sodium source, an optional M′ source, a titanium source with a solvent to obtain a first slurry; sequentially performing a first drying and a first sintering on the first slurry to obtain a first sintered product; and sequentially crushing and drying the first sintered product to obtain a coating layer, wherein the coating layer has a composition represented by formula II: Na2−βTi6−αM′αO13 (formula II), where 0≤α<0.6, −2≤β<1; and M′ is selected from at least one of Li, Mg, Fe, Al, Ga, In, Ge, Y, Sc, and Zr; (2) performing a second mixing on a second sodium source, a nickel source, a manganese source, an M source, and an optional titanium source, and sequentially performing a second drying and a second sintering on the obtained second mixture to obtain a matrix, wherein the matrix has a composition represented by formula I: Na1−x[NiyMnzMu]TivO2 (formula I), where −0.45≤x≤0.4, 0.2≤y≤0.6, 0.1≤z≤0.5, 0.1≤u≤0.5, 0≤v≤0.02, y+z+u+v=1; and M is selected from at least one of Fe, Mg, Al, Cu, Zn, Zr, Nb, Co, Y, V, Sc, Cr, W, La, Mo, Os, Pr, Re, Ru, Sr, Sm, and Ta; and (3) performing a third mixing on the coating layer and the matrix, and performing a heat treatment on the obtained third mixture to obtain the sodium-ion cathode material. The first sintering is performed in a non-oxidizing gas.
In the present disclosure, by adopting the preparation method according to the second aspect of the present disclosure, the coating layer having a specific composition and the matrix having a specific composition are mixed and then subjected to a heat treatment to obtain the sodium-ion cathode material according to the first aspect of the present disclosure. In the sodium-ion cathode material, the coating layer Na2−βTi6−αM′αO13 having a specific composition and the matrix both partially contain the same Na2Ti6O13 phase, and the Na2Ti6O13 phase in the coating layer has the same crystal structure as the Na2Ti6O13 phase in the matrix. The Na—Ti—O chemical bonds existing in both the coating layer and the matrix may be organically bonded to achieve an object of tight coating. In this way, the sodium-ion cathode material including the matrix and the Na2−βTi6−αM′αO13 coating layer coated on the matrix can have a high ionic and electronic conductivity, and excellent structural and chemical stability.
According to the present disclosure, the content of the residual alkali on a surface of the matrix is ≤2 wt %.
In the present disclosure, since the residual alkali on the surface is an inert layer, an excessively high content of residual alkali may form a thick inert layer between the coating layer and the matrix, thereby affecting the chemical bonding between the matrix and the coating layer. In order to achieve a tight bonding between the coating layer and the matrix, it is required to control the content of the residual alkali on the surface of the matrix to be no more than 2 wt %. Preferably, the content of the residual alkali on the surface of the matrix is controlled in the range from 0.1 wt % to 1 wt %.
Further, in the present disclosure, the first sintering is performed in a non-oxidizing gas to prepare the coating layer, to reduce a content of Ti4+ in the coating layer Na2−βTi6−αM′αO13 and increase a certain amount of oxygen vacancies, thereby allowing the coating layer material to have a certain degree of activity. The coating layer, in the process of coating the matrix, can be more prone to bond with oxygen dangling bonds on the surface of the matrix, thereby improving the tight bonding between the coating layer and the matrix, and improving the structural stability and cycle performance of the sodium-ion cathode material.
In the present disclosure, unless otherwise specified, the respective materials are fed in the amount that they can all be used to generate products. That is, the feed amounts of the first sodium source, M′ source, and titanium source satisfy the composition of formula II; and the feed amounts of the second sodium source, the nickel source, the manganese source, and the M source satisfy the composition of formula I.
In the present disclosure, the non-oxidizing gas refers to a gas that does not contain oxygen. Preferably, the non-oxidizing gas includes, but is not limited to, nitrogen, helium, argon, neon, etc.
In the present disclosure, a manner of the first mixing in step (1) can be selected from a relatively broad range, as long as the first sodium source, the M′ source, the titanium source, and the solvent can be mixed uniformly.
In the present disclosure, in step (1), the first sodium source, the M′ source, and the titanium source can be selected from various types, as long as the first sodium source, the M′ source, and the titanium source contain Na, M′, and Ti, respectively. M′ is selected from at least one of Li, Mg, Fe, Al, Ga, In, Ge, Y, Sc, and Zr, and preferably, M′ is selected from at least one of Mg, Fe, Al, Y, and Zr. Preferably, the first sodium source, the M′ source, and the titanium source are each independently selected from at least one of oxides, hydroxides, nitrates, carbonates, and organic compounds containing Na, M′, and Ti.
In some embodiments of the present disclosure, preferably, in step (1), the feeding amounts of the first sodium source, the M′ source, and the titanium source satisfy: n(Na):n(Ti):n(M)=(2−β):(6−α):α, where 0≤α<0.6, −2≤3<1.
In some preferred embodiments of the present disclosure, preferably, in step (1), 0≤α<0.6, −2≤β<1, wherein 0<α<0.5, −2≤β<1, and more preferably, 0.01≤α<0.3, −2≤β<0.5.
In the present disclosure, the first drying is intended to remove the solvent in the first slurry. Preferably, the equipment for the first drying includes, but is not limited to, a spray dryer, a blast oven, a vacuum oven, a freeze dryer, etc. In the present disclosure, the conditions for the first drying are not specifically limited, as long as the solvent in the first slurry can be removed.
In some embodiments of the present disclosure, preferably, the first slurry has a solid content ranging from 30 wt % to 55 wt %. In the present disclosure, when the solid content of the first slurry is controlled to satisfy the above range, the respective materials in the slurry have good dispersibility, and adverse effects on the matrix structure are avoided due to the presence of excessive solvent. For example, the excessive solvent may cause an escape of sodium ions in the matrix from the phase.
In the present disclosure, a type of solvent can be selected from a relatively broad range, as long as the first sodium source, the M′ source, and the titanium source can be dissolved by the solvent. Preferably, the solvent includes, but is not limited to, common solvents such as water, ethanol, ethylene glycol, glycerol, etc.
In the present disclosure, the amount of the solvent used can be in a relatively broad range, as long as the solid content of the first slurry ranges from 30 wt % to 55 wt %.
In some embodiments of the present disclosure, preferably, in step (1), conditions of the first sintering include: a temperature ranging from 500° C. to 1,200° C., and preferably, from 700° C. to 850° C.; and a duration ranging from 4 hours to 10 hours, and preferably, from 6 hours to 8 hours.
In the present disclosure, when the conditions of the first sintering are controlled to satisfy the above-mentioned ranges, a pure-phase coating layer can be obtained, such that the prepared coating layer can have excellent crystallinity and structural stability. When the coating layer is used to coat the matrix, a dense and uniform coating layer can be formed on the surface of the matrix, thereby significantly improving the charge and discharge capacity and cycle performance of the sodium-ion cathode material. Specifically, if the sintering temperature is excessively low or the sintering duration is excessively short, a heterogeneous phase may appear in the prepared coating layer. If the sintering temperature is excessively high or the sintering duration is excessively long, the prepared coating layer may have great hardness and thus it may be difficult to be crushed.
In some embodiments of the present disclosure, preferably, in step (1), said crushing includes: crushing the first sintered product and the solvent at a weight ratio of 100:(50 to 100).
In the present disclosure, by crushing the first sintered product according to the above-mentioned method, a crushing efficiency is high, and meanwhile, the obtained coating layer can have excellent structural stability and dispersibility.
In the present disclosure, the type of solvent during ball milling is not specifically limited herein, as long as the first sintered product can be uniformly dispersed.
In the present disclosure, equipment for the crushing includes, but is not limited to, a jaw crusher, a roller mill, a ball mill, a jet mill, a mechanical mill, a sand mill, a colloid mill, etc.
In some embodiments of the present disclosure, preferably, said crushing allows the average particle size D50 of the coating layer in the range from 10 nm to 200 nm, preferably, from 10 nm to 100 nm, and more preferably, from 50 nm to 100 nm.
In some embodiments of the present disclosure, preferably, conditions of said drying include: a temperature ranging from 60° C. to 120° C. and a duration ranging from 0.5 hours to 5 hours.
In some embodiments of the present disclosure, preferably, the dried product is crushed.
In the present disclosure, a manner of a second mixing in step (2) can be selected from a relatively broad range, as long as the second sodium source, the nickel source, the manganese source, and the M source can be mixed uniformly.
In the present disclosure, the second sodium source, the nickel source, the manganese source, and the M source can be selected from various types, as long as the second sodium source, the nickel source, the manganese source, and the M source contain Na, Ti, Mn, and M, respectively. M is selected from at least one of Fe, Mg, Al, Cu, Zn, Zr, Nb, Co, Ti, Y, V, Sc, Cr, W, La, Mo, Os, Pr, Re, Ru, Sr, Sm and Ta, and preferably, M is selected from at least one of Fe, Cu, Nb, Co, V and Cr. Preferably, in step (2), the second sodium source, the nickel source, the manganese source, and the M source are each independently selected from at least one of oxides, hydroxides, carbonates, nitrates, and organic compounds containing Na, Ni, Mn, and M.
In the present disclosure, the second drying is intended to remove moisture from the second mixture. Equipment for the drying includes, but is not limited to, a spray dryer, a blast oven, a vacuum oven, a freeze dryer, etc.
In some embodiments of the present disclosure, preferably, feeding amounts of the second sodium source, the nickel source, the manganese source, the M source, and the optional titanium source satisfy: n(Na):n(Ni):n(Mn):n(M):n(Ti)=1−x): y:z:u:v, where −0.4≤x≤0.4, 0.2≤y≤0.6, 0.1≤z≤0.5, 0≤v≤0.2, and y+z+u+v=1.
In some preferred embodiments of the present disclosure, preferably, feeding amounts of the second sodium source, the nickel source, the manganese source, the M source, and the optional titanium source satisfy: n(Na):n(Ni):n(Mn):n(M):n(Ti)=(1−x): y:z:w:v, where −0.2≤x≤0.4, 0.2≤y≤0.5, 0.2≤z≤u≤0.5, 0.1≤v≤0.02, y+z++v=1. More preferably, 0≤x≤0.35, 0.3≤y≤0.4, 0.2≤z≤0.4, 0.2≤u≤0.4, 0.01≤v≤0.02, y+z+u+v=1.
In some embodiments of the present disclosure, preferably, the second mixing includes: performing coprecipitation on the nickel source, the manganese source, and the M source to obtain a precursor NiyMnzMu(OH)2; performing a mixing I on the precursor NiyMnzMu(OH)2 with the titanium source; and then performing a mixing II on a mixture of the precursor NiyMnzMu(OH)2 and the titanium source with the second sodium source, to obtain a second mixture.
In the present disclosure, the second mixing is performed according to the above steps, that is, performing a mixing on the precursor with the titanium source, and then performing a mixing on a mixture of the precursor and the titanium source with the second sodium source, and performing the second sintering is performed. The duration of the second sintering is controlled. In this way, element Ti can be distributed in a gradient in the matrix. In particular, in a direction from the center of the matrix to the surface of the matrix, element Ti is distributed in an increasing gradient.
In the present disclosure, conditions of the coprecipitation are not specifically limited herein. The coprecipitation of the nickel source, the manganese source, and the M source can be performed under conventional conditions in the art.
In the present disclosure, conditions of the mixing I and mixing II are not specifically limited herein, as long as the precursor and the titanium source as well as the mixture of the precursor and the titanium source and the second sodium source can be fully and uniformly mixed.
In some embodiments of the present disclosure, preferably, conditions of the second sintering include: a temperature ranging from 600° C. to 1,200° C., and preferably, from 750° C. to 1,200° C.; and a duration ranging from 6 hours to 10 hours, and preferably, from 8 hours to 10 hours.
In the present disclosure, when the conditions of the second sintering are controlled to satisfy the above-mentioned ranges, it can be ensured that the prepared matrix has excellent crystallinity and structural stability, thereby significantly improving the charge and discharge capacity and cycle performance of the sodium-ion cathode material containing the matrix material. Specifically, if the sintering temperature is excessively low or the sintering duration is excessively short, a heterogeneous phase may appear in the matrix due to an incomplete reaction of the materials in the matrix. If the sintering temperature is excessively high or the sintering duration is excessively long, the sodium-ions in the matrix may volatilize, thereby affecting the electrochemical performance of the battery containing the prepared sodium-ion cathode material. In the present disclosure, a manner of the third mixing method in step (3) can be selected from a relatively broad range, as long as the coating layer and the matrix can be mixed uniformly.
In some embodiments of the present disclosure, preferably, in step (3), the heat treatment is performed in a non-oxidizing gas. In the present disclosure, by controlling the heat treatment to be performed in a non-oxidizing gas, the coating layer material can be bonded with the oxygen dangling bonds on the surface of the matrix material. In this way, the coating layer and the matrix can be more tightly bonded, thereby further improving the cycle performance of the sodium-ion battery containing the sodium-ion cathode material.
In some embodiments of the present disclosure, preferably, in step (3), conditions of the heat treatment include: a temperature ranging from 200° C. to 600° C., and preferably, from 400° C. to 600° C.; and a duration ranging from 4 hours to 8 hours, and preferably, from 6 hours to 8 hours.
In the present disclosure, when the conditions of the heat treatment are controlled to satisfy the above ranges, it can be ensured that the matrix and the coating layer fully react, and thus they can be tightly bonded, thereby improving the cycle performance of the sodium-ion battery containing the sodium-ion cathode material.
In some embodiments of the present disclosure, preferably, the third mixing includes: directly performing the third mixing on the coating layer with the matrix; or mixing the coating layer with the solvent and performing ball milling on the mixture to obtain a second slurry, and performing the third mixing on the second slurry with the matrix.
In the present disclosure, the conditions for ball milling are not specifically limited herein, as long as the coating layer and the solvent can be fully and uniformly mixed.
In the present disclosure, the amount of solvent used during ball milling is not specifically limited herein, as long as it can ensure that the solid content of the obtained second slurry subsequent to the ball milling ranges from 30 wt % to 55 wt %. In the present disclosure, the type of the solvent during ball milling is not specifically limited herein, as long as the coating layer can be uniformly dispersed.
In some embodiments of the present disclosure, preferably, a weight ratio of the coating layer to the matrix is (0.01 to 5):100, for example, 0.01:100, 0.05:100, 0.1:100, 1:100, 3:100, 5:100, and any value in the range consisting of any two of the above-mentioned values, and preferably, (0.05 to 3):100. At the preferred weight ratio, the coating layer can form a uniform coating on the matrix with a relatively high coating density, which can effectively inhibit side reactions between the matrix and the electrolyte. At the same time, the coating layer is not too thick to affect exertion of the capacity and rate performance of the cathode material. When the weight ratio is less than 0.01:100, the matrix cannot be completely coated by the coating layer, and side reactions with the electrolyte may still occur at the exposed parts without coating, causing a rapid deterioration in the cycle performance. When the weight ratio is greater than 5:100, the thickness of the coating layer on the surface of the matrix may be excessively great and thus the transmission path of the lithium ions is prolonged, thereby affect the exertion of the capacity and rate performance.
In third aspect, the present disclosure provides a sodium-ion cathode material prepared by the preparation method according to the second aspect.
In a fourth aspect, the present disclosure provides use of the sodium-ion cathode material according to the first aspect or the third aspect in a sodium-ion battery.
In a fifth aspect, the present disclosure provides a sodium-ion battery. The sodium-ion battery includes a positive electrode pole piece prepared by the sodium-ion cathode material according to the first aspect or the third aspect.
In some embodiments of the present disclosure, preferably, subsequent to 80 cycles at 25° C., the sodium-ion battery has a cycle retention rate of ≥75%, and preferably, from 90% to 100%
In some embodiments of the present disclosure, preferably, in a 4.2V charging state, the positive electrode pole piece has a DSC exothermic temperature of ≥280° C., and preferably, from 290° C. to 350° C.
In a sixth aspect, the present disclosure provides a sodium-ion battery pack. The sodium-ion battery pack includes the sodium-ion battery according to the fifth aspect.
In a seventh aspect, the present disclosure provides a device including the sodium-ion battery pack according to the sixth aspect.
Based on the above-mentioned technical solutions, the sodium-ion cathode material, the preparation method and use thereof, the sodium-ion battery, the sodium-ion battery pack, and the device according to the present disclosure have the following beneficial effects.
The present disclosure is described in detail below through examples.
The ionic conductivity was measured using an electrochemical workstation.
The concentration gradient of element Ti was measured using scanning electron microscopy (EDS).
The electronic conductivity was measured using a powder resistance tester through a four-probe method.
The content of residual alkali was measured using a potentiometric titrator through a national standard method.
The physical phases of the cathode material and the coating layer were measured using an XRD diffractometer based on a national standard method.
The raw materials used in the examples and comparative examples were all commercially available products.
Nickel sulfate, manganese sulfate, and ferrous sulfate were mixed according to a feeding amount of n(Ni):n(Mn):n(Fe)=0.33:0.33:0.33. The mixture was coprecipitated with ammonia water and sodium hydroxide at 55° C. for 46 hours. Subsequent to washing and drying, a precursor Ni0.33Fe0.33Mn0.33(OH)2 was obtained.
The sodium-ion cathode material was prepared based on the method in Example 1. Specifically:
The sodium-ion cathode material was prepared based on the method in Example 1. Specifically:
The sodium-ion cathode material was prepared based on the method in Example 1. Specifically:
The sodium-ion cathode material was prepared based on the method in Example 1. Specifically:
The sodium-ion cathode material was prepared based on the method in Example 1. Specifically:
The sodium-ion cathode material was prepared based on the method in Example 1. Specifically:
The sodium-ion cathode material was prepared based on the method in Example 1. Specifically:
The sodium-ion cathode material was prepared based on the method in Example 1. Specifically:
The feeding amount of Na2CO3, Ni0.33Fe0.33Mn0.33(OH)2, and TiO2 satisfied: n(Na):[n(Ni)+n(Mn)+n(M)]:n(Ti)=1.03:0.99:0.01. Na2CO3, Ni0.33Fe0.33Mn0.33(OH)2, and TiO2 were subjected to dry ball milling and mixing in a mixing tank at a rotation speed of 850 rpm for 4 hours. The obtained mixture was sintered in a muffle furnace at 950° C. for 8 hours to obtain a cathode material D1. D1 had a chemical composition of Na1.03Ni0.33Fe0.33Mn0.33Ti0.01O2.
The sodium-ion cathode material was prepared based on the method in Example 1. Comparative Example 3 differed from Example 1 in that: in step (1), the dried powder was sintered under an oxygen atmosphere to obtain a coating layer DC2. The coating layer DC2 had a chemical composition of Na1.8Ti5.9Fe0.1O12.9 and an average particle size of 100 nm.
Step (2) was the same as step (2) in Example 1.
Step (3) was the same as step (3) in Example 1. A sodium-ion cathode material DS2 was prepared.
The sodium-ion cathode material was prepared based on the method in Example 1. Comparative Example 3 differed from Example 1 in that: in step (1), the feeding amount of Na2CO3, TiO2, and Fe2O3 satisfied n(Na):n(Ti):n(Fe)=2:2.9:0.1; and the dried powder was sintered under an oxygen atmosphere. A coating layer DC3 was prepared. The coating layer DC3 had a chemical composition of Na2Ti2.9Fe0.1O7 and an average particle size of 100 nm.
Step (2) was the same as step (2) in Example 1.
Step (3) was the same as step (3) in Example 1. A sodium-ion cathode material DS3 was prepared.
The particle size, ionic conductivity, electronic conductivity, and volume impedance of the sodium-ion cathode materials prepared in the examples and comparative examples were tested, and the results are shown in Table 2.
The cathode materials prepared in the examples and comparative examples were subjected to an initial charge-discharge performance test and a cycle performance test.
A button battery was prepared according to the following steps:
95 g of cathode material, 2.5 g of acetylene black, and 2.5 g of polyvinylidene fluoride (PVDF) were mixed, coated on an aluminum foil and dried, and punched with a pressure of 100 MPa to obtain a positive electrode pole piece having a diameter of 12 mm and a thickness of 120 μm. Then, the positive electrode pole piece was placed in a vacuum drying oven and dried at 120° C. for 12 hours;
A Na metal plate having a diameter of 17 mm and a thickness of 1 mm was used as a negative electrode. A polyethylene porous film having a thickness of 25 μm was used as a separator. A mixture having equal amounts of 1 mol/L NaPF6, ethylene carbonate (EC), and diethyl carbonate (DEC) was used as an electrolyte. The positive electrode pole piece, the separator, the negative electrode plate, and the electrolyte were assembled into a button battery of 2025 type in an Ar gas glove box having a water content and an oxygen content of less than 5 ppm.
The assembled button battery of 2025 type was left to stand for 12 hours. Parameters of the first charge/discharge capacity were measured in a button test cabinet at a temperature of 25° C. and 0.1C@2.0-4.0V. Then, the charging and discharging were carried out sequentially at a rate of 0.1 C and a rate of 1 C to test parameters of the rate performance. The cycle performance was tested at a rate of 1 C for 80 cycles. Subsequent to charging and discharging 2 times at 0.1 C, the button battery was recharged to 4.2V. The battery was disassembled, and the positive electrode pole piece was taken out and placed in a differential thermal-thermogravimetric tester for DSC test. The results were shown in Table 3.
As can be seen from the results in Table 3, compared with Comparative Example 1 to Comparative Example 3, the sodium-ion batteries including the positive electrode pole pieces prepared by the sodium-ion cathode materials in Example 1 to Example 10 have a higher charge/discharge capacity and cycle performance, and the positive electrode pole pieces have a higher thermal runaway temperature, indicating that thermal runaway of these cathode materials can only occur when the ambient temperature is higher. Therefore, the batteries can have the meaningful battery safety.
Further, in the sodium-ion cathode material of Example 1, the coating layer contains doping elements, and element Ti in the matrix is distributed in a gradient. When the sodium-ion cathode material is used in a sodium-ion battery, the charge and discharge capacity, cycle performance, and exothermic temperature are further improved.
The preferred embodiments of the present disclosure are described in detail above. However, the present disclosure is not limited thereto. Within the scope of technical conception of the present disclosure, a variety of simple variations may be made to the technical solutions of the present disclosure, including the combination of various technical features in any other suitable manner. These simple variations and combinations shall be regarded as the contents disclosed by the present disclosure, and all of them fall within the scope of protection of the present disclosure.
| Number | Date | Country | Kind |
|---|---|---|---|
| 202310183846.2 | Feb 2023 | CN | national |
This application is a continuation of International Application No. PCT/CN2023/085544, filed on Mar. 31, 2023, which claims priority to Chinese Patent Application No. 202310183846.2, filed on Feb. 28, 2023. The disclosures of the aforementioned applications are hereby incorporated by reference in their entireties.
| Number | Date | Country | |
|---|---|---|---|
| Parent | PCT/CN2023/085544 | Mar 2023 | WO |
| Child | 18815853 | US |
