Patent Application
20250006922
The present invention relates to sodium-ion secondary batteries.
Lithium-ion secondary batteries have secured their place as high-capacity and light-weight power sources essential for mobile devices, electric vehicles, and so on. However, current lithium-ion secondary batteries employ as their electrolytes, mainly, combustible organic electrolytic solutions, which raises concerns about the risk of fire or explosion. Particularly, secondary batteries for power sources for electric vehicles are required to be those having high energy density and high capacity for long-distance cruising. In the meantime, secondary batteries are also required to have high safety. Therefore, there is a demand to develop a high-performance electricity storage device satisfying both high energy density and high safety.
In the current lithium-ion secondary batteries employing organic electrolytic solutions, ternary positive-electrode active materials, including an NCA (Li(Ni-Co-Al)O2-based) active material and an NCM (Li(Ni-Co-Mn)O2-based) active material, are used as their positive-electrode active materials. However, these positive-electrode active materials are layered oxides, are therefore thermally unstable, and, due to exothermic reaction during short circuit, may decompose while releasing oxygen and heat from their crystals, i.e., cause thermal runaway, which raises concerns about safety. To cope with this, LFP (LiFePO4) containing P in its crystal structure is used as a positive-electrode active material having relatively high thermal stability and high safety (see, for example, Patent Literature 1).
Even LFP is insufficient in safety and is demanded to further improve the safety. In addition, LFP contains Li being a rare metal and, therefore, has a problem of uncertainty of stable supply thereof.
In view of the foregoing, the present invention has an object of providing a sodium-ion secondary battery having a high capacity and excellent safety.
A sodium-ion secondary battery of Aspect 1 in the present invention includes: a positive electrode containing a positive-electrode active material made of a crystallized glass containing crystals represented by a general formula NaxMyP2Oz (where 1≤x≤2.8, 0.95≤y≤1.6, 6.5≤z≤8, and M is at least one selected from among Fe, Ni, Co, Mn, and Cr); a negative electrode containing a negative-electrode active material made of hard carbon; and a non-aqueous electrolyte.
As described above, LFP containing P in its crystal structure has relatively high thermal stability. On the other hand, a positive-electrode active material made of a crystallized glass containing crystals represented by a general formula NaxMyP2Oz contains a pyrophosphate backbone in the crystal, wherein a P atom and an O atom are tightly bound to oxygen. Therefore, this positive-electrode active material is a more thermally stable material than LFP. Furthermore, the surface of the positive-electrode active material made of a crystallized glass is formed of a low-electrically-conductive glass layer. Therefore, in the event of a short circuit, no abrupt reaction occurs, energy is gradually released, and the internal temperature of the battery is less likely to rise. For example, even if the battery exterior and the electrolytic solution burn when exposed to high temperatures of 600° C. or higher due to fire or others, the glass layer on the surface of the positive-electrode active material melts into an insulating glass melt, which can prevent thermal runaway due to battery reaction.
Moreover, the positive-electrode active material containing pyrophosphoric acid is operable at a high voltage and can make up a safe and high-energy-density battery in combination with hard carbon operable at an extremely low potential and a high capacity as a negative-electrode active material. In addition, Na ions rich as a resource are used as a carrier and, therefore, can be stably supplied.
In the present disclosure, a crystallized glass means a glass obtained by heating (firing) a precursor glass containing an amorphous phase to precipitate crystals (crystallize the precursor glass). The amorphous phase may fully transition into a crystal phase or the amorphous phase may partially remain. Furthermore, a single kind of crystal may be precipitated or two or more kinds of crystals may be precipitated. For example, whether or not to be a crystallized glass can be determined by a peak angle shown by powder X-ray diffraction (XRD).
A sodium-ion secondary battery of Aspect 2 in the present invention is the sodium-ion secondary battery according to Aspect 1, wherein the hard carbon is preferably coated with a coating layer containing beta-alumina crystals or NASICON crystals.
Hard carbon has excellent electronic conductivity. Therefore, in the event of a short circuit, most of the negative-electrode active material may abruptly react to concentrate electric current on a short-circuited portion, which makes it likely that a temperature increase occurs. For this reason, the hard carbon is coated with a coating layer containing a solid electrolyte, such as beta-alumina crystals or NASICON crystals. Thus, the electronic conductivity in the negative electrode is decreased while the ionic conductivity is maintained, and, therefore, electric current concentration can be suppressed. As a result, the temperature increase in the event of a short circuit can be suppressed and, thus, the safety can be further increased.
A sodium-ion secondary battery of Aspect 3 in the present invention is the sodium-ion secondary battery according to Aspect 1 or 2, wherein the positive-electrode active material is preferably made of a crystallized glass containing crystals represented by a general formula NaxMP2O7 (where 1≤x≤2 and M is at least one selected from among Fe, Ni, Co, Mn, and Cr)
A sodium-ion secondary battery of Aspect 4 in the present invention is the sodium-ion secondary battery according to Aspect 3, wherein the positive-electrode active material is preferably made of a crystallized glass containing crystals represented by a general formula NaxFeP2O7 (where 1≤x≤2)
A sodium-ion secondary battery of Aspect 5 in the present invention is the sodium-ion secondary battery according to any one of Aspects 1 to 4, wherein the positive-electrode active material is preferably coated with a carbon material. In the present disclosure, coating is a concept different from mixing; mixed powder is a simple set of a positive-electrode active material and a carbon material, whereas coated powder is powder in which a carbon material is present on the surfaces of positive-electrode active material particles forming the powder. For example, coating means that a positive-electrode active material particle forms a core and the periphery (surface) of the core is partially or fully coated with a carbon material.
A sodium-ion secondary battery of Aspect 6 in the present invention is the sodium-ion secondary battery according to any one of Aspects 1 to 5, wherein the positive-electrode active material is preferably formed of secondary particles. If a positive-electrode active material formed of primary particles is used to form a paste coating, the particle diameter of the positive-electrode active material is small and, therefore, the cohesion of the particles during drying of the paste coating is great, resulting in the tendency for the electrode to crack during the drying of the paste coating. If in this case the particle diameter of the primary particles is increased, the specific surface area decreases, which presents a problem of reduction in electronic conductivity and ionic conductivity. Unlike the above, a positive-electrode active material formed of secondary particles has a relatively large specific surface area and can be increased in particle diameter, which can suppress cracking of the electrode during drying of a paste coating and reduction in electronic conductivity and ionic conductivity described above.
In the present disclosure, a secondary particle means a particle in which primary particles having an average particle diameter of 50 nm or more gather together (agglomerate).
A sodium-ion secondary battery of Aspect 7 in the present invention is the sodium-ion secondary battery according to any one of Aspects 1 to 6, wherein the non-aqueous electrolyte preferably contains an organic electrolytic solution and/or a gel polymer electrolyte.
In an electrical device of Aspect 8 in the present invention, the sodium-ion secondary battery according to any one of Aspects 1 to 7 is used.
The present invention enables provision of a sodium-ion secondary battery having a high capacity and excellent safety.
A sodium-ion secondary battery according to the present invention at least includes a positive electrode, a negative electrode, and a non-aqueous electrolyte. The non-aqueous electrolyte is present between the positive electrode and the negative electrode and serves to conduct sodium ions acting as a carrier between the positive electrode and the negative electrode. The positive electrode and/or the negative electrode is preferably impregnated with the non-aqueous electrolyte and, thus, the ionic conductivity of the positive electrode and/or the negative electrode can be increased. A separator having an insulation property is preferably provided between the positive electrode and the negative electrode in order to prevent the positive electrode and the negative electrode from making contact with each other and thus short-circuiting. For example, when the positive electrode and the negative electrode are layered through the separator and, in this state, the separator is impregnated with the non-aqueous electrolyte, an ionic conduction path between the positive electrode and the negative electrode can be formed while contact between the positive electrode and the negative electrode is prevented.
The sodium-ion secondary battery according to the present invention may include a single set of a positive electrode and a negative electrode or have a structure which includes a plurality of sets of a positive electrode and a negative electrode and in which these sets are layered, as shown in Examples below.
When the battery has a structure in which a plurality of sets of a positive electrode and a negative electrode are layered, the battery can be increased in capacity.
Hereinafter, a detailed description will be given of respective embodiments of components of the sodium-ion secondary battery according to the present invention. However, the following embodiments are merely illustrative and the present invention is not intended to be limited to the following embodiments.
The positive electrode in the present invention contains a positive-electrode active material made of a crystallized glass containing crystals represented by a general formula NaxMyP2Oz (where 1≤x≤2.8, 0.95≤y≤1.6, 6.5≤z≤8, and M is at least one selected from among Fe, Ni, Co, Mn, and Cr).
In the above general formula, the number of sodium atoms, x, is preferably 1 to 2.8, more preferably 1.2 to 2.8, even more preferably 1.3 to 2.3, and particularly preferably 1.7 to 1.85. Within this range, an active material having high charge and discharge capacities can be obtained. Specifically, if x is too small, the number of sodium ions involved in absorption and release is small and, therefore, the charge and discharge capacities tend to decrease. On the other hand, if x is too large, heterogenous crystals, such as Na3PO4, not involved in charge and discharge are likely to precipitate and, therefore, the charge and discharge capacities tend to decrease.
In the above general formula, the number of M atoms, y, is preferably 0.95 to 1.6, more preferably 0.95 to 1.4, and particularly preferably 1.0 to 1.2. Within this range, an active material having high charge and discharge capacities can be obtained. Specifically, if y is too small, the number of transition metal ions causing a redox reaction is small, the number of sodium ions involved in absorption and release thus becomes small, and, therefore, the charge and discharge capacities tend to decrease. On the other hand, if y is too large, heterogenous crystals, such as NaFePO4, not involved in charge and discharge are likely to precipitate and, therefore, the charge and discharge capacities tend to decrease.
P2Oz forms a three-dimensional network and has a function to stabilize the structure of the positive-electrode active material. The number of oxygen atoms, z, is preferably 6.5 to 8, more preferably 7 to 7.8, even more preferably 7 to 7.5, and particularly preferably 7 to 7.3. Within this range, an active material having a long life and a high capacity can be obtained.
Specifically, if z is too small, the valence of M becomes lower than bivalence and, thus, metal is likely to precipitate during charge and discharge. The precipitated metal may be eluted into the electrolyte to induce deterioration of the battery. On the other hand, if z is too large, the valence of M becomes higher than bivalence and, thus, a redox reaction associated with charge and discharge of the battery is less likely to occur. As a result, the number of sodium ions absorbed and released becomes small and, therefore, the charge and discharge capacities tend to decrease.
A specific example of the positive-electrode active material made of a crystallized glass containing crystals represented by a general formula NaxMyP2Oz is a positive-electrode active material made of a crystallized glass containing crystals represented by a general formula NaxMP2O7 (where 1×2 and M is at least one selected from among Fe, Ni, Co, Mn, and Cr) Particularly, a crystallizable glass containing crystals represented by a general formula NaxFeP2O7 (1×2) is preferred because it not only has a strong pyrophosphate backbone and therefore excellent safety without release of oxygen during overcharge, but also has excellent cycle characteristics. In addition, Fe is used as a transition metal element causing a redox reaction and the crystallized glass is free of rare metal, which is preferred from the viewpoint of resource. Furthermore, the glass precipitating the above crystals is stable in vitrification and, therefore, has the advantage of being easily producible.
Particularly, Na2Fe1.33P2O7.33 (=Na3Fe2 (PO4)P2O7) has a high capacity per unit mass and a high operating voltage and, therefore, enables production of a battery having a higher energy density.
The form of the positive-electrode active material made of a crystallized glass containing crystals represented by a general formula NaxMyP2Oz is not particularly limited, but is preferably a powdered form. In this case, the average particle diameter of the positive-electrode active material is preferably 0.01 to 30 μm, more preferably 0.05 to 12 μm, and particularly preferably 0.1 to 10 μm. By passing the powder through a mesh with sub-50 μm openings, the powder can be adjusted to fall within the above range. Within this range, an electrode having excellent surface smoothness is easily producible and, therefore, a low-resistant battery can be obtained. Specifically, if the average particle diameter of the positive-electrode active material powder is too small, the cohesion between powder particles increases and, therefore, the powder tends to be poor in dispersibility when formed into a paste. In addition, the electrode tends to crack during drying of the paste coating. As a result, the internal resistance of the battery becomes high and the operating voltage is likely to decrease. Furthermore, the electrode density tends to decrease, thus decreasing the capacity per unit volume of the battery. On the other hand, if the average particle diameter of the positive-electrode active material powder is too large, sodium ions are less likely to diffuse and the internal resistance tends to increase. In addition, the surface smoothness of the electrode tends to be poor.
The positive-electrode active material is preferably formed of secondary particles. By doing so, as described previously, cracking of the electrode during drying of a paste coating and reduction in electronic conductivity and ionic conductivity can be suppressed. When the positive-electrode active material is formed of secondary particles, the average particle diameter of the secondary particles preferably satisfies the above-described preferred range of average particle diameters of the positive-electrode active material. The form of the positive-electrode secondary particles is not particularly limited. Specifically, the form of the particles may be any of powdered forms, including spherical, ellipsoidal, faceted, strip-shaped, fibrous, flaky, toroidal, and hollow particles.
The average particle diameter used herein means D50 (a volume-based average particle diameter) and refers to a value measured by the laser diffraction/scattering method.
The positive-electrode active material made of a crystallized glass containing crystals represented by a general formula NaxMyP2Oz can be produced by subjecting a raw material prepared to have a predetermined composition to melting, forming, and, if necessary, grinding to obtain a precursor glass and then heat-treating the precursor glass at a predetermined temperature to crystallize it.
The precursor glass preferably contains, in terms of % by mole of the following oxides, 25 to 55% Na2O, 20 to 60% FeO+NiO+CoO+MnO+CrO, and 25 to 55% P2O5. The reasons why the composition is limited as just described will be described below.
Na2O is a component constituting part of NaxMyP2Oz crystals. The content of Na2O is preferably 25 to 55% and particularly preferably 30 to 50%. If the content of Na2O is too small or too large, NaxMyP2Oz crystals are less likely to precipitate.
FeO, NiO, CoO, MnO, and CrO are also components constituting part of NaxMyP2Oz crystals. The total content of FeO, NiO, CoO, MnO, and CrO is preferably 20 to 60% and particularly preferably 30 to 50%. If the content of these components is too small, NaxMyP2Oz crystals are less likely to precipitate. If the content of these components is too large, NaxMyP2Oz crystals are less likely to precipitate and undesirable crystals, such as FeO, NiO, CoO, MnO or CrO, are likely to precipitate. Particularly, in order to increase the cycle characteristics and rapid charge and discharge characteristics, FeO is preferably positively contained in the precursor glass. All of the above components may not necessarily be contained as essential components and one or some of the components may not be contained (i.e., the content of one or some of the components may be 0%). The preferred range of contents of each component of FeO, NiO, CoO, MnO, and CrO is preferably 0 to 60%, more preferably 10 to 60%, even more preferably 20 to 60%, and particularly preferably 30 to 50%.
P2O5 is also a component constituting part of NaxMyP2Oz crystals. The content of P2O5 is preferably 25 to 55% and particularly preferably 30 to 50%. If the content of P2O5 is too small or too large, NaxMyP2Oz crystals are less likely to precipitate.
The precursor glass may contain, in addition to the above components, Nb2O5, MgO, Al2O3, TiO2, ZrO2 or Sc2O3. These components become incorporated into NaxMyP2Oz crystals to increase the electronic conductivity and, therefore, the rapid charge and discharge characteristics are likely to increase. The total content of these components is preferably 0 to 25% and particularly preferably 0.2 to 10%. If the content of these components is too large, heterogeneous crystals are generated and the amount of NaxMyP2Oz crystals precipitated is likely to decrease.
Furthermore, the precursor glass may contain SiO2, B2O3, GeO2, Ga2O3, Sb2O3 or Bi2O3. These components increase the glass formation ability and, therefore, a homogeneous amorphous material is likely to be obtained. The total content of these components is preferably 0 to 25% and particularly preferably 0.2 to 10%. If the content of these components is too large, the amount of NaxMyP2Oz crystals precipitated is likely to decrease.
The composition of the resultant crystallized glass is the same as that of the precursor glass and the description thereof will therefore be omitted.
A negative-electrode active material made of hard carbon is preferably used in powdered form. In this case, the average particle diameter of the negative-electrode active material is preferably 0.1 to 30 μm, more preferably 0.5 to 15 μm, and particularly preferably 1 to 10 μm. Within this range, a battery having a high charge-discharge efficiency and a low resistance can be obtained. Specifically, if the average particle diameter of the negative-electrode active material is too small, the surface area of the active material is large and, therefore, the non-aqueous electrolyte tends to be likely to be reductively decomposed at the surface of the active material to form a coating. As a result, the initial charge-discharge efficiency of the battery becomes low. In addition, the formed coating tends to interfere with ion conduction and increase the internal resistance of the battery. On the other hand, if the average particle diameter of the negative-electrode active material powder is too large, the internal resistance tends to increase.
In addition, the surface smoothness of the electrode tends to be poor.
Hard carbon can also be produced by firing a hard carbon precursor. Examples of the hard carbon precursor include: sugars, such as sucrose, cellulose, D-glucose, and fructose; biomass, such as lignin, cornstalk, sorghum stalk, pine cone, mangosteen, argan nut shell, chaff, dandelion, straw core, ramie fiber, cotton, kelp, and coconut meat skin; and polymers, such as PAN (polyacrylonitrile), pitch, PVC (polyvinyl chloride) nanofiber, polyaniline, sodium polyacrylate, tire (polymer for tire), and phosphorous-doped PAN.
The hard carbon is preferably coated with a coating layer containing beta-alumina crystals or NASICON crystals. By doing so, as described previously, the temperature increase in the event of a short circuit can be suppressed and, thus, the safety can be further increased.
Beta-alumina crystals include two types of crystals: β-alumina (theoretical composition formula: Na2O·11Al2O3) and β″-alumina (theoretical composition formula: Na2O·5.3Al2O3). β″-alumina is a metastable material and is therefore generally used in a state in which Li2O or MgO is added as a stabilizing agent thereto. β″-alumina has a higher sodium-ion conductivity than β-alumina. Therefore, β″-alumina alone or a mixture of β″-alumina and β-alumina is preferably used and Li2O-stabilized β″-alumina (Na1.7Li0.3Al10.7O17) or MgO-stabilized β″-alumina ((Al10.32Mg0.68O16) (Na1.68O)) is more preferably used.
Examples of the NASICON crystals include compounds represented by a general formula Na1+xX2P3−xSixO12 (where X represents at least one transition metal element selected from group IV elements and 0≤x≤3). Particularly, the NASICON crystals preferably contain at least one of a first compound and a second compound both described below. The first compound is a compound represented by a general formula Na1+xZr2P3−xSixO12 (where 0≤x≤3). The second compound is a compound in which a part of Zr in the first compound is substituted with at least one element selected from the group consisting of Ca, Mg, Ba, Sr, Al, Nb, Ta, In, Ga, and group III elements. An example of the group III element is at least one selected from the group consisting of Sc, Y, and La.
Examples of the first compound and the second compound include Na3Zr2Si2PO12, Na3Zr1.6Ti0.4Si2PO12, and Na3Zr1.88Y0.12Si2PO12. Other examples of the NASICON crystals include Na3.2Zr1.3Si2.2P0.7O10.5, Na3Hf2Si2PO12, Na3.4Zr0.9Hf1.4Al0.6Si1.2P1.8O12, Na3Zr1.7Nb0.24Si2PO12, Na3.6Ti0.2Y0.7Si2.8O9, Na3.12Zr1.88Y0.12Si2PO12, Na3.6Zr0.13Yb1.67Si0.11P2.9O12, and Na3.12Zr1.88Y0.12Si2PO12.
Hard carbon coated with a coating layer containing beta-alumina crystals or NASICON crystal can be produced by mixing a precursor of the coating layer and hard carbon powder, drying the mixture, and then grinding it. Hereinafter, a description will be given of a precursor of the coating layer containing beta-alumina crystals or NASICON crystals. In the present disclosure, coating is a concept different from mixing; mixed powder is a simple set of beta-alumina crystals or NASICON crystals and hard carbon, whereas coated powder is powder in which beta-alumina crystals or NASICON crystals are present on the surfaces of hard carbon particles forming the powder. For example, coating means that a hard carbon particle forms a core and the periphery (surface) of the core is partially or fully coated with beta-alumina crystals or NASICON crystals.
The form of the hard carbon coated with a coating layer containing beta-alumina crystals or NASICON crystal is not particularly limited. Specifically, the form of the particles may be any of powdered forms, including spherical, ellipsoidal, faceted, strip-shaped, fibrous, flaky, toroidal, and hollow particles. Furthermore, the hard carbon particles preferably satisfy the above-described preferred range of average particle diameters of the negative-electrode active material.
For the coating layer containing beta-alumina crystals, the precursor of the coating layer can be obtained, for example, by mixing aluminum nitrate, sodium nitrate, and lithium nitrate. In doing so, the ratio among the above materials is adjusted to give a desired composition ratio of the beta-alumina crystals.
For the coating layer of NASICON crystals, an example of the precursor of the coating layer is a solution containing: an alkali metal element and a transition metal element both constituting part of the NASICON crystals; and carbonate ions. In the solution, the sodium metal element is contained as sodium ions and the transition metal element is contained as transition metal ions. The precursor of the coating layer may be formed, not as a solution, but as a gelled material or dried material of the solution.
The transition metal element is, for example, at least one element selected from the group consisting of group III elements and group IV elements. The transition metal element is preferably Ti, Zr, Hf, Sc, Y, La, Sm, Dy or Gd, more preferably Zr, Hf, Sc, Y, La, Sm, Dy or Gd, even more preferably Zr, Hf, Sc, Y, La or Sm, and particularly preferably Zr, Hf, Y, La or Sm. Other than these transition metal elements, the precursor of the coating layer may include at least one selected from the group consisting of Ca, Mg, Ba, Sr, Al, Nb, Ta, In, and Ga. In the precursor of the coating layer, carbonate ions may be contained as a carbonate (a carbonate of a transition metal) or a mixture of carbonate ions and a carbonate.
As the precursor of the coating layer, a solution containing nitrate ions instead of carbonate ions may be used. However, the precursor of the coating layer is preferably a solution containing carbonate ions for the following reasons.
When a solution containing nitrate ions is used as the precursor of the coating layer, there is a tendency that components in the solution heterogeneously precipitate during mixing or drying of the solution and, thus, a heterogeneous phase causing a decrease in ionic conductivity after firing is formed. Furthermore, the weight reduction due to decomposition of nitrate ions in the firing process is significant, which makes it difficult to form a homogeneous thin film layer. In addition, the production cost of facilities and so on for treating corrosive gas, such as NOx, generating in the firing process may increase. Furthermore, the solution containing nitrate ions is highly acidic and, therefore, requires high-level chemical durability of production facilities. Also in this respect, the production cost may increase.
On the other hand, when a solution containing carbonate ions is used as the precursor of the coating layer, a transition metal element in a transition metal oxide, such as ZrO2 or Y2O3, normally dissolvable in an acidic region only is dissolved in the solution by being coordinated by carbonate ions to form a complex, which enables preparation of a metallic salt solution having neutrality to weak basicity (pH 7 or more, preferably 7.5 or more, more preferably 8 or more, even more preferably 8.5 or more, and particularly preferably 9 or more). In this case, not only a sodium metal component constituting part of the coating layer can be dissolved as a carbonate or a hydroxide in the solution, but also a Si component constituting another part of the coating layer can be added as liquid glass (sodium silicate: Na2O·nSiO2). Therefore, a precursor of the coating layer can be easily prepared.
In the precursor solution of the coating layer, carbonate ions are preferably coordinated bidentately to the transition metal element. In this case, the transition metal element can be stably present in the solution.
The precursor solution of the coating layer preferably contains NR4+ (where Rs are each independently a substituent of at least one selected from the group consisting of H, CH3, C2H5, and CH2CH2OH) as counterions to the carbonate ions. By doing so, the transition metal element can be stably present in the solution.
The precursor solution of the coating layer can be obtained, for example, by mixing liquid glass (sodium silicate), sodium tripolyphosphate, and zirconium ammonium carbonate aqueous solution.
The coating layer may contain hard carbon. By doing so, the battery can be increased in capacity while being increased in electronic conductivity. The coating layer containing hard carbon can be produced, for example, by mixing the above-described hard carbon precursor into a precursor solution of the coating layer and firing the mixture.
Examples of the non-aqueous electrolyte include one containing an organic electrolytic solution and one containing a gel polymer electrolyte. Furthermore, when the non-aqueous electrolyte contains a sodium salt (a sodium supporting salt), it functions as an electrolyte for a sodium-ion secondary battery.
Examples of the organic electrolytic solution include propylene carbonate (PC), ethylene carbonate (EC), 1,2-dimethoxyethane (DME) γ-butyrolactone (GBL), tetrahydrofuran (THF), 2-methyltetrahydrofuran (2-MeTHF), 1,3-dioxolan, sulfolane, acetonitrile (AN), diethyl carbonate (DEC), dimethyl carbonate (DMC), methylethyl carbonate (MEC), and dipropyl carbonate (DPC). Alternatively, other examples include: ionic liquids of aliphatic quaternary ammonium salts, such as N,N,N-trimethyl-N-propyl ammonium bis(trifluoromethanesulfonyl)imide [abbr. TMPA-TFSI], N-methyl-N-propylpiperidinium bis(trifluoromethanesulfonyl)imide [abbr. PP13-TFSI], N-methyl-N-propylpyrrolidinium bis(trifluoromethanesulfonyl)imide [abbr. P13-TFSI], and N-methyl-N-butylpyrrolidinium bis(trifluoromethanesulfonyl)imide [abbr. P14-TFSI]; and ionic liquids of quaternary alkylimidazolium salts, such as 1-methyl-3-ethylimidazolium tetrafluoroborate [abbr. EMIBF4], 1-methyl-3-ethylimidazolium bis(trifluoromethanesulfonyl)imide [abbr. EMITFSI], 1-allyl-3-ethylimidazolium bromide [abbr. AEImBr], 1-allyl-3-ethylimidazolium tetrafluoroborate [abbr. AEImBF4], 1-allyl-3-ethylimidazolium bis(trifluoromethanesulfonyl)imide [abbr. AEImTFSI], 1,3-diallylimidazolium bromide [abbr. AAImBr], 1,3-diallylimidazolium tetrafluoroborate [abbr. AAImBF4], and 1,3-diallylimidazolium bis(trifluoromethanesulfonyl)imide [abbr. AAImTFSI]. These non-aqueous solvents may be used singly or in a mixture of two or more of them.
Examples of the gel polymer electrolyte include polyacrylonitrile (PAN), polyethylene oxide (PEO), polypropylene oxide (PPO), polyethylene glycol (PEG), polyethylene imine (PEI), polymethyl methacrylic acid (PMMA), poly(vinylidene fluoride (VDF)-hexafluoropropylene (HFP)) copolymer (PVDF-HFP), and polymers of any combination of them. With the use of a non-aqueous electrolyte containing a gel polymer electrolyte, the electrolyte is less likely to catch fire and, therefore, the safety of the secondary battery can be further increased.
Examples of the sodium salt include sodium salts of PF6-, BF4−, (CF3SO2)2N− (bis(trifluoromethanesulfonyl)imide, commonly called TFSI), CF3SO3− (commonly called TFS), (C2F5SO2)2N− (bis(pentafluoroethanesulfonyl)amide, commonly called BETI), ClO4−, AsF6−, SbF6−, bis(oxalato) boric acid (B(C2O4)2−, commonly called BOB), and difluoro(trifluoro-2-oxide-2-trifluoro-methyl propionate (2-)-0,0)boric acid (BF2OCOOC(CF3)3−, commonly called B(HHIB)). These electrolyte salts may be used singly or in a mixture of two or more of them. Particularly, sodium salts of PF6− and BF4−, which are inexpensive, are preferred. The electrolyte salt concentration is appropriately adjusted, generally, within a range of 0.5 to 3 M/L.
The non-aqueous electrolyte may contain an additive, such as vinylene carbonate (VC), vinylene acetate (VA), vinylene butyrate, vinylene hexanoate, vinylene crotonate or catechol carbonate. These additives serve to form a protective film on the surface of the active material. The concentration of the additive is, relative to 100 parts by mass of non-aqueous electrolyte, preferably 0.1 to 3 parts by mass and particularly preferably 0.5 to 1 part by mass.
The positive electrode and the negative electrode may contain a conductive agent and/or a binder.
The conductive agent is a component that forms a conducting path in the positive electrode and the negative electrode. For example, a conductive carbon can be used as the conductive agent. Preferred examples of the conductive carbon include powdered or fibrous conductive carbons, including highly conductive carbon blacks, such as acetylene black or Ketjenblack.
The binder is a material for binding together the source material components (source material component powders) for the positive electrode and the negative electrode. Examples of the binder include: cellulose derivatives, such as carboxymethyl cellulose, hydroxypropylmethyl cellulose, hydroxypropyl cellulose, ethyl cellulose, hydroxyethyl cellulose, and hydroxymethyl cellulose, or water-soluble polymers, such as polyvinyl alcohol; thermosetting resins, such as thermosetting polyimide, phenolic resin, epoxy resin, urea resin, melamine resin, unsaturated polyester resin, and polyurethane; polycarbonate-based resins, such as polypropylene carbonate; and polyvinylidene fluoride.
A current collector layer is preferably provided on the outside surfaces of the positive electrode and/or the negative electrode. Thus, electrons generated by battery reaction can be collected and efficiently extracted to the outside. The current collector layer is made of, for example, a metal foil. Specifically, the material for the metal foil is at least one selected from among Al, Ti, Fe, Ni, Sn, Bi, Cu, Pb, Mo, Ag, and Au. Among these materials, Al is preferred because of its excellent electrical conductivity and light weight.
The thickness of the current collector layer is preferably 0.1 to 1000 μm, more preferably 0.1 to 500 μm, and particularly preferably 0.2 to 20 μm. Within this range, a battery having excellent output characteristics and a high energy density can be obtained. Specifically, if the current collector layer is too thin, the resistance becomes excessively high. If the current collector layer is too thick, the energy density per unit volume and energy density per unit weight of the sodium secondary battery tend to decrease.
The sodium-ion secondary battery according to the present disclosure has excellent safety and, therefore, can be used as a power source for various electrical devices, for example, an air conditioner, a washing machine, a TV set, a refrigerator, a freezer, a cooling apparatus, a notebook computer, a tablet computer, a smartphone, a PC keyboard, a PC display, a desktop PC, a CRT monitor, a PC rack, a printer, a 3D printer, an integrated PC, a mouse, a hard disk, PC peripherals, a clothes iron, a clothes drier, a window fan, a transceiver, a blower, a ventilating fan, a TV set, a music recorder, a music player, an oven, a range, a toilet seat with a warm-water shower feature, a convection space heater, car components, a car navigation device, a flashlight, a humidifier, a portable karaoke device, an extractor fan, a dryer, an air purifier, a mobile phone, an emergency light, a gaming device, a sphygmomanometer, a coffee mill, a coffee maker, a kotatsu, a copier, a disc changer, a radio, a shaver, a juicer, a shredder, a water purifier, a lighting fixture, a dehumidifier, a dish dryer, a rice cooker, a stereo, a stove, a speaker, a trouser press, a cleaner, a body fat scale, a weight scale, a bathroom scale, a video player, an electrically heated carpet, an electric rice cooker, a rice cooker, an electric razor, a desk lamp, an electric pot, an electronic gaming device, a portable gaming device, an electronic dictionary, an electronic organizer, a microwave, an electromagnetic cooker, a calculator, an electric cart, an electric wheelchair, power tools, an electric toothbrush, a footwarmer, a haircutting device, a telephone, a clock, an intercom, an air circulator, an insect electrocutor, a copying machine, a hot plate, a toaster, a hair dryer, an electric drill, a water heater, a panel heater, a grinder mill, a soldering iron, a video camera, a video disc recorder, a facsimile machine, a fan heater, a food processor, a bedding dryer, headphones, an electric pot, a heated floor mat, a microphone, a massage machine, a midget lamp, a mixer, a sewing machine, a rice-cake making machine, a floor heating panel, a lantern, a remote control, a chilling/heating cabinet, a water cooler, a freezer storage, an air cooler, a word processor, a whisk, a GPS, electronic music instruments, a motorcycle, toys, a lawn mower, a floater, an electric reel, an electric shocker for tuna fishing, an underwater scooter, a fish finder, a bicycle, a motorcycle, a motor vehicle, a hybrid motor vehicle, a plug-in hybrid motor vehicle, an electric vehicle, railroads, a ship, an airplane, a submarine, an aircraft, a satellite, and an emergency power supply system.
Hereinafter, the present invention will be described in further detail with reference to examples, but the present invention is not at all limited to these examples.
Tables 1 and 2 show Examples 1 to 7 and Comparative Examples 1 to 3.
A raw material prepared to provide, in terms of molar ratio, 40Na2O-20Fe2O3-40P2O5 as a glass composition was melt at 1200° C. for an hour in the atmosphere and cooled by twin rollers, thus producing a glass film. The obtained glass film was ground for 60 hours in a ball mill using a mixture of 5-mm diameter ZrO2 balls, 3-mm diameter ZrO2 balls, and 1-mm diameter ZrO2 balls in ethanol, thus obtaining a glass powder having a specific surface area of 11.1 m2/g. The obtained glass powder was further ground for five hours in a planetary ball mill at 300 rpm using 0.3-mm diameter ZrO2 balls in ethanol, thus obtaining a glass powder having a specific surface area of 32.1 m2/g.
An amount of 25 parts by mass of polyethylene oxide nonylphenyl ether (HLB value: 13.3, mass average molecular weight: 660), which is a non-ionic surfactant, was added as a carbon source to 100 parts by mass of the obtained glass powder, and these materials were mixed with a planetary centrifugal mixer and then dried. The obtained powder was fired in a nitrogen atmosphere at 620° C. for 30 minutes, thus obtaining a positive-electrode active material powder made of a crystallized glass containing Na2FeP2O7 crystals surface-coated with carbon.
The obtained positive-electrode active material powder was ground in an alumina mortar and then passed through a mesh with 50 μm openings. An amount of 5 parts by mass of acetylene black as a conductive agent was added to 95 parts by mass of the obtained powder, thus obtaining a positive electrode composite material powder. An amount of 5 parts by mass of polyvinylidene fluoride was further added to the powder and N-methyl-2-pyrrolidone was further added as a solvent to the powder to give the positive electrode composite material powder a concentration of 50% by mass. These materials were mixed with a planetary centrifugal mixer, thus producing a positive-electrode paste.
The produced positive-electrode paste was coated, using a doctor blade, on both surfaces of a current collector layer 11 made of a 20 μm thick aluminum foil to provide a capacity of 2.5 mAh/cm2 for each surface. Thereafter, the current collector layer 11 was dried for an hour by a dryer at 80° C. and pressed by a roll press, thus forming a positive electrode layer 12. Using a Thomson blade, the obtained laminate was punched into ten pieces with a 55 mm×40 mm portion where the positive electrode layer was formed and a 10 mm×10 mm tab 15 where the positive electrode layer 12 was not formed (see
An amount of 5 parts by mass of acetylene black as a conductive agent was added to 95 parts by mass of hard carbon powder having an average particle diameter of 5 μm, thus obtaining a negative electrode composite material powder. An amount of 5 parts by mass of polyvinylidene fluoride was further added to the powder and N-methyl-2-pyrrolidone was further added as a solvent to the powder to give the negative electrode composite material powder a concentration of 50% by mass. These materials were mixed with a planetary centrifugal mixer, thus producing a negative-electrode paste.
The produced negative-electrode paste was coated, using a doctor blade, on both surfaces of a 20 μm thick aluminum current collector foil to provide a capacity of 2.5 mAh/cm2 for each surface. Thereafter, the current collector foil was dried for an hour by a dryer at 80° C. and pressed by a roll press, thus forming a negative electrode layer. Using a Thomson blade, the obtained laminate was punched into nine pieces with a 60 mm×45 mm portion where the negative electrode layer was formed and a 10 mm×10 mm aluminum tab where the negative electrode layer was not formed. In this manner, negative electrodes were produced. Aside from this, two negative electrodes where a negative electrode layer was formed on only one surface were produced.
Using a Thomson blade, a 16 μm thick polyolefin-based porous film (a polypropylene microporous film both surfaces of which were coated with alumina) was punched into ten separators each having a size of 65 mm×50 mm.
The negative electrodes, the separators, and the positive electrodes obtained as described above were layered one by one in this order within an aluminum laminate film drawn to a size of 65 mm×50 mm. Specifically, as shown in
A cell capacity was calculated from the mass of the supported positive-electrode active material with reference to a theoretical capacity of 96 mAh/g and, based on the calculated cell capacity, the test cell was constant-current charged at a current value set to give a C-rate of 0.05 (charge and discharge for 20 hours) in a thermostat bath at 30° C. The cut-off voltage was 4.2 V. The charge capacity is shown in Table 1. As seen from Table 1, all the cells show comparative charge capacities.
A 3 mm diameter soft steel nail with a type K thermocouple inside was driven, at a rate of 1 mm/sec, into the laminate cell in a fully charged state until it penetrated through the cell. Temperature changes in the inside of the cell after the nail was driven into the cell were measured with the thermocouple. The peak temperature (internal temperature) in the inside of the cell is shown in Table 1. Furthermore, a graph of the temperature changes in the inside of the cell is shown in
A test cell was produced in the same manner as in Example 1 except that a negative-electrode paste was obtained in the following manner.
Liquid glass (sodium silicate: Na2O·nSiO2), a zirconium ammonium carbonate aqueous solution ((NH4)2Zr(OH)2(CO3)2), and sodium tripolyphosphate (Na5P3O10) were weighed 25 g in total to provide NASICON crystals having a composition of Na3Zr2Si2PO12. These materials were added to 150 g of pure water, followed by stirring with a hot stirrer at 50° C. for 24 hours. Thus, an alkali-ion conductive solid electrolyte precursor solution (pH=9.7) was obtained. Next, this solution was allowed to stand overnight in a thermostat bath at approximately 5° C., thus turning it into a gel. In this manner, an alkali-ion conductive solid electrolyte precursor was prepared.
Sucrose serving as a hard carbon source and the alkali-ion conductive solid electrolyte precursor obtained in the above manner were mixed for an hour in a stirrer to give a mass ratio of 4:1, thus obtaining a mixed liquid.
An amount of 40 parts by mass of mixed liquid obtained as described above was added to 100 parts by mass of hard carbon powder having an average particle diameter of 5 μm, followed by mixing with a planetary centrifugal mixer. This mixture was dried and then ground. The obtained powder was put into a carbon crucible and fired at 1000° C. in a nitrogen atmosphere in a quartz tubular furnace. From the difference between the powdered mass of the secondary particles after the firing and the mass of hard carbon powder before the firing, the amount of the coating layer was determined to be 11 parts by mass relative to 100 parts by mass of hard carbon powder. An amount of 5 parts by mass of acetylene black as a conductive agent was added to 95 parts by mass of the coated hard carbon powder, thus obtaining a negative electrode composite material powder. An amount of 5 parts by mass of polyvinylidene fluoride was further added to the powder and N-methyl-2-pyrrolidone was further added as a solvent to the powder to give the negative electrode composite material powder a concentration of 50% by mass. These materials were mixed with a planetary centrifugal mixer, thus producing a negative-electrode paste.
A test cell thus produced underwent the charge/discharge test and the nail penetration test in the same manner as in Example 1. The results are shown in Table 1.
A test cell was produced in the same manner as in Example 2 except that a gel polymer produced in the following manner was used instead of an electrolytic solution.
PAN (polyacrylonitrile, an average molecular weight of 150000) and NaCF3SO3 (sodium trifluoromethanesulfonate, abbr. NaTFS) serving as a supporting salt were mixed to give a mass ratio of 7:3. An amount of 90 parts by mass of EC:DEC=1:1 solvent (a solvent of a mixture of ethylene carbonate and diethyl carbonate at a volume ratio of 1:1) was added to 10 parts by mass of mixture obtained as above, thus obtaining a gel polymer.
A test cell thus produced underwent the charge/discharge test and the nail penetration test in the same manner as in Example 1. The results are shown in Table 1.
A test cell was produced in the same manner as in Example 2 except that a gel polymer produced in the following manner was used instead of an electrolytic solution.
PEO (polyethylene oxide, an average molecular weight of 60000) and (CF3SO2)2NNa (sodium bis(trifluoromethanesulfonyl)imide, abbr. NaTFSI) serving as a supporting salt were mixed to give a mass ratio of 8:2. An amount of 90 parts by mass of EC:DEC=1:1 solvent was added to 10 parts by mass of mixture obtained as above, thus obtaining a gel polymer.
A test cell thus produced underwent the charge/discharge test and the nail penetration test in the same manner as in Example 1. The results are shown in Table 1.
A test cell was produced in the same manner as in Example 1 except that a positive-electrode active material powder was produced in the following manner in the process for producing a positive electrode.
A raw material prepared to provide, in terms of molar ratio, 37.5Na2O-25Fe2O3-37.5P2O5 as a glass composition was melt at 1200° C. for an hour in the atmosphere and cooled by twin rollers, thus producing a glass film. The obtained glass film was ground for 60 hours in a ball mill using a mixture of 5-mm diameter ZrO2 balls, 3-mm diameter ZrO2 balls, and 1-mm diameter ZrO2 balls in ethanol, thus obtaining a glass powder having a specific surface area of 11.1 m2/g. The obtained glass powder was further ground for five hours in a planetary ball mill at 300 rpm using 0.3-mm diameter ZrO2 balls in ethanol, thus obtaining a glass powder having a specific surface area of 29.4 m2/g.
An amount of 25 parts by mass of polyethylene oxide nonylphenyl ether (HLB value: 13.3, mass average molecular weight: 660), which is a non-ionic surfactant, was added as a carbon source to 100 parts by mass of the obtained glass powder, and these materials were mixed with a planetary centrifugal mixer and then dried. The obtained powder was fired in a nitrogen atmosphere at 620° C. for 30 minutes, thus obtaining a positive-electrode active material powder made of a crystallized glass containing Na3Fe2 (PO4) P2O7(=Na2Fe1.33P2O7.33) crystals surface-coated with carbon.
A test cell thus produced underwent the charge/discharge test and the nail penetration test in the same manner as in Example 1. The results are shown in Table 2.
A test cell was produced in the same manner as in Example 5 except that a negative-electrode paste was obtained in the following manner.
Liquid glass (sodium silicate: Na2O-nSiO2), a zirconium ammonium carbonate aqueous solution ((NH4)2Zr(OH)2(CO3)2), and sodium tripolyphosphate (Na5P3O10) were weighed 25 g in total to provide NASICON crystals having a composition of Na3Zr2Si2PO12. These materials were added to 150 g of pure water, followed by stirring with a hot stirrer at 50° C. for 24 hours. Thus, an alkali-ion conductive solid electrolyte precursor solution (pH=9.7) was obtained. Next, this solution was allowed to stand overnight in a thermostat bath at approximately 5° C., thus turning it into a gel. In this manner, an alkali-ion conductive solid electrolyte precursor was prepared.
Sucrose serving as a hard carbon source and the alkali-ion conductive solid electrolyte precursor obtained in the above manner were mixed for an hour in a stirrer to give a mass ratio of 4:1, thus obtaining a mixed liquid.
An amount of 40 parts by mass of mixed liquid obtained as described above was added to 100 parts by mass of hard carbon powder having an average particle diameter of 5 μm, followed by mixing with a planetary centrifugal mixer. This mixture was dried and then ground. The obtained powder was put into a carbon crucible and fired at 1000° C. in a nitrogen atmosphere in a quartz tubular furnace. From the difference between the powdered mass of the secondary particles after the firing and the mass of hard carbon powder before the firing, the amount of the coating layer was determined to be 11 parts by mass relative to 100 parts by mass of hard carbon powder. An amount of 5 parts by mass of acetylene black as a conductive agent was added to 95 parts by mass of the coated hard carbon powder, thus obtaining a negative electrode composite material powder. An amount of 5 parts by mass of polyvinylidene fluoride was further added to the powder and N-methyl-2-pyrrolidone was further added as a solvent to the powder to give the negative electrode composite material powder a concentration of 50% by mass. These materials were mixed with a planetary centrifugal mixer, thus producing a negative-electrode paste.
A test cell thus produced underwent the charge/discharge test and the nail penetration test in the same manner as in Example 1. The results are shown in Table 2.
A test cell was produced in the same manner as in Example 6 except that a gel polymer produced in the following manner was used instead of an electrolytic solution.
PEO (polyethylene oxide, an average molecular weight of 60000) and (CF3SO2)2NNa (sodium bis(trifluoromethanesulfonyl)imide, abbr. NaTFSI) serving as a supporting salt were mixed to give a mass ratio of 8:2. An amount of 90 parts by mass of EC:DEC=1:1 solvent was added to 10 parts by mass of mixture obtained as above, thus obtaining a gel polymer.
A test cell thus produced underwent the charge/discharge test and the nail penetration test in the same manner as in Example 1. The results are shown in Table 2.
A test cell was produced in the same manner as in Example 1 except that NCA (LiNi0.8Co0.15Al0.05O) having an average particle diameter of 15 μm was used as a positive-electrode active material, graphite having an average particle diameter of 10 μm was used as a negative-electrode active material, and 1 M/L LiPF6 solution/EC:DEC=1:1 (an electrolytic solution in which LiPF6 was dissolved at a concentration of 1 M/L into a solvent of a mixture of ethylene carbonate and diethyl carbonate at a volume ratio of 1:1) was used as an electrolyte.
A test cell thus produced underwent the charge/discharge test and the nail penetration test in the same manner as in Example 1. The results are shown in Table 1. Furthermore, a graph of temperature changes in the inside of the cell is shown in
A test cell was produced in the same manner as in Comparative Example 1 except that NCM811 (LiNi0.8Co0.1Mn0.1O2) having an average particle diameter of 10 μm was used as a positive-electrode active material and the test cell underwent the charge/discharge test and the nail penetration test in the same manner as in Example 1. The results are shown in Table 1.
A test cell was produced in the same manner as in Comparative Example 1 except that carbon-coated LFP (LiFePO4) having an average secondary particle diameter of 10 μm was used as a positive-electrode active material and the test cell underwent the charge/discharge test and the nail penetration test in the same manner as in Example 1. The results are shown in Table 1.
As shown in Tables 1 and 2, although all the test cells showed comparative charge capacities, the test cells of Examples 1 to 7 exhibited an internal temperature as low as 150° C. or lower on the nail penetration test and emitted no smoke or flame.
Particularly, in Examples 2 to 4, 6, and 7 where hard carbon coated with a coating layer containing NASICON crystals was used as a negative-electrode active material, the internal temperature was as low as 80° C. or lower. Furthermore, in Examples 3, 4, and 7 where a gel polymer was used as an electrolyte, the internal temperature was an even lower value of 60° C. or lower.
On the other hand, in Comparative Examples 1 to 3, an internal temperature as high as 210° C. or higher was exhibited on the nail penetration test and smoke or flame was emitted.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2021-192328 | Nov 2021 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2022/043133 | 11/22/2022 | WO |
