Patent Application
20240266520
This application claims priority under 35 USC 119 from Japanese Patent Application No. 2023-016475 filed on Feb. 6, 2023, the disclosure of which is incorporated by reference herein in its entirety.
The present disclosure relates to a negative electrode active material, a negative electrode, and a solid-state battery.
In recent years, secondary batteries such as lithium ion secondary batteries and the like have been suitably used as portable power sources for personal computers, portable terminals and the like, and as power sources for the driving of vehicles such as electric vehicles (EVs), hybrid vehicles (HVs), plug-in hybrid vehicles (PHVs) and the like, and the like.
Because electrolytic liquids containing flammable organic solvents are used in secondary batteries, there is the need for improvement in structures and materials for preventing short-circuiting and for mounting safety devices that suppress a rise in temperature at the time of short-circuiting. To address this, solid-state batteries, which use a solid electrolyte layer instead of an electrolytic liquid and in which the materials are made solid, do not use flammable organic solvents at the battery interior, and therefore, it is thought that simplification of safety devices is devised, and the manufacturing cost and mass producibility are improved. A technique of improving energy density by including Si in a negative electrode active material is known as a technique relating to the negative electrode of a solid-state battery. With such a negative electrode active material that contains Si, the energy density can be improved by the inclusion of Si. However, on the other hand, due to volumetric expansion/contraction that accompanies charging/discharging, gaps arise between the negative electrode active material layer and the solid electrolyte layer, and due thereto, there is the tendency for a phenomenon, in which the cell resistance after charging/discharging increases, to occur. Therefore, recently, a technique has been known that attempts to suppress the formation of gaps between the negative electrode active material layer and the solid electrolyte layer due to volumetric expansion/contraction that accompanies charging/discharging, by using, as the negative electrode active material, granulated particles of primary particles, which contain a silicon material, and a binder resin such as a fluorine-based polymer or the like (for example, Japanese Patent Application Laid-Open (JP-A) No. 2019-021571).
However, in a conventional negative electrode active material that is granulated particles of primary particles, which contain a silicon material, and a fluorine-based polymer, the silicon and the fluorine-based polymer surface charges are respectively charged negatively, and therefore, it is easy for the primary particles and the fluorine-based polymer to electrostatically repel one another. Therefore, the adhesion between the primary particles and the fluorine-based polymer is low, and due thereto, there is the tendency for the granulated particles to be weak, and the cycle characteristic (e.g., the discharge capacity maintenance rate after 200 cycles) to deteriorate.
Thus, in view of the above-described circumstances, a topic of the present disclosure is the provision of a negative electrode active material, a negative electrode and a solid-state battery that suppress a deterioration in the cycle characteristic when a battery has the negative electrode that contains the negative electrode active material in a negative electrode active material layer.
Techniques for addressing the above-described topic include the following aspects.
According to the present disclosure, a negative electrode active material, a negative electrode and a solid-state battery that suppress deterioration in cycle characteristics when used in a solid-state battery, are provided.
Exemplary embodiments of the present disclosure will be described in detail based on the following figures, wherein:
Embodiments that are examples of the present disclosure are described hereinafter. The description thereof and the Examples are for exemplifying embodiments, and are not intended to limit the scope of the present disclosure.
In the present disclosure, numerical ranges expressed by using “˜” mean ranges in which the numerical values listed before and after the “˜” are included as the minimum value and the maximum value.
In numerical value ranges that are expressed in a stepwise manner in the present disclosure, the upper limit value or the lower limit value listed in a numerical value range may be substituted by the upper limit value or the lower limit value of another numerical value range that is expressed in a stepwise manner. Further, in the numerical value ranges put forth in the present disclosure, the upper limit value or the lower limit value of a numerical value range may be substituted by a value shown in the Examples.
In the present disclosure, in a case in which there are plural materials corresponding to respective components in a composition, the amount of the respective components in the composition means the total amount of the plural materials existing in the composition, unless otherwise indicated.
In the present disclosure “mass” and “weight” have the same meanings, and “mass %” and “weight %” have the same meanings.
In the present disclosure, combinations of two or more aspects are more aspects.
When describing groups (atom groups) in the present disclosure, if it is not stated whether a group is substituted or unsubstituted, the group may be either substituted or unsubstituted.
In the present disclosure, the term “layer” includes cases in which, when observing a region in which a layer exists, the layer is formed at the entirety of that region, and in addition thereto, also includes cases in which the layer is formed only at a portion of that region.
In the present disclosure, the term “step” is not only an independent step and includes steps that, in a case in which that step cannot be clearly distinguished from another step, achieve the intended object of that step.
The negative electrode active material relating to the present disclosure is granulated particles that contain primary particles, which contain at least a silicon material and a cationic polymer, and a fluorine-based polymer.
In accordance with the present disclosure, because the primary particles contain a cationic polymer in addition to the silicon material, the surface charge of the primary particles being a negative charge is suppressed. As a result, electrostatic repulsion of the primary particles and the fluorine-based polymer is suppressed, and the adhesion of the both can be improved. Therefore, at a battery that has a negative electrode including a negative electrode active material layer that contains the negative electrode active material, a deterioration in the cycle characteristic (e.g., the discharge capacity maintenance rate after 200 cycles) is suppressed.
The primary particles contain at least a silicon material and a cationic polymer.
The primary particles may further contain other materials that are other than a silicon material and a cationic polymer. Examples of these other materials are binder materials such as polyvinylidene fluoride (PVdF), styrene-butadiene rubber (SBR) and the like, and the like.
In some embodiments, for example, from the standpoint of improving the adhesion between the primary particles and the fluorine-based polymer and obtaining a better cycle characteristic, the primary particles are primary particles in which the cationic polymer covers at least partial regions of the particle surfaces of the silicon material, and are primary particles in which the cationic polymer covers the entire particle surfaces of the silicon material.
The aforementioned form of covering the primary particles can be confirmed by the strength ratio of C and Si measured by energy diffraction spectrometry (EDS) (measuring conditions: acceleration voltage: 5 kV, emission current).
Specifying of the silicon material in the primary particles can be confirmed by X-ray diffraction (XRD) measurement (scanning speed: 1 deg/min).
Specifying of the cationic polymer in the primary particles can be confirmed by gas chromatography-mass spectrometry (GC-MS). Further, in confirming that the polymer is a cationic polymer, the charge of the polymer can be confirmed by dissolving a sample of the polymer in water and measuring the zeta potential by a zeta potentiometer.
The silicon material contains silicon. The silicon is not particularly limited provided that it is a material that can be employed as a negative electrode active material, and examples thereof are elemental silicon particles, silicon alloy particles (e.g., alloys or the like of Si and one or more metals selected from the group consisting of Sn, Ti, Fe, Ni, Cu, Co and Al), porous silicon, silicon clathrate compounds, silicon oxides, compounds of these, and the like.
In some embodiments, thereamong, from the standpoint of better suppressing volumetric expansion/contraction that accompanies charging/discharging, the silicon material contains at least one of porous silicon or a silicon clathrate compound.
One type of silicon material may be used alone, or two or more types may be used in combination.
The silicon material may be, for example, a mixture of porous silicon or a silicon clathrate compound, i.e., may be in a state in which a silicon monocrystal and a silicon cluster both exist within a single particle.
Porous silicon means a monocrystalline silicon that has been made porous.
Silicon clathrate compounds mean compounds in which a silicon cluster is the structural unit of the crystal, and, more specifically, mean compounds having a silicon clathrate type crystal phase.
Silicon clathrate compounds are classified into type I and type II in accordance with the type of the crystal phase thereof.
In some embodiments, in the silicon clathrate compound, the silicon material contains at least one crystal phase among type I and type II, has one crystal phase among type I and type II as the main phase, or has type II as the main phase. Here, “has a silicon clathrate type I or type II crystal phase as the main phase” means that any peak belonging to a silicon clathrate type I or type II crystal phase is the peak of the largest diffracted intensity among the peaks observed by X-ray diffraction measurement.
In some embodiments, silicon clathrate compounds are from the standpoint that, because metal ions such as Li ions and the like can enter into the three-dimensional, cage-shaped structure, the amount of expansion is small, and, because fluctuations in volume accompanying charging/discharging of the battery are small, the cycle characteristic is even better.
A cationic polymer means a polymer having a cationic group or a group that becomes a cationic group when ionized. Amphoteric polymers that are cationic as a polymer on the whole also are included in this concept.
Examples of cationic polymers are polyethyleneimine; polyvinylamine; polyallylamine; polyaniline; polypyrrole; polyvinyl pyridine; polymers and copolymers of allylamine, pyridinium salt, allylamine hydrochloride, allylamine acetate, allylamine sulfate, diallylamine, diallylamine hydrochloride, diallylamine acetate, diallylamine sulfate, diallylmethylamine and salts thereof (examples of the salts are hydrochloride, acetate, sulfate and the like), and the like; polymers and copolymers of diallylethylamine and salts thereof (examples of the salts are hydrochloride, acetate, sulfate and the like), and the like; polymers and copolymers of diallyldimethyl ammonium salts (chloride, acetate ions, sulfate ions and the like are examples of counter anions of these salts) (e.g., polydiallyldimethyl ammonium chloride: PDADMAC). One type of cationic polymer may be used alone or two or more types may be used in combination.
In some embodiments, thereamong, from the standpoint of more efficiently making the primary particles cationic and improving the adhesion between the primary particles and the fluorine-based polymer, the cationic polymer contains a polymer and copolymer of diallyldimethyl ammonium salt or the like, and in some embodiments, contains PDADMAC.
Examples of the cationic polymer are polymers having a primary amino group, a secondary amino group, a tertiary amino group or a quaternary ammonium salt group as the cation. One type of cationic polymer may be used alone or two or more types may be used in combination.
In some embodiments, thereamong, from the standpoint of more efficiently making the primary particles cationic and improving the adhesion between the primary particles and the fluorine-based polymer, the cationic polymer contains a polymer having a quaternary ammonium salt group as the cation, and in some embodiments, contains a polymer having a quaternary ammonium salt group.
Note that counter anions of the quaternary ammonium salt are not particularly limited, and known anions can be used. However, from the standpoint of not impeding the battery characteristics even better, the counter anions may be chlorine ions.
In some embodiments, the polystyrene conversion weight average molecular weight (Mw) of the cationic polymer determined by gel permeation chromatography (GPC) is not particularly limited, and, for example, from the standpoint of more efficiently making the primary particles cationic and improving the adhesion between the primary particles and the fluorine-based polymer, is from 50,000 to 600,000, from 80,000 to 5,500,000, or from 100,000 to 5,000,000.
In some embodiments, from the standpoint of more efficiently making the primary particles cationic and improving the adhesion between the primary particles and the fluorine-based polymer, the content of the cationic polymer, with respect to the total amount of the polymer components of the negative electrode active material, is from 1 mass % to 15 mass %, from 3 mass % to 15 mass %, or from 3 mass % to 10 mass %.
The primary particles may further contain other materials other than a silicon material and a cationic polymer, within ranges in which the effects of the present disclosure can be exhibited. Examples of these other materials are binder materials such as polyvinylidene fluoride (PVdF), styrene-butadiene rubber (SBR) and the like, and the like.
The fluorine-based polymer means a polymer containing a structural unit derived from a fluorine-group-containing compound.
The fluorine-based polymer is not particularly limited, and known materials can be used therefor. Examples of the fluorine-based polymer are vinylidene fluoride resin (PVdF), poly(vinylidene fluoride-co-hexafluoropropylene) (PVdF-HFP), polytetrafluoroethylene (PTFE), perfluoroethylene propylene copolymer (FEP), poly chlorotrifluoroethylene resin (PCTFE), poly vinyl fluoride resin (PVF), poly tetrafluoroethylene perfluoroalkyl vinyl ether resin (PFA), ethylene-tetrafluoroethylen resin (ETFE), ethylenechlorotrifluoroethylene resin (ECTFE) and the like. One type of fluorine-based polymer may be used alone, or two or more types may be used in combination.
In some embodiments, thereamong, from the standpoint of more efficiently improving the adhesion between the primary particles and the fluorine-based polymer, and from the standpoint of the battery characteristics, the fluorine-based polymer may be a polymer containing a structural unit derived from vinylidene fluoride. In some embodiments, at least one of PVdF and PVdF-HFP may be contained as the fluorine-based polymer.
In some embodiments, the polystyrene conversion weight average molecular weight (Mw) of the fluorine-based polymer determined by gel permeation chromatography (GPC) is not particularly limited, and, for example, from the standpoint of more efficiently making the primary particles cationic and improving the adhesion between the primary particles and the fluorine-based polymer, is from 50,000 to 1,000,000, from 200,000 to 900,000, or from 300,000 to 800,000.
In some embodiments, in the negative electrode active material, from the standpoint of more efficiently making the primary particles cationic and improving the adhesion between the primary particles and the fluorine-based polymer, and from the standpoint of the battery characteristics, the total amount of the polymer components with respect to the negative electrode active material is from 5 mass % to 25 mass %, and the content of the cationic polymer with respect to the total amount of the polymer components of the granulated particles is from 3 mass % to 10 mass %.
In some embodiments, from the standpoint of more efficiently making the primary particles cationic and improving the adhesion between the primary particles and the fluorine-based polymer, and from the standpoint of the battery characteristics, the total amount of the polymer components in the negative electrode active material (i.e., the total amount of the polymer components including the cationic polymer and the fluorine-based polymer) with respect to the negative electrode active material is from 1 mass % to 30 mass %, from 5 mass % to 25 mass %, or from 10 mass % to 20 mass %.
The negative electrode active material may be granulated particles that further include other materials in addition to the primary particles and the fluorine-based polymer, and that have been granulated. Examples of these other materials are binder materials such as polyvinylidene fluoride (PVdF), styrene-butadiene rubber (SBR) and the like, and the like.
An example of the shape of the negative electrode active material is particle-shaped.
In some embodiments, the particle diameter of the negative electrode active material is not particularly limited, and, for example, from the standpoint of the battery characteristics, is from 10 μm to 100 μm, or from 10 μm to 50 μm.
In some embodiments, from the standpoint of having a better cycle characteristic, the particle diameter of the negative electrode active material is from 0.5 μm to 100 μm or from 1 μm to 50 μm.
With regard to the particle diameter of the negative electrode active material, the negative electrode active material is dispersed in a dispersion medium, and the volume-based particle size distribution is measured by using a laser diffraction particle size analyzer. The particle diameter, at which the value of the obtained volume-based cumulative particle size distribution corresponds to 50%, is used as the particle diameter of the negative electrode active material.
The method of manufacturing the negative electrode active material of the present disclosure is not particularly limited, and a known method of manufacturing a negative electrode active material can be used. The negative electrode active material of the present disclosure may manufactured by, for example, mixing a silicon material and a cationic polymer together in a solution, and thereafter, heating and kneading and forming primary particles, and thereafter, dispersing and granulating the primary particles in a solution system containing a fluorine-based polymer.
The negative electrode of the present disclosure contains the negative electrode active material of the present disclosure.
In accordance with the present disclosure, when the negative electrode is used in a solid-state battery, deterioration of the cycle characteristic is suppressed.
The negative electrode of the present disclosure is, for example, a layer that has a negative electrode collector and a negative electrode active material layer that is provided on the negative electrode collector and contains the negative electrode active material. As needed, the negative electrode active material layer may further contain at least one of a conductive material, a solid electrolyte and a binder.
Examples of the conductive material are carbon materials, conductive polymers, metal particles, and the like.
Examples of carbon materials are particle-shaped carbon materials, fiber-shaped carbon materials and the like. Examples of particle-shaped carbon materials are acetylene black (AB), ketjen black (KB) and the like. Examples of fiber-shaped carbon materials are carbon nanotubes (CNT), carbon nanofibers (CNF), VGCF, and the like.
Examples of conductive polymers are polythiophene, polyacetylene, poly(p-phenylene), polyisothianaphthene, and the like.
Examples of metal particles are particles made of nickel, copper, iron, stainless steel and the like.
Examples of the solid electrolyte are similar to those exemplified as the solid electrolytes that can be contained in the solid electrolyte layer.
Examples of the binder are rubber binders, fluoride binders, and the like. Examples of rubber binders are butadiene rubber, hydrogenated butadiene rubber, styrene-butadiene rubber (SBR), hydrogenated styrene-butadiene rubber, nitrile butadiene rubber, hydrogenated nitrile butadiene rubber, ethylene propylene rubber and the like. Examples of fluoride binders are polyvinylidene fluoride (PVDF), polyvinylidene fluoride-polyhexafluoropropylene copolymer (PVDF-HFP), polytetrafluoroethylene, fluororubbers, and the like.
The negative electrode collector performs power collection at the negative electrode layer. The negative electrode collector is disposed at a position which is at the side of the negative electrode layer opposite the side at which the solid electrolyte layer is disposed. Examples of the material of the negative electrode collector are stainless steel, copper, nickel, carbon and the like. Examples of the form of the negative electrode collector are the form of a foil and the form of a mesh.
In some embodiments, the thickness of the negative electrode active material layer is not particularly limited, and is from 0.1 μm to 100 μm, from 1 μm to 100 μm, or from 30 μm to 100 μm.
The solid-state battery of the present disclosure has the negative electrode of the present disclosure (hereinafter called negative electrode layer), a positive electrode (hereinafter called positive electrode layer), and a solid electrolyte layer.
Solid-state batteries include solid state batteries that use an inorganic solid electrolyte (i.e., whose content of electrolytic liquid that serves as the electrolyte is less than 10 mass % of the entire amount of the electrolyte).
In accordance with the present disclosure, a deterioration in the cycle characteristic is suppressed.
In
The solid-state battery may be structured such that the layer end surfaces (side surfaces) of a layered structure of a positive electrode/a solid electrolyte layer/a negative electrode are sealed by a resin. The collector of the electrode may be a structure in which a shock-absorbing layer, an elastic layer or a PTC (Positive Temperature Coefficient) thermistor layer is disposed on the surface of the collector.
Given that the power generating unit is the set of the positive electrode layer, the solid electrolyte layer and the negative electrode layer, the solid-state battery may have only one power generating unit or may have two or more power generating units. In a case in which the solid-state battery has two or more power generating units, these power generating units may be connected in series or may be connected in parallel.
The solid-state battery includes a negative electrode layer. The negative electrode layer is structured by the above-described negative electrode of the present disclosure.
The solid-state battery includes a positive electrode layer. The positive electrode layer contains a positive electrode active material.
The positive electrode layer is a layer having, for example, a positive electrode collector and a positive electrode active material layer that is provided on the positive electrode collector and contains a positive electrode active material.
In some embodiments, the positive electrode active material contains a lithium composite oxide. The lithium composite oxide may contain at least one type selected from the group consisting of F, Cl, N, S, Br and I. Further, the lithium composite oxide may have a crystal structure belonging to at least one space group selected from space groups R-3m, Immm, and P63-mmc (also called P63mc, P6/mmc). In the lithium composite oxide, the main sequence of a transition metal, oxygen and lithium may be an O2-type structure.
Examples of lithium composite oxides having a crystal structure belonging to R-3m are compounds expressed by LixMeyOαXβ (Me represents at least one type selected from the group consisting of Mn, Co, Ni, Fe, Al, Cu, V, Nb, Mo, Ti, Cr, Zr, Zn, Na, K, Ca, Mg, Pt, Au, Ag, Ru, W, B, Si and P, and X represents at least one type selected from the group consisting of F, Cl, N, S, Br and I, and 0.5≤x≤1.5, 0.5≤y≤1.0, 1≤α<2, 0<β≤1 are satisfied).
Examples of lithium composite oxides having a crystal structure belonging to Immm are composite oxides expressed by Lix1M1A12 (1.5≤x1≤2.3 is satisfied, M1 includes at least one type selected from the group consisting of Ni, Co, Mn, Cu and Fe, A1 includes at least oxygen, and the ratio of the oxygen contained in A1 is greater than or equal to 85 atom %) (a specific example is Li2NiO2), and composite oxides expressed by Lix1M1A1−x2M1Bx2O2−yA2y (0≤x2≤0.5 and 0≤y≤0.3, at least one of x2 and y is not 0, M1A represents at least one type selected from the group consisting of Ni, Co, Mn, Cu and Fe, M1B represents at least one type selected from the group consisting of Al, Mg, Sc, Ti, Cr, V, Zn, Ga, Zr, Mo, Nb, Ta and W, and A2 represents at least one type selected from the group consisting of F, Cl, Br, S and P).
Examples of lithium composite oxides having a crystal structure belonging to P63-mmc are composite oxides expressed by M1xM2yO2 (M1 represents an alkali metal (in some embodiments at least one of Na and K may be used), M2 represents a transition metal (at least one type selected from the group consisting of Mn, Ni, in some embodiments, Co and Fe may be used), and x+y satisfies 0<x+y≤2).
Examples of lithium composite oxides having an O2-type structure are composite oxides expressed by Lix[Liα(MnaCobMc)1−α]O2 (0.5<x<1.1, 0.1<α<0.33, 0.17<a<0.93, 0.03<b<0.50, 0.04<c<0.33, and M represents at least one type selected from the group consisting of Ni, Mg, Ti, Fe, Sn, Zr, Nb, Mo, W and Bi). Specific examples are Li0.744[Li0.145Mn0.625Co0.115Ni0.115]O2 and the like.
The positive electrode layer may further contain at least one of a conductive material, a solid electrolyte and a binder as needed. In some embodiments, thereamong, the positive electrode layer may contain a solid electrolyte.
Examples of the conductive material are similar to those exemplified as conductive materials that can be contained in the negative electrode layer.
In some embodiments, for example, at least one type of solid electrolyte selected from the group of solid electrolytes consisting of sulfide solid electrolytes, oxide solid electrolytes, and halide solid electrolytes is contained as the solid electrolyte.
In some embodiments, at the positive electrode layer, a form in which at least a portion of the surface of the positive electrode active material is covered by a sulfide solid electrolyte, an oxide solid electrolyte or a halide solid electrolyte is used. In some embodiments, Li6−(4−x)b(Ti1−xAlx)bF6 (0<x<1, 0<b≤1.5) [LTAF electrolyte] is used as the halide solid electrolyte that covers at least a portion of the surface of the positive electrode active material.
Examples of the binder are similar to those exemplified as binders that can be contained in the negative electrode layer.
In some embodiments, the thickness of the positive electrode active material layer is from 0.1 μm to 100 μm, from 1 μm to 100 μm, or from 30 μm to 100 μm.
The positive electrode collector carries out power collection of the positive electrode layer. The positive electrode collector is disposed at a position at the side of the positive electrode layer, which side is opposite the side at which the solid electrolyte layer is located. Examples of the material of positive electrode collector are stainless steel, aluminum, nickel, iron, titanium, carbon and the like. Examples of the form of the positive electrode collector are the form of a foil and the form of a mesh.
The solid-state battery includes a solid electrolyte layer.
In some embodiments, at least one type of solid electrolyte selected from the group of solid electrolytes consisting of sulfide solid electrolytes, oxide solid electrolytes, and halide solid electrolytes is contained as the solid electrolyte.
In some embodiments, the sulfide solid electrolyte contains sulfur (S) as the main component that is an anion element, and in some embodiments, contains, for example, the element Li, element A and the element S. Element A is at least one type selected from the group consisting of P, As, Sb, Si, Ge, Sn, B, Al, Ga and In. The sulfide solid electrolyte may further contain at least one of O and a halogen element. Examples of the halogen element (X) are F, Cl, Br, I and the like. The composition of the sulfide solid electrolyte is not particularly limited, and examples are xLi2S·(100−x)P2S5 (70≤x≤80) and yLiI·zLiBr·(100−y−z)(xLi2S·(1−x)P2S5) (0.7≤x≤0.8, 0≤y≤30, 0≤z≤30). The sulfide solid electrolyte may have the composition expressed by following general formula (1).
Li4−xGe1−xPxS4(0<x<1) formula (1)
In formula (1), at least a portion of Ge may be substituted by at least one selected from the group consisting of Sb, Si, Sn, B, Al, Ga, In, Ti, Zr, V and Nb. Further, at least a portion of P may be substituted by at least one selected from the group consisting of Sb, Si, Sn, B, Al, Ga, In, Ti, Zr, V and Nb. A portion of Li may be substituted by at least one selected from the group consisting of Na, K, Mg, Ca and Zn. A portion of S may be substituted by a halogen. The halogen is at least one of F, Cl, Br and I.
In some embodiments, the oxide solid electrolyte contains oxygen (O) as the main component that is an anion element, and, for example, may contain Li, element Q (Q represents at least one of Nb, B, Al, Si, P, Ti, Zr, Mo, W and S), and O. Examples of the oxide solid electrolyte are garnet type solid electrolytes, perovskite type solid electrolytes, NASICON type solid electrolytes, Li—P—O solid electrolytes, Li—B—O solid electrolytes, and the like. Examples of garnet type solid electrolytes are Li7La3Zr2O12, Li7−xLa3(Zr2−xNbx)O12 (0≤x≤2), Li5La3Nb2O12, and the like. Examples of perovskite type solid electrolytes are (Li,La)TiO3, (Li,La)NbO3, (Li,Sr)(Ta,Zr)O3 and the like. Examples of NASICON type solid electrolytes are Li(Al,Ti)(PO4)3, Li(Al,Ga)(PO4)3, and the like. Examples of Li—P—O solid electrolytes are Li3PO4 and LIPON (compounds in which some of the O in Li3PO4 is substituted with N). Examples of Li—B—O solid electrolytes are Li3BO3, compounds in which some of the O in Li3BO3 is substituted with C, and the like.
As the halide solid electrolyte, solid electrolytes containing Li, M and X (M represents at least one of Ti, Al and Y, and X represents F, Cl or Br) are suitable. In some embodiments, Li6−3zYzX6 (X represents Cl or Br, and z satisfies 0<z<2) and Li6−(4−x)b(Ti 1−xAlx)bF6 (0<x<1, 0<b≤1.5) are used. In some embodiments, among Li6−3zYzX6, from the standpoint of having lithium ion conductivity, Li3YX6 (X represents Cl or Br) is used, and in some embodiments, Li3YCl6 is used. In some embodiments, from standpoints such as, for example, suppressing oxidative decomposition of the sulfide solid electrolyte and the like, Li6−(4−x)b(Ti1−xAlx)bF6 (0<x<1, 0<b≤1.5) may be contained together with a solid electrolyte such as a sulfide solid electrolyte or the like.
In some embodiments, the ratio of the negative electrode active material layer and the solid electrolyte layer (negative electrode active material layer/solid electrolyte layer) is not particularly limited, but, for example, is from 85/15 to 30/70, or is from 80/20 to 40/60.
In some embodiments, the ratio of the positive electrode active material layer and the solid electrolyte layer (positive electrode active material layer/solid electrolyte layer) is not particularly limited, but, for example, is from 85/15 to 30/70, and is from 80/20 to 50/50.
The solid-state battery may further have an exterior body. The exterior body houses at least the above-described power generating unit. Examples of the exterior body are a laminate-type exterior body, a case-type exterior body, and the like.
The solid-state battery may further have a restraining member. The restraining member applies restraining pressure in the thickness direction to the positive electrode layer, the solid electrolyte layer and the negative electrode layer. In some embodiments, the restraining pressure is 0.1 MPa or more, 1 MPa or more, or 5 MPa or more. In some embodiments, the restraining pressure is 100 MPa or less, 50 MPa or less, or 20 MPa or less. In some embodiments, the restraining pressure is from 0.1 MPa to 100 MPa.
The solid-state battery of the present disclosure is a typical solid-state secondary battery (in some embodiments, a solid-state lithium ion secondary battery). The solid-state battery can be used, for example, as the power source of a vehicle, electronic equipment, electrical storage devices, and the like. Examples of vehicles are electric four-wheel vehicles, electric two-wheel vehicles, gasoline-powered vehicles, diesel-powered vehicles and the like. Examples of electric four-wheel vehicles are electric vehicles (BEVs), plug-in hybrid vehicles (PHEVs), hybrid vehicles (BEVs), and the like. Examples of electric two-wheel vehicles are electric motorbikes, electrically assisted bicycles and the like. Examples of electronic equipment are handheld devices (e.g., smartphones, tablet computers, audio players and the like), portable devices (e.g., notebook computers, CD (compact disc) players, and the like), mobile equipment (e.g., power tools, commercial video cameras, and the like), and the like. In some embodiments, thereamong, the solid-state battery of the present disclosure is used as a power source for the driving of hybrid vehicles, plug-in hybrid vehicles, and electric vehicles.
5 parts of porous Si that is a porous material, and 0.125 parts of an aqueous solution of 20 volume % poly(diallyldimethylammonium chloride) (PDADMAC) (manufactured by Sigma-Aldrich, weight average molecular weight (Mw): 200,000˜350,000) that is a cationic polymer having a quaternary ammonium salt group as the cation, were weighed-out into a mortar, and 20 mL of water was added thereto. Thereafter, by kneading the mixture while heating, water was evaporated, and primary particles containing a silicon material and a cationic polymer (more specifically, porous Si at which partial regions where coated by PDADMAC) were obtained.
Next, the primary particles that were prepared as described above were dispersed in a solution in which poly(vinylidene fluoride-co-hexafluoropropylene) (PVdF-HFP, a fluorine-based polymer containing a structural unit derived from vinylidene fluoride, KF8300 manufactured by Kureha Corporation) was dissolved in dimethyl carbonate such that the mass ratio of the PDADMAC and PVdF-HFP was 5:95. By using a spray drier, the solution was granulated, and a negative electrode active material, which was granulated particles containing primary particles containing silicon material and a cationic polymer, and a fluorine-based polymer, was obtained.
In the obtained granulated particles, the total amount of the polymer components (i.e., the total amount of the cationic polymer and the fluorine-based polymer) with respect to the granulated particles on the whole was 10 mass %, and the content of the cationic polymer (PDADMAC) with respect to the total amount of the polymer components of the granulated particles was 5 mass %.
A negative electrode active material was obtained by using the same specifications as Example 1, except that the mass ratio of PDADMAC and PVdF-HFP was made to be 10:90 (i.e., the content of the cationic polymer (PDADMAC) with respect to the total amount of the polymer components of the granulated particles was made to be 10 mass %).
A negative electrode active material was obtained by using the same specifications as Example 1, except that the added amounts of the cationic polymer and the fluorine-based polymer were adjusted such that the total amount of the polymer components (i.e., the total amount of the cationic polymer and the fluorine-based polymer) with respect to the granulated particles on the whole was 20 mass %.
A negative electrode active material was obtained by using the same specifications as Example 1, except that the mass ratio of PDADMAC and PVdF-HFP was made to be 10:90 (i.e., the content of the cationic polymer (PDADMAC) with respect to the total amount of the polymer components of the granulated particles was made to be 10 mass %), and the added amounts of the cationic polymer and the fluorine-based polymer were adjusted such that the total amount of the polymer components (i.e., the total amount of the cationic polymer and the fluorine-based polymer) with respect to the granulated particles on the whole was 20 mass %.
5 parts of porous Si that is a porous material was added into a dimethyl carbonate solution in which 0.5 parts of PVdF-HFP that is a fluorine-based polymer was dissolved, and thereafter, stirring was carried out and the porous Si was dispersed. By using a spray drier, the solution was granulated, and a negative electrode active material, which was granulated particles that contained primary particles containing a silicon material, and a fluorine-based polymer, was obtained.
In the obtained granulated particles, the total amount of the polymer components (i.e., the total amount of the cationic polymer and the fluorine-based polymer) with respect to the granulated particles on the whole was 10 mass %, and the content of the cationic polymer (PDADMAC) with respect to the total amount of the polymer components of the granulated particles was 0 mass %.
A mixed solvent of dibutylether and mesitylene, a butyl acetate solution of 5 wt % PVDF binder, VGCF that is a conduction assistant, and Li2S—P2S5 glass ceramic that is a solid electrolyte were placed in a container made of PP and stirred. Thereafter, the negative electrode active material of each example was further added thereto, and this mixture was stirred for 30 seconds by an ultrasonic disperser (UH-50 manufactured by SMT Co., Ltd.). Next, the mixture was shaken for 30 minutes by a shaker (TTM-1 manufactured by Sibata Scientific Technology Ltd.). The mixture was then coated on a Cu foil (manufactured by UACJ) by a blade method using an applicator. The coated electrode was dried for 30 minutes on a hot plate of 100° C., and a negative electrode layer was obtained.
A butyl acetate solvent, a butyl acetate solution of 5 wt % PVDF binder, LiNi1/3Co1/3Mn1/3O2 of an average particle diameter of 6 μm that is a positive electrode active material, an Li2S—P2S5 glass ceramic that is a sulfide solid electrolyte, and VGCF that is a conduction assistant were placed in a container made of PP and mixed together, and were stirred for 30 seconds by an ultrasonic disperser (UH-50 manufactured by SMT Co., Ltd.). Next, the mixture was shaken for 3 minutes by a shaker (TTM-1 manufactured by Sibata Scientific Technology Ltd.), and was further stirred for 30 seconds by the ultrasonic disperser. Thereafter, this solution was coated on an Al foil (manufactured by Showa Denko) by a blade method using an applicator. The coated electrode was dried for 30 minutes on a hot plate of 100° C., and a positive electrode layer was obtained.
A heptane solvent, a heptane solution of 5 wt % SBR binder, and an Li2S—P2S5 glass ceramic that is a solid electrolyte were added into a container made of PP, and were stirred for 30 seconds by an ultrasonic disperser (UH-50 manufactured by SMT Co., Ltd.). Next, the mixture was shaken for 30 minutes by a shaker (TTM-1 manufactured by Sibata Scientific Technology Ltd.). Thereafter, this solution was coated on an Al foil by a blade method using an applicator. The coated electrode was dried for 30 minutes on a hot plate of 100° C., and a solid electrolyte layer was obtained.
The above-described positive electrode layer and a first solid electrolyte layer were layered in that order. This layered body was set in a roll press, and was pressed with the press pressure in this first pressing step being 100 kN/cm and the pressing temperature being 165° C., and a positive electrode layered body was thereby obtained.
The above-described negative electrode layer was set in a roll press, and was pressed with the press pressure in this second pressing step being 60 kN/cm and the pressing temperature being 25° C., and a negative electrode layered body was thereby obtained.
Moreover, an Al foil serving as a peel-off sheet, an intermediate solid electrolyte layer formed on this Al foil, and the above-described negative electrode layered body that had a second solid electrolyte layer, a negative electrode active material layer and a Cu foil serving as the negative electrode collector, were layered in that order. This layered body was set in a flat, uniaxial press machine, and was temporarily pressed for 10 seconds at 100 MPa and 25° C. The Al foil was peeled-off from the intermediate solid electrolyte layer of this layered body, and a negative electrode layered body in which an intermediate solid electrolyte layer was further layered (intermediate solid electrolyte layer/second solid electrolyte layer/negative electrode active material layer/negative electrode collector layer) was obtained. Note that the negative electrode layered body and the positive electrode layered body were fabricated such that the surface area of the negative electrode layered body was larger than the surface area of the positive electrode layered body.
The above-described positive electrode layered body, and the negative electrode layered body in which the first solid electrolyte layer was further layered, were layered in that order. This layered body (positive electrode layered body/first solid electrolyte layer/intermediate solid electrolyte layer/second solid electrolyte layer/negative electrode active material layer/negative electrode collector layer) was set in a flat, uniaxial press machine, and was pressed for one minute with the press pressure in this third pressing step being 200 MPa and the pressing temperature being 120° C. A solid-state battery was thereby obtained.
The solid-state batteries fabricated by using the negative electrode active materials of the respective examples were restrained at a predetermined restraining pressure by using a restraining jig, and were charged at a constant current at 1/10 C until 4.55 V, and thereafter, were discharged at 1 C to 3.0 V, and constant current-constant voltage charging was carried out at 1/3 C to 4.35 V, and constant current-constant voltage discharging was carried out at 1/3 C until 3.00 V. Thereafter, a constant current charging/discharging test was repeated 200 times at 2 C as a cycling test. The maintenance rate from the initial discharge capacity of the cycling test that was obtained was calculated as the discharge capacity maintenance rate after 200 cycles. The discharge capacity maintenance rates after 200 cycles in the Examples were relative values with respect to the discharge capacity maintenance rate after 200 cycles of Comparative Example 1.
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| Number | Date | Country | Kind |
|---|---|---|---|
| 2023-016475 | Feb 2023 | JP | national |
