Patent Application
20230246183
Embodiments of the present invention relate to a secondary battery including a positive electrode active material and a manufacturing method thereof. Furthermore, one embodiment of the present invention relates to a portable information terminal, a vehicle, and the like each including a secondary battery.
One embodiment of the present invention relates to an object, a method, or a manufacturing method. The present invention relates to a process, a machine, manufacture, or a composition of matter. One embodiment of the present invention relates to a semiconductor device, a display device, a light-emitting device, a power storage device, a lighting device, an electronic device, or a manufacturing method thereof.
Note that electronic devices in this specification generally refer to devices including power storage devices, and electro-optical devices including power storage devices, information terminal devices including power storage devices, and the like are all electronic devices.
Note that power storage devices in this specification generally refer to elements and devices having a function of storing power. For example, power storage devices (also referred to as secondary batteries) such as a lithium-ion secondary battery, a lithium-ion capacitor, and an electric double layer capacitor are included.
In recent years, a variety of power storage devices such as lithium-ion secondary batteries, lithium-ion capacitors, and air batteries have been actively developed. In particular, demand for lithium-ion secondary batteries with high output and high energy density has rapidly grown with the development of the semiconductor industry, for portable information terminals such as mobile phones, smartphones, and laptop computers, portable music players, digital cameras, medical equipment, next-generation clean energy vehicles such as hybrid electric vehicles (HVs), electric vehicles (EVs), and plug-in hybrid electric vehicles (PHVs), and the like, and the lithium-ion secondary batteries are essential as rechargeable energy supply sources for today's information society.
Thus, improvement of positive electrode active materials has been studied to increase the cycle performance and the capacity of lithium-ion secondary batteries (e.g., Patent Document 1 and Non-Patent Document 1).
In addition, crystal structures of positive electrode active materials have also been studied (Non-Patent Document 2 to Non-Patent Document 4). In addition, physical properties of fluorides such as fluorite (calcium fluoride) have long been studied (Non-Patent Document 5). Furthermore, analysis of X-ray diffraction (XRD) of crystal structures of positive electrode active materials with the use of the ICSD (Inorganic Crystal Structure Database) described in Non-Patent Document 6 have been studied.
The performances required for power storage devices are safe operation and longer-term reliability under various environments, for example.
An object of one embodiment of the present invention is to provide a positive electrode active material with high charge and discharge capacity. Another object is to provide a positive electrode active material with high charge and discharge voltage. Another object is to provide a positive electrode active material which hardly deteriorates. Another object is to provide a novel positive electrode active material. Another object is to provide a secondary battery with high charge and discharge capacity. Another object is to provide a secondary battery with high charge and discharge voltage. Another object is to provide a highly safe or reliable secondary battery. Another object is to provide a secondary battery which hardly deteriorates. Another object is to provide a long-life secondary battery. Another object is to provide a novel secondary battery.
Another object of one embodiment of the present invention is to provide a novel material, a novel active material, a novel power storage device, or a manufacturing method thereof.
Note that the description of these objects does not preclude the existence of other objects. One embodiment of the present invention does not have to achieve all the objects. Other objects can be derived from the description of the specification, the drawings, and the claims.
One embodiment of the present invention is a secondary battery with a layered crystal structure, including a composite oxide containing at least lithium and an oxide containing zirconium in at least part of the surface of the composite oxide. The configuration disclosed in this specification is a secondary battery including a positive electrode and a negative electrode. The positive electrode includes a positive electrode active material containing lithium and cobalt, and the positive electrode active material contains at least one or more of fluorine, zirconium, nickel, magnesium, aluminum, titanium, lanthanum, and calcium. The positive electrode active material includes a plurality of projections, and the projection contains a zirconium compound. The projection contains zirconium oxide in a polycrystalline state.
In the above configuration, the projection is a zirconium compound, e.g., zirconium dioxide or lithium zirconate. Note that zirconium oxide typified by zirconium dioxide is also referred to as zirconia. Furthermore, the projection has crystallinity and contains zirconium oxide in a polycrystalline state. The positive electrode active material disclosed in this specification may also be referred to as a particulate material where the surface of mother particles is covered with daughter particles (zirconium oxide) in a non-uniform state. The coverage rate with the daughter particles is less than 50%, and the surface of the mother particles that is not covered is exposed. Note that in this specification, even if the projection does not have a function such as lithium ion insertion or extraction in charging or discharging, as a positive electrode active material, the projection is believed to reduce deterioration caused by repeated charge and discharge cycles and contribute to the structure preservation of the positive electrode active material as a whole and thus is regarded as part of the positive electrode active material and referred to as part of the positive electrode active material.
In each of the above configurations, the concentration of fluorine in the positive electrode active material is higher in a surface portion than in a central portion of the positive electrode active material. This concentration distribution of fluorine is attributable to the fact that fluorine is added in two stages, i.e., after the formation of particles containing lithium and cobalt, in a formation method of the positive electrode active material.
In each of the above configurations, it is preferable that the positive electrode active material containing fluorine, lithium, zirconium, and cobalt be formed by a solid-phase method or a sol-gel method.
A formation method to obtain the above configurations is also one aspect of the present invention; one of the configuration is a method for forming a positive electrode active material including a first step of forming a first mixture where a first material, a second material, and a third material are mixed, a second step of forming a second mixture by heating the first mixture under a first temperature condition, a third step of forming a third mixture where the second mixture and a fourth material are mixed, a fourth step of forming a fourth mixture where the third mixture, a fifth material, and a sixth material are mixed, and a fifth step of forming a fifth mixture by heating the fourth mixture under a second temperature condition. The first material is a halogen compound containing lithium, the second material contains magnesium, the third material is a metal oxide containing lithium and cobalt, the fourth material contains nickel, the heating in the second step and the fifth step is performed in an atmosphere containing oxygen, the first temperature condition is in a temperature range of 600° C. to 950° C. inclusive, and performed for one hour to 100 hours inclusive, and the second temperature condition is in a temperature range of 600° C. to 900° C. inclusive, and performed for one hour to 100 hours inclusive.
In the above formation method, the fifth material contains aluminum and the sixth material contains zirconium. In addition, in the above formation method, any one or more of dry mixing, wet mixing, a solid-phase method, a sol-gel method, a sputtering method, a mechanochemical method, and a CVD method can be used as a mixing method for obtaining the first mixture, the second mixture, the third mixture, the fourth mixture, or the fifth mixture.
According to one embodiment of the present invention, a positive electrode active material with high energy density and high charge and discharge capacity can be provided. Furthermore, a positive electrode active material with high energy density and high charge and discharge voltage can be provided. Furthermore, a positive electrode active material which hardly deteriorates can be provided. Furthermore, a novel positive electrode active material can be provided. Furthermore, a secondary battery with high charge and discharge capacity can be provided. Furthermore, a secondary battery with high charge and discharge voltage can be provided. Furthermore, a highly safe or reliable secondary battery can be provided. Furthermore, a secondary battery which hardly deteriorates can be provided. Furthermore, a long-life secondary battery can be provided. Furthermore, a novel secondary battery can be provided.
According to one embodiment of the present invention, a novel material, a novel active material, a novel power storage device, or a manufacturing method thereof can be provided.
Note that the description of the effects does not preclude the existence of other effects. One embodiment of the present invention does not have to have all of these effects. Other effects will be apparent from the descriptions of the specification, the drawings, the claims, and the like, and other effects can be derived from the descriptions of the specification, the drawings, the claims, and the like.
Embodiments of the present invention will be described in detail below with reference to the drawings. Note that the present invention is not limited to the following description, and it is readily understood by those skilled in the art that modes and details of the present invention can be modified in various ways. In addition, the present invention should not be construed as being limited to the description of the following embodiments.
A secondary battery includes a positive electrode and a negative electrode, for example. A positive electrode active material is a material included in the positive electrode. The positive electrode active material is a substance that performs a reaction contributing to the charge and discharge capacity, for example. Note that the positive electrode active material may partly contain a substance that does not contribute to the charge and discharge capacity.
In this specification and the like, the positive electrode active material of one embodiment of the present invention is expressed as a positive electrode material, a secondary battery positive electrode material, a composite oxide, or the like in some cases. In this specification and the like, the positive electrode active material of one embodiment of the present invention preferably contains a compound. In this specification and the like, the positive electrode active material of one embodiment of the present invention preferably contains a composition. In this specification and the like, the positive electrode active material of one embodiment of the present invention preferably contains a composite.
In this specification and the like, uneven distribution refers to a phenomenon in which in a solid made of a plurality of elements (e.g., A, B, and C), a certain element (e.g., B) is spatially non-uniformly distributed.
In this specification and the like, a surface portion of a particle of an active material or the like is a region that is less than or equal to 50 nm, preferably less than or equal to 35 nm, further preferably less than or equal to 20 nm, most preferably less than or equal to 10 nm inward from the surface, for example. A plane generated by a split or a crack may also be referred to as a surface. In addition, a region whose position is deeper than that of the surface portion is referred to as an inner portion. In this specification and the like, a grain boundary refers to a portion where particles adhere to each other, a portion where crystal orientation changes inside a particle (including a central portion), a portion including many defects, a portion with a disordered crystal structure, or the like. The grain boundary can be regarded as a plane defect. The vicinity of a grain boundary refers to a region positioned within 10 nm from the grain boundary. In this specification and the like, particles are not necessarily spherical (with a circular cross section). Other examples of the cross-sectional shapes of particles include an ellipse, a rectangle, a trapezoid, a conical or pyramidal shape, a quadrilateral with rounded corners, and an asymmetrical shape, and a particle may have an indefinite shape.
In this specification and the like, the Miller index is used for the expression of crystal planes and orientations. An individual plane that shows a crystal plane is denoted by “( )”. In the crystallography, a bar is placed over a number in the expression of crystal planes, orientations, and space groups; in this specification and the like, because of application format limitations, crystal planes, orientations, and space groups are sometimes expressed by placing a minus sign (−) in front of the number instead of placing a bar over the number.
In this specification and the like, a layered rock-salt crystal structure of a composite oxide containing lithium and a transition metal refers to a crystal structure in which a rock-salt ion arrangement where cations and anions are alternately arranged is included and lithium and the transition metal are regularly arranged to form a two-dimensional plane, so that lithium can be diffused two-dimensionally. Note that a defect such as a cation or anion vacancy may exist. In the layered rock-salt crystal structure, strictly, a lattice of a rock-salt crystal is distorted in some cases.
In this specification and the like, a rock-salt crystal structure refers to a structure in which cations and anions are alternately arranged. Note that a cation or anion vacancy may exist.
A material with a layered rock-salt crystal structure, such as lithium cobalt oxide (LiCoO2), is known to have a high discharge capacity and excel as a positive electrode active material of a secondary battery. As an example of the material with a layered rock-salt crystal structure, a composite oxide represented by LiMO2 is given. The remaining amount of lithium that can be inserted into and extracted from a positive electrode active material is represented by x in a compositional formula, e.g., LixCoO2 or LixMO2. In this specification, LixCoO2 can be read as LixMO2, as appropriate. In the case of a positive electrode active material in a secondary battery, x can be represented by charge capacity/theoretical capacity. For example, when a secondary battery using LiCoO2 as a positive electrode active material is charged to 219.2 mAh/g, the positive electrode active material can be represented by Li0.8CoO2, i.e., x=0.8. Note that “x in LixCoO2 is small” means, for example, 0.1≤x≤0.24.
It is known that the Jahn-Teller effect in a transition metal compound varies in degree according to the number of electrons in the d orbital of the transition metal.
In a compound containing nickel, distortion is likely to be caused because of the Jahn-Teller effect in some cases. Accordingly, when charging and discharging that make x smaller in LixNiO2 are performed, the crystal structure might be broken because of the distortion. The influence of the Jahn-Teller effect is suggested to be small in LiCoO2, and LixCoO2 with smaller x is preferable because the tolerance is higher in some cases.
Positive electrode active materials are described with reference to
Lithium cobalt oxide (LiCoO2) can have varied crystal structures depending on the occupancy rate x of Li in the lithium site. A change in the crystal structure of the conventional positive electrode active material is shown in
In
Conventional lithium cobalt oxide with x of approximately 0.5 is known to have an improved symmetry of lithium and have a monoclinic crystal structure belonging to the space group P2/m. This structure includes one CoO2 layer in a unit cell. Thus, this crystal structure is referred to as an O1 type structure or a monoclinic O1 type structure in some cases. A positive electrode active material with x of 0 has a crystal structure belonging to the space group P-3m1 and includes one CoO2 layer in a unit cell. Hence, this crystal structure is referred to as an O1 type crystal structure in some cases.
Conventional lithium cobalt oxide with x of approximately 0.24 has the crystal structure belonging to the space group R-3m. This structure can also be regarded as a structure in which CoO2 structures such as P-3m1 (O1) and LiCoO2 structures such as R-3m (O3) are alternately stacked. Thus, this crystal structure is referred to as an H1-3 type crystal structure in some cases. The number of cobalt atoms per unit cell in the actual H1-3 type crystal structure is twice that in other structures. However, in this specification including
For the H1-3 type crystal structure, as disclosed in Non-Patent Document 3, the coordinates of cobalt and oxygen in the unit cell can be expressed as follows, for example: Co (0, 0, 0.42150±0.00016), O1 (0, 0, 0.27671±0.00045), and O2 (0, 0, 0.11535±0.00045). Note that O1 and O2 are each an oxygen atom. In this manner, the H1-3 type crystal structure is represented by a unit cell including one cobalt and two oxygen. Meanwhile, the O3′ type crystal structure of one embodiment of the present invention is preferably represented by a unit cell including one cobalt and one oxygen, as described later. This means that the symmetry of cobalt and oxygen differs between the O3′ type crystal structure and the H1-3 type structure, and the amount of change from the O3 structure is smaller in the O3′ type crystal structure than in the H1-3 type structure. A preferred unit cell for representing a crystal structure in a positive electrode active material can be selected by Rietveld analysis of XRD patterns, for example. In this case, a unit cell is selected such that the value of GOF (goodness of fit) is small.
When charge and discharge are repeated so that x in LixCoO2 becomes 0.24 or less, the crystal structure of lithium cobalt oxide repeatedly changes between the H1-3 type crystal structure and the R-3m (O3) structure in a discharged state (i.e., an unbalanced phase change).
However, there is a large shift in the CoO2 layers between these two crystal structures. As denoted by the dotted line and the arrow in
A difference in volume is also large. When the H1-3 type crystal structure and the 03 type crystal structure in a discharged state contain the same number of cobalt atoms, these structures have a difference in volume of 3.0% or more.
In addition, a structure in which CoO2 layers are arranged continuously, such as the structure belonging to P-3m1 (O1), included in the H1-3 type crystal structure is highly likely to be unstable.
Accordingly, the repeated charge and discharge that make x be 0.24 or less gradually break the crystal structure of lithium cobalt oxide. The broken crystal structure triggers deterioration of the cycle performance. This is because the broken crystal structure has a smaller number of sites where lithium can exist stably and makes it difficult to insert and extract lithium.
Anions of a layered rock-salt crystal and anions of a rock-salt crystal have a cubic close-packed structure (face-centered cubic lattice structure). Anions of an O3′ type crystal are also presumed to form a cubic close-packed structure. When there crystals are in contact with the layered rock-salt crystal and the rock-salt crystal, there is a crystal plane at which orientations of cubic close-packed structures composed of anions are aligned. Note that a space group of the layered rock-salt crystal and the O3′ type crystal structure is R-3m, which is different from a space group Fm-3m of a rock-salt crystal (a space group of a general rock-salt crystal) and a space group Fd-3m of a rock-salt crystal (a space group of a rock-salt crystal having the simplest symmetry); thus, the Miller index of the crystal plane satisfying the above conditions in the layered rock-salt crystal and the O3′ type crystal structure is different from that in the rock-salt crystal. In this specification, a state where the orientations of the cubic close-packed structures composed of anions in the layered rock-salt crystal, the O3′ type crystal structure, and the rock-salt crystal are aligned is sometimes referred to as a state where crystal orientations are substantially aligned.
The orientations of crystals in two regions being substantially aligned with each other can be judged, for example, from a TEM (Transmission Electron Microscope) image, a STEM (Scanning Transmission Electron Microscope) image, a HAADF-STEM (High-Angle Annular Dark Field Scanning TEM) image, an ABF-STEM (Annular Bright-Field Scanning Transmission Electron Microscopy) image, or the like. X-ray diffraction (XRD), electron diffraction, neutron diffraction, and the like can also be used for judging. In a TEM image and the like, alignment of cations and anions can be observed as repetition of bright lines and dark lines. When the orientations of cubic close-packed structures in the layered rock-salt crystal and the rock-salt crystal are aligned, a state where an angle made by the repetition of bright lines and dark lines in the crystals is less than or equal to 5°, preferably less than or equal to 2.5° can be observed. Note that in a TEM image and the like, a light element typified by oxygen or fluorine cannot be clearly observed in some cases; in such a case, alignment of orientations can be judged by arrangement of metal elements.
In this specification and the like, a theoretical capacity of a positive electrode active material refers to the amount of electricity obtained when all lithium that can be inserted and extracted and is contained in the positive electrode active material is extracted. For example, the theoretical capacity of LiCoO2 is 274 mAh/g, the theoretical capacity of LiNiO2 is 274 mAh/g, and the theoretical capacity of LiMn2O4 is 148 mAh/g.
Lithium cobalt oxide to be used for a positive electrode, which has been appropriately synthesized and almost satisfies the stoichiometric proportion, is LiCoO2 with x=1. For a secondary battery after its discharge ends, it can be said that lithium cobalt oxide is LiCoO2 or x=1. Here, “discharge ends” means that a voltage becomes 3.0 V or 2.5 V or lower at a current of 100 mAh/g or lower, for example. Charge capacity and/or discharge capacity used for calculation of x in LixCoO2 is preferably measured under the condition where there is no influence or small influence of a short circuit and/or decomposition of an electrolyte. For example, data of a secondary battery that is measured while a sudden change in capacity that seems to be derived from a short circuit should not be used for calculation of x.
The discharging rate refers to the relative ratio of current at the time of discharging to battery capacity and is expressed in a unit C. A current corresponding to 1 C in a battery with a rated capacity X (Ah) is X (A). The case where discharging is performed at a current of 2X (A) is rephrased as to perform discharging at 2 C, and the case where discharging is performed at a current of X/5 (A) is rephrased as to perform discharging at 0.2 C. The same applies to the charging rate; the case where charging is performed at a current of 2X (A) is rephrased as to perform charging at 2 C, and the case where charging is performed at a current of X/5 (A) is rephrased as to perform charging at 0.2 C.
Constant-current charging refers to, for example, a method for performing charging at a constant charging rate. Constant voltage charging refers to a charging method in which voltage is fixed when reaching the upper voltage limit, for example. Constant-current discharging refers to, for example, a method for performing discharging at a constant discharging rate.
In this specification and the like, an approximate value of a given value A refers to a value greater than or equal to 0.9 A and less than or equal to 1.1 A.
In this specification and the like, an example in which a lithium metal is used as a counter electrode in a secondary battery using a positive electrode and a positive electrode active material of one embodiment of the present invention is described in some cases; however, the secondary battery of one embodiment of the present invention is not limited to this example. Another material such as graphite or lithium titanate may be used as a negative electrode, for example. The properties of the positive electrode and the positive electrode active material of one embodiment of the present invention, such as a crystal structure unlikely to be broken by repeated charging and discharging and excellent cycle performance, are not affected by the material of the negative electrode. The secondary battery of one embodiment of the present invention using a lithium counter electrode is charged and discharged at a voltage higher than a general charge voltage of approximately 4.7 V in some cases; however, charging and discharging may be performed at a lower voltage. Charging and discharging at a lower voltage may lead to the cycle performance better than that described in this specification and the like.
In this embodiment, a positive electrode active material of one embodiment of the present invention will be described with reference to
The positive electrode active material of one embodiment of the present invention has a structure in which the surface of the positive electrode active material is prevented from being reduced by reacting with an electrolyte solution, to improve its reliability. Part of the positive electrode active material surface is provided with projections through a sol-gel method so that the area where the positive electrode active material and the electrolyte solution react is reduced and decomposition of the electrolyte solution or reduction of the positive electrode active material are suppressed, whereby the cycle performance is improved.
A positive electrode active material 100, which is a single particle, includes a plurality of projections. A schematic view of the single particle of the positive electrode active material 100 including projections 101, 102, and 103, which are varied in shape, is shown in
An STEM photograph of the periphery of the projection 103 is shown in
For comparison, the quantitative values of elements (carbon, nitrogen, oxygen, fluorine, Zr, Al, Si, Ti, Co, Ni, Cu, and Ga) detected in Area 1 and Area 2, which is an area inside the positive electrode active material particle in
The results indicate that the projection 103 includes zirconium oxide. The projection 103 also includes cobalt. There are more fluorine, silicon, and Cu included in the projection 103 than in Area 2, the area inside the positive electrode active material particle. Cobalt and aluminum are detected more in Area 2, the area inside the positive electrode active material particle, than in Area 1. As indicated by
The result of electron diffraction with the use of HD-2700 produced by Hitachi High-Technologies Corporation in Area 1 is shown in
The XPS analysis results of the obtained positive electrode active material are shown in
The results in
A region from the surface to a depth of approximately 2 nm to 8 nm inclusive (normally, approximately 5 nm) can be analyzed by X-ray photoelectron spectroscopy (XPS); thus, the concentration of each element in approximately half of the surface portion can be quantitatively analyzed. The bonding states of the elements can be analyzed by narrow scanning. Note that the quantitative accuracy of XPS is approximately ±1 atomic % in many cases. The lower detection limit is approximately 1 atomic % but depends on the element.
In the case where XPS analysis is performed, monochromatic aluminum can be used as an X-ray source, for example. The output can be set to 1486.6 eV, for example. An extraction angle is, for example, 45°. With such measurement conditions, a region from the surface to a depth of approximately 2 nm to 8 nm inclusive (normally, approximately 5 nm) can be analyzed, as mentioned above. Note that Quantera2 produced by ULVAC-PHI, Inc. was used for XPS analysis.
In addition, when the positive electrode active material of one embodiment of the present invention is analyzed by XPS, a peak indicating the bonding energy of fluorine with another element (Binding Energy) is preferably at greater than or equal to 682 eV and less than 685 eV, further preferably approximately 684.3 eV, as shown in
Furthermore, when the positive electrode active material of one embodiment of the present invention is analyzed by XPS, a peak indicating the bonding energy of magnesium with another element is preferably at greater than or equal to 1302 eV and less than 1304 eV, further preferably approximately 1303 eV, as shown in
In addition, data related to aluminum, from the XPS analysis of the positive electrode active material of one embodiment of the present invention, is shown in
The concentrations of the added elements that preferably exist in the surface portion in a large amount, such as magnesium, aluminum, titanium, and the like measured by XPS or the like are preferably higher than the concentrations measured by ICP-MS (inductively coupled plasma mass spectrometry), GD-MS (glow discharge mass spectrometry), or the like.
When a cross section of the positive electrode active material is exposed by processing and analyzed by TEM-EDX, the concentrations of magnesium, aluminum, and titanium in the surface portion are preferably higher than those in the inner portion. For example, in the TEM-EDX analysis, the magnesium concentration preferably attenuates, at a depth of 1 nm from a point where the concentration reaches a peak, to less than or equal to 60% of the peak concentration. In addition, the magnesium concentration preferably attenuates, at a depth of 2 nm from the point where the concentration reaches the peak, to less than or equal to 30% of the peak concentration. The processing can be performed with an FIB (focused ion beam) system, for example.
In the XPS (X-ray photoelectron spectroscopy) analysis, the number of magnesium atoms is preferably greater than or equal to 0.4 times and less than or equal to 1.5 times the number of cobalt atoms. In the ICP-MS analysis, the atomic ratio of magnesium to cobalt (Mg/Co) is preferably greater than or equal to 0.001 and less than or equal to 0.06.
By contrast, it is preferable that nickel not be unevenly distributed in the surface portion but be distributed in the entire positive electrode active material.
The positive electrode active material 100 has the O3′ type crystal structure. In the positive electrode active material 100 of one embodiment of the present invention shown in
The positive electrode active material of one embodiment of the present invention has a small change in the crystal structure and a small difference in volume per the same number of transition metal atoms between a sufficiently discharging state and a high-voltage charging state.
The positive electrode active material 100 in
Note that in the O3′ type crystal structure, an ion of cobalt, nickel, magnesium, or the like occupies a site coordinated to six oxygen atoms. Note that in the O3′ type crystal structure, a light element such as lithium sometimes occupies a site coordinated to four oxygen atoms.
Although a chance of the existence of lithium is the same in all lithium sites in the O3′ type crystal structure in
The O3′ type crystal structure can also be regarded as a crystal structure that contains Li between layers at random but is similar to a CdCl2 type crystal structure. The crystal structure similar to the CdCl2 type crystal structure is close to a crystal structure of lithium nickel oxide when charged up to a charge depth of Li0.06NiO2; however, pure lithium cobalt oxide or a layered rock-salt positive electrode active material containing a large amount of cobalt is known not to have the CdCl2 type crystal structure in general.
In the positive electrode active material 100 of one embodiment of the present invention, a change in the crystal structure caused by extraction of a large amount of lithium in a state where x in LixCoO2 is 0.24 or less is smaller than that in a conventional positive electrode active material. For example, as denoted by the dotted lines in
As described above, in the positive electrode active material 100 of one embodiment of the present invention, a change in the crystal structure caused when x in LxCoO2 is small, i.e., when a large amount of lithium is extracted, is smaller than that in a conventional positive electrode active material. In addition, a change in the volume in the case where the positive electrode active materials having the same number of cobalt atoms are compared is inhibited. Thus, the crystal structure of the positive electrode active material 100 is less likely to break even when charge and discharge are repeated so that x becomes 0.24 or less. Therefore, a decrease in charge and discharge capacity of the positive electrode active material 100 in charge and discharge cycles is inhibited. Furthermore, the positive electrode active material 100 can stably use a large amount of lithium than a conventional positive electrode active material and thus has large discharge capacity per weight and per volume. Thus, with the use of the positive electrode active material 100, a secondary battery with large discharge capacity per weight and per volume can be fabricated. Note that the positive electrode active material 100 is confirmed to have the O3′ type crystal structure in some cases when x in LixCoO2 is greater than or equal to 0.15 and less than or equal to 0.24, and is assumed to have the O3′ type crystal structure even when x is greater than 0.24 and less than or equal to 0.27. However, the crystal structure is influenced by not only x in LixCoO2 but also the number of charge and discharge cycles, a charge current and a discharge current, temperature, an electrolyte, and the like, so that the range of x is not limited to the above. Hence, when x in LixCoO2 in the positive electrode active material 100 is greater than 0.1 and less than or equal to 0.24, not all of the inner portion 100b of the positive electrode active material 100 has to have the O3′ type crystal structure. Another crystal structure may be contained, or part of the inner portion 100b may be amorphous. In order to make x in LixCoO2 small, charge at a high charge voltage is necessary in general. Therefore, the state where x in LixCoO2 is small can be rephrased as a state where charge at a high charge voltage has been performed. For example, when CC/CV charge is performed at 25° C. and 4.6 V or higher using the potential of a lithium metal as a reference, the H1-3 type crystal structure appears in a conventional positive electrode active material. Therefore, a charge voltage of 4.6 V or higher can be regarded as a high charge voltage with reference to the potential of a lithium metal. In this specification and the like, unless otherwise specified, charge voltage is shown with reference to the potential of a lithium metal. Thus, the positive electrode active material 100 of one embodiment of the present invention is preferable because the crystal structure with the symmetry of R-3m O3 can be maintained even when charge at a high charge voltage of 4.6 V or higher is performed at 25° C., for example. Moreover, the positive electrode active material 100 of one embodiment of the present invention is preferable because the O3′ type crystal structure can be obtained when charge at a higher charge voltage, e.g., a voltage higher than or equal to 4.65 V and lower than or equal to 4.7 V is performed at 25° C.
In the positive electrode active material 100, when the charge voltage is increased, the H1-3 type crystal is eventually observed in some cases. As described above, the crystal structure is influenced by the number of charge and discharge cycles, a charge current and a discharge current, an electrolyte, and the like, so that the positive electrode active material 100 of one embodiment of the present invention sometimes has the O3′ type crystal structure even at a lower charge voltage, e.g., a charge voltage of higher than or equal to 4.5 V and lower than 4.6 V at 25° C.
Note that in the case where graphite is used as a negative electrode active material in a secondary battery, for example, the voltage of the secondary battery is lower than the above-mentioned voltages by the potential of graphite. The potential of graphite is approximately 0.05 V to 0.2 V with reference to the potential of a potential lithium metal. Therefore, for a secondary battery using graphite as a negative electrode active material, a similar crystal structure is obtained at a voltage corresponding to a difference between the above-described voltage and the potential of the graphite.
In the positive electrode active material 100, the O3 type crystal structure and the O3′ type crystal structure in a discharged state that contain the same number of cobalt atoms have a difference in volume of 2.5% or less, specifically 2.2% or less, typically 1.8%. As shown in
A slight amount of an additive, e.g., magnesium, existing between the CoO2 layers, i.e., in lithium sites at random, has an effect of inhibiting a deviation in the CoO2 layers. Thus, when magnesium exists between the CoO2 layers, the O3′ type crystal structure is likely to be formed.
However, cation mixing occurs when the heat treatment temperature is excessively high, so that the additive, e.g., magnesium, is highly likely to enter the cobalt sites. Magnesium existing in the cobalt sites does not have an effect of maintaining the R-3m structure in a state where x in LixCoO2 is 0.24 or less. Furthermore, when the heat treatment temperature is excessively high, adverse effects such as reduction of cobalt to have a valence of two and transpiration of lithium are concerned.
In view of the above, a halogen compound such as a fluorine compound is preferably added to lithium cobalt oxide before the heat treatment for distributing magnesium in the surface portion. The addition of the halogen compound decreases the melting point of lithium cobalt oxide. The decrease in the melting point makes it easier to distribute magnesium in the surface portion at a temperature at which the cation mixing is unlikely to occur. Furthermore, it is expected that the existence of the fluorine compound can improve corrosion resistance to hydrofluoric acid generated by decomposition of an electrolyte solution.
When the magnesium concentration is higher than or equal to a predetermined value, the effect of stabilizing a crystal structure becomes small in some cases. This is probably because magnesium enters the cobalt sites in addition to the lithium sites. The number of magnesium atoms in the positive electrode active material of one embodiment of the present invention is preferably 0.001 to 0.1 times, preferably larger than 0.01 and less than 0.04, still further preferably approximately 0.02 the number of atoms of transition metal. The magnesium concentration described here may be a value obtained by element analysis on the entire particle of the positive electrode active material using ICP-MS or the like, or may be a value based on the ratio of the raw materials mixed in the forming process of the positive electrode active material, for example.
To lithium cobalt oxide, as a metal other than cobalt (hereinafter, a metal Z), one or more metals selected from nickel, aluminum, manganese, titanium, vanadium, and chromium may be added, for example, and in particular, at least one of nickel and aluminum is preferably added. In some cases, manganese, titanium, vanadium, and chromium are likely to have a valence of four stably and thus contribute highly to a stable structure. The addition of the metal Z may enable the positive electrode active material of one embodiment of the present invention to have a more stable crystal structure in the state where x in LixCoO2 is 0.24 or less, for example. Here, in the positive electrode active material of one embodiment of the present invention, the metal Z is preferably added at a concentration that does not greatly change the crystallinity of the lithium cobalt oxide. For example, the metal Z is preferably added at an amount with which the aforementioned Jahn-Teller effect is not exhibited.
As shown in the legend in
The oxygen atoms in
The apparatus and conditions adopted in the XRD measurement are not particularly limited. For example, D8 ADVANCE manufactured by Bruker Corporation can be used as the measurement apparatus. The following measurement conditions can be employed, for example: with use of the CuKαX ray source and powder setting, the sample is sprinkled on a reflection-free silicon plate to which grease is applied, and the measurement plane is aligned with the measurement plane required by the apparatus to be measured.
As shown in
It can be said that the positions of the XRD diffraction peaks exhibited by the crystal structure with x being 1 and the crystal structure with x being 0.24 or less are close to each other. More specifically, it can be said that a difference in the positions of two or more, preferably three or more of the main diffraction peaks between the crystal structure with x being 1 and the crystal structure with x being 0.24 or less is 2θ=0.7 or less, preferably 2θ=0.5 or less.
Although the positive electrode active material 100 of one embodiment of the present invention has the O3′ type crystal structure at the time of high-voltage charging, not all of the particle inside necessarily has the O3′ type crystal structure. Another crystal structure may be contained, or part of the particle inside may be amorphous. Note that when the XRD patterns are analyzed by the Rietveld analysis, the O3′ type crystal structure preferably accounts for more than or equal to 50 wt %, further preferably more than or equal to 60 wt %, and still further preferably more than or equal to 66 wt %. The positive electrode active material in which the O3′ type crystal structure accounts for more than or equal to 50 wt %, further preferably more than or equal to 60 wt %, still further preferably more than or equal to 66 wt % can have sufficiently good cycle performance.
Furthermore, even after 100 or more cycles of charging and discharging, the O3′ type crystal structure preferably accounts for more than or equal to 35 wt %, further preferably more than or equal to 40 wt %, still further preferably more than or equal to 43 wt % when the Rietveld analysis is performed.
The crystallite size of the O3′ type crystal structure included in the positive electrode active material particle does not decrease to less than approximately one-twentieth that of LiCoO2 (O3) in the discharged state. Thus, a clear peak of the O3′ type crystal structure can be observed when x in LixCoO2 is small, even under the same XRD measurement conditions as those of a positive electrode before the charge and discharge. In contrast, simple LiCoO2 has a small crystallite size and a broad, small peak even when it can have a structure part of which is similar to the O3′ type crystal structure. The crystallite size can be calculated from the half width of the XRD peak.
As described above, the influence of the Jahn-Teller effect is preferably small in the positive electrode active material of one embodiment of the present invention. It is preferable that the positive electrode active material of one embodiment of the present invention have a layered rock-salt crystal structure and mainly contain cobalt as a transition metal. The positive electrode active material of one embodiment of the present invention may contain the above-described metal Z in addition to cobalt as long as the influence of the Jahn-Teller effect is small.
In this embodiment, an example of a method of forming a positive electrode active material of one embodiment of the present invention will be described with reference to
First, in Step S11 in
As the lithium source, for example, lithium carbonate, lithium hydroxide, lithium nitrate, lithium fluoride, or the like can be used.
As the transition metal M, a metal that can form, together with lithium, a composite oxide having the layered rock-salt structure belonging to the space group R-3m is preferably used. For example, at least one of manganese, cobalt, and nickel can be used. That is, as the transition metal M source, only cobalt may be used; only nickel may be used; two types of metals of cobalt and manganese or cobalt and nickel may be used; or three types of metals of cobalt, manganese, and nickel may be used.
When metals that can form a layered rock-salt composite oxide are used, cobalt, manganese, and nickel are preferably mixed at the ratio at which the composite oxide can have a layered rock-salt crystal structure. In addition, aluminum may be added to the transition metal as long as the composite oxide can have a layered rock-salt crystal structure.
As the transition metal M source, an oxide or a hydroxide of the metal described as an example of the transition metal M, or the like can be used. As a cobalt source, for example, cobalt oxide, cobalt hydroxide, or the like can be used. As a manganese source, manganese oxide, manganese hydroxide, or the like can be used. As a nickel source, nickel oxide, nickel hydroxide, or the like can be used. As an aluminum source, aluminum oxide, aluminum hydroxide, or the like can be used.
Next, in Step S12, the lithium source and the transition metal M source are mixed. The mixing can be performed by a dry method or a wet method. For example, a ball mill, a bead mill, or the like can be used for the mixing. When the ball mill is used, a zirconia ball is preferably used as grinding media, for example.
Next, in Step S13, the materials mixed in the above manner are heated. This step is sometimes referred to as baking or first heating to distinguish this step from a heating step performed later. The heating is preferably performed at higher than or equal to 800° C. and lower than 1100° C., further preferably at higher than or equal to 900° C. and lower than or equal to 1000° C., still further preferably at approximately 950° C. Alternatively, the heating is preferably performed at higher than or equal to 800° C. and lower than or equal to 1000° C. Alternatively, the heating is preferably performed at higher than or equal to 900° C. and lower than or equal to 1100° C. An excessively low temperature might lead to insufficient decomposition and melting of the lithium source and the transition metal M source. An excessively high temperature, on the other hand, might cause a defect due to excessive reduction of the metal taking part in an oxidation-reduction reaction and used as the transition metal M, evaporation of lithium, or the like. The use of cobalt as the transition metal M, for example, may lead to a defect in which cobalt has divalence.
The heating time can be longer than or equal to 1 hour and shorter than or equal to 100 hours, for example, and is preferably longer than or equal to 2 hours and shorter than or equal to 20 hours. Alternatively, the heating time is preferably longer than or equal to 1 hour and shorter than or equal to 20 hours. Alternatively, the heating time is preferably longer than or equal to 2 hours and shorter than or equal to 100 hours. Baking is preferably performed in an atmosphere with few moisture, such as dry air (e.g., the dew point is lower than or equal to −50° C., further preferably lower than or equal to −100° C.). For example, it is preferable that the heating be performed at 1000° C. for 10 hours, the temperature rise be 200° C./h, and the flow rate of a dry atmosphere be 10 L/min. After that, the heated materials can be cooled to room temperature (25° C.). The temperature decreasing time from the specified temperature to room temperature is preferably longer than or equal to 10 hours and shorter than or equal to 50 hours, for example.
Note that the cooling to room temperature in Step S13 is not essential. As long as later steps of Step S41 to Step S43 are performed without problems, the cooling may be performed to a temperature higher than room temperature.
Next, in Step S14, the materials baked in the above manner are collected, whereby the composite oxide (LiMO2) containing lithium, the transition metal M, and oxygen is obtained. Specifically, lithium cobalt oxide, lithium manganese oxide, lithium nickel oxide, lithium cobalt oxide in which manganese is substituted for part of cobalt, lithium cobalt oxide in which nickel is substituted for part of cobalt, lithium nickel-manganese-cobalt oxide, or the like is obtained.
Alternatively, a composite oxide containing lithium, the transition metal M, and oxygen that is synthesized in advance may be used in Step S14. In that case, Step S11 to Step S13 can be omitted.
For example, as a composite oxide synthesized in advance, a lithium cobalt oxide particle (product name: CELLSEED C-10N) manufactured by NIPPON CHEMICAL INDUSTRIAL CO., LTD. can be used. This is lithium cobalt oxide in which the average particle diameter (D50) is approximately 12 μm, and in the impurity analysis by a glow discharge mass spectroscopy method (GD-MS), the magnesium concentration and the fluorine concentration are less than or equal to 50 ppm wt, the calcium concentration, the aluminum concentration, and the silicon concentration are less than or equal to 100 ppm wt, the nickel concentration is less than or equal to 150 ppm wt, the sulfur concentration is less than or equal to 500 ppm wt, the arsenic concentration is less than or equal to 1100 ppm wt, and the concentrations of elements other than lithium, cobalt, and oxygen are less than or equal to 150 ppm wt.
Alternatively, a lithium cobalt oxide particle (product name: CELLSEED C-5H) manufactured by NIPPON CHEMICAL INDUSTRIAL CO., LTD. can be used. This is lithium cobalt oxide in which the average particle diameter (D50) is approximately 6.5 μm, and the concentrations of elements other than lithium, cobalt, and oxygen are approximately equal to or less than those of C-10N in the impurity analysis by GD-MS.
In this embodiment, cobalt is used as the metal M, and the lithium cobalt oxide particle synthesized in advance (Cellseed C-10N produced by NIPPON CHEMICAL INDUSTRIAL CO., LTD.) is used.
Next, in Step S21, a halogen source such as a fluorine source or a chlorine source and a magnesium source are prepared as materials of a mixture 902. In addition, a lithium source is preferably prepared as well.
As the fluorine source, for example, lithium fluoride (LiF), magnesium fluoride (MgF2), aluminum fluoride (AlF3), titanium fluoride (TiF4 and TiF3), cobalt fluoride (CoF2 and CoF3), nickel fluoride (NiF2), zirconium fluoride (ZrF4), vanadium fluoride (VF5), manganese fluoride (MnF2 and MnF3), iron fluoride (FeF2 and FeF3), chromium fluoride (CrF2 and CrF3), niobium fluoride (NbF5), zinc fluoride (ZnF2), calcium fluoride (CaF2), sodium fluoride (NaF), potassium fluoride (KF), barium fluoride (BaF2), cerium fluoride (CeF2), lanthanum fluoride (LaF3), or sodium aluminum hexafluoride (Na3AlF6) can be used. A plurality of fluorine sources may be mixed to be used. Among them, lithium fluoride, which has a relatively low melting point of 848° C., is preferable because it is easily melted in an annealing step described later.
As the chlorine source, for example, lithium chloride, magnesium chloride, or the like can be used.
As the magnesium source, for example, magnesium fluoride, magnesium oxide, magnesium hydroxide, magnesium carbonate, or the like can be used.
As the lithium source, for example, lithium fluoride, lithium carbonate, or the like can be used. That is, lithium fluoride can be used as both the lithium source and the fluorine source. In addition, magnesium fluoride can be used as both the fluorine source and the magnesium source.
In this embodiment, lithium fluoride LiF is prepared as the fluorine source, and magnesium fluoride (MgF2) is prepared as the fluorine source and the magnesium source. When lithium fluoride LiF and magnesium fluoride (MgF2) are mixed at a molar ratio of approximately LiF:MgF2=65:35, the effect of lowering the melting point becomes the highest. On the other hand, when the amount of lithium fluoride increases, cycle performance might deteriorate because of a too large amount of lithium. Therefore, the molar ratio of lithium fluoride LiF to magnesium fluoride (MgF2) is preferably LiF:MgF2=x:1 (0≤x≤1.9), further preferably LiF:MgF2=x:1 (0.1≤x≤0.5), still further preferably LiF:MgF2=x:1 (x=the vicinity of 0.33). Note that in this specification and the like, the vicinity means a value greater than 0.9 times and smaller than 1.1 times a certain value.
In addition, in the case where the following mixing and grinding steps are performed by a wet method, a solvent is prepared. As the solvent, ketone such as acetone; alcohol such as ethanol or isopropanol; ether such as diethyl ether; dioxane; acetonitrile; N-methyl-2-pyrrolidone (NMP); or the like can be used. An aprotic solvent that hardly reacts with lithium is further preferably used. In this embodiment, acetone is used.
Next, in Step S22, the materials of the mixture 902 are ground and mixed. Although the mixing can be performed by a dry method or a wet method, the wet method is preferable because the materials can be ground to a smaller size. For example, a ball mill, a bead mill, or the like can be used for the mixing. When the ball mill is used, a zirconia ball is preferably used as grinding media, for example. The mixing step and the grinding step are preferably performed sufficiently to pulverize the mixture 902.
Next, in Step S23, the materials mixed and ground in the above manner are collected, whereby the mixture 902 is obtained.
For example, the mixture 902 preferably has a D50 (median diameter) of greater than or equal to 600 nm and less than or equal to 20 μm, further preferably greater than or equal to 1 μm and less than or equal to 10 μm. Alternatively, the D50 is preferably greater than or equal to 600 nm and less than or equal to 10 μm. Alternatively, the D50 is preferably greater than or equal to 1 μm and less than or equal to 20 μm. When mixed with a composite oxide containing lithium, the transition metal M, and oxygen in the later step, the mixture 902 pulverized to such a small size is likely to exist on surfaces of composite oxide particles uniformly.
Next, in Step S41, LiMO2 obtained in Step S14 and the mixture 902 are mixed. The atomic ratio of the transition metal M in the composite oxide containing lithium, the transition metal, and oxygen to magnesium Mg in the mixture 902 (M:Mg) is preferably 100:y (0.1≤y≤6), further preferably 100:y (0.3≤y≤3).
The conditions of the mixing in Step S41 are preferably milder than those of the mixing in Step S12 in order not to damage the particles of the composite oxide. For example, conditions with a lower rotation frequency or shorter time than the mixing in Step S12 are preferable. In addition, it can be said that conditions of the dry method are less likely to break the particles than those of the wet method. For example, a ball mill, a bead mill, or the like can be used for the mixing. When the ball mill is used, a zirconia ball is preferably used as grinding media, for example.
Next, in Step S42, the materials mixed in the above manner are collected, whereby a mixture 903 is obtained.
Note that this embodiment describes a method for adding the mixture of lithium fluoride and magnesium fluoride to lithium cobalt oxide with few impurities; however, one embodiment of the present invention is not limited thereto. A mixture obtained through baking after addition of a magnesium source, a fluorine source, and the like to the starting material of lithium cobalt oxide may be used instead of the mixture 903 in Step S42. In that case, there is no need to separate steps of Step S11 to Step S14 and steps of Step S21 to Step S23, which is simple and productive.
Alternatively, lithium cobalt oxide to which magnesium and fluorine are added in advance may be used. When lithium cobalt oxide to which magnesium and fluorine are added is used, the process can be simpler because steps up to Step S42 can be omitted.
In addition, a magnesium source and a fluorine source may be further added to the lithium cobalt oxide to which magnesium and fluorine are added in advance.
Next, in Step S43, the mixture 903 is heated in an atmosphere containing oxygen. This step is referred to as first annealing (first temperature condition) to be distinguish from the other heating step, in some cases. The heating further preferably has the adhesion preventing effect to prevent particles of the mixture 903 from adhering to one another.
Examples of the heating having the adhesion preventing effect are heating while the mixture 903 is being stirred and heating while a container containing the mixture 903 is being vibrated.
The heating temperature in Step S43 needs to be higher than or equal to the temperature at which a reaction between LiMO2 and the mixture 902 proceeds. Here, the temperature at which the reaction proceeds is a temperature at which interdiffusion between elements included in LiMO2 and the mixture 902 occurs. Thus, the heating temperature may be lower than the melting temperatures of these materials. For example, in salts and an oxide, solid-phase diffusion occurs at a temperature that is 0.757 times (Tamman temperature TO the melting temperature T.
A temperature higher than or equal to the temperature at which at least part of the mixture 903 is melted is preferable because the reaction proceeds more easily. Accordingly, the annealing temperature is preferably higher than or equal to the eutectic point of the mixture 902. In the case where the mixture 902 includes LiF and MgF2, the temperature in Step S43 is preferably set to higher than or equal to 742° C. that is the eutectic point.
The mixture 903 obtained by mixing such that LiCoO2:LiF:MgF2=100:0.33:1 (molar ratio) exhibits an endothermic peak at around 830° C. in differential scanning calorimetry measurement (DSC measurement). Thus, the annealing temperature is further preferably higher than or equal to 830° C. The mixture 903 includes at least fluorine, lithium, cobalt, and magnesium. The mixture 903 has the O3′ type crystal structure.
A higher annealing temperature is preferable because it facilitates the reaction, shortens the annealing time, and enables high productivity.
Note that the annealing temperature needs to be lower than or equal to a decomposition temperature of LiMO2 (1130° C. in the case of LiCoO2). At around the decomposition temperature, a slight amount of LiMO2 might be decomposed. Thus, the annealing temperature is preferably lower than or equal to 1130° C., further preferably lower than or equal to 1000° C., further preferably lower than or equal to 950° C., and further preferably lower than or equal to 900° C.
In view of the above, the annealing temperature is preferably higher than or equal to 500° C. and lower than or equal to 1130° C., further preferably higher than or equal to 500° C. and lower than or equal to 1000° C., still further preferably higher than or equal to 500° C. and lower than or equal to 950° C., yet still further preferably higher than or equal to 500° C. and lower than or equal to 900° C. Furthermore, the annealing temperature is preferably higher than or equal to 742° C. and lower than or equal to 1130° C., further preferably higher than or equal to 742° C. and lower than or equal to 1000° C., still further preferably higher than or equal to 742° C. and lower than or equal to 950° C., yet still further preferably higher than or equal to 742° C. and lower than or equal to 900° C. Furthermore, the annealing temperature is preferably higher than or equal to 830° C. and lower than or equal to 1130° C., further preferably higher than or equal to 830° C. and lower than or equal to 1000° C., still further preferably higher than or equal to 830° C. and lower than or equal to 950° C., yet still further preferably higher than or equal to 830° C. and lower than or equal to 900° C.
In addition, at the time of heating the mixture 903, the partial pressure of fluorine or a fluoride in the atmosphere is preferably controlled to be within an appropriate range.
In the formation method described in this embodiment, some of the materials, e.g., LiF as the fluorine source, function as flux. Owing to this function, the annealing temperature can be lower than or equal to the decomposition temperature of LiMO2, e.g., a temperature higher than or equal to 742° C. and lower than or equal to 950° C., which allows distribution of the additive such as magnesium in the surface portion more densely than in the core portion and formation of the positive electrode active material having favorable performance.
However, LiF is lighter than an oxygen molecule and thus volatilized and dissipated by the heating. In that case, the amount of LiF in the mixture 903 is reduced, and the function as flux is lowered. Therefore, heating needs to be performed while volatilization of LiF is inhibited. Note that even when LiF is not used as the fluorine source or the like, there is a possibility in that Li and F at a surface of LiMO2 react with each other to generate LiF and vaporize. Therefore, the volatilization needs to be inhibited also when a fluoride having a higher melting point than LiF is used.
In view of this, the mixture 903 is preferably heated in an atmosphere containing LiF, i.e., the mixture 903 is preferably heated in a state where the partial pressure of LiF in a heating furnace is high. Such heating can inhibit volatilization of LiF in the mixture 903.
The annealing is preferably performed for an appropriate time. The appropriate annealing time is changed depending on conditions, such as the annealing temperature, and the particle size and composition of LiMO2 in Step S14. In the case where the particle size is small, the annealing is preferably performed at a lower temperature or for a shorter time than the case where the particle size is large, in some cases.
When the average particle diameter (D50) of the particles in Step S14 is approximately 12 μm, for example, the annealing temperature is preferably higher than or equal to 600° C. and lower than or equal to 950° C., for example. The annealing time is preferably longer than or equal to three hours, further preferably longer than or equal to 10 hours, still further preferably longer than or equal to 60 hours, for example.
On the other hand, when the average particle diameter (D50) of the particles in Step S24 is approximately 5 μm, the annealing temperature is preferably higher than or equal to 600° C. and lower than or equal to 950° C., for example. The annealing time is preferably longer than or equal to one hour and shorter than or equal to 10 hours, further preferably approximately two hours, for example.
The temperature decreasing time after the heating is, for example, preferably longer than or equal to 10 hours and shorter than or equal to 50 hours.
Next, in Step S31, an additive source is prepared. As the elements included in the additive source, one or more selected from zirconium, aluminum, nickel, manganese, titanium, vanadium, iron, chromium, niobium, cobalt, arsenic, zinc, silicon, sulfur, phosphorus, and boron can be used, for example. In
The additive sources are preferably oxides, hydroxides, fluorides, alkoxides, or the like.
Next, the mixture 903 after the annealing and the additive source are mixed in Step S61. In other words, the additive is attached and included to/in the surface of the mixture 903 after the annealing.
For example, a solid phase method, a sol-gel method, a sputtering method, a mechanochemical method, a CVD method, or the like can be used as a method for mixing. The solid phase method and the sol-gel method are preferable because these methods enable the additive to be attached and included to/in the surface of the mixture 903 after the annealing easily at the atmospheric pressure and room temperature.
Note that in this specification and the like, the sol-gel method refers to a method in which an organic compound solution of a metal as a starting material is turned into a sol where fine particles of an oxide or hydroxide of the metal is dissolved by hydrolysis or polymerization of the compound in the solution, and a film or crystalline body is formed by heating an amorphous porous gel obtained by further proceeding the reaction.
In the case where the sol-gel method is used, an alkoxide of an additive source dissolved in alcohol and the mixture 903 after annealing are mixed first.
In the case where zirconium is used as the additive source, for example, zirconium(IV)tetrapropoxide can be used. As alcohol, for example, isopropanol (2-propanol) can be used.
Next, the mixed solution of the isopropanol solution of zirconium(IV)tetrapropoxide and the mixture 903 after annealing is stirred. The stirring can be performed with a magnetic stirrer, for example. The stirring can be performed for a time long enough for water in the atmosphere and zirconium(IV)tetrapropoxide to develop hydrolysis and a polycondensation reaction, e.g., for 60 hours, at room temperature.
After the above process, precipitate is collected from the mixed solution. As the collection method, filtration, centrifugation, evaporation to dryness, and the like can be used. In this embodiment, evaporation to dryness is used. In this embodiment, circulation drying at 95° C. is performed.
Next, in Step S62, the materials dried in the above manner are collected, whereby a mixture 904 is obtained.
Next, the mixture 904 synthesized in Step S62 is heated (in the case where S43 is referred to as first annealing, heating in S63 may be referred to as second annealing (second temperature condition)). In the heating, the retention time within a specified temperature range is preferably shorter than or equal to 50 hours, further preferably longer than or equal to two hours and shorter than or equal to 10 hours, still further preferably longer than or equal to one hour and shorter than or equal to three hours.
The range of the specified temperature is preferably higher than or equal to 500° C. and lower than or equal to 1200° C., further preferably higher than or equal to 800° C. and lower than or equal to 1000° C.
The heating is performed preferably in an oxygen-containing atmosphere.
In this embodiment, the specified temperature is 800° C. and kept for two hours, the temperature rising rate is 200° C./h, and the flow rate in a dry atmosphere is 10 L/min.
In Step S64, crushing is performed, and mixing is performed as necessary.
Next, in Step S66, the material crushed in the above manner is collected, whereby the positive electrode active material 100 can be formed. Here, the collected particles are preferably made to pass through a sieve. Through the sieve, adhesion between the positive electrode active material particles can be solved.
Next, formation methods that are different from
In
As the additive, one or more selected from nickel, aluminum, manganese, titanium, zirconium, vanadium, iron, chromium, niobium, cobalt, arsenic, zinc, silicon, sulfur, phosphorus, and boron can be used, for example.
As a mixing method of the additives, a solid phase method, a sol-gel method, a sputtering method, a mechanochemical method, a CVD method, or the like can be used, for example. A combination of a plurality of methods may also be used.
As illustrated in
As shown in
As shown in
When the step of introducing the transition metal M and the step of introducing the additive are separately performed in such a manner, the profiles in the depth direction of the elements can be made different from each other in some cases. For example, the concentration of the additive can be made higher in the surface portion than in the central portion of the particle. Furthermore, with the number of atoms of the transition metal M as a reference, the ratio of the number of atoms of the additive with respect to the reference can be higher in the surface portion than in the central portion. The concentration of the additive element is made high in the projection, in particular.
This embodiment can be used in combination with the other embodiments.
In this embodiment, a lithium-ion secondary battery including a positive electrode active material of one embodiment of the present invention will be described. The secondary battery at least includes an exterior body, a current collector, an active material (a positive electrode active material or a negative electrode active material), a conductive additive, and a binder. An electrolyte solution in which a lithium salt or the like is dissolved is also included. In the secondary battery using an electrolyte solution, a positive electrode, a negative electrode, and a separator between the positive electrode and the negative electrode are provided.
The positive electrode includes a positive electrode active material layer and a positive electrode current collector. The positive electrode active material layer preferably includes the positive electrode active material described in Embodiment 1, and may further includes a binder, a conductive additive, or the like.
A current collector 550 is metal foil, and the positive electrode is formed by applying slurry onto the metal foil and drying the slurry. Pressing may be performed after drying. The positive electrode is a component obtained by forming an active material layer over the current collector 550.
Slurry refers to a material solution that is used to form an active material layer over the current collector 550 and at least includes an active material, a binder, and a solvent, preferably and also a conductive additive mixed therewith. Slurry may also be referred to as slurry for an electrode or active material slurry; in some cases, slurry for forming a positive electrode active material layer is referred to as slurry for a positive electrode, and slurry for forming a negative electrode active material layer is referred to as slurry for a negative electrode.
A conductive additive is also referred to as a conductivity-imparting agent or a conductive material, and a carbon material is used as the conductive additive. A conductive additive is attached between a plurality of active materials, whereby the plurality of active materials are electrically connected to each other, and the conductivity increases. Note that the term “attach” refers not only to a state where an active material and a conductive additive are physically in close contact with each other, and includes, for example, the following concepts: the case where covalent bonding occurs, the case where bonding with the Van der Waals force occurs, the case where a conductive additive covers part of the surface of an active material, the case where a conductive additive is embedded in surface roughness of an active material, and the case where an active material and a conductive additive are electrically connected to each other without being in contact with each other.
Typical examples of the carbon material used as the conductive additive include carbon black (e.g., furnace black, acetylene black, and graphite).
In
In the positive electrode of the secondary battery, a binder (a resin) is mixed in order to fix the current collector 550 such as metal foil and the active material. The binder is also referred to as a binding agent. Since the binder is a high molecular material, a large amount of binder lowers the proportion of the active material in the positive electrode, thereby reducing the discharge capacity of the secondary battery. Therefore, the amount of binder mixed is reduced to a minimum. In
Although
In the positive electrode in
Graphene, which has electrically, mechanically, or chemically remarkable characteristics, is a carbon material that is expected to be applied to a variety of fields, such as field-effect transistors and solar batteries.
In
In the step of mixing the graphene 554 and the acetylene black 553 to obtain an electrode slurry, the weight of mixed carbon black is preferably 1.5 times to 20 times, further preferably 2 times to 9.5 times the weight of graphene.
When the graphene 554 and the acetylene black 553 are mixed in the above ratio range, the acetylene black 553 can be dispersed uniformly and less likely to be aggregated at the time of preparing the slurry. Furthermore, when the graphene 554 and the acetylene black 553 are mixed in the above ratio range, the electrode density can be higher than that of an electrode using only the acetylene black 553 as a conductive additive. As the electrode density is higher, the capacity per unit weight can be higher. Specifically, the density of the positive electrode active material layer measured by gravimetry can be higher than 3.5 g/cc. In addition, it is preferable that the positive electrode active material 100 described in Embodiment 1 be used for the positive electrode and the graphene 554 and the acetylene black 553 be mixed in the above ratio range, in which case synergy for higher capacity of the secondary battery can be expected.
The electrode density is lower than that of a positive electrode containing only graphene as a conductive additive, but when a first carbon material (graphene) and a second carbon material (acetylene black) are mixed in the above ratio range, fast charging can be achieved. In addition, it is preferable that the positive electrode active material 100 described in Embodiment 1 be used for the positive electrode and the graphene 554 and the acetylene black 553 be mixed in the above ratio range, in which case synergy for higher stability and compatibility with faster charging of the secondary battery can be expected.
The above features are advantageous for secondary batteries for vehicles.
When a vehicle becomes heavier with increasing number of secondary batteries, more energy is consumed to move the vehicle, which shortens the driving range. With the use of a high-density secondary battery, the driving range of the vehicle can be maintained with almost no change in the total weight of a vehicle including a secondary battery having the same weight.
Since power is needed to charge the secondary battery with higher capacity in the vehicle, it is desirable to end charging fast. What is called a regenerative charging, in which electric power is temporarily generated when the vehicle is braked and the electric power is used for charging, is performed under high rate charging conditions; thus, a secondary battery for a vehicle is desired to have favorable rate characteristics.
Using the positive electrode active material 100 described in Embodiment 1 for the positive electrode and mixing acetylene black and graphene within an optimal range enable both higher electrode density and formation of an appropriate space needed for ion conduction, whereby a secondary battery for a vehicle which has high energy density and favorable output characteristics can be obtained.
This structure is also effective in a portable information terminal, and using the positive electrode active material 100 described in Embodiment 1 for the positive electrode and mixing acetylene black and graphene within an optimal range enable a small secondary battery with high capacity. Mixing acetylene black and graphene within an optimal range also enables fast charging of a portable information terminal.
In
Using the positive electrode active material 100 described in Embodiment 1 for the positive electrode and mixing acetylene black and graphene within an optimal range enable both higher electrode density and formation of an appropriate space needed for ion conduction, whereby a secondary battery which has high energy density and favorable output characteristics can be obtained.
In
In
The positive electrode in any one of
Although the above structure is an example of a secondary battery using an electrolyte solution, one embodiment of the present invention is not limited thereto.
For example, a semi-solid-state battery or an all-solid-state battery can be fabricated using the positive electrode active material 100 described in Embodiment 1.
In this specification and the like, a semi-solid-state battery refers to a battery in which at least one of an electrolyte layer, a positive electrode, and a negative electrode includes a semi-solid-state material. The term “semi-solid-state” here does not mean that the proportion of a solid-state material is 50%. The term “semi-solid-state” means having properties of a solid, such as a small volume change, and also having some of properties close to those of a liquid, such as flexibility. A single material or a plurality of materials can be used to satisfy the above properties. For example, a porous solid-state material infiltrated with a liquid material may be used.
In this specification and the like, a polymer electrolyte secondary battery refers to a secondary battery in which an electrolyte layer between a positive electrode and a negative electrode includes a polymer. Polymer electrolyte secondary batteries include a dry (or true) polymer electrolyte battery and a polymer gel electrolyte battery. A polymer electrolyte secondary battery may be referred to as a semi-solid-state battery.
A semi-solid-state battery fabricated using the positive electrode active material 100 described in Embodiment 1 is a secondary battery having high charge and discharge capacity. The semi-solid-state battery can have high charge and discharge voltage. Alternatively, a highly safe or highly reliable semi-solid-state battery can be achieved.
The positive electrode active material described in Embodiment 1 and another positive electrode active material may be mixed to be used.
Examples of another positive electrode active material include composite oxides having an olivine crystal structure, a layered rock-salt crystal structure, and a spinel crystal structure. Examples include compounds such as LiFePO4, LiFeO2, LiNiO2, LiMn2O4, V2O5, Cr2O5, and MnO2.
As another positive electrode active material, it is preferable to mix lithium nickel oxide (LiNiO2 or LiNi1−xMxO2 (0<x<1) (M=Co, Al, or the like)) with a lithium-containing material that has a spinel crystal structure and contains manganese, such as LiMn2O4. This composition can improve the characteristics of the secondary battery.
As another positive electrode active material, a lithium-manganese composite oxide that can be represented by a composition formula LiaMnbMcOd can be used. Here, the element M is preferably silicon, phosphorus, or a metal element other than lithium and manganese, and further preferably nickel. When the whole particle of a lithium-manganese composite oxide is measured, it is preferable to satisfy 0<a/(b+c)<2; c>0; and 0.26 (b+c)/d<0.5 at the time of discharging. Note that the proportions of metals, silicon, phosphorus, and the like in the whole particle of a lithium-manganese composite oxide can be measured with, for example, an ICP-MS (inductively coupled plasma-mass spectrometer). The proportion of oxygen in the whole particle of a lithium-manganese composite oxide can be measured by, for example, EDX (energy dispersive X-ray spectroscopy). Moreover, the proportion of oxygen can be measured using fusion gas analysis and valence evaluation with XAFS (X-ray absorption fine structure) spectroscopy in combination with ICPMS analysis. Note that a lithium-manganese composite oxide is an oxide containing at least lithium and manganese, and may contain at least one element selected from a group consisting of chromium, cobalt, aluminum, nickel, iron, magnesium, molybdenum, zinc, indium, gallium, copper, titanium, niobium, silicon, phosphorus, and the like.
As the binder, a rubber material such as styrene-butadiene rubber (SBR), styrene-isoprene-styrene rubber, acrylonitrile-butadiene rubber, butadiene rubber, or ethylene-propylene-diene copolymer is preferably used, for example. Alternatively, fluororubber can be used as the binder.
As the binder, for example, water-soluble polymers are preferably used. As the water-soluble polymers, a polysaccharide can be used, for example. As the polysaccharide, starch, a cellulose derivative such as carboxymethyl cellulose (CMC), methyl cellulose, ethyl cellulose, hydroxypropyl cellulose, diacetyl cellulose, or regenerated cellulose, or the like can be used. It is further preferable that such water-soluble polymers be used in combination with any of the above rubber materials.
Alternatively, as the binder, a material such as polystyrene, poly(methyl acrylate), poly(methyl methacrylate) (PMMA), sodium polyacrylate, polyvinyl alcohol (PVA), polyethylene oxide (PEO), polypropylene oxide, polyimide, polyvinyl chloride, polytetrafluoroethylene, polyethylene, polypropylene, polyisobutylene, polyethylene terephthalate, nylon, polyvinylidene fluoride (PVDF), polyacrylonitrile (PAN), ethylene-propylene-diene polymer, polyvinyl acetate, or nitrocellulose is preferably used.
At least two of the above materials may be used in combination for the binder.
For example, a material having a significant viscosity modifying effect and another material may be used in combination. For example, a rubber material or the like has high adhesion and high elasticity but may have difficulty in viscosity modification when mixed in a solvent. In such a case, a rubber material or the like is preferably mixed with a material having a significant viscosity modifying effect, for example. As a material having a significant viscosity modifying effect, for instance, a water-soluble polymer is preferably used. An example of a water-soluble polymer having a significant viscosity modifying effect is the above-mentioned polysaccharide; for instance, a cellulose derivative such as carboxymethyl cellulose (CMC), methyl cellulose, ethyl cellulose, hydroxypropyl cellulose, diacetyl cellulose, or regenerated cellulose, or starch can be used.
Note that a cellulose derivative such as carboxymethyl cellulose obtains a higher solubility when converted into a salt such as a sodium salt or an ammonium salt of carboxymethyl cellulose, and thus easily exerts an effect as a viscosity modifier. A high solubility can also increase the dispersibility of an active material and other components in the formation of slurry for an electrode. In this specification, cellulose and a cellulose derivative used as a binder of an electrode include salts thereof.
A water-soluble polymer stabilizes the viscosity by being dissolved in water and allows stable dispersion of the active material and another material combined as a binder, such as styrene-butadiene rubber, in an aqueous solution. Furthermore, a water-soluble polymer is expected to be easily and stably adsorbed onto an active material surface because it has a functional group. Many cellulose derivatives, such as carboxymethyl cellulose, have a functional group such as a hydroxyl group or a carboxyl group. Because of functional groups, polymers are expected to interact with each other and cover an active material surface in a large area.
In the case where the binder that covers the active material surface or is in contact with the surface forms a film, the film is expected to serve also as a passivation film to suppress the decomposition of the electrolyte solution. Here, a passivation film refers to a film without electric conductivity or a film with extremely low electric conductivity, and can inhibit the decomposition of an electrolyte solution at a potential at which a battery reaction occurs when the passivation film is formed on the active material surface, for example. It is preferred that the passivation film can conduct lithium ions while suppressing electrical conduction.
The current collector can be formed using a material that has high conductivity, such as a metal like stainless steel, gold, platinum, aluminum, or titanium, or an alloy thereof. It is preferred that a material used for the positive electrode current collector not dissolve at the potential of the positive electrode. It is also possible to use an aluminum alloy to which an element that improves heat resistance, such as silicon, titanium, neodymium, scandium, or molybdenum, is added. A metal element that forms silicide by reacting with silicon may be used. Examples of the metal element that forms silicide by reacting with silicon include zirconium, titanium, hafnium, vanadium, niobium, tantalum, chromium, molybdenum, tungsten, cobalt, and nickel. The current collector can have a foil-like shape, a plate-like shape, a sheet-like shape, a net-like shape, a punching-metal shape, an expanded-metal shape, or the like as appropriate. The current collector preferably has a thickness greater than or equal to 5 μm and less than or equal to 30 μm.
The negative electrode includes a negative electrode active material layer and a negative electrode current collector. The negative electrode active material layer includes a negative electrode active material, and may also include a conductive additive and a binder.
As the negative electrode active material, an alloy-based material, a carbon-based material, or the like can be used, for example.
As the negative electrode active material, an element that enables charge and discharge reactions by alloying and dealloying reactions with lithium can be used. For example, a material containing at least one of silicon, tin, gallium, aluminum, germanium, lead, antimony, bismuth, silver, zinc, cadmium, indium, and the like can be used. Such elements have higher capacity than carbon. In particular, silicon has a high theoretical capacity of 4200 mAh/g. For this reason, silicon is preferably used as the negative electrode active material. Alternatively, a compound containing any of the above elements may be used. For example, SiO, Mg2Si, Mg2Ge, SnO, SnO2, Mg2Sn, SnS2, V2Sn3, FeSn2, CoSn2, Ni3Sn2, Cu6Sn5, Ag3Sn, Ag3Sb, Ni2MnSb, CeSb3, LaSn3, La3Co2Sn7, CoSb3, InSb, and SbSn are given. Here, an element that enables charge and discharge reactions by alloying and dealloying reactions with lithium, a compound containing the element, and the like may be referred to as an alloy-based material.
In this specification and the like, SiO refers to silicon monoxide, for example. Note that SiO can alternatively be expressed as SiO)x. Here, it is preferred that x be 1 or have an approximate value of 1. For example, x is preferably more than or equal to 0.2 and less than or equal to 1.5, and preferably more than or equal to 0.3 and less than or equal to 1.2.
As the carbon-based material, graphite, graphitizing carbon (soft carbon), non-graphitizing carbon (hard carbon), carbon nanotube, graphene, carbon black, or the like can be used.
Examples of graphite include artificial graphite and natural graphite. Examples of artificial graphite include mesocarbon microbeads (MCMB), coke-based artificial graphite, and pitch-based artificial graphite. Here, as artificial graphite, spherical graphite having a spherical shape can be used. For example, MCMB is preferable because it may have a spherical shape. Moreover, MCMB may be preferable because it can relatively easily have a small surface area. Examples of natural graphite include flake graphite and spherical natural graphite.
Graphite has a low potential substantially equal to that of a lithium metal (higher than or equal to 0.05 V and lower than or equal to 0.3 V vs. Li/Li+) when lithium ions are intercalated into the graphite (while a lithium-graphite intercalation compound is generated). For this reason, a lithium-ion secondary battery including graphite can have a high operating voltage. In addition, graphite is preferred because of its advantages such as a relatively high capacity per unit volume, relatively small volume expansion, low cost, and higher level of safety than that of a lithium metal.
As the negative electrode active material, an oxide such as titanium dioxide (TiO2), lithium titanium oxide (Li4Ti5O12), a lithium-graphite intercalation compound (LixC6), niobium pentoxide (Nb2O5), tungsten oxide (WO2), or molybdenum oxide (MoO2) can be used.
Alternatively, as the negative electrode active material, Li3−xMxN (M is Co, Ni, or Cu) with a Li3N structure, which is a composite nitride containing lithium and a transition metal, can be used. For example, Li2.6Co0.4N3 is preferable because of high charge and discharge capacity (900 mAh/g and 1890 mAh/cm3).
A composite nitride containing lithium and a transition metal is preferably used, in which case lithium ions are contained in the negative electrode active material and thus the negative electrode active material can be used in combination with a positive electrode active material that does not contain lithium ions, such as V2O5 or Cr3O8. Note that in the case of using a material containing lithium ions as a positive electrode active material, the composite nitride containing lithium and a transition metal can be used as the negative electrode active material by extracting the lithium ions contained in the positive electrode active material in advance.
Alternatively, a material that causes a conversion reaction can be used as the negative electrode active material. For example, a transition metal oxide that does not form an alloy with lithium, such as cobalt oxide (CoO), nickel oxide (NiO), and iron oxide (FeO), may be used as the negative electrode active material. Other examples of the material that causes a conversion reaction include oxides such as Fe2O3, CuO, Cu2O, RuO2, and Cr2O3, sulfides such as CoS0.89, NiS, and CuS, nitrides such as Zn3N2, Cu3N, and Ge3N4, phosphides such as NiP2, FeP2, and CoP3, and fluorides such as FeF3 and BiF3.
For the conductive additive and the binder that can be included in the negative electrode active material layer, materials similar to those for the conductive additive and the binder that can be included in the positive electrode active material layer can be used.
For the negative electrode current collector, copper or the like can be used in addition to a material similar to that for the positive electrode current collector. Note that a material that is not alloyed with carrier ions of lithium or the like is preferably used for the negative electrode current collector.
The separator is positioned between the positive electrode and the negative electrode. The separator can be formed using, for example, a fiber containing cellulose, such as paper, nonwoven fabric, glass fiber, ceramics, or synthetic fiber containing nylon (polyamide), vinylon (polyvinyl alcohol-based fiber), polyester, acrylic, polyolefin, or polyurethane. The separator is preferably processed into a bag-like shape to enclose one of the positive electrode and the negative electrode.
The separator may have a multilayer structure. For example, an organic material film of polypropylene, polyethylene, or the like can be coated with a ceramic-based material, a fluorine-based material, a polyamide-based material, a mixture thereof, or the like. Examples of the ceramic-based material include aluminum oxide particles and silicon oxide particles. Examples of the fluorine-based material include PVDF and polytetrafluoroethylene. Examples of the polyamide-based material include nylon and aramid (meta-based aramid and para-based aramid).
When the separator is coated with the ceramic-based material, the oxidation resistance is improved; hence, deterioration of the separator in charging and discharging at high voltage can be suppressed and thus the reliability of the secondary battery can be improved. When the separator is coated with the fluorine-based material, the separator is easily brought into close contact with an electrode, resulting in high output characteristics. When the separator is coated with the polyamide-based material, in particular, aramid, the safety of the secondary battery is improved because heat resistance is improved.
For example, both surfaces of a polypropylene film may be coated with a mixed material of aluminum oxide and aramid. Alternatively, a surface of a polypropylene film that is in contact with the positive electrode may be coated with a mixed material of aluminum oxide and aramid, and a surface of the polypropylene film that is in contact with the negative electrode may be coated with the fluorine-based material.
With the use of a separator having a multilayer structure, the capacity per volume of the secondary battery can be increased because the safety of the secondary battery can be maintained even when the total thickness of the separator is small.
The electrolyte solution contains a solvent and an electrolyte. As the solvent of the electrolyte solution, an aprotic organic solvent is preferably used. For example, one of ethylene carbonate (EC), propylene carbonate (PC), butylene carbonate, chloroethylene carbonate, vinylene carbonate, γ-butyrolactone, γ-valerolactone, dimethyl carbonate (DMC), diethyl carbonate (DEC), ethyl methyl carbonate (EMC), methyl formate, methyl acetate, ethyl acetate, methyl propionate, ethyl propionate, propyl propionate, methyl butyrate, 1,3-dioxane, 1,4-dioxane, dimethoxyethane (DME), dimethyl sulfoxide, diethyl ether, methyl diglyme, acetonitrile, benzonitrile, tetrahydrofuran, sulfolane, and sultone can be used, or two or more of these solvents can be used in an appropriate combination in an appropriate ratio.
Alternatively, the use of one or more kinds of ionic liquids (room temperature molten salts) which have features of non-flammability and non-volatility as the solvent of the electrolyte solution can prevent a power storage device from exploding or catching fire even when the power storage device internally shorts out or the internal temperature increases owing to overcharging or the like. An ionic liquid contains a cation and an anion, specifically, an organic cation and an anion. Examples of the organic cation used for the electrolyte solution include aliphatic onium cations such as a quaternary ammonium cation, a tertiary sulfonium cation, and a quaternary phosphonium cation, and aromatic cations such as an imidazolium cation and a pyridinium cation. Examples of the anion used for the electrolyte solution include a monovalent amide-based anion, a monovalent methide-based anion, a fluorosulfonate anion, a perfluoroalkylsulfonate anion, a tetrafluoroborate anion, a perfluoroalkylborate anion, a hexafluorophosphate anion, and a perfluoroalkylphosphate anion.
As the electrolyte dissolved in the above-described solvent, one of lithium salts such as LiPF6, LiClO4, LiAsF6, LiBF4, LiAlCl4, LiSCN, LiBr, LiI, Li2SO4, Li2B10Cl10, Li2B12Cl12, LiCF3SO3, LiC4F9SO3, LiC(CF3SO2)3, LiC(C2F5SO2)3, LiN(CF3SO2)2, LiN(C4F9SO2) (CF3SO2), LiN(C2F5SO2)2, and lithium bis(oxalate)borate (Li(C2O4)2, LiBOB) can be used, or two or more of these lithium salts can be used in an appropriate combination in an appropriate ratio.
The electrolyte solution used for the power storage device is preferably highly purified and contains a small amount of dust particles and elements other than the constituent elements of the electrolyte solution (hereinafter also simply referred to as “impurities”). Specifically, the weight ratio of impurities to the electrolyte solution is preferably less than or equal to 1%, further preferably less than or equal to 0.1%, still further preferably less than or equal to 0.01%.
Furthermore, an additive agent such as vinylene carbonate, propane sultone (PS), tert-butylbenzene (TBB), fluoroethylene carbonate (FEC), lithium bis(oxalate)borate (LiBOB), or a dinitrile compound like succinonitrile or adiponitrile may be added to the electrolyte solution. The concentration of such an additive agent in the solvent is, for example, higher than or equal to 0.1 wt % and lower than or equal to 5 wt %.
Alternatively, a polymer gel electrolyte obtained in such a manner that a polymer is swelled with an electrolyte solution may be used.
When a polymer gel electrolyte is used, safety against liquid leakage and the like is improved. Moreover, the secondary battery can be thinner and more lightweight.
As a polymer that undergoes gelation, a silicone gel, an acrylic gel, an acrylonitrile gel, a polyethylene oxide-based gel, a polypropylene oxide-based gel, a fluorine-based polymer gel, or the like can be used. For example, a polymer having a polyalkylene oxide structure, such as polyethylene oxide (PEO), PVDF, polyacrylonitrile, or a copolymer containing any of them can be used. For example, PVDF-HFP, which is a copolymer of PVDF and hexafluoropropylene (HFP), can be used. The formed polymer may be porous.
Instead of the electrolyte solution, a solid electrolyte including an inorganic material such as a sulfide-based or oxide-based inorganic material, and a solid electrolyte including a polymer material such as a PEO (polyethylene oxide)-based polymer material may alternatively be used. When the solid electrolyte is used, a separator or a spacer is not necessary. Furthermore, the battery can be entirely solidified; therefore, there is no possibility of liquid leakage and thus the safety is dramatically improved.
Accordingly, the positive electrode active material 100 obtained in Embodiment 1 can also be applied to all-solid-state batteries. By using the positive electrode slurry or the electrode in an all-solid-state battery, an all-solid-state battery with a high degree of safety and favorable characteristics can be obtained.
For the exterior body included in the secondary battery, a metal material such as aluminum or a resin material can be used, for example. A film-like exterior body can also be used. As the film, for example, it is possible to use a film having a three-layer structure in which a highly flexible metal thin film of aluminum, stainless steel, copper, nickel, or the like is provided over a film formed of polyethylene, polypropylene, polycarbonate, ionomer, polyamide, or the like and an insulating synthetic resin film of a polyamide-based resin, a polyester-based resin, or the like is provided over the metal thin film as the outer surface of the exterior body.
This embodiment can be used in combination with the other embodiments.
This embodiment will describe examples of shapes of several types of secondary batteries including a positive electrode or a negative electrode formed by the manufacturing method described in the foregoing embodiment.
An example of a coin-type secondary battery will be described.
For easy understanding,
In
The positive electrode 304 is a stack in which a positive electrode active material layer 306 is formed over a positive electrode current collector 305.
To prevent a short circuit between the positive electrode and the negative electrode, the separator 310 and a ring-shaped insulator 313 are provided to cover the side surface and top surface of the positive electrode 304. The separator 310 has a larger flat surface area than the positive electrode 304.
In a coin-type secondary battery 300, the positive electrode can 301 doubling as a positive electrode terminal and the negative electrode can 302 doubling as a negative electrode terminal are insulated from each other and sealed by a gasket 303 made of polypropylene or the like. The positive electrode 304 includes the positive electrode current collector 305 and the positive electrode active material layer 306 provided in contact with the positive electrode current collector 305. The negative electrode 307 includes a negative electrode current collector 308 and a negative electrode active material layer 309 provided in contact with the negative electrode current collector 308. The negative electrode 307 is not limited to having a stacked-layer structure, and lithium metal foil or lithium-aluminum alloy foil may be used.
Note that only one surface of each of the positive electrode 304 and the negative electrode 307 used for the coin-type secondary battery 300 is provided with an active material layer.
For the positive electrode can 301 and the negative electrode can 302, a metal having corrosion resistance to an electrolyte solution, such as nickel, aluminum, or titanium, an alloy of such a metal, or an alloy of such a metal and another metal (e.g., stainless steel) can be used. The positive electrode can 301 and the negative electrode can 302 are preferably covered with nickel, aluminum, or the like in order to prevent corrosion due to the electrolyte solution, for example. The positive electrode can 301 and the negative electrode can 302 are electrically connected to the positive electrode 304 and the negative electrode 307, respectively.
The negative electrode 307, the positive electrode 304, and the separator 310 are immersed in the electrolyte solution. Then, as illustrated in
With this secondary battery, the coin-type secondary battery 300 can have high capacity, high charging and discharging capacity, and excellent cycle performance. Note that in the case where a secondary battery is between the negative electrode 307 and the positive electrode 304, the separator 310 may be unnecessary.
An example of a cylindrical secondary battery is described with reference to
Inside the battery can 602 having a hollow cylindrical shape, a battery element in which a strip-like positive electrode 604 and a strip-like negative electrode 606 are wound with a strip-like separator 605 located therebetween is provided. Although not illustrated, the battery element is wound around the central axis. One end of the battery can 602 is close and the other end thereof is open. For the battery can 602, a metal having corrosion resistance to an electrolyte solution, such as nickel, aluminum, or titanium, an alloy of such a metal, or an alloy of such a metal and another metal (e.g., stainless steel) can be used. The battery can 602 is preferably covered with nickel, aluminum, or the like in order to prevent corrosion due to the electrolyte solution. Inside the battery can 602, the battery element in which the positive electrode, the negative electrode, and the separator are wound is provided between a pair of insulating plates 608 and 609 that face each other. The inside of the battery can 602 provided with the battery element is filled with a nonaqueous electrolyte solution (not illustrated). As the nonaqueous electrolyte solution, an electrolyte solution similar to that for the coin-type secondary battery can be used.
Since a positive electrode and a negative electrode that are used for a cylindrical storage battery are wound, active materials are preferably formed on both surfaces of a current collector.
The positive electrode active material 100 obtained in Embodiment 1 is used in the positive electrode 604, whereby the cylindrical secondary battery 616 can have high capacity, high charging and discharging capacity and excellent cycle performance.
A positive electrode terminal (positive electrode current collecting lead) 603 is connected to the positive electrode 604, and a negative electrode terminal (negative electrode current collecting lead) 607 is connected to the negative electrode 606. Both the positive electrode terminal 603 and the negative electrode terminal 607 can be formed using a metal material such as aluminum. The positive electrode terminal 603 and the negative electrode terminal 607 are resistance-welded to a safety valve mechanism 613 and the bottom of the battery can 602, respectively. The safety valve mechanism 613 is electrically connected to the positive electrode cap 601 through a PTC element (positive temperature coefficient) 611. The safety valve mechanism 613 cuts off electrical connection between the positive electrode cap 601 and the positive electrode 604 when the internal pressure of the battery exceeds a predetermined threshold. The PTC element 611, which is a thermally sensitive resistor whose resistance increases as temperature rises, limits the amount of current by increasing the resistance, in order to prevent abnormal heat generation. Barium titanate (BaTiO3)-based semiconductor ceramic or the like can be used for the PTC element.
The plurality of secondary batteries 616 may be connected in series after being connected in parallel.
A temperature control device may be provided between the plurality of secondary batteries 616. The secondary batteries 616 can be cooled with the temperature control device when overheated, whereas the secondary batteries 616 can be heated with the temperature control device when cooled too much. Thus, the performance of the power storage system 615 is less likely to be influenced by the outside temperature.
In
Structure examples of secondary batteries are described with reference to
A secondary battery 913 illustrated in
Note that as illustrated in
For the housing 930a, an insulating material such as an organic resin can be used. In particular, when a material such as an organic resin is used for the side on which an antenna is formed, blocking of an electric field by the secondary battery 913 can be inhibited. When an electric field is not significantly blocked by the housing 930a, an antenna may be provided inside the housing 930a. For the housing 930b, a metal material can be used, for example.
As illustrated in
The positive electrode active material 100 obtained in Embodiment 1 is used in the positive electrode 932, whereby the secondary battery 913 can have high capacity, high charging and discharging capacity, and excellent cycle performance.
The separator 933 has a larger width than the negative electrode active material layer 931a and the positive electrode active material layer 932a, and is wound to overlap the negative electrode active material layer 931a and the positive electrode active material layer 932a. In terms of safety, the width of the negative electrode active material layer 931a is preferably larger than that of the positive electrode active material layer 932a. The wound body 950a having such a shape is preferable because of its high degree of safety and high productivity.
As illustrated in
As illustrated in
As illustrated in
Next, examples of the appearance of a laminated secondary battery are shown in
Here, an example of a method for manufacturing the laminated secondary battery having the appearance illustrated in
First, the negative electrode 506, the separator 507, and the positive electrode 503 are stacked.
Then, the negative electrodes 506, the separators 507, and the positive electrodes 503 are placed over the exterior body 509.
Subsequently, the exterior body 509 is folded along a dashed line as illustrated in
Next, the electrolyte solution 508 (not illustrated) is introduced into the exterior body 509 from the inlet of the exterior body 509. The electrolyte solution 508 is preferably introduced in a reduced pressure atmosphere or in an inert atmosphere. Lastly, the inlet is sealed by bonding. In this manner, the laminated secondary battery 500 can be manufactured.
The positive electrode active material 100 obtained in Embodiment 1 is used in the positive electrodes 503, whereby the secondary battery 500 can have high capacity, high charging and discharging capacity, and excellent cycle performance.
Examples of a secondary battery pack of one embodiment of the present invention that is capable of wireless charging using an antenna will be described with reference to
As for the internal structure of the secondary battery 513, the secondary battery 513 may include a wound body or a stack.
In the secondary battery pack 531, a control circuit 590 is provided over the circuit board 540 as illustrated in
Alternatively, as illustrated in
Note that the shape of the antenna 517 is not limited to a coil shape and may be a linear shape or a plate shape, for example. Furthermore, a planar antenna, an aperture antenna, a traveling-wave antenna, an EH antenna, a magnetic-field antenna, a dielectric antenna, or the like may be used. Alternatively, the antenna 517 may be a flat-plate conductor. The flat-plate conductor can serve as one of conductors for electric field coupling. That is, the antenna 517 can function as one of two conductors of a capacitor. Thus, electric power can be transmitted and received not only by an electromagnetic field or a magnetic field but also by an electric field.
The secondary battery pack 531 includes a layer 519 between the antenna 517 and the secondary battery 513. The layer 519 has a function of blocking an electromagnetic field from the secondary battery 513, for example. As the layer 519, a magnetic material can be used, for example.
This embodiment can be freely combined with the other embodiments.
This embodiment will describe an example in which an all-solid-state battery is manufactured using the positive electrode active material 100 obtained in Embodiment 1.
As illustrated in
The positive electrode 410 includes a positive electrode current collector 413 and a positive electrode active material layer 414. The positive electrode active material layer 414 includes a positive electrode active material 411 and a solid electrolyte 421. The positive electrode active material 100 obtained in Embodiment 1 is used as the positive electrode active material 411, and the boundary between the core region and the shell region is indicated by a dotted line. The positive electrode active material layer 414 may also include a conductive additive and a binder.
The solid electrolyte layer 420 includes the solid electrolyte 421. The solid electrolyte layer 420 is positioned between the positive electrode 410 and the negative electrode 430 and is a region that includes neither the positive electrode active material 411 nor a negative electrode active material 431.
The negative electrode 430 includes a negative electrode current collector 433 and a negative electrode active material layer 434. The negative electrode active material layer 434 includes the negative electrode active material 431 and the solid electrolyte 421. The negative electrode active material layer 434 may also include a conductive additive and a binder. Note that when metal lithium is used for the negative electrode 430, the negative electrode 430 that does not include the solid electrolyte 421 can be formed, as illustrated in
As the solid electrolyte 421 included in the solid electrolyte layer 420, a sulfide-based solid electrolyte, an oxide-based solid electrolyte, or a halide-based solid electrolyte can be used, for example.
Examples of the sulfide-based solid electrolyte include a thio-silicon-based material (e.g., Li10GeP2S12 and Li3.25Ge0.25P0.75S4), sulfide glass (e.g., 70Li2S·30P2S5, 30Li2S·26B2S3·44LiI, 63Li2S·38SiS2·1Li3PO4, 57Li2S·38SiS2·5Li4SiO4, and 50Li2S·50GeS2), and sulfide-based crystallized glass (e.g., Li7P3S11 and Li3.25P0.95S4). The sulfide-based solid electrolyte has advantages such as high conductivity of some materials, low-temperature synthesis, and ease of maintaining a path for electrical conduction after charging and discharging because of its relative softness.
Examples of the oxide-based solid electrolyte include a material with a perovskite crystal structure (e.g., La2/3−xLi3xTiO3), a material with a NASICON crystal structure (e.g., Li1-YAlYTi2-Y(PO4)3), a material with a garnet crystal structure (e.g., Li7La3Zr2O12), a material with a LISICON crystal structure (e.g., Li14ZnGe4O16), LLZO (Li7La3Zr2O12), oxide glass (e.g., Li3PO4—Li4SiO4 and 50Li4SiO4·50Li3BO3), and oxide-based crystallized glass (e.g., Li1.07Al0.69Ti1.46(PO4)3 and Li1.5Al0.5Ge1.5(PO4)3). The oxide-based solid electrolyte has an advantage of stability in the air.
Examples of the halide-based solid electrolyte include LiAlCl4, Li3InBr6, LiF, LiCl, LiBr, and LiI. Moreover, a composite material in which pores of porous aluminum oxide or porous silica are filled with such a halide-based solid electrolyte can be used as the solid electrolyte.
Alternatively, different solid electrolytes may be mixed and used.
In particular, Li1+xAlxTi2−x(PO4)3 (0 [x [1) having a NASICON crystal structure (hereinafter LATP) is preferable because LATP contains aluminum and titanium, each of which is the element the positive electrode active material used in the secondary battery 400 of one embodiment of the present invention is allowed to contain, and thus a synergistic effect of improving the cycle performance is expected. Moreover, higher productivity due to the reduction in the number of steps is expected. Note that in this specification and the like, a material having a NASICON crystal structure refers to a compound that is represented by M2(XO4)3 (M: transition metal; X: S, P, As, Mo, W, or the like) and has a structure in which MO6 octahedra and XO4 tetrahedra that share common corners are arranged three-dimensionally.
An exterior body of the secondary battery 400 of one embodiment of the present invention can employ a variety of materials and have a variety of shapes, and preferably has a function of applying pressure to the positive electrode, the solid electrolyte layer, and the negative electrode.
The evaluation material is placed on an electrode plate 751, surrounded by an insulating tube 752, and pressed from above by the electrode plate 753.
A stack of a positive electrode 750a, a solid electrolyte layer 750b, and a negative electrode 750c is shown here as an example of the evaluation material, and its cross section is shown in
The electrode plate 751 and the lower component 761 that are electrically connected to the positive electrode 750a correspond to a positive electrode terminal. The electrode plate 753 and the upper component 762 that are electrically connected to the negative electrode 750c correspond to a negative electrode terminal. The electric resistance or the like can be measured while pressure is applied to the evaluation material through the electrode plate 751 and the electrode plate 753.
The exterior body of the secondary battery of one embodiment of the present invention is preferably a package having excellent airtightness. For example, a ceramic package or a resin package can be used. The exterior body is sealed preferably in a closed atmosphere where the outside air is blocked, for example, in a glove box.
The external electrode 771 is electrically connected to the positive electrode 750a through the electrode layer 773a and functions as a positive electrode terminal. The external electrode 772 is electrically connected to the negative electrode 750c through the electrode layer 773b and functions as a negative electrode terminal.
The use of the positive electrode active material 100 obtained in Embodiment 1 achieves an all-solid-state secondary battery having high energy density and favorable output characteristics.
This embodiment can be implemented in appropriate combination with any of the other embodiments.
In this embodiment, an example of application to an electric vehicle (EV) will be described with reference to
The electric vehicle is provided with first batteries 1301a and 1301b as main secondary batteries for driving and a second battery 1311 that supplies electric power to an inverter 1312 for starting a motor 1304. The second battery 1311 is also referred to as a cranking battery (also referred to as a starter battery). The second battery 1311 needs high output and high capacity is not so necessary, and the capacity of the second battery 1311 is lower than that of the first batteries 1301a and 1301b.
The internal structure of the first battery 1301a may be the wound structure illustrated in
Although this embodiment describes an example in which two first batteries 1301a and 1301b are connected in parallel, three or more first batteries may be connected in parallel. When the first battery 1301a is capable of storing sufficient electric power, the first battery 1301b may be omitted. With a battery pack including a plurality of secondary batteries, large electric power can be extracted. The plurality of secondary batteries may be connected in parallel, connected in series, or connected in series after being connected in parallel. The plurality of secondary batteries can also be referred to as an assembled battery.
An in-vehicle secondary battery includes a service plug or a circuit breaker that can cut off high voltage without the use of equipment in order to cut off electric power from a plurality of secondary batteries. The first battery 1301a is provided with such a service plug or a circuit breaker.
Electric power from the first batteries 1301a and 1301b is mainly used to rotate the motor 1304 and is also supplied to in-vehicle parts for 42 V (such as an electric power steering 1307, a heater 1308, and a defogger 1309) through a DC-DC circuit 1306. In the case where there is a rear motor 1317 for the rear wheels, the first battery 1301a is used to rotate the rear motor 1317.
The second battery 1311 supplies electric power to in-vehicle parts for 14 V (such as an audio 1313, power windows 1314, and lamps 1315) through a DC-DC circuit 1310.
The first battery 1301a will be described with reference to
The control circuit portion 1320 may include a memory circuit including a transistor using an oxide semiconductor. A charge control circuit or a battery control system that includes a memory circuit including a transistor using an oxide semiconductor may be referred to as a BTOS (Battery operating system or Battery oxide semiconductor).
A metal oxide functioning as an oxide semiconductor is preferably used. For example, as the oxide 530, a metal oxide such as an In-M-Zn oxide (the element M is one or more selected from aluminum, gallium, yttrium, copper, vanadium, beryllium, boron, titanium, iron, nickel, germanium, zirconium, molybdenum, lanthanum, cerium, neodymium, hafnium, tantalum, tungsten, magnesium, and the like) is preferably used. In particular, the In-M-Zn oxide that can be used as the oxide 530 is preferably a CAAC-OS (C-AxIs Aligned Crystal Oxide Semiconductor) or a CAC-OS (Cloud-Aligned Composite Oxide Semiconductor). Alternatively, an In—Ga oxide or an In—Zn oxide may be used as the oxide 530. The CAAC-OS is an oxide semiconductor that has a plurality of crystal regions each of which has c-axis alignment in a particular direction. Note that the particular direction refers to the thickness direction of a CAAC-OS film, the normal direction of the surface where the CAAC-OS film is formed, or the normal direction of the surface of the CAAC-OS film. The crystal region refers to a region having a periodic atomic arrangement. When an atomic arrangement is regarded as a lattice arrangement, the crystal region also refers to a region with a uniform lattice arrangement. The CAAC-OS has a region where a plurality of crystal regions are connected in the a-b plane direction, and the region has distortion in some cases. Note that distortion refers to a portion where the direction of a lattice arrangement changes between a region with a uniform lattice arrangement and another region with a uniform lattice arrangement in a region where a plurality of crystal regions are connected. That is, the CAAC-OS is an oxide semiconductor having c-axis alignment and having no clear alignment in the a-b plane direction. In addition, the CAC-OS refers to one composition of a material in which elements constituting a metal oxide are unevenly distributed with a size greater than or equal to 0.5 nm and less than or equal to 10 nm, preferably greater than or equal to 1 nm and less than or equal to 3 nm, or a similar size, for example. Note that a state in which one or more metal elements are unevenly distributed and regions including the metal element(s) are mixed with a size greater than or equal to 0.5 nm and less than or equal to 10 nm, preferably greater than or equal to 1 nm and less than or equal to 3 nm, or a similar size in a metal oxide is hereinafter referred to as a mosaic pattern or a patch-like pattern.
In addition, the CAC-OS has a composition in which materials are separated into a first region and a second region to form a mosaic pattern, and the first regions are distributed in the film (this composition is hereinafter also referred to as a cloud-like composition). That is, the CAC-OS is a composite metal oxide having a composition in which the first regions and the second regions are mixed.
Here, the atomic ratios of In, Ga, and Zn to the metal elements contained in the CAC-OS in an In—Ga—Zn oxide are denoted by [In], [Ga], and [Zn], respectively. For example, the first region in the CAC-OS in the In—Ga—Zn oxide has [In] higher than [In] in the composition of the CAC-OS film. Moreover, the second region has [Ga] higher than [Ga] in the composition of the CAC-OS film. Alternatively, for example, the first region has [In] higher than [In] in the second region and [Ga] lower than [Ga] in the second region. Moreover, the second region has [Ga] higher than [Ga] in the first region and [In] lower than [In] in the first region.
Specifically, the first region is a region including indium oxide, indium zinc oxide, or the like as its main component. The second region is a region including gallium oxide, gallium zinc oxide, or the like as its main component. That is, the first region can be referred to as a region containing In as its main component. The second region can be referred to as a region containing Ga as its main component.
Note that a clear boundary between the first region and the second region cannot be observed in some cases.
For example, in EDX mapping obtained by energy dispersive X-ray spectroscopy (EDX), it is confirmed that the CAC-OS in the In—Ga—Zn oxide has a structure in which the region containing In as its main component (the first region) and the region containing Ga as its main component (the second region) are unevenly distributed and mixed.
In the case where the CAC-OS is used for a transistor, a switching function (on/off switching function) can be given to the CAC-OS owing to the complementary action of the conductivity derived from the first region and the insulating property derived from the second region. That is, the CAC-OS has a conducting function in part of the material and has an insulating function in another part of the material; as a whole, the CAC-OS has a function of a semiconductor. Separation of the conducting function and the insulating function can maximize each function. Thus, when the CAC-OS is used for a transistor, high on-state current (Ion), high field-effect mobility (4 and favorable switching operation can be achieved.
An oxide semiconductor has various structures with different properties. Two or more kinds among the amorphous oxide semiconductor, the polycrystalline oxide semiconductor, the a-like OS, the CAC-OS, the nc-OS, and the CAAC-OS may be included in an oxide semiconductor of one embodiment of the present invention.
The control circuit portion 1320 preferably uses a transistor using an oxide semiconductor because the transistor using an oxide semiconductor can be used in a high-temperature environment. For the process simplicity, the control circuit portion 1320 may be formed using transistors of the same conductivity type. A transistor using an oxide semiconductor in its semiconductor layer has an operating ambient temperature range of −40° C. to 150° C., which is wider than that of a single crystal Si transistor, and thus shows a smaller change in characteristics than the single crystal Si transistor when the secondary battery is heated. The off-state current of the transistor using an oxide semiconductor is lower than or equal to the lower measurement limit even at 150° C. regardless of the temperature. On the other hand, the off-state current characteristics of the single crystal Si transistor largely depend on the temperature. For example, at 150° C., the off-state current of the single crystal Si transistor increases, and a sufficiently high current on/off ratio cannot be obtained. The control circuit portion 1320 can improve the degree of safety. When the control circuit portion 1320 is used in combination with a secondary battery including a positive electrode using the positive electrode active material 100 obtained in Embodiment 1, the synergy on safety can be obtained. The secondary battery including the positive electrode using the positive electrode active material 100 obtained in Embodiment 1 and the control circuit portion 1320 can contribute greatly to elimination of accidents due to secondary batteries, such as fires.
The control circuit portion 1320 that uses a memory circuit including a transistor using an oxide semiconductor can also function as an automatic control device for the secondary battery to resolve ten items of causes of instability, such as a micro-short circuit. Examples of functions of resolving the ten items of causes of instability include prevention of overcharging, prevention of overcurrent, control of overheating during charging, maintenance of cell balance of an assembled battery, prevention of overdischarging, a battery indicator, automatic control of charge voltage and current amount according to temperature, control of the amount of charge current according to the degree of deterioration, abnormal behavior detection for a micro-short circuit, and anomaly prediction regarding a micro-short circuit. The control circuit portion 1320 has at least one of these functions. Furthermore, the automatic control device for the secondary battery can be extremely small in size.
A micro-short circuit refers to a minute short circuit caused in a secondary battery. A micro-short circuit refers to not a state where the positive electrode and the negative electrode of a secondary battery are short-circuited so that charging and discharging are impossible, but a phenomenon in which a slight short-circuit current flows through a minute short-circuit portion. Since a large voltage change is caused even when a micro-short circuit occurs in a relatively short time in a minute area, the abnormal voltage value might adversely affect estimation to be performed subsequently.
A cause of a micro-short circuit is a plurality of charging and discharging; an uneven distribution of positive electrode active materials leads to local concentration of current in part of the positive electrode and the negative electrode; and then part of a separator stops functioning or a by-product is generated by a side reaction, which is thought to generate a micro short-circuit.
It can be said that the control circuit portion 1320 not only detects a micro-short circuit but also senses a terminal voltage of the secondary battery and controls the charge and discharge state of the secondary battery. For example, to prevent overcharging, the control circuit portion 1320 can turn off an output transistor of a charging circuit and an interruption switch substantially at the same time.
The control circuit portion 1320 includes a switch portion 1324 that includes at least a switch for preventing overcharging and a switch for preventing overdischarging, a control circuit 1322 for controlling the switch portion 1324, and a portion for measuring the voltage of the first battery 1301a. The control circuit portion 1320 is set to have the upper limit voltage and the lower limit voltage of the secondary battery used, and controls the upper limit of current from the outside, the upper limit of output current to the outside, or the like. The range from the lower limit voltage to the upper limit voltage of the secondary battery is a recommended voltage range, and when a voltage is out of the range, the switch portion 1324 operates and functions as a protection circuit. The control circuit portion 1320 can also be referred to as a protection circuit because it controls the switch portion 1324 to prevent overdischarging and overcharging. For example, when the control circuit 1322 detects a voltage that is likely to cause overcharging, current is interrupted by turning off the switch in the switch portion 1324. Furthermore, a function of interrupting current in accordance with a temperature rise may be set by providing a PTC element in the charge and discharge path. The control circuit portion 1320 includes an external terminal 1325 (+IN) and an external terminal 1326 (−IN).
The switch portion 1324 can be formed by a combination of an n-channel transistor and a p-channel transistor. The switch portion 1324 is not limited to including a switch having a Si transistor using single crystal silicon; the switch portion 1324 may be formed using a power transistor containing Ge (germanium), SiGe (silicon germanium), GaAs (gallium arsenide), GaAlAs (gallium aluminum arsenide), InP (indium phosphide), SiC (silicon carbide), ZnSe (zinc selenide), GaN (gallium nitride), GaOx (gallium oxide; x is a real number greater than 0), or the like. A memory element using an OS transistor can be freely placed by being stacked over a circuit using a Si transistor, for example; hence, integration can be easy. Furthermore, an OS transistor can be manufactured with a manufacturing apparatus similar to that for a Si transistor and thus can be manufactured at low cost. That is, the control circuit portion 1320 using OS transistors can be stacked over the switch portion 1324 so that they can be integrated into one chip. Since the area occupied by the control circuit portion 1320 can be reduced, a reduction in size is possible.
The first batteries 1301a and 1301b mainly supply electric power to in-vehicle parts for 42 V (for a high-voltage system), and the second battery 1311 supplies electric power to in-vehicle parts for 14 V (for a low-voltage system). Lead batteries are usually used for the second battery 1311 due to cost advantage. Lead batteries have disadvantages compared with lithium-ion secondary batteries in that they have a larger amount of self-discharge and are more likely to degrade due to a phenomenon called sulfation. There is an advantage that the second battery 1311 can be maintenance-free when it uses a lithium-ion secondary battery; however, in the case of long-term use, for example three years or more, anomalous occurrence that cannot be determined at the time of manufacturing might occur. In particular, when the second battery 1311 that starts the inverter becomes inoperative, the motor cannot be started even when the first batteries 1301a and 1301b have remaining capacity; thus, in order to prevent this, in the case where the second battery 1311 is a lead storage battery, the second battery is supplied with electric power from the first battery to constantly maintain a fully-charged state.
In this embodiment, an example in which a lithium-ion secondary battery is used as each of the first battery 1301a and the second battery 1311 is described. As the second battery 1311, a lead storage battery, an all-solid-state battery, or an electric double layer capacitor may be used. For example, the all-solid-state battery in Embodiment 5 may be used. Using the all-solid-state battery in Embodiment 5 as the second battery 1311 achieves high capacity, a high degree of safety, reduction in size, and reduction in weight.
Regenerative energy generated by rolling of tires 1316 is transmitted to the motor 1304 through a gear 1305, and is stored in the second battery 1311 from a motor controller 1303 and a battery controller 1302 through a control circuit portion 1321. Alternatively, the regenerative energy is stored in the first battery 1301a from the battery controller 1302 through the control circuit portion 1320. Alternatively, the regenerative energy is stored in the first battery 1301b from the battery controller 1302 through the control circuit portion 1320. For efficient charging with regenerative energy, the first batteries 1301a and 1301b are preferably capable of fast charging.
The battery controller 1302 can set the charge voltage, charge current, and the like of the first batteries 1301a and 1301b. The battery controller 1302 can set charge conditions in accordance with charge characteristics of a secondary battery used, so that fast charging can be performed.
Although not illustrated, when the electric vehicle is connected to an external charger, a plug of the charger or a connection cable of the charger is electrically connected to the battery controller 1302. Electric power supplied from the external charger is stored in the first batteries 1301a and 1301b through the battery controller 1302. Some chargers are provided with a control circuit, in which case the function of the battery controller 1302 is not used; to prevent overcharging, the first batteries 1301a and 1301b are preferably charged through the control circuit portion 1320. In addition, a connection cable or a connection cable of the charger is sometimes provided with a control circuit. The control circuit portion 1320 is also referred to as an ECU (Electronic Control Unit). The ECU is connected to a CAN (Controller Area Network) provided in the electric vehicle. The CAN is a type of a serial communication standard used as an in-vehicle LAN. The ECU includes a microcomputer. Moreover, the ECU uses a CPU or a GPU.
External chargers installed at charging stations and the like have a 100 V outlet, a 200 V outlet, or a three-phase 200V outlet with 50 kW, for example. Furthermore, charging can be performed with electric power supplied from external charging equipment by a contactless power feeding system or the like.
For fast charging, secondary batteries that can withstand high-voltage charging have been desired to perform charging in a short time.
The above-described secondary battery in this embodiment includes a high-density positive electrode with use of the positive electrode active material 100 obtained in Embodiment 1. Moreover, it is possible to achieve a secondary battery in which graphene is used as a conductive additive, the electrode layer is formed thick to increase the loading amount while suppressing a reduction in capacity, and the electrical characteristics are significantly improved in synergy with maintenance of high capacity. This secondary battery is particularly effectively used in a vehicle and can achieve a vehicle that has a long range, specifically a driving range per charge of 500 km or longer, without increasing the proportion of the weight of the secondary battery to the weight of the entire vehicle.
Specifically, in the above-described secondary battery in this embodiment, the use of the positive electrode active material 100 described in Embodiment 1 can increase the operating voltage of the secondary battery, and the increase in charging voltage can increase the available capacity. Moreover, using the positive electrode active material 100 described in Embodiment 1 in the positive electrode can provide an automotive secondary battery having excellent cycle performance.
Next, examples in which the secondary battery of one embodiment of the present invention is mounted on a vehicle, typically a transport vehicle, will be described.
Mounting the secondary battery illustrated in any of
The automobile 2001 can be charged when the secondary battery of the automobile 2001 receives electric power from an external charging equipment through a plug-in system, a contactless charging system, or the like. In charging, a given method such as CHAdeMO (registered trademark) or Combined Charging System may be employed as a charging method, the standard of a connector, and the like as appropriate. The secondary battery may be a charging station provided in a commerce facility or a household power supply. For example, a plug-in technique enables an exterior power supply to charge a power storage device incorporated in the automobile 2001. Charging can be performed by converting AC power into DC power through a converter such as an ACDC converter.
Although not illustrated, the vehicle can include a power receiving device so as to be charged by being supplied with electric power from an above-ground power transmitting device in a contactless manner. For the contactless power feeding system, by fitting a power transmitting device in a road or an exterior wall, charging can be performed not only when the vehicle is stopped but also when driven. In addition, the contactless power feeding system may be utilized to perform transmission and reception of electric power between two vehicles. Furthermore, a solar cell may be provided in the exterior of the vehicle to charge the secondary battery when the vehicle stops or moves. To supply electric power in such a contactless manner, an electromagnetic induction method or a magnetic resonance method can be used.
The secondary battery module of the aircraft 2004 has eight 4 V secondary batteries connected in series, which has the maximum voltage of 32 V, for example. A battery pack 2203 has a function similar to that in
This embodiment can be implemented in appropriate combination with any of the other embodiments.
In this embodiment, examples in which the secondary battery of one embodiment of the present invention is mounted on a building will be described with reference to
A house illustrated in
The electric power stored in the power storage device 2612 can also be supplied to other electronic devices in the house. Thus, with the use of the power storage device 2612 of one embodiment of the present invention as an uninterruptible power source, electronic devices can be used even when electric power cannot be supplied from a commercial power source due to power failure or the like.
The power storage device 791 is provided with a control device 790, and the control device 790 is electrically connected to a distribution board 703, a power storage controller (also referred to as control device) 705, an indicator 706, and a router 709 through wirings.
Electric power is transmitted from a commercial power source 701 to the distribution board 703 through a service wire mounting portion 710. Moreover, electric power is transmitted to the distribution board 703 from the power storage device 791 and the commercial power source 701, and the distribution board 703 supplies the transmitted electric power to a general load 707 and a power storage load 708 through outlets (not illustrated).
The general load 707 is, for example, an electronic device such as a TV or a personal computer. The power storage load 708 is, for example, an electronic device such as a microwave, a refrigerator, or an air conditioner.
The power storage controller 705 includes a measuring portion 711, a predicting portion 712, and a planning portion 713. The measuring portion 711 has a function of measuring the amount of electric power consumed by the general load 707 and the power storage load 708 during a day (e.g., from midnight to midnight). The measuring portion 711 may have a function of measuring the amount of electric power of the power storage device 791 and the amount of electric power supplied from the commercial power source 701. The predicting portion 712 has a function of predicting, on the basis of the amount of electric power consumed by the general load 707 and the power storage load 708 during a given day, the demand for electric power consumed by the general load 707 and the power storage load 708 during the next day. The planning portion 713 has a function of making a charge and discharge plan of the power storage device 791 on the basis of the demand for electric power predicted by the predicting portion 712.
The amount of electric power consumed by the general load 707 and the power storage load 708 and measured by the measuring portion 711 can be checked with the indicator 706. It can be checked with an electronic device such as a TV or a personal computer through the router 709. Furthermore, it can be checked with a portable electronic terminal such as a smartphone or a tablet through the router 709. With the indicator 706, the electronic device, or the portable electronic terminal, for example, the demand for electric power depending on a time period (or per hour) that is predicted by the predicting portion 712 can be checked.
This embodiment can be implemented in appropriate combination with any of the other embodiments.
This embodiment will describe examples in which the power storage device of one embodiment of the present invention is mounted on a motorcycle and a bicycle.
The electric bicycle 8700 includes a power storage device 8702. The power storage device 8702 can supply electricity to a motor that assists a rider. The power storage device 8702 is portable, and
In the motor scooter 8600 illustrated in
In this embodiment, examples of electronic devices each including the secondary battery of one embodiment of the present invention will be described. Examples of the electronic device including the secondary battery include a television device (also referred to as a television or a television receiver), a monitor of a computer and the like, a digital camera, a digital video camera, a digital photo frame, a mobile phone (also referred to as a cellular phone or a mobile phone device), a portable game console, a portable information terminal, an audio reproducing device, and a large-sized game machine such as a pachinko machine. Examples of the portable information terminal include a laptop personal computer, a tablet terminal, an e-book terminal, and a mobile phone.
The mobile phone 2100 is capable of executing a variety of applications such as mobile phone calls, e-mailing, viewing and editing texts, music reproduction, Internet communication, and a computer game.
With the operation button 2103, a variety of functions such as time setting, power on/off, on/off of wireless communication, setting and cancellation of a silent mode, and setting and cancellation of a power saving mode can be performed. For example, the functions of the operation button 2103 can be set freely by the operating system incorporated in the mobile phone 2100.
The mobile phone 2100 can employ near field communication based on an existing communication standard. For example, mutual communication between the mobile phone 2100 and a headset capable of wireless communication can be performed, and thus hands-free calling is possible.
Moreover, the mobile phone 2100 includes the external connection port 2104, and data can be directly transmitted to and received from another information terminal via a connector. In addition, charging can be performed via the external connection port 2104. Note that the charging operation may be performed by wireless power feeding without using the external connection port 2104.
The mobile phone 2100 preferably includes a sensor. As the sensor, a human body sensor such as a fingerprint sensor, a pulse sensor, or a temperature sensor, a touch sensor, a pressure sensitive sensor, or an acceleration sensor is preferably mounted, for example.
The microphone 6402 has a function of detecting a speaking voice of a user, an environmental sound, and the like. The speaker 6404 has a function of outputting sound. The robot 6400 can communicate with the user using the microphone 6402 and the speaker 6404.
The display portion 6405 has a function of displaying various kinds of information. The robot 6400 can display information desired by the user on the display portion 6405. The display portion 6405 may be provided with a touch panel. Moreover, the display portion 6405 may be a detachable information terminal, in which case charging and data communication can be performed when the display portion 6405 is set at the home position of the robot 6400.
The upper camera 6403 and the lower camera 6406 each have a function of taking an image of the surroundings of the robot 6400. The obstacle sensor 6407 can detect an obstacle in the direction where the robot 6400 advances with the moving mechanism 6408. The robot 6400 can move safely by recognizing the surroundings with the upper camera 6403, the lower camera 6406, and the obstacle sensor 6407.
The robot 6400 further includes, in its inner region, the secondary battery 6409 of one embodiment of the present invention and a semiconductor device or an electronic component. A secondary battery including a positive electrode using the positive electrode active material 100 obtained in Embodiment 1 has high energy density and a high degree of safety, and thus can be used safely for a long time over a long period of time and is preferable as the secondary battery 6409 included in the robot 6400.
For example, the cleaning robot 6300 can determine whether there is an obstacle such as a wall, furniture, or a step by analyzing images taken by the cameras 6303. In the case where the cleaning robot 6300 detects an object, such as a wire, that is likely to be caught in the brush 6304 by image analysis, the rotation of the brush 6304 can be stopped. The cleaning robot 6300 includes, in its inner region, the secondary battery 6306 of one embodiment of the present invention and a semiconductor device or an electronic component. A secondary battery including a positive electrode using the positive electrode active material 100 obtained in Embodiment 1 has high energy density and a high degree of safety, and thus can be used safely for a long time over a long period of time and is preferable as the secondary battery 6306 included in the cleaning robot 6300.
For example, the secondary battery of one embodiment of the present invention can be provided in a glasses-type device 4000 illustrated in
The secondary battery of one embodiment of the present invention can be provided in a headset-type device 4001. The headset-type device 4001 includes at least a microphone part 4001a, a flexible pipe 4001b, and an earphone portion 4001c. The secondary battery can be provided in the flexible pipe 4001b or the earphone portion 4001c. A secondary battery including a positive electrode using the positive electrode active material 100 obtained in Embodiment 1 has high energy density and achieves a structure that accommodates space saving due to a reduction in size of the housing.
The secondary battery of one embodiment of the present invention can be provided in a device 4002 that can be attached directly to a body. A secondary battery 4002b can be provided in a thin housing 4002a of the device 4002. A secondary battery including a positive electrode using the positive electrode active material 100 obtained in Embodiment 1 has high energy density and achieves a structure that accommodates space saving due to a reduction in size of the housing.
The secondary battery of one embodiment of the present invention can be provided in a device 4003 that can be attached to clothes. A secondary battery 4003b can be provided in a thin housing 4003a of the device 4003. A secondary battery including a positive electrode using the positive electrode active material 100 obtained in Embodiment 1 has high energy density and achieves a structure that accommodates space saving due to a reduction in size of the housing.
The secondary battery of one embodiment of the present invention can be provided in a belt-type device 4006. The belt-type device 4006 includes a belt portion 4006a and a wireless power feeding and receiving portion 4006b, and the secondary battery can be provided in the inner region of the belt portion 4006a. A secondary battery including a positive electrode using the positive electrode active material 100 obtained in Embodiment 1 has high energy density and achieves a structure that accommodates space saving due to a reduction in size of the housing.
The secondary battery of one embodiment of the present invention can be provided in a watch-type device 4005. The watch-type device 4005 includes a display portion 4005a and a belt portion 4005b, and the secondary battery can be provided in the display portion 4005a or the belt portion 4005b. A secondary battery including a positive electrode using the positive electrode active material 100 obtained in Embodiment 1 has high energy density and achieves a structure that accommodates space saving due to a reduction in size of the housing.
The display portion 4005a can display various kinds of information such as time and reception information of an e-mail and an incoming call.
The watch-type device 4005 is a wearable device that is wound around an arm directly; thus, a sensor that measures the pulse, the blood pressure, or the like of the user may be incorporated therein. Data on the exercise quantity and health of the user can be stored to be used for health maintenance.
Since the secondary battery in the watch-type device 4005 is required to be small and lightweight, the use of the positive electrode active material 100 obtained in Embodiment 1 in the positive electrode of the secondary battery 913 enables the secondary battery 913 to have high energy density and a small size.
This embodiment can be implemented in appropriate combination with the other embodiments.
(Example 1) In this example, after the positive electrode active material of one embodiment of the present invention was formed, a plurality of coin-type battery cells were fabricated and their cycle performance was evaluated.
Samples fabricated in this example are described. Four samples were fabricated; the samples were fabricated under the same conditions by the same procedures except for a solvent in a sol-gel method (the amount of 2-propanol). The samples were fabricated with the amount of 2-propanol being 0 ml, 1 ml, 5 ml, or 10 ml.
The positive electrode active material obtained by the method described in Embodiment 1 was used as positive electrode active materials of the samples. The positive electrode active material 100 was obtained in accordance with the flow of
The samples fabricated in this example will be described with reference to the fabrication method shown in
As LiMO2 in Step S14, with the use of cobalt as the transition metal M, commercially available lithium cobalt oxide (Cellseed C-10N produced by NIPPON CHEMICAL INDUSTRIAL CO., LTD.) not containing any additive was prepared. Lithium fluoride and magnesium fluoride were mixed therewith by a solid phase method, as in Step S21 to Step S23 and Step S41 and Step S42. Lithium fluoride and magnesium fluoride were added such that the number of molecules of lithium fluoride was 0.33 and the number of molecules of magnesium fluoride was 1 with the number of cobalt atoms assumed as 100. The mixture here is the mixture 903.
Next, annealing was performed in a manner similar to that of Step S43. In a square-shaped alumina container, 30 g of the mixture 903 was placed, a lid was put on the container, and heating was performed in a muffle furnace. The atmosphere in the furnace was purged and an oxygen gas was introduced; the oxygen flow was stopped during the heating. The annealing temperature was 900° C., and the annealing time was 20 hours.
To the composite oxide that had been heated, nickel hydroxide was added and mixed by a dry method as Step S61-1. Nickel hydroxide was added so that when the number of cobalt atoms is 100, the number of nickel atoms is 0.5.
Then, mixing was performed by a sol-gel method as Step S61-2. In the case where a sol-gel method is used, a solvent used for the sol-gel method is prepared. As the solvent, ketone such as acetone, alcohol such as ethanol or isopropanol, ether, dioxane, acetonitrile, N-methyl-2-pyrrolidone (NMP), or the like can be used. An aprotic solvent that hardly reacts with lithium is further preferably used. In this example, aluminum alkoxide was used a metal alkoxide; in the case of aluminum, for example, aluminum alkoxide was added such that the number of aluminum atoms is 0.5 with the number of cobalt atoms regarded as 100. In the case where zirconium is used, zirconium alkoxide such as zirconium isopropoxide or the like can be used. In the case of zirconium, zirconium alkoxide was added such that the number of zirconium atoms is 0.1 at %, 0.25 at %, 0.5 at %, or 1 at % in each of the samples with the number of cobalt atoms regarded as 100. Step S63, a heat treatment after the sol-gel method, was performed at 850° C. for two hours. The positive electrode active material 100 obtained through the above steps was used in the samples.
Acetylene black was used as a conductive additive, the formed positive electrode active material and the conductive additive were mixed to form a slurry, and the slurry was applied to a current collector of aluminum.
After the slurry was applied onto the current collector, a solvent was volatilized. After that, pressure was applied at 210 kN/m, and then pressure was applied at 1467 kN/m. Through the above process, the positive electrode was obtained. The loading amount of the positive electrode was approximately 7 mg/cm2.
Using the formed positive electrodes, CR2032 type coin-type battery cells (a diameter of 20 mm, a height of 3.2 mm) were fabricated.
A lithium metal was used for a counter electrode.
As an electrolyte of the sample, 1 mol/L of lithium hexafluorophosphate (LiPF6) was used, and ethylene carbonate (EC) and diethyl carbonate (DEC) were mixed at EC:DEC=3:7 (volume ratio). The amount of vinylene carbonate (VC) added as an additive was set to 2 wt % with respect to the solvent.
As a separator, 25-μm-thick polypropylene was used.
A positive electrode can and a negative electrode can that were formed using stainless steel (SUS) were used.
In the evaluation of cycle performance, the charging voltage was 4.7 V. The measurement temperature was set to 25° C. CC/CV charging (0.5 C, 0.05 C cut) and CC discharging (0.5 C, 2.5 V cut) were performed, and a 10-minute break was taken before the next charging. Note that 1 C was 200 mA/g in this example and the like.
The graphs indicate that the positive electrode active material of one embodiment of the present invention, in the sample with the amount of 2-propanol being 5 ml and the sample with the amount of 2-propanol being 10 ml, is a positive electrode active material where reduction of charge and discharge capacity is reduced even when high-voltage (e.g., at 4.7 V) charge and discharge are repeated.
A sample in which the amount of 2-propanol was 40 ml was also fabricated; however, good cycle performance was not obtained.
Note that the comparative example in
In addition,
Among these samples, those in the sample with the amount of zirconium being 0.1 at % and the sample with the amount of zirconium being 0.25 at %, in particular, were found to be positive electrode active materials where a reduction in charge and discharge capacity is suppressed even when charge and discharge at a high voltage such as 4.7 V are repeated.
The powder resistivity of the obtained positive electrode active material particles was measured, using a powder resistivity measurement system (MCP-PD51, produced by Mitsubishi Chemical Analytech Co., Ltd.). The positive electrode active material was put in a measuring cell, and the powder was compressed by pressure applied with the use of a compression rod from above. At this time, while the pressure and volume were measured, current was made to flow through the powder and the resistance value was measured by Loresta-GP with the use of a four probe method. Note that the powder resistivity depends on the density.
(Example 2) In this example, after the positive electrode active material of one embodiment of the present invention was formed in accordance with the flow shown in
Sample 1 that was fabricated in this example will be described with reference to the formation method shown in
As LiMO2 in Step S14, with the use of cobalt as the transition metal M, commercially available lithium cobalt oxide (Cellseed C-10N produced by NIPPON CHEMICAL INDUSTRIAL CO., LTD.) not containing any additive was prepared. Lithium fluoride and magnesium fluoride were mixed therewith by a solid phase method, as in Step S21 to Step S23 and Step S41 and Step S42. Lithium fluoride and magnesium fluoride were added such that the number of molecules of lithium fluoride was 0.33 and the number of molecules of magnesium fluoride was 1 with the number of cobalt atoms assumed as 100. The mixture here is the mixture 903.
Next, annealing was performed in a manner similar to that of Step S43. In a square-shaped alumina container, 30 g of the mixture 903 was placed, a lid was put on the container, and heating was performed in a muffle furnace. The atmosphere in the furnace was purged and an oxygen gas was introduced; the oxygen flow continued during the heating. The annealing temperature was 850° C., and the annealing time was 60 hours.
To the composite oxide that had been heated, nickel hydroxide was added and mixed by a dry method as Step S61-1. Nickel hydroxide was added so that when the number of cobalt atoms is 100, the number of nickel atoms is 0.5.
Then, mixing was performed by a sol-gel method as Step S61-2. In the case of employing the sol-gel method, a solvent used for the sol-gel method is prepared. As the solvent, ketone such as acetone, alcohol such as ethanol or isopropanol, ether, dioxane, acetonitrile, N-methyl-2-pyrrolidone (NMP), or the like can be used. An aprotic solvent that hardly reacts with lithium is further preferably used. As the solvent used in this example, the amount of 2-propanol was set to 10 ml.
In this example, aluminum alkoxide was used as a metal alkoxide; in the case of aluminum, for example, aluminum alkoxide was added such that the number of aluminum atoms is 0.5 with the number of cobalt atoms regarded as 100. In the case where zirconium is used, zirconium alkoxide such as zirconium isopropoxide or the like can be used. In the case of zirconium, for example, zirconium alkoxide was added such that the number of zirconium atoms is 0.25 with the number of cobalt atoms regarded as 100. Heat treatment of Step S63 after the sol-gel method was performed at 850° C. for two hours. Then, crushing was performed as Step S64, and the positive electrode active material 100 that was collected and obtained was used for the sample.
A slurry obtained by mixing positive electrode active material particles having a plurality of projections containing Zr on the surface, AB (acetylene black), and PVDF (polyvinylidene fluoride) such that the positive electrode active material: AB:PVDF=95:3:2 (weight ratio) was applied onto a current collector (aluminum foil) was used. As a solvent of the slurry, NMP (N-methyl-2-pyrrolidone) was used.
After the slurry was applied onto the current collector, a solvent was volatilized. After that, pressure was applied at 210 kN/m, and then pressure was applied at 1467 kN/m. Through the above process, the positive electrode was obtained. The carried amount of the positive electrode was approximately 20 mg/cm2.
As an electrolyte contained in an electrolytic solution, 1 mol/L of lithium hexafluorophosphate (LiPF6) was used. As the electrolytic solution, a solution in which ethylene carbonate (EC) and diethyl carbonate (DEC) were mixed at EC:DEC=3:7 (volume ratio) was used. Note that for secondary batteries used for evaluating the cycle performance, 2 wt % of vinylene carbonate (VC) was added to the electrolytic solution.
As a separator, 25-μm-thick polypropylene was used.
Graphite was used for the negative electrode. A slurry in which graphite, carbon nanotube (VGCF (registered trademark)), CMC (carboxymethyl cellulose) thickener, and SBR (styrene-butadiene rubber) were mixed at 96:1:1:2 was applied onto a current collector (copper foil).
Note that the representative values of vapor-grown carbon fiber (VGCF (registered trademark)) that was used are as follows: the fiber diameter is 150 nm; the fiber length is 10 μm to 20 μm, inclusive; the real density is 2.1 g/cm3; and the specific surface area is 13 m2/g. Note that when a cross section perpendicular to a fiber axis is regarded as a cutting plane in a two-dimensional SEM image, the fiber diameter is a diameter of a perfect circle that circumscribes the cutting plane. The real density is a density calculated using a volume occupied by a substance itself. The specific surface area is the surface area of an object per unit mass or per unit volume.
The measurement temperature was set to 25° C. Two hundred thirty three cycles of charging and discharging were performed at 4.5 V (CCCV, 0.2 C, a cutoff current of 0.1 C) and 3 V (CC, 0.2 C), respectively. One-minute break was taken in the cycle test. Note that here, 1 C was set to 200 mA/g, which was a current value per weight of the positive electrode active material.
The capacity retention rate of Sample 1 right after the 233 cycles was 95.6%. The maximum value of the capacity of Sample 1 was 192.4 mAh/g. Note that, although only the data shown in
Note that the comparative example is the same as Sample 1 except that a positive electrode active material to which Zr was not added was used for the comparative example. The maximum value of the capacity of the comparative example was 188 mAh/g, and the capacity retention rate was 91.5% right after the 233 cycles.
In this example, an SEM image of the positive electrode active material obtained under the same conditions as those for the formation in Example 1 is shown in
A half cell was fabricated as Sample 2, using the same sample, and the cycle test that is the same as Example 1 (cycle test with a charging voltage of 4.7 V at 25° C.) was performed. The obtained cycle performance is shown in
In
In
The experimental results of the samples with different fabrication flows are described in this example; although there was a difference in results, the results with high reliability were obtained.
100: positive electrode active material, 101: projection, 102: projection, 103: projection, 300: secondary battery, 301: positive electrode can, 302: negative electrode can, 303: gasket, 304: positive electrode, 305: positive electrode current collector, 306: positive electrode active material layer, 307: negative electrode, 308: negative electrode current collector, 309: negative electrode active material layer, 310: separator, 312: washer, 313: ring-shaped insulator, 322: spacer, 400: secondary battery, 410: positive electrode, 411: positive electrode active material, 413: positive electrode current collector, 414: positive electrode active material layer, 420: solid electrolyte layer, 421: solid electrolyte, 430: negative electrode, 431: negative electrode active material, 433: negative electrode current collector, 434: negative electrode active material layer, 500: secondary battery, 501: positive electrode current collector, 502: positive electrode active material layer, 503: positive electrode, 504: negative electrode current collector, 505: negative electrode active material layer, 506: negative electrode, 507: separator, 508: electrolyte solution, 509: exterior body, 510: positive electrode lead electrode, 511: negative electrode lead electrode, 513: secondary battery, 514: terminal, 515: sealant, 517: antenna, 519: layer, 529: label, 530: oxide, 531: secondary battery pack, 540: circuit board, 550: current collector, 551: one, 552: other, 553: acetylene black, 554: graphene, 555: carbon nanotube, 561: active material, 562: active material, 590: control circuit, 590a: circuit system, 590b: circuit system, 600: secondary battery, 601: positive electrode cap, 602: battery can, 603: positive electrode terminal, 604: positive electrode, 605: separator, 606: negative electrode, 607: negative electrode terminal, 608: insulating plate, 609: insulating plate, 611: PTC element, 613: safety valve mechanism, 614: conductive plate, 615: power storage system, 616: secondary battery, 620: control circuit, 621: wiring, 622: wiring, 623: wiring, 624: conductor, 625: insulator, 626: wiring, 627: wiring, 628: conductive plate, 700: power storage device, 701: commercial power source, 703: distribution board, 705: power storage controller, 706: indicator, 707: general load, 708: power storage load, 709: router, 710: wire mounting portion, 711: measuring portion, 712: predicting portion, 713: planning portion, 750a: positive electrode, 750b: solid electrolyte layer, 750c: negative electrode, 751: electrode plate, 752: insulating tube, 753: electrode plate, 761: lower component, 762: upper component, 764: butterfly nut, 765: O ring, 766: insulator, 770a: package component, 770b: package component, 770c: package component, 771: external electrode, 772: external electrode, 773a: electrode layer, 773b: electrode layer, 790: control device, 791: power storage device, 796: underfloor space, 799: building, 902: mixture, 903: mixture, 904: mixture, 911a: terminal, 911b: terminal, 913: secondary battery, 930: housing, 930a: housing, 930b: housing, 931: negative electrode, 931a: negative electrode active material layer, 932: positive electrode, 932a: positive electrode active material layer, 933: separator, 950: wound body, 950a: wound body, 951: terminal, 952: terminal, 1300: rectangular secondary battery, 1301a: battery, 1301b: battery, 1302: battery controller, 1303: motor controller, 1304: motor, 1305: gear, 1306: DC-DC circuit, 1307: electric power steering, 1308: heater, 1309: defogger, 1310: DC-DC circuit, 1311: battery, 1312: inverter, 1313: audio, 1314: power window, 1315: lamp, 1316: tire, 1317: rear motor, 1320: control circuit portion, 1321: control circuit portion, 1322: control circuit, 1324: switch portion, 1325: external terminal, 1326: external terminal, 1413: fixing portion, 1414: fixing portion, 1415: battery pack, 1421: wiring, 1422: wiring, 2001: automobile, 2002: transporter, 2003: transport vehicle, 2004: aircraft, 2100: mobile phone, 2101: housing, 2102: display portion, 2103: operation button, 2104: external connection port, 2105: speaker, 2106: microphone, 2107: secondary battery, 2200: battery pack, 2201: battery pack, 2202: battery pack, 2203: battery pack, 2300: unmanned aircraft, 2301: secondary battery, 2302: rotor, 2303: camera, 2603: vehicle, 2604: charging equipment, 2610: solar panel, 2611: wiring, 2612: power storage device, 4000: glasses-type device, 4000a: frame, 4000b: display portion, 4001: headset-type device, 4001a: microphone part, 4001b: flexible pipe, 4001c: earphone portion, 4002: device, 4002a: housing, 4002b: secondary battery, 4003: device, 4003a: housing, 4003b: secondary battery, 4005: watch-type device, 4005a: display portion, 4005b: belt portion, 4006: belt-type device, 4006a: belt portion, 4006b: wireless power feeding and receiving portion, 6300: cleaning robot, 6301: housing, 6302: display portion, 6303: camera, 6304: brush, 6305: operation button, 6306: secondary battery, 6310: dust, 6400: robot, 6401: illuminance sensor, 6402: microphone, 6403: upper camera, 6404: speaker, 6405: display portion, 6406: lower camera, 6407: obstacle sensor, 6408: moving mechanism, 6409: secondary battery, 8600: scooter, 8601: side mirror, 8602: power storage device, 8603: indicator light, 8604: under-seat storage unit, 8700: electric bicycle, 8701: storage battery, 8702: power storage device, 8703: display portion, 8704: control circuit
| Number | Date | Country | Kind |
|---|---|---|---|
| 2020-098575 | Jun 2020 | JP | national |
| 2020-150851 | Sep 2020 | JP | national |
| 2021-066280 | Apr 2021 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/IB2021/054818 | 6/2/2021 | WO |
