WO2015004856A1 - リチウム二次電池用混合活物質、リチウム二次電池用電極、リチウム二次電池及び蓄電装置 - Google Patents
リチウム二次電池用混合活物質、リチウム二次電池用電極、リチウム二次電池及び蓄電装置 Download PDFInfo
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Definitions
- the present invention relates to a mixed active material for a lithium secondary battery, an electrode for a lithium secondary battery containing the mixed active material, a lithium secondary battery including the electrode, and a power storage device including the battery.
- non-aqueous electrolyte secondary batteries represented by lithium ion secondary batteries, in particular lithium secondary batteries, are widely installed in portable terminals and the like.
- LiCoO 2 is mainly used as a positive electrode active material.
- the discharge capacity of LiCoO 2 is about 120 to 130 mAh / g.
- LiCoO 2 and other compounds are known as a positive electrode active material for a lithium secondary battery.
- Li [Co 1-2x Ni x Mn x ] O 2 (0 ⁇ x ⁇ 1/2), which has an ⁇ -NaFeO 2 type crystal structure and is a solid solution of three components of LiCoO 2 , LiNiO 2 and LiMnO 2 ” was announced in 2001.
- LiNi 1/2 Mn 1/2 O 2 and LiCo 1/3 Ni 1/3 Mn 1/3 O 2 which are examples of the solid solution, have a discharge capacity of 150 to 180 mAh / g, and are charged / discharged. Excellent cycle performance.
- LiMeO 2 type active material For the so-called “LiMeO 2 type” active material as described above, the composition ratio Li / Me of lithium (Li) with respect to the ratio of transition metal (Me) is larger than 1, for example, Li / Me is 1.25 to 1.6.
- lithium-rich active materials see, for example, Patent Documents 1 and 2).
- Such a material can be expressed as Li 1 + ⁇ Me 1- ⁇ O 2 ( ⁇ > 0).
- Patent Documents 1 and 2 describe active materials as described above. Further, in these patent documents, a positive electrode potential range of 4.3 V (vs. Li / Li + ) and 4.8 V or less (vs. Li / Li + ) is described as a battery manufacturing method using the active material. In this case, the maximum potential of the positive electrode during charging is 4.3 V (vs. Li / Li + ) or less. Or even if it is a case where the charge method which is less than 4.4V (vs.Li/Li ⁇ +> ) is employ
- Patent Document 3 “a method for producing a positive electrode active material for obtaining a positive electrode active material from a lithium-containing oxide, including a step of treating the lithium-containing oxide with an acidic aqueous solution, 1 + includes x (Mn y M 1-y ) 1-x O 2 (0 ⁇ x ⁇ 0.4,0 ⁇ y ⁇ 1), wherein M includes at least one transition metal except manganese, the acidic aqueous solution
- the amount of hydrogen ions therein is xmol or more and less than 5xmol with respect to 1 mol of the lithium-containing oxide.
- the invention of (Claim 5) is described. "Providing a high-capacity positive electrode active material and a method for producing the positive electrode active material that enable excellent load characteristics and high initial charge / discharge efficiency of the nonaqueous electrolyte secondary battery” (paragraph [0009]) Has been .
- Patent Document 4 states that “compositional formula: xLi 2 M 1 O 3. (1-x) LiM 2 O 2 (M 1 is one or more metal elements in which tetravalent manganese is essential, and M 2 is one or more. A metal element of 0 ⁇ x ⁇ 1, Li may be partially substituted with hydrogen.)
- An acid treatment step in which an acid solution is brought into contact with the active material represented by: A method for producing a positive electrode active material for a lithium ion secondary battery, wherein the material comprises a lithium filling step in which a lithium solution containing a lithium compound is brought into contact with the substance.
- “Electricity by activation of cathode active material And to provide a method for producing a cathode active material for a lithium ion secondary battery capable of suppressing a reduction in capacity “(paragraph [0011]) are shown.
- Patent Document 5 states that “general formula (2) Li 2-0.5x Mn 1-x M 1.5x O 3 (2) (in formula (2), Li is lithium, Mn is manganese, and M is Ni. ⁇ Co ⁇ Mn ⁇ (Ni is nickel, Co is cobalt, Mn is manganese, ⁇ , ⁇ and ⁇ are 0 ⁇ ⁇ 0.5, 0 ⁇ ⁇ ⁇ 0.33, 0 ⁇ ⁇ 0.5 And x satisfies the relationship of 0 ⁇ x ⁇ 1.00.) And a layered transition metal oxide having a crystal structure belonging to the space group C2 / m in an acidic solution.
- a positive electrode active material for a lithium ion secondary battery according to claim 1 or 2 characterized in that it is obtained by dipping.
- Patent Document 6 states that “the oxide represented by the general formula (1), having Li vacancies and oxygen vacancies in the crystal structure, and the square of the primary particle surface according to JIS B 0601: 2001”.
- Lithium transition metal compound powder for a positive electrode material of a lithium secondary battery characterized by having an average square root roughness (RMS) of 1.5 nm or less, xLi 2 MO 3. (1-x) LiNO 2.
- Patent Document 7 states that “a nonaqueous electrolyte secondary battery including a positive electrode, a negative electrode, a separator, and a nonaqueous electrolyte, wherein the positive electrode includes a first positive electrode active material and a second positive electrode active material.
- At least one positive electrode active material selected from the group consisting of general composition formula Li (1 + a) Mn x Ni y Co (1-xyz) M z O 2 (where M is , Ti, Zr, Nb, Mo, W, Al, Si, Ga, Ge and Sn, at least one element selected from the group consisting of -0.15 ⁇ a ⁇ 0.15, 0.1 ⁇ x ⁇ 0.5, 0.6 ⁇ x + y + z ⁇ 1.0, 0 ⁇ z ⁇ 0.1), and the second positive electrode active material has a general composition formula Li (1-sb) Mg s Co (1 -tu) Al t M ′ u O 2 (where M ′ is at least one element selected from the group consisting of Ti, Zr and Ge, and 0.01 ⁇ s ⁇ 0.1, 0 ⁇ u ⁇ 0.1, 0.01 ⁇ t + u ⁇ 0.1, ⁇ 0.06 ⁇ b ⁇ 0.05), and the surface of the positive electrode is represented by —SO n
- a compound having a bond represented, and the content of sulfur present as a bond represented by the —SO n — (1 ⁇ n ⁇ 4) on the surface of the positive electrode was analyzed by X-ray photoelectron spectroscopy.
- the non-aqueous electrolyte secondary battery is characterized in that it is 0.2 atomic% or more and 1.5 atomic% or less.
- “(Claim 1) is described as an object of the present invention. It provides a non-aqueous electrolyte secondary battery that is further excellent in cycle characteristics and storage characteristics while realizing high capacity by charging "(paragraph [0011]).
- This specification discloses a technique for providing a mixed active material for a lithium secondary battery in which both battery capacity and cycle characteristics are improved, an electrode using the mixed active material, and a lithium secondary battery.
- the lithium transition metal composite oxide has an ⁇ -NaFeO 2 structure
- the transition metal (Me) includes Co, Ni, and Mn
- the molar ratio Mn / Me is Mn / Me> 0.5
- this embodiment is realizable as an electrode for lithium secondary batteries containing the said mixed active material for lithium secondary batteries.
- this embodiment is realizable as a lithium secondary battery provided with the said electrode for lithium secondary batteries.
- the present embodiment can be realized as a power storage device configured by collecting a plurality of the lithium secondary batteries.
- the lithium transition metal composite oxide has an ⁇ -NaFeO 2 structure
- the transition metal (Me) includes Co, Ni, and Mn
- the molar ratio Mn / Me is Mn / Me> 0.5
- a lithium secondary battery having a specific surface area of 4.4 m 2 / g or less and an S content of 0.2 to 1.2% by mass. It is a mixed active material for batteries.
- Lithium transition metal composite oxide having an ⁇ -NaFeO 2 structure, transition metal (Me) containing Co, Ni and Mn, and molar ratio Mn / Me> Mn / Me> 0.5 Type lithium transition metal composite oxide ”) increases in specific surface area as described above when treated with acid, but the transition metal (Me) contains Co, Ni and Mn, and the molar ratio Mn / Me is 0 ⁇ Mn. /Me ⁇ 0.5 lithium transition metal composite oxide (hereinafter referred to as “LiMeO 2 type lithium transition metal composite oxide”) is treated to the extent of lithium excess lithium transition metal composite oxide by acid treatment. It was found that no increase in specific surface area was observed.
- the transition metal (Me) contains Co, Ni, and Mn, and the acid treatment of the lithium transition metal composite oxide in which the molar ratio Mn / Me is 0 ⁇ Mn / Me ⁇ 0.5 is performed. It is good also as containing S.
- the mixing ratio of the lithium-excess type lithium transition metal composite oxide and the acid-treated LiMeO 2 type lithium transition metal composite oxide is preferably 70:30 to 95: 5, and more preferably 80:20 to 90:10.
- the specific surface area of the mixed active material of the lithium-excess type lithium transition metal composite oxide and the LiMeO 2 type lithium transition metal composite oxide is 4.4 m 2 / g or less. . It is preferably 4.2 m 2 / g or less, and more preferably 3.8 m 2 / g or less. Further, by acid treatment with sulfuric acid LiMeO 2 type lithium transition metal composite oxide, it is preferred to incorporate S in the positive electrode active material. When the lithium-excess type lithium transition metal composite oxide is acid-treated, the specific surface area becomes too large. In the present embodiment, in order to improve battery capacity and cycle characteristics, the S content is 0.2 to 1.2% by mass, preferably 0.2 to 1.0% by mass, More preferably, the content is set to 0.8% by mass.
- the lithium-rich lithium transition metal composite oxide typically has a composition formula Li 1 + ⁇ Me 1- ⁇ O 2 (where Me is a transition metal element containing Co, Ni and Mn, (1 + ⁇ ) / (1- ⁇ )> 1.2, molar ratio Mn / Me> 0.5).
- the LiMeO 2 type lithium transition metal composite oxide typically has a composition formula Li x MeO 2 (where Me is a transition metal element containing Co, Ni and Mn, x ⁇ 1.2, 0 ⁇ molar ratio Mn / Me ⁇ 0.5).
- the transition metal (Me) contains Co, Ni, and Mn
- the lithium transition metal composite oxide having a molar ratio Mn / Me of Mn / Me> 0.5 is represented by the composition formula Li 1 + ⁇ Me 1- ⁇
- the molar ratio Li / Me of Li to the transition metal element Me is represented by (1 + ⁇ ) / (1- ⁇ ).
- the molar ratio Li / Me may be greater than 1.
- the Li / Me ratio is 1.25 ⁇ (1 + ⁇ ) / (1- ⁇ ) from the viewpoint of obtaining a lithium secondary battery having a particularly large discharge capacity and excellent cycle characteristics and high rate discharge performance. More preferably, ⁇ 1.5.
- the mole of Co relative to the transition metal element Me of the lithium-excess type lithium transition metal composite oxide is preferably 0.05 to 0.40, and more preferably 0.10 to 0.30.
- the molar ratio Mn / Mn of the transition metal element Me of the lithium-excess type lithium transition metal composite oxide is 0. Larger than .5.
- the molar ratio Mn / Me is larger than 0.5, the spinel transition occurs when charged, and it does not have the structure attributed to the ⁇ -NaFeO 2 structure. While there was a problem as an active material for a lithium secondary battery, the lithium-excess type lithium transition metal composite oxide had ⁇ -NaFeO 2 even when charged with a molar ratio Mn / Me larger than 0.5.
- the configuration in which the molar ratio Mn / Me is larger than 0.5 characterizes the positive electrode active material made of a so-called lithium-excess type lithium transition metal composite oxide.
- the molar ratio Mn / Me is preferably 0.5 ⁇ Mn / Me ⁇ 0.8, and more preferably 0.5 ⁇ Mn / Me ⁇ 0.75.
- the content of Na is more preferably 2000 to 10,000 ppm.
- a sodium precursor such as sodium hydroxide or sodium carbonate is used as a neutralizing agent in the step of preparing a hydroxide precursor or carbonate precursor described later, and Na remains in the washing step.
- a method of adding a sodium compound such as sodium carbonate in the subsequent firing step can be employed.
- the lithium-excess type lithium transition metal composite oxide according to this embodiment has an ⁇ -NaFeO 2 structure.
- the lithium transition metal composite oxide after synthesis (before charge and discharge) is attributed to the space group P3 1 12 or R3-m.
- the charge is performed and Li in the crystal is desorbed, the symmetry of the crystal changes, whereby the superlattice peak disappears and the lithium transition metal composite oxide belongs to the space group R3-m. Will come to be.
- P3 1 12 is a crystal structure model in which the atomic positions of the 3a, 3b, and 6c sites in R3-m are subdivided, and when ordering is recognized in the atomic arrangement in R3-m, the P3 1 12 model Is adopted. Note that “R3-m” should be represented by adding a bar “-” on “3” of “R3m”.
- the lithium-rich lithium transition metal composite oxide according to the present embodiment has a half-value width of the diffraction peak attributed to the (003) plane when the space group R3-m is used as a crystal structure model based on the X-ray diffraction pattern.
- a range of 0.18 ° to 0.22 ° is preferable. By doing so, it is possible to increase the discharge capacity of the positive electrode active material and improve the high rate discharge performance.
- the structure of the lithium-excess type lithium transition metal composite oxide does not change during overcharge. This can be confirmed by observation as a single phase belonging to the space group R3-m on the X-ray diffraction diagram when electrochemically oxidized to a potential of 5.0 V (vs. Li / Li + ). Thereby, the lithium secondary battery excellent in charge / discharge cycle performance can be obtained.
- the oxygen positional parameter obtained from the crystal structure analysis by the Rietveld method based on the X-ray diffraction pattern is 0.262 at the end of discharge of 2 V (vs. Li / Li + ).
- it is preferably 0.267 or more at the end of charge of 4.3 V (vs. Li / Li + ) after overcharge formation.
- the oxygen positional parameter is Me (transition metal) spatial coordinates (0, 0, 0) for the ⁇ -NaFeO 2 type crystal structure of the lithium transition metal composite oxide belonging to the space group R3-m, This is the value of z when the spatial coordinates of Li (lithium) are defined as (0, 0, 1/2) and the spatial coordinates of O (oxygen) are defined as (0, 0, z).
- the oxygen position parameter is a relative index indicating how far the O (oxygen) position is from the Me (transition metal) position (see Patent Documents 1 and 2).
- the lithium-rich lithium transition metal composite oxide according to this embodiment is produced from a carbonate precursor or a hydroxide precursor.
- D50 which is the particle diameter at which the cumulative volume in the particle size distribution of the secondary particles is 50%, is preferably 5 ⁇ m or more, and is 5 to 18 ⁇ m. More preferably.
- D50 is preferably 8 ⁇ m or less, and more preferably 8 to 1 ⁇ m.
- a lithium-excess type lithium transition metal composite oxide produced from a carbonate precursor is subjected to a nitrogen gas adsorption method.
- the peak differential pore volume is not less than 0.75 mm 3 / (g ⁇ nm) in the range of the pore diameter where the differential pore volume obtained by the BJH method shows the maximum value from the adsorption isotherm used, and the range is 30 to 40 nm. Is preferable (see Patent Document 2).
- the tap density of the positive electrode active material according to the present embodiment is preferably 1.25 g / cc or more, and preferably 1.7 g / cc or more in order to obtain a lithium secondary battery having excellent cycle characteristics and high rate discharge performance. More preferred.
- the lithium-excess type lithium transition metal composite oxide of this embodiment is basically a lithium transition metal composite oxide intended for the metal elements (Li, Mn, Co, Ni) constituting the lithium transition metal composite oxide. It can be obtained by adjusting the raw materials contained according to the composition and firing them. However, with respect to the amount of the Li raw material, it is preferable to add an excess of about 1 to 5% in view of the disappearance of a part of the Li raw material during firing.
- a so-called “solid phase method” in which salts of Li, Co, Ni, and Mn are mixed and fired, or Co, Ni, and Mn were previously present in one particle.
- a “coprecipitation method” is known in which a coprecipitation precursor is prepared, and a Li salt is mixed and fired therein.
- a coprecipitation precursor is prepared, and a Li salt is mixed and fired therein.
- Mn is difficult to uniformly dissolve in Co and Ni, so it is difficult to obtain a sample in which each element is uniformly distributed in one particle.
- the “coprecipitation method” is selected. It is easier to obtain a homogeneous phase at the atomic level. Therefore, in the embodiments described later, the “coprecipitation method” is adopted.
- Mn is easily oxidized among Co, Ni and Mn, and it is not easy to prepare a coprecipitation precursor in which Co, Ni and Mn are uniformly distributed in a divalent state. Uniform mixing at the atomic level of Co, Ni and Mn tends to be insufficient.
- the Mn ratio is higher than the Co and Ni ratios, it is particularly important to remove dissolved oxygen in the aqueous solution.
- the method for removing dissolved oxygen include a method of bubbling a gas not containing oxygen.
- the gas not containing oxygen is not limited, but nitrogen gas, argon gas, carbon dioxide (CO 2 ), or the like can be used. Among these, when producing a coprecipitated carbonate precursor, it is preferable to employ carbon dioxide as a gas not containing oxygen because an environment in which carbonate is more easily generated is provided.
- the pH in the step of producing a precursor by co-precipitation of a compound containing Co, Ni and Mn in a solution is not limited, an attempt is made to produce the co-precipitation precursor as a co-precipitation hydroxide precursor.
- the coprecipitation precursor can be 10 to 14.
- the coprecipitation precursor can be 7.5 to 11.
- tap density can be made into 1.25 g / cc or more by making pH into 9.4 or less, and a high rate discharge performance can be improved.
- the particle growth rate can be accelerated by setting the pH to 8.0 or less, the stirring continuation time after completion of dropping of the raw material aqueous solution can be shortened.
- the coprecipitation precursor is preferably a compound in which Mn, Ni and Co are uniformly mixed.
- a precursor having a larger bulk density can be produced by using a crystallization reaction using a complexing agent. At that time, a higher density active material can be obtained by mixing and firing with a Li source, so that the energy density per electrode area can be improved.
- the raw material of the coprecipitation precursor is manganese oxide, manganese carbonate, manganese sulfate, manganese nitrate, manganese acetate, etc. as the Mn compound, and nickel hydroxide, nickel carbonate, nickel sulfate, nickel nitrate, nickel acetate as the Ni compound.
- the Co compound cobalt sulfate, cobalt nitrate, cobalt acetate, and the like can be given as examples.
- a reaction crystallization method in which a raw material aqueous solution of the coprecipitation precursor is continuously supplied dropwise to a reaction tank that maintains alkalinity to obtain the coprecipitation precursor.
- lithium compounds, sodium compounds, potassium compounds and the like can be used as the neutralizing agent, but when the coprecipitation precursor is prepared as a coprecipitation hydroxide precursor, sodium hydroxide, hydroxide It is preferable to use a mixture of sodium and lithium hydroxide, or sodium hydroxide and potassium hydroxide, and when preparing the coprecipitation precursor as a coprecipitation carbonate precursor, sodium carbonate, sodium carbonate It is preferable to use lithium carbonate or a mixture of sodium carbonate and potassium carbonate.
- Na / Li which is a molar ratio of sodium carbonate (sodium hydroxide) and lithium carbonate (lithium hydroxide), or sodium carbonate (sodium hydroxide) and potassium carbonate (potassium hydroxide) in order to leave Na 1000 ppm or more
- Na / K which is the molar ratio is 1/1 [M] or more.
- the dropping speed of the raw material aqueous solution greatly affects the uniformity of the element distribution within one particle of the coprecipitation precursor to be generated.
- Mn is difficult to form a uniform element distribution with Co and Ni, so care must be taken.
- the preferred dropping rate is influenced by the reaction vessel size, stirring conditions, pH, reaction temperature, etc., but is preferably 30 ml / min or less. In order to improve the discharge capacity, the dropping rate is more preferably 10 ml / min or less, and most preferably 5 ml / min or less.
- the particle rotation and revolution in the stirring tank are promoted by continuing the stirring after the dropwise addition of the raw material aqueous solution.
- the particles grow concentrically in stages while colliding with each other. That is, the coprecipitation precursor undergoes a reaction in two stages: a metal complex formation reaction when the raw material aqueous solution is dropped into the reaction tank, and a precipitation formation reaction that occurs while the metal complex is retained in the reaction tank. It is formed. Therefore, a coprecipitation precursor having a target particle size can be obtained by appropriately selecting a time for continuing stirring after the dropping of the raw material aqueous solution.
- the preferable stirring duration after completion of dropping of the raw material aqueous solution is influenced by the size of the reaction vessel, stirring conditions, pH, reaction temperature, etc., but 0.5 h or more is required to grow the particles as uniform spherical particles. Preferably, 1 h or more is more preferable. Further, in order to reduce the possibility that the output performance in the low SOC region of the battery is not sufficient due to the particle size becoming too large, 30 h or less is preferable, 25 h or less is more preferable, and 20 h or less is most preferable.
- a preferable stirring duration time for setting the 50% particle diameter (D50) of the composite oxide to 5 to 18 ⁇ m varies depending on the pH to be controlled. For example, for a coprecipitated hydroxide precursor, when the pH is controlled to 10 to 12, the stirring duration is preferably 1 to 10 h, and when the pH is controlled to 12 to 14, the stirring duration is 3 ⁇ 20h is preferred.
- the stirring duration is preferably 1 to 20 h, and when the pH is controlled to 8.3 to 9.4. The stirring duration is preferably 3 to 24 h.
- coprecipitation precursor particles are prepared using sodium compounds such as sodium hydroxide and sodium carbonate as neutralizing agents, sodium ions adhering to the particles are washed away in the subsequent washing step.
- a condition such that the number of washings with 200 ml of ion-exchanged water is 5 times can be employed.
- the coprecipitation precursor is preferably dried at 80 ° C. to less than 100 ° C. in an air atmosphere under normal pressure. By drying at 100 ° C. or higher, more water can be removed in a short time, but by drying at 80 ° C. for a long time, an active material having more excellent electrode characteristics can be obtained.
- the reason for this is not always clear, but the inventors have inferred the carbonate precursor as follows. That is, since the carbonate precursor is a porous body having a specific surface area of 50 to 100 m 2 / g, it has a structure that easily adsorbs moisture.
- the hues of the respective precursors are measured, and the standard colors for paints (JPMA Standard) issued by the Japan Paint Industry Association based on JIS Z 8721 are measured.
- JPMA Standard Japanese Paint Industry Association
- a color reader CR10 manufactured by Konica Minolta Co., Ltd. was used for measuring the hue. According to this measuring method, the value of dL * representing lightness is larger in white and smaller in black. Further, the value of da * representing the hue is larger when red is stronger and smaller when green is stronger (red is weaker).
- the value of db * representing the hue becomes larger when yellow is stronger and larger when blue is stronger (yellow is weaker).
- the hue of the dried product at 100 ° C. is in the range reaching the standard color F05-40D in the red direction compared to the standard color F05-20B, and the standard color FN ⁇ in the white direction compared to the standard color FN-10. It was found to be in the range up to 25. Among them, it was recognized that the color difference from the hue exhibited by the standard color F05-20B was the smallest. On the other hand, the hue of the dried product at 80 ° C.
- the hue of the carbonate precursor is preferably positive in all of dL, da and db as compared with the standard color F05-20B, dL is +5 or more, da is +2 or more, and db is It can be said that +5 or more is more preferable.
- the lithium-excess type lithium transition metal composite oxide of this embodiment can be suitably prepared by mixing the hydroxide precursor or carbonate precursor and the Li compound, and then performing a heat treatment.
- a Li compound it can manufacture suitably by using lithium hydroxide, lithium carbonate, lithium nitrate, lithium acetate, etc.
- the amount of the Li compound it is preferable to add an excess of about 1 to 5% in view of the disappearance of a part of the Li compound during firing.
- the amount of Na contained in the active material can be made 1000 ppm or more by mixing the Na compound together with the Li compound and the hydroxide precursor or carbonate precursor.
- Na compound sodium carbonate is preferable.
- the firing temperature affects the reversible capacity of the active material.
- the firing temperature is preferably less than the temperature at which the oxygen release reaction of the active material affects.
- the oxygen release temperature of the active material is approximately 1000 ° C. or higher in the composition range according to the present embodiment, but there is a slight difference in the oxygen release temperature depending on the composition of the active material. It is preferable to confirm. In particular, it is confirmed that the oxygen release temperature of the precursor shifts to the lower temperature side as the amount of Co contained in the sample increases.
- a mixture of a coprecipitation precursor and a lithium compound may be subjected to thermogravimetric analysis (DTA-TG measurement) in order to simulate the firing reaction process.
- DTA-TG measurement thermogravimetric analysis
- the platinum used in the sample chamber of the measuring instrument may be corroded by the Li component volatilized, and the instrument may be damaged. Therefore, a composition in which crystallization is advanced to some extent by adopting a firing temperature of about 500 ° C. in advance. Goods should be subjected to thermogravimetric analysis.
- the firing temperature is preferably at least 700 ° C. or higher.
- the firing temperature is preferably at least 800 ° C. or higher.
- the optimum firing temperature tends to be lower as the amount of Co contained in the precursor is larger.
- the present inventors analyzed the half width of the diffraction peak of the active material according to the present embodiment in detail, and in the case where the precursor is a coprecipitated hydroxide, the synthesis is performed at a temperature of less than 650 ° C. In the sample, strain remains in the lattice, and it can be remarkably removed by synthesizing at a temperature of 650 ° C. or higher, and when the precursor is a coprecipitated carbonate, firing is performed. In the sample synthesized at a temperature of less than 750 ° C., strain remained in the lattice, and it was confirmed that the strain could be remarkably removed by synthesis at a temperature of 750 ° C. or higher.
- the crystallite size was increased in proportion to the increase in the synthesis temperature. Therefore, even in the composition of the active material according to the present embodiment, a favorable discharge capacity can be obtained by aiming at a particle having almost no lattice distortion in the system and having a sufficiently grown crystallite size. Specifically, it is preferable to employ a synthesis temperature (firing temperature) and a Li / Me ratio composition in which the strain amount affecting the lattice constant is 2% or less and the crystallite size is grown to 50 nm or more. all right. Although changes due to expansion and contraction are observed by charging and discharging by molding these as electrodes, it is preferable as an effect that the crystallite size is maintained at 30 nm or more in the charging and discharging process.
- the calcination temperature is related to the oxygen release temperature of the active material, but crystallization is caused by large growth of primary particles at 900 ° C. or higher without reaching the calcination temperature at which oxygen is released from the active material.
- the phenomenon is seen. This can be confirmed by observing the fired active material with a scanning electron microscope (SEM).
- SEM scanning electron microscope
- the active material synthesized through a synthesis temperature exceeding 900 ° C. has primary particles grown to 0.5 ⁇ m or more, and is in a disadvantageous state for Li + movement in the active material during the charge / discharge reaction, and has a high rate discharge performance. Decreases.
- the size of the primary particles is preferably less than 0.5 ⁇ m, and more preferably 0.3 ⁇ m or less.
- the Li / Me molar ratio (1 + ⁇ ) / (1- ⁇ ) is 1.2 ⁇ (1 + ⁇ ) / (1- ⁇ ).
- the firing temperature is preferably 750 to 900 ° C., more preferably 800 to 900 ° C.
- the transition metal element constituting the lithium-excess type lithium transition metal composite oxide is other than the transition metal site of the layered rock salt type crystal structure. It is preferable that the ratio existing in the portion is small. This is because, in the precursor to be subjected to the firing step, the transition metal elements such as Co, Ni, and Mn in the precursor core particles are sufficiently uniformly distributed, and appropriate for promoting the crystallization of the active material sample. This can be achieved by selecting the conditions for the firing process. If the distribution of the transition metal in the precursor core particles subjected to the firing step is not uniform, a sufficient discharge capacity cannot be obtained.
- the resulting lithium transition metal composite oxide has a layered rock salt type crystal structure other than the transition metal site.
- the present inventors speculate that this is due to the occurrence of so-called cation mixing, in which a part of the transition metal element is present at the lithium site. The same inference can be applied to the crystallization process in the firing step. If the crystallization of the active material sample is insufficient, cation mixing in the layered rock salt type crystal structure is likely to occur.
- the intensity ratio of the diffraction peaks of the (003) plane and the (104) plane when the X-ray diffraction measurement result belongs to the space group R3-m is large.
- the intensity ratio I (003) / I (104) of diffraction peaks of the (003) plane and the (104) plane measured by X-ray diffraction measurement is 1.0 or more at the end of discharge and 1. It is preferable that it is 75 or more. If the precursor synthesis conditions and procedure are inadequate, the peak intensity ratio will be smaller and often less than 1.
- the lithium-excess type lithium transition metal composite oxide according to the present embodiment has been described above.
- LiMeO 2 type lithium transition metal composite oxide of the present embodiment can be used those known.
- a typical example is represented by a composition formula Li x MeO 2 (where Me is a transition metal element containing Co, Ni and Mn, x ⁇ 1.2, 0 ⁇ molar ratio Mn / Me ⁇ 0.5).
- Me is a transition metal element containing Co, Ni and Mn, x ⁇ 1.2, 0 ⁇ molar ratio Mn / Me ⁇ 0.5
- LiCo 1/3 Ni 1/3 Mn 1/3 O 2 but a mixed solution of a salt of Co, Ni, and Mn is dropped into an alkaline solution to produce a coprecipitated hydroxide, which is Li It can be produced by a method such as mixing with salt and baking.
- LiCo 2/3 Ni 1/6 Mn 1/6 O 2 , LiCo 0.3 Ni 0.5 Mn 0.2 O 2 or the like in which the ratio of Co, Ni, and Mn is changed can also be used.
- the LiMeO 2 type lithium transition metal composite oxide is acid-treated. It is preferable to use sulfuric acid for the acid treatment. Hydrochloric acid and nitric acid are not preferable because the speed of dissolving the active material is high.
- S is contained in the LiMeO 2 type lithium transition metal composite oxide.
- the LiMeO 2 type lithium transition metal composite oxide is put into an aqueous sulfuric acid solution, stirred, filtered, washed, and dried to contain S.
- the S content can be changed by controlling the sulfuric acid concentration.
- the lithium-excess type lithium transition metal composite oxide produced as described above and the acid-treated LiMeO 2 type lithium transition metal composite oxide are mixed to obtain a mixed active material.
- the S content after the mixed active material is 0.2 to 1.0 mass%.
- the specific surface area of the LiMeO 2 type lithium transition metal composite oxide is not greatly increased by the acid treatment, the specific surface area of the mixed active material can be made 4.2 m 2 / g or less.
- the negative electrode material is not limited, and any negative electrode material that can deposit or occlude lithium ions may be selected.
- titanium-based materials such as lithium titanate having a spinel crystal structure represented by Li [Li 1/3 Ti 5/3 ] O 4
- alloy-based materials such as Si, Sb, and Sn-based lithium metal
- lithium alloys Lithium metal-containing alloys such as lithium-silicon, lithium-aluminum, lithium-lead, lithium-tin, lithium-aluminum-tin, lithium-gallium, and wood alloys
- lithium composite oxide lithium-titanium
- silicon oxide silicon oxide
- an alloy capable of inserting and extracting lithium a carbon material (for example, graphite, hard carbon, low-temperature fired carbon, amorphous carbon, etc.) can be used.
- the positive electrode active material powder and the negative electrode material powder have an average particle size of 100 ⁇ m or less.
- the positive electrode active material powder is desirably 10 ⁇ m or less for the purpose of improving the high output characteristics of the non-aqueous electrolyte battery.
- a pulverizer or a classifier is used.
- a mortar, a ball mill, a sand mill, a vibrating ball mill, a planetary ball mill, a jet mill, a counter jet mill, a swirling air flow type jet mill or a sieve is used.
- wet pulverization in the presence of water or an organic solvent such as hexane may be used.
- an organic solvent such as hexane
- the positive electrode active material and the negative electrode material which are the main components of the positive electrode and the negative electrode, have been described in detail above.
- the positive electrode and the negative electrode include a conductive agent, a binder, a thickener, and a filler. Etc. may be contained as other constituents.
- the conductive agent is not limited as long as it is an electron conductive material that does not adversely affect the battery performance.
- natural graphite such as scaly graphite, scaly graphite, earthy graphite
- artificial graphite carbon black, acetylene black
- Conductive materials such as ketjen black, carbon whisker, carbon fiber, metal (copper, nickel, aluminum, silver, gold, etc.) powder, metal fiber, and conductive ceramic material can be included as one kind or a mixture thereof. .
- acetylene black is desirable from the viewpoints of electron conductivity and coatability.
- the addition amount of the conductive agent is preferably 0.1% by weight to 50% by weight, and particularly preferably 0.5% by weight to 30% by weight with respect to the total weight of the positive electrode or the negative electrode.
- These mixing methods are physical mixing, and the ideal is uniform mixing. Therefore, powder mixers such as V-type mixers, S-type mixers, crackers, ball mills, and planetary ball mills can be mixed dry or wet.
- the binder is usually a thermoplastic resin such as polytetrafluoroethylene (PTFE), polyvinylidene fluoride (PVDF), polyethylene, polypropylene, ethylene-propylene-diene terpolymer (EPDM), sulfonated EPDM, styrene butadiene.
- PTFE polytetrafluoroethylene
- PVDF polyvinylidene fluoride
- EPDM ethylene-propylene-diene terpolymer
- SBR rubber
- the amount of the binder added is preferably 1 to 50% by weight, particularly 2 to 30% by weight, based on the total weight of the positive electrode or the negative electrode.
- any material that does not adversely affect battery performance may be used.
- olefin polymers such as polypropylene and polyethylene, amorphous silica, alumina, zeolite, glass, carbon and the like are used.
- the addition amount of the filler is preferably 30% by weight or less with respect to the total weight of the positive electrode or the negative electrode.
- the main components positive electrode active material for the positive electrode, negative electrode material for the negative electrode
- an organic solvent such as N-methylpyrrolidone or toluene or water.
- the obtained mixed liquid is applied on a current collector such as an aluminum foil or copper foil, or pressed and heat-treated at a temperature of about 50 ° C. to 250 ° C. for about 2 hours. Is done.
- roller coating such as applicator roll, screen coating, doctor blade method, spin coating, bar coater, etc. It is not limited.
- Nonaqueous electrolyte used in the lithium secondary battery according to the present embodiment is not limited, and those generally proposed for use in lithium batteries and the like can be used.
- Nonaqueous solvents used for the nonaqueous electrolyte include cyclic carbonates such as propylene carbonate, ethylene carbonate, butylene carbonate, chloroethylene carbonate, and vinylene carbonate; cyclic esters such as ⁇ -butyrolactone and ⁇ -valerolactone; dimethyl carbonate, Chain carbonates such as diethyl carbonate and ethyl methyl carbonate; chain esters such as methyl formate, methyl acetate and methyl butyrate; tetrahydrofuran or derivatives thereof; 1,3-dioxane, 1,4-dioxane, 1,2-dimethoxy Ethers such as ethane, 1,4-dibutoxyethane and methyldiglyme; Nitriles such as acetonitrile and benzonitrile;
- electrolyte salt used for the nonaqueous electrolyte examples include LiClO 4 , LiBF 4 , LiAsF 6 , LiPF 6 , LiSCN, LiBr, LiI, Li 2 SO 4 , Li 2 B 10 Cl 10 , NaClO 4 , NaI, NaSCN, NaBr.
- LiCF 3 SO 3 LiN (CF 3 SO 2 ) 2 , LiN (C 2 F 5 SO 2 ) 2 , LiN (CF 3 SO 2 ) (C 4 F 9 SO 2 ), LiC (CF 3 SO 2 ) 3 , LiC (C 2 F 5 SO 2 ) 3 , (CH 3 ) 4 NBF 4 , ( CH 3 ) 4 NBr, (C 2 H 5 ) 4 NClO 4 , (C 2 H 5 ) 4 NI, (C 3 H 7 ) 4 NBr, (n-C 4 H 9 ) 4 NClO 4 , (n-C 4 H 9) 4 NI, ( C 2 H 5) 4 N-mal ate, (C 2 H 5) 4 N-benzoate, (C 2 H 5) 4 N-phtalate, lithium stearyl sulfon
- the viscosity of the electrolyte can be further reduced.
- the low temperature characteristics can be further improved, and self-discharge can be suppressed, which is more desirable.
- a room temperature molten salt or ionic liquid may be used as the non-aqueous electrolyte.
- the concentration of the electrolyte salt in the non-aqueous electrolyte is preferably 0.1 mol / l to 5 mol / l, more preferably 0.5 mol / l to 2 in order to reliably obtain a non-aqueous electrolyte battery having high battery characteristics. .5 mol / l.
- the separator it is preferable to use a porous film or a non-woven fabric exhibiting excellent high rate discharge performance alone or in combination.
- the material constituting the separator for a nonaqueous electrolyte battery include polyolefin resins typified by polyethylene and polypropylene, polyester resins typified by polyethylene terephthalate and polybutylene terephthalate, polyvinylidene fluoride, and vinylidene fluoride-hexa.
- Fluoropropylene copolymer vinylidene fluoride-perfluorovinyl ether copolymer, vinylidene fluoride-tetrafluoroethylene copolymer, vinylidene fluoride-trifluoroethylene copolymer, vinylidene fluoride-fluoroethylene copolymer, fluorine Vinylidene fluoride-hexafluoroacetone copolymer, vinylidene fluoride-ethylene copolymer, vinylidene fluoride-propylene copolymer, vinylidene fluoride-trifluoropropylene copolymer, vinylidene fluoride - tetrafluoroethylene - hexafluoropropylene copolymer, vinylidene fluoride - ethylene - can be mentioned tetrafluoroethylene copolymer.
- the porosity of the separator is preferably 98% by volume or less from the viewpoint of strength. Further, the porosity is preferably 20% by volume or more from the viewpoint of charge / discharge characteristics.
- the separator may be a polymer gel composed of a polymer such as acrylonitrile, ethylene oxide, propylene oxide, methyl methacrylate, vinyl acetate, vinyl pyrrolidone, polyvinylidene fluoride, and an electrolyte.
- a polymer such as acrylonitrile, ethylene oxide, propylene oxide, methyl methacrylate, vinyl acetate, vinyl pyrrolidone, polyvinylidene fluoride, and an electrolyte.
- the separator is used in combination with the above-described porous film, nonwoven fabric or the like and a polymer gel because the liquid retention of the electrolyte is improved. That is, by forming a film in which the surface of the polyethylene microporous membrane and the microporous wall are coated with a solvophilic polymer having a thickness of several ⁇ m or less, and holding the electrolyte in the micropores of the film, Gels.
- solvophilic polymer examples include polyvinylidene fluoride, an acrylate monomer having an ethylene oxide group or an ester group, an epoxy monomer, a polymer having a monomer having an isocyanate group, and the like crosslinked.
- the monomer can be subjected to a crosslinking reaction using a radical initiator in combination with heating or ultraviolet rays (UV), or using an actinic ray such as an electron beam (EB).
- UV ultraviolet rays
- EB electron beam
- the configuration of the lithium secondary battery of the present embodiment is not particularly limited, and examples thereof include a cylindrical battery having a positive electrode, a negative electrode, and a roll separator, a square battery, and a flat battery.
- a battery module having a plurality of lithium secondary batteries Assembled battery.
- the lithium secondary battery of this embodiment may constitute a power storage device such as an assembled battery or a battery pack.
- the assembled battery 101 is configured by assembling a plurality of lithium secondary batteries 100.
- the battery pack 102 may include a plurality of assembled batteries 101.
- Both the conventional positive electrode active material and the active material of this embodiment can be charged and discharged when the positive electrode potential reaches around 4.5 V (vs. Li / Li + ).
- the positive electrode potential during charging is too high, the nonaqueous electrolyte may be oxidized and decomposed, resulting in a decrease in battery performance. Therefore, in use, a lithium secondary battery capable of obtaining a sufficient discharge capacity even when a charging method is adopted in which the maximum potential of the positive electrode during charging is 4.3 V (vs. Li / Li + ) or less. May be required.
- the active material of this embodiment is used, the maximum potential of the positive electrode during charging is lower than 4.5 V (vs.
- Li / Li + during use, for example, 4.4 V (vs. Li / li +) or less and 4.3V (vs.Li/Li +) be adopted charging manner to become less, taking out the discharge quantity of electricity exceeds the capacity of a conventional positive active material of about 200 mAh / g or more Is possible.
- a high-performance positive electrode active material as described above can be obtained.
- the temperature of the reaction vessel was set to 50 ° C. ( ⁇ 2 ° C.), and the aqueous sulfate solution was stirred at a rate of 3 ml / min while stirring the inside of the reaction vessel at a rotational speed of 700 rpm using a paddle blade equipped with a stirring motor. It was dripped.
- an aqueous solution containing 2.0 M sodium carbonate and 0.4 M ammonia is appropriately dropped, so that the pH in the reaction tank is always 7.9 ( ⁇ 0.05 ) Was controlled.
- stirring in the reaction vessel was continued for 3 hours. After the stirring was stopped, the mixture was allowed to stand for 12 hours or more.
- the coprecipitated carbonate particles generated in the reaction vessel are separated, and further, washing is performed 5 times when 200 ml is washed once with ion-exchanged water.
- Sodium ions adhering to the particles were washed and removed under the conditions, and dried for 20 hours at 80 ° C. under normal pressure in an air atmosphere using an electric furnace.
- the box-type electric furnace has internal dimensions of 10 cm in length, 20 cm in width, and 30 cm in depth, and heating wires are inserted at intervals of 20 cm in the width direction. After firing, the heater was turned off and allowed to cool naturally with the alumina boat placed in the furnace. As a result, the temperature of the furnace decreases to about 200 ° C. after 5 hours, but the subsequent temperature decrease rate is somewhat moderate. After the passage of day and night, it was confirmed that the furnace temperature was 100 ° C. or lower, and then the pellets were taken out and pulverized for several minutes in a smoked automatic mortar in order to make the particle diameter uniform.
- a mixture of the lithium-excess type lithium transition metal composite oxide produced as described above and the acid-treated LiMeO 2 type lithium transition metal composite oxide at a mass ratio of 9: 1 was used as the mixed active material of the first embodiment. .
- Embodiment 2 In the acid treatment process of LiMeO 2 type lithium transition metal composite oxide, the concentration of the sulfuric acid aqueous solution into which LiCo 0.33 Ni 0.33 Mn 0.33 O 2 was added was changed from 0.5M to 1.0M. In the same manner as in Embodiment 1, a mixed active material according to Embodiment 2 was produced.
- Embodiment 3 In the acid treatment step of LiMeO 2 type lithium transition metal composite oxide, the concentration of the sulfuric acid aqueous solution into which LiCo 0.33 Ni 0.33 Mn 0.33 O 2 was added was changed from 0.5M to 1.5M. In the same manner as in Embodiment 1, a mixed active material according to Embodiment 3 was produced.
- Comparative Example 1 In the production process of the lithium-excess type lithium transition metal composite oxide, 1.047 g of lithium carbonate is added to 2.204 g of the coprecipitated carbonate precursor, and the molar ratio of Li: (Co, Ni, Mn) is 145: 100. Comparative Example 1 was carried out in the same manner as in Embodiment 6 except that a mixed powder was prepared and lithium transition metal composite oxide Li 1.184 Co 0.102 Ni 0.163 Mn 0.551 O 2 was produced. A mixed active material according to was prepared.
- Comparative Example 4 In the acid treatment process of LiMeO 2 type lithium transition metal composite oxide, the concentration of the sulfuric acid aqueous solution into which LiCo 0.33 Ni 0.33 Mn 0.33 O 2 was added was changed from 1.75M to 2M. In the same manner as in Form 7, a mixed active material according to Comparative Example 4 was produced.
- Comparative Example 5 In the acid treatment process of LiMeO 2 type lithium transition metal composite oxide, the concentration of the sulfuric acid aqueous solution into which LiCo 0.33 Ni 0.33 Mn 0.33 O 2 was added was changed from 1.75M to 2M. In the same manner as in Form 8, a mixed active material according to Comparative Example 5 was produced.
- Comparative Example 7 In the acid treatment process of LiMeO 2 type lithium transition metal composite oxide, the concentration of the sulfuric acid aqueous solution into which LiCo 0.33 Ni 0.33 Mn 0.33 O 2 was added was changed from 1.75M to 2M. In the same manner as in Form 10, a mixed active material according to Comparative Example 7 was produced.
- Comparative Example 8 In the acid treatment step of the LiMeO 2 type lithium transition metal composite oxide, the concentration of the sulfuric acid aqueous solution into which LiCo 0.33 Ni 0.33 Mn 0.33 O 2 was added was changed from 1.75M to 2M. In the same manner as in Example 1, a mixed active material according to Comparative Example 8 was produced.
- Comparative Example 10 In the acid treatment step of the LiMeO 2 type lithium transition metal composite oxide, the concentration of the sulfuric acid aqueous solution into which LiCo 0.33 Ni 0.33 Mn 0.33 O 2 was added was changed from 1.75M to 2M. In the same manner as in Example 3, a mixed active material according to Comparative Example 10 was produced.
- Comparative Example 11 The mixing according to Comparative Example 11 was performed in the same manner as in Embodiment 1 except that LiMeO 2 type lithium transition metal composite oxide was not subjected to acid treatment in the acid treatment step, and LiCo 0.33 Ni 0.33 Mn 0.33 O 2 was not acid-treated. An active material was prepared.
- Comparative Example 13 instead of non-acid-treated Li 1.17 Co 0.10 Ni 0.17 Mn 0.56 O 2 , the acid-treated Li 1.17 Co 0.10 Ni 0.17 Mn 0.56 of Comparative Example 12 A mixed active material according to Comparative Example 13 was produced in the same manner as in Embodiment 1 except that O 2 was used.
- Comparative Example 14 An active material according to Comparative Example 14 was produced in the same manner as in Embodiment 1 except that LiCo 0.33 Ni 0.33 Mn 0.33 O 2 was not mixed.
- Comparative Example 15 An active material according to Comparative Example 15 was produced in the same manner as Comparative Example 12 except that LiCo 0.33 Ni 0.33 Mn 0.33 O 2 was not mixed.
- Comparative Example 16 LiCoO 2 type lithium transition metal composite oxide in the acid treatment step, LiCo 0.33 Ni 0.33 Mn 0.33 O 2 treated with hydrochloric acid (1M 100 mL hydrochloric acid aqueous solution used in place of 0.5 M sulfuric acid aqueous solution 100 mL) Otherwise, a mixed active material according to Comparative Example 16 was produced in the same manner as in Embodiment 1.
- Comparative Example 17 LiCo 0.33 Ni 0.33 Mn 0.33 O 2 is treated with nitric acid in the acid treatment step of LiMeO 2 type lithium transition metal composite oxide (1M 100 mL nitric acid aqueous solution is used instead of 0.5 M sulfuric acid aqueous solution 100 mL) Otherwise, a mixed active material according to Comparative Example 17 was produced in the same manner as in Embodiment 1.
- Comparative Example 18 An active material according to Comparative Example 18 was produced in the same manner as Comparative Example 11 except that Li 1.17 Co 0.10 Ni 0.17 Mn 0.56 O 2 was not mixed.
- Comparative Example 19 An active material according to Comparative Example 19 was produced in the same manner as in Embodiment 1 except that Li 1.17 Co 0.10 Ni 0.17 Mn 0.56 O 2 was not mixed.
- lithium secondary batteries (model cells) were produced by the following procedure, and battery characteristics were evaluated.
- the paste thus obtained was manually coated on 20 ⁇ m aluminum foil using a Yoshimitsu applicator. Furthermore, the NMP solvent was removed by drying it on a 120 ° C. hot plate.
- the electrode was cut out to 5.0 cm ⁇ 3.0 cm, and the electrode was passed through a roll press several times to obtain an electrode having a porosity adjusted to 35%. Finally, the electrode was vacuum-dried at 120 ° C. for 6 hours or longer to completely remove moisture and obtain a positive electrode.
- the negative electrode was coated with a mixture on the copper foil so that the weight ratio of graphite / PVdF was 94: 6. Other conditions were the same as for the positive electrode. The coating weight was adjusted so that the active material weight was 60 mg for both positive and negative electrodes.
- the model cell using the positive and negative electrodes prepared above was produced according to the following procedure. In order to avoid the mixing of water, all work for model cell production was performed in a dry room. First, the active material in the lead attachment part of the positive and negative electrodes having a predetermined size (5.0 cm ⁇ 3.0 cm) was peeled off and cut into an L shape. Subsequently, after measuring the mass of the electrode plate, an aluminum lead is ultrasonically welded to the positive electrode and a nickel lead is ultrasonically welded so that the positive electrode faces the single PE separator bag (H6022, Asahi Kasei, 25 ⁇ m). Inserted.
- the battery was run at a constant current of 0.1 C until the voltage reached 4.5 V, and then charged until the current value decayed to 0.02 C. Thereafter, after 10 minutes of rest, the battery was discharged to 2.0 V at a constant current of 0.1 C, and then rested for 10 minutes. This charge / discharge cycle was performed twice. Subsequently, a charge / discharge cycle in which the charge voltage was changed to 4.2 V was performed, and the discharge capacity obtained at that time was defined as the battery capacity. In addition, after changing the current value to the 1C rate and performing 30 cycles, the current value was changed to 0.1C and the discharge test was performed. The energy density maintenance rate at this time was defined as the cycle energy density maintenance rate.
- the S content was calculated by ICP measurement. 50 mg of the active material was dissolved in 10 ml of 35% aqueous hydrochloric acid solution to prepare a sample for measurement. In addition, a standard curve was separately prepared using a standard solution, and the content was determined by comparison with it.
- the above active materials were measured for the mixed active material specific surface area, analyzed for S content, initial efficiency, battery capacity, and cycle energy density maintenance rate.
- Table 1-2 shows the test results of the lithium secondary batteries using each of.
- lithium-rich lithium transition metal composite oxide and acid-treated (treated with sulfuric acid) LiMeO 2 type lithium transition metal composite oxide are mixed, and the specific surface area is 4.4 m 2 / g or less,
- the mixed active materials of Embodiments 1 to 10 having an S content of 0.2 to 1.2% by mass have high initial efficiency, a large battery capacity, and a high cycle energy density retention rate.
- the lithium-rich lithium transition metal composite oxide and the LiMeO 2 type lithium transition metal composite oxide are mixed, the specific surface area is 4.4 m 2 / g or less, and S
- a positive electrode active material for a lithium secondary battery having a content of 0.2 to 1.2% by mass the battery capacity and the cycle characteristics are both improved.
- the lithium secondary battery using the positive electrode active material of the present embodiment which has improved both battery capacity and cycle characteristics while suppressing an increase in specific surface area, is particularly a lithium secondary battery for hybrid vehicles and electric vehicles. Useful as.
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Abstract
Description
また、本実施形態は、前記リチウム二次電池用混合活物質を含有するリチウム二次電池用電極として実現できる。
また、本実施形態は、前記リチウム二次電池用電極を備えたリチウム二次電池として実現できる。
また、本実施形態は、前記リチウム二次電池を複数個集合して構成した蓄電装置として実現できる。
また、「LiMeO2型」正極活物質については、酸処理により、「リチウム過剰型」正極活物質に比べて比表面籍の増加は大きくないが、容量やサイクル特性などの向上は認められないことがわかった。
本実施形態は、α-NaFeO2構造を有し、遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/MeがMn/Me>0.5であるリチウム遷移金属複合酸化物、及び、α-NaFeO2構造を有し、遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/Meが0<Mn/Me≦0.5であるリチウム遷移金属複合酸化物を含有するリチウム二次電池用混合活物質であって、比表面積が4.4m2/g以下であり、且つS含有量が0.2~1.2質量%であることを特徴とするリチウム二次電池用混合活物質である。
そこで、本実施形態においては、遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/Meが0<Mn/Me≦0.5であるリチウム遷移金属複合酸化物の酸処理により前記Sを含有させることとしてもよい。比表面積の増加を抑制しつつ、電池容量とサイクル特性を両立して向上させるために、リチウム過剰型リチウム遷移金属複合酸化物に、酸処理したLiMeO2型リチウム遷移金属複合酸化物を混合することが好ましい。リチウム過剰型リチウム遷移金属複合酸化物と、酸処理したLiMeO2型リチウム遷移金属複合酸化物の混合割合は、70:30~95:5が好ましく、80:20~90:10がより好ましい。
また、LiMeO2型リチウム遷移金属複合酸化物の硫酸を用いた酸処理により、正極活物質にSを含有させることが好ましい。リチウム過剰型リチウム遷移金属複合酸化物を酸処理すると比表面積が大きくなりすぎる。本実施形態においては、電池容量、サイクル特性を向上させるために、S含有量は0.2~1.2質量%とし、0.2~1.0質量%とすることが好ましく、0.2~0.8質量%とすることがより好ましい。
炭酸塩前駆体から作製されるリチウム遷移金属複合酸化物粒子は、2次粒子の粒度分布における累積体積が50%となる粒子径であるD50が、5μm以上であることが好ましく、5~18μmであることがより好ましい。また、水酸化物前駆体から作製されるリチウム遷移金属複合酸化物粒子は、D50が、8μm以下であることが好ましく、8~1μmであることがより好ましい。
本実施形態のリチウム過剰型リチウム遷移金属複合酸化物は、基本的に、リチウム遷移金属複合酸化物を構成する金属元素(Li,Mn,Co,Ni)を目的とするリチウム遷移金属複合酸化物の組成通りに含有する原料を調整し、これを焼成することによって得ることができる。但し、Li原料の量については、焼成中にLi原料の一部が消失することを見込んで、1~5%程度過剰に仕込むことが好ましい。
目的とする組成の酸化物を作製するにあたり、Li,Co,Ni,Mnのそれぞれの塩を混合・焼成するいわゆる「固相法」や、あらかじめCo,Ni,Mnを一粒子中に存在させた共沈前駆体を作製しておき、これにLi塩を混合・焼成する「共沈法」が知られている。「固相法」による合成過程では、特にMnはCo,Niに対して均一に固溶しにくいため、各元素が一粒子中に均一に分布した試料を得ることは困難である。これまで文献などにおいては固相法によってNiやCoの一部にMnを固溶(LiNi1-xMnxO2など)しようという試みが多数なされているが、「共沈法」を選択する方が原子レベルで均一相を得ることが容易である。そこで、後述する実施形態においては、「共沈法」を採用した。
また、色相を表すda*の値は、赤色が強い方が大きくなり、緑色が強い方(赤色が弱い方)が小さくなる。また、色相を表すdb*の値は、黄色が強い方が大きくなり、青色が強い方(黄色が弱い方)が大きくなる。
100℃乾燥品の色相は、標準色F05-20Bと比べて、赤色方向に標準色F05-40Dに至る範囲内にあり、また、標準色FN-10と比べて、白色方向に標準色FN-25に至る範囲内にあることがわかった。中でも、標準色F05-20Bが呈する色相との色差が最も小さいものと認められた。
一方、80℃乾燥品の色相は、標準色F19-50Fと比べて、白色方向に標準色F19-70Fに至る範囲内にあり、また、標準色F09-80Dと比べて、黒色方向に標準色F09-60Hに至る範囲内にあることがわかった。中でも、標準色F19-50Fが呈する色相との色差が最も小さいものと認められた。
以上の知見から、炭酸塩前駆体の色相は、標準色F05-20Bに比べて、dL,da及びdbの全てにおいて+方向であるものが好ましく、dLが+5以上、daが+2以上、dbが+5以上であることがより好ましいといえる。
Li化合物としては、水酸化リチウム、炭酸リチウム、硝酸リチウム、酢酸リチウム等を用いることで好適に製造することができる。但し、Li化合物の量については、焼成中にLi化合物の一部が消失することを見込んで、1~5%程度過剰に仕込むことが好ましい。
焼成温度が高すぎると、得られた活物質が酸素放出反応を伴って崩壊すると共に、主相の六方晶に加えて単斜晶のLi[Li1/3Mn2/3]O2型に規定される相が、固溶相としてではなく、分相して観察される傾向がある。このような分相が多く含まれすぎると、活物質の可逆容量の減少を導くので好ましくない。このような材料では、X線回折図上35°付近及び45°付近に不純物ピークが観察される。従って、焼成温度は、活物質の酸素放出反応の影響する温度未満とすることが好ましい。活物質の酸素放出温度は、本実施形態に係る組成範囲においては、概ね1000℃以上であるが、活物質の組成によって酸素放出温度に若干の差があるので、あらかじめ活物質の酸素放出温度を確認しておくことが好ましい。特に試料に含まれるCo量が多いほど前駆体の酸素放出温度は低温側にシフトすることが確認されているので注意が必要である。活物質の酸素放出温度を確認する方法としては、焼成反応過程をシミュレートするために、共沈前駆体とリチウム化合物を混合したものを熱重量分析(DTA-TG測定)に供してもよいが、この方法では測定機器の試料室に用いている白金が揮発したLi成分により腐食されて機器を痛めるおそれがあるので、あらかじめ500℃程度の焼成温度を採用してある程度結晶化を進行させた組成物を熱重量分析に供するのが良い。
本発明者らは、本実施形態に係る活物質の回折ピークの半値幅を詳細に解析することにより、前駆体が共沈水酸化物である場合においては、焼成温度が650℃未満の温度で合成した試料においては格子内にひずみが残存しており、650℃以上の温度で合成することで顕著にひずみを除去することができること、及び、前駆体が共沈炭酸塩である場合においては、焼成温度が750℃未満の温度で合成した試料においては格子内にひずみが残存しており、750℃以上の温度で合成することで顕著にひずみを除去することができることを確認した。また、結晶子のサイズは合成温度が上昇するに比例して大きくなるものであった。
よって、本実施形態に係る活物質の組成においても、系内に格子のひずみがほとんどなく、かつ結晶子サイズが十分成長した粒子を志向することで良好な放電容量を得られるものであった。
具体的には、格子定数に及ぼすひずみ量が2%以下、かつ結晶子サイズが50nm以上に成長しているような合成温度(焼成温度)及びLi/Me比組成を採用することが好ましいことがわかった。これらを電極として成型して充放電をおこなうことで膨張収縮による変化も見られるが、充放電過程においても結晶子サイズは30nm以上を保っていることが得られる効果として好ましい。
本実施形態において、X線回折測定による前記(003)面と(104)面の回折ピークの強度比I(003)/I(104)は、放電末において1.0以上、充電末において1.75以上であることが好ましい。前駆体の合成条件や合成手順が不適切である場合、前記ピーク強度比はより小さい値となり、しばしば1未満の値となる。
以上、本実施形態のリチウム過剰型リチウム遷移金属複合酸化物について説明した。
そのため、V型混合機、S型混合機、擂かい機、ボールミル、遊星ボールミルといったような粉体混合機を乾式、あるいは湿式で混合することが可能である。
本願明細書に記載した合成条件及び合成手順を採用することにより、上記のような高性能の正極活物質を得ることができる。
硫酸コバルト7水和物14.08g、硫酸ニッケル6水和物21.00g及び硫酸マンガン5水和物65.27gを秤量し、これらの全量をイオン交換水200mlに溶解させ、Co:Ni:Mnのモル比が12.5:20.0:67.5となる2.0Mの硫酸塩水溶液を作製した。一方、2Lの反応槽に750mlのイオン交換水を注ぎ、CO2ガスを30minバブリングさせることにより、イオン交換水中にCO2を溶解させた。反応槽の温度を50℃(±2℃)に設定し、攪拌モーターを備えたパドル翼を用いて反応槽内を700rpmの回転速度で攪拌しながら、前記硫酸塩水溶液を3ml/minの速度で滴下した。ここで、滴下の開始から終了までの間、2.0Mの炭酸ナトリウム及び0.4Mのアンモニアを含有する水溶液を適宜滴下することにより、反応槽中のpHが常に7.9(±0.05)を保つように制御した。滴下終了後、反応槽内の攪拌をさらに3h継続した。攪拌の停止後、12h以上静置した。
このリチウム遷移金属複合酸化物がα-NaFeO2構造を有することをエックス線回折測定により確認した。
LiCo0.33Ni0.33Mn0.33O2を5g秤量し、0.5Mの硫酸水溶液100mLに投入し、マグネチックスターラーを用いて30min室温にて撹拌した。その後、濾過およびイオン交換水による洗浄を行い、110℃にて常圧乾燥を20時間行った。
LiMeO2型リチウム遷移金属複合酸化物の酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を投入する硫酸水溶液の濃度を、0.5Mから1.0Mに変更した他は、実施形態1と同様にして、実施形態2に係る混合活物質を作製した。
LiMeO2型リチウム遷移金属複合酸化物の酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を投入する硫酸水溶液の濃度を、0.5Mから1.5Mに変更した他は、実施形態1と同様にして、実施形態3に係る混合活物質を作製した。
リチウム過剰型リチウム遷移金属複合酸化物の作製工程において、前記共沈炭酸塩前駆体2.304gに、炭酸リチウム0.943gを加え、Li:(Co,Ni,Mn)のモル比が125:100である混合粉体を調製し、リチウム遷移金属複合酸化物Li1.111Co0.111Ni0.178Mn0.600O2を作製した他は、実施形態1と同様にして、実施形態4に係る混合活物質を作製した。
リチウム過剰型リチウム遷移金属複合酸化物の作製工程において、前記共沈炭酸塩前駆体2.180gに、炭酸リチウム1.071gを加え、Li:(Co,Ni,Mn)のモル比が150:100である混合粉体を調製し、リチウム遷移金属複合酸化物Li1.20Co0.10Ni0.16Mn0.54O2を作製した他は、実施形態1と同様にして、実施形態5に係る混合活物質を作製した。
リチウム過剰型リチウム遷移金属複合酸化物の作製工程において、前記共沈炭酸塩前駆体2.145gに、炭酸リチウム1.107gを加え、Li:(Co,Ni,Mn)のモル比が157.5:100である混合粉体を調製し、リチウム遷移金属複合酸化物Li1.223Co0.087Ni0.155Mn0.525O2を作製し、かつ、LiMeO2型リチウム遷移金属複合酸化物の酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を投入する硫酸水溶液の濃度を、0.5Mから1.75Mに変更した他は、実施形態1と同様にして、実施形態6に係る混合活物質を作製した。
リチウム過剰型リチウム遷移金属複合酸化物の作製工程において、前記共沈炭酸塩前駆体2.157gに、炭酸リチウム1.095gを加え、Li:(Co,Ni,Mn)のモル比が155:100である混合粉体を調製し、リチウム遷移金属複合酸化物Li1.216Co0.098Ni0.157Mn0.529O2を作製した他は、実施形態6と同様にして、実施形態7に係る混合活物質を作製した。
リチウム過剰型リチウム遷移金属複合酸化物の作製工程において、前記共沈炭酸塩前駆体2.168gに、炭酸リチウム1.083gを加え、Li:(Co,Ni,Mn)のモル比が152.5:100である混合粉体を調製し、リチウム遷移金属複合酸化物Li1.208Co0.099Ni0.158Mn0.535O2を作製した他は、実施形態6と同様にして、実施形態8に係る混合活物質を作製した。
リチウム過剰型リチウム遷移金属複合酸化物の作製工程において、前記共沈炭酸塩前駆体2.180gに、炭酸リチウム1.071gを加え、Li:(Co,Ni,Mn)のモル比が150:100である混合粉体を調製し、リチウム遷移金属複合酸化物Li1.20Co0.10Ni0.16Mn0.54O2を作製した他は、実施形態6と同様にして、実施形態9に係る混合活物質を作製した。
リチウム過剰型リチウム遷移金属複合酸化物の作製工程において、前記共沈炭酸塩前駆体2.192gに、炭酸リチウム1.059gを加え、Li:(Co,Ni,Mn)のモル比が147.5:100である混合粉体を調製し、リチウム遷移金属複合酸化物Li1.192Co0.101Ni0.162Mn0.545O2を作製した他は、実施形態6と同様にして、実施形態10に係る混合活物質を作製した。
リチウム過剰型リチウム遷移金属複合酸化物の作製工程において、前記共沈炭酸塩前駆体2.204gに、炭酸リチウム1.047gを加え、Li:(Co,Ni,Mn)のモル比が145:100である混合粉体を調製し、リチウム遷移金属複合酸化物Li1.184Co0.102Ni0.163Mn0.551O2を作製した他は、実施形態6と同様にして、比較例1に係る混合活物質を作製した。
リチウム過剰型リチウム遷移金属複合酸化物の作製工程において、前記共沈炭酸塩前駆体2.216gに、炭酸リチウム1.034gを加え、Li:(Co,Ni,Mn)のモル比が142.5:100である混合粉体を調製し、リチウム遷移金属複合酸化物Li1.175Co0.103Ni0.165Mn0.557O2を作製した他は、実施形態6と同様にして、比較例2に係る混合活物質を作製した。
LiMeO2型リチウム遷移金属複合酸化物の酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を投入する硫酸水溶液の濃度を、0.5Mから1.75Mに変更した他は、実施形態1と同様にして、比較例3に係る混合活物質を作製した。
LiMeO2型リチウム遷移金属複合酸化物の酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を投入する硫酸水溶液の濃度を、1.75Mから2Mに変更した他は、実施形態7と同様にして、比較例4に係る混合活物質を作製した。
LiMeO2型リチウム遷移金属複合酸化物の酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を投入する硫酸水溶液の濃度を、1.75Mから2Mに変更した他は、実施形態8と同様にして、比較例5に係る混合活物質を作製した。
LiMeO2型リチウム遷移金属複合酸化物の酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を投入する硫酸水溶液の濃度を、1.75Mから2Mに変更した他は、実施形態9と同様にして、比較例6に係る混合活物質を作製した。
LiMeO2型リチウム遷移金属複合酸化物の酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を投入する硫酸水溶液の濃度を、1.75Mから2Mに変更した他は、実施形態10と同様にして、比較例7に係る混合活物質を作製した。
LiMeO2型リチウム遷移金属複合酸化物の酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を投入する硫酸水溶液の濃度を、1.75Mから2Mに変更した他は、比較例1と同様にして、比較例8に係る混合活物質を作製した。
LiMeO2型リチウム遷移金属複合酸化物の酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を投入する硫酸水溶液の濃度を、1.75Mから2Mに変更した他は、比較例2と同様にして、比較例9に係る混合活物質を作製した。
LiMeO2型リチウム遷移金属複合酸化物の酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を投入する硫酸水溶液の濃度を、1.75Mから2Mに変更した他は、比較例3と同様にして、比較例10に係る混合活物質を作製した。
LiMeO2型リチウム遷移金属複合酸化物を酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を酸処理しない他は、実施形態1と同様にして、比較例11に係る混合活物質を作製した。
リチウム過剰型リチウム遷移金属複合酸化物の作製工程において、作製したリチウム遷移金属複合酸化物Li1.17Co0.10Ni0.17Mn0.56O2を5g秤量し、1.75Mの硫酸水溶液100mLに投入し、マグネチックスターラーを用いて30min室温にて撹拌した。その後、濾過およびイオン交換水による洗浄を行い、110℃にて常圧乾燥を20時間行った。この酸処理したLi1.17Co0.10Ni0.17Mn0.56O2を、酸処理していないLiCo0.33Ni0.33Mn0.33O2と混合した他は、実施形態1と同様にして、比較例12に係る混合活物質を作製した。
酸処理していないLi1.17Co0.10Ni0.17Mn0.56O2の代わりに、比較例12の酸処理したLi1.17Co0.10Ni0.17Mn0.56O2を用いた他は、実施形態1と同様にして、比較例13に係る混合活物質を作製した。
LiCo0.33Ni0.33Mn0.33O2を混合しない他は、実施形態1と同様にして、比較例14に係る活物質を作製した。
LiCo0.33Ni0.33Mn0.33O2を混合しない他は、比較例12と同様にして、比較例15に係る活物質を作製した。
LiMeO2型リチウム遷移金属複合酸化物を酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を塩酸処理(0.5Mの硫酸水溶液100mLの代わりに1M100mLの塩酸水溶液を使用)した他は、実施形態1と同様にして、比較例16に係る混合活物質を作製した。
LiMeO2型リチウム遷移金属複合酸化物を酸処理工程において、LiCo0.33Ni0.33Mn0.33O2を硝酸処理(0.5Mの硫酸水溶液100mLの代わりに1M100mLの硝酸水溶液を使用)した他は、実施形態1と同様にして、比較例17に係る混合活物質を作製した。
Li1.17Co0.10Ni0.17Mn0.56O2を混合しない他は、比較例11と同様にして、比較例18に係る活物質を作製した。
Li1.17Co0.10Ni0.17Mn0.56O2を混合しない他は、実施形態1と同様にして、比較例19に係る活物質を作製した。
実施形態1~10及び比較例1~19のそれぞれの活物質を用いて、以下の手順でリチウム二次電池(モデルセル)を作製し、電池特性を評価した。
正負極とも活物質重量が60mgとなるように塗布重量を調整した。
この活物質の比表面積の測定及びS含有量の分析については、試験電池における電極中における活物質を採取することで行った。放電状態にて解体した正極板を取り出し、DMCをもちいて電極に付着した電解液をよく洗浄した。その後Al集電体(アルミニウム箔)上の合剤を採取し、この合剤を前述の小型電気炉を用いて600℃で4時間焼成することで導電剤であるカーボンおよび結着剤であるPVdFバインダーを除去し、混合活物質のみを得た。
比表面積の測定は、BET1点法にて行い、混合活物質重量で割った数値を求めた。
また、S含有量についてはICP測定によって算出した。活物質50mgを35%塩酸水溶液10mlに溶解させ、測定用のサンプルとした。また、別途標準溶液を用いて検量線を作成しておき、それと比較して含有量を求めた。
上記方法にて解体して得られた正極板をDMCで洗浄後、十分乾燥したのちに20kNの平板プレス(理研製油圧ポンプ TYPE P-1B、プレス台CDM-20M)を行い、Al集電体からの合剤剥離をチェックした。その結果、集電体からの剥離は認められなかった。
これに対して、比較例1~10のように、混合活物質の比表面積が4.4m2/gを超える場合、及び/又は、S含有量が1.2質量%を超える(LiMeO2型リチウム遷移金属複合酸化物の酸処理の程度が高い)場合、サイクルエネルギー密度維持率が低くなり、比較例11のように、LiMeO2型リチウム遷移金属複合酸化物を酸処理しない(S含有量が0である)場合、初期効率が低く、電池容量が小さくなり、比較例12、13及び15のように、酸処理したリチウム過剰型リチウム遷移金属複合酸化物を用いた(比表面積が4.4m2/gを超える)場合、サイクルエネルギー密度維持率が低くなり、比較例14のように、LiMeO2型リチウム遷移金属複合酸化物を含有しない(S含有量が0である)場合、初期効率が低く、電池容量が小さくなり、比較例16のように、LiMeO2型リチウム遷移金属複合酸化物を塩酸で処理した(S含有量が0である)場合、電池容量が小さく、サイクルエネルギー密度維持率が低くなり、比較例17のように、LiMeO2型リチウム遷移金属複合酸化物を硝酸で処理した(S含有量が0である)場合、サイクルエネルギー密度維持率が低くなり、比較例18のように、酸処理していないLiMeO2型リチウム遷移金属複合酸化物を用い、リチウム過剰型リチウム遷移金属複合酸化物を含有しない(S含有量が0である)場合、初期効率が低く、電池容量が小さくなり、比較例19のように、酸処理したLiMeO2型リチウム遷移金属複合酸化物を用い、比表面積を4.4m2/g以下、且つS含有量を0.2~1.2質量%としても、リチウム過剰型リチウム遷移金属複合酸化物を含有しない場合、電池容量が小さくなる。
101 組電池
102 電池パック
Claims (19)
- α-NaFeO2構造を有し、遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/MeがMn/Me>0.5であるリチウム遷移金属複合酸化物、及び、α-NaFeO2構造を有し、遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/Meが0<Mn/Me≦0.5であるリチウム遷移金属複合酸化物を含有するリチウム二次電池用混合活物質であって、比表面積が4.4m2/g以下であり、且つS含有量が0.2~1.2質量%であることを特徴とするリチウム二次電池用混合活物質。
- 遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/Meが0<Mn/Me≦0.5であるリチウム遷移金属複合酸化物の酸処理により前記Sを含有させることを特徴とする請求項1に記載のリチウム二次電池用混合活物質。
- 前記遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/MeがMn/Me>0.5であるリチウム遷移金属複合酸化物と、前記遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/Meが0<Mn/Me≦0.5であるリチウム遷移金属複合酸化物と、の混合割合は、70:30~95:5である請求項1又は2に記載のリチウム二次電池用混合活物質。
- 前記遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/MeがMn/Me>0.5であるリチウム遷移金属複合酸化物と、前記遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/Meが0<Mn/Me≦0.5であるリチウム遷移金属複合酸化物と、の混合割合は、80:20~90:10である請求項1又は2に記載のリチウム二次電池用混合活物質。
- 前記前記遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/MeがMn/Me>0.5であるリチウム遷移金属複合酸化物は、前記遷移金属元素Meに対するCoのモル比Co/Meは、0.05~0.40である請求項1~4のいずれかに記載のリチウム二次電池用混合活物質。
- 前記前記遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/MeがMn/Me>0.5であるリチウム遷移金属複合酸化物は、前記遷移金属元素Meに対するCoのモル比Co/Meは、0.10~0.30である請求項1~4のいずれかに記載のリチウム二次電池用混合活物質。
- 前記比表面積は4.2m2/g以下である請求項1~6のいずれかに記載のリチウム二次電池用混合活物質。
- 前記比表面積は3.8m2/g以下である請求項1~6のいずれかに記載のリチウム二次電池用混合活物質。
- 前記S含有量が0.2~1.0質量%である請求項1~8のいずれかに記載のリチウム二次電池用混合活物質。
- 前記S含有量が0.2~0.8質量%である請求項1~8のいずれかに記載のリチウム二次電池用混合活物質。
- 前記前記遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/MeがMn/Me>0.5であるリチウム遷移金属複合酸化物は、前記モル比Mn/Meは0.5<Mn/Me≦0.8である請求項1~10のいずれかに記載のリチウム二次電池用混合活物質。
- 前記前記遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/Meが0.5<Mn/Me≦0.75であるリチウム遷移金属複合酸化物は、前記モル比Mn/Meは0.5<Mn/Me≦0.8である請求項1~10のいずれかに記載のリチウム二次電池用混合活物質。
- 前記前記遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/MeがMn/Me>0.5であるリチウム遷移金属複合酸化物は、前記遷移金属に対するリチウム(Li)のモル比Li/Meが1より大きい請求項1~12のいずれかに記載のリチウム二次電池用混合活物質。
- 前記前記遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/MeがMn/Me>0.5であるリチウム遷移金属複合酸化物は、前記遷移金属に対するリチウム(Li)のモル比Li/Meが1.2より大きい請求項1~12のいずれかに記載のリチウム二次電池用混合活物質。
- 前記前記遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/MeがMn/Me>0.5であるリチウム遷移金属複合酸化物は、前記遷移金属に対するリチウム(Li)のモル比Li/Meが1.2を超え1.6未満である請求項1~12のいずれかに記載のリチウム二次電池用混合活物質。
- 前記前記遷移金属(Me)がCo、Ni及びMnを含み、モル比Mn/MeがMn/Me>0.5であるリチウム遷移金属複合酸化物は、前記遷移金属に対するリチウム(Li)のモル比Li/Meが1.25以上1.5以下である請求項1~12のいずれかに記載のリチウム二次電池用混合活物質。
- 請求項1~16のいずれか1項に記載のリチウム二次電池用混合活物質を含有するリチウム二次電池用電極。
- 請求項17に記載のリチウム二次電池用電極を備えたリチウム二次電池。
- 請求項18に記載のリチウム二次電池を複数個集合して構成した蓄電装置。
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JPWO2018012384A1 (ja) * | 2016-07-14 | 2019-05-30 | 株式会社Gsユアサ | リチウム遷移金属複合酸化物、遷移金属水酸化物前駆体、遷移金属水酸化物前駆体の製造方法、リチウム遷移金属複合酸化物の製造方法、非水電解質二次電池用正極活物質、非水電解質二次電池用電極、非水電解質二次電池及び蓄電装置 |
JP7004959B2 (ja) | 2016-07-14 | 2022-01-21 | 株式会社Gsユアサ | リチウム遷移金属複合酸化物、遷移金属水酸化物前駆体、遷移金属水酸化物前駆体の製造方法、リチウム遷移金属複合酸化物の製造方法、非水電解質二次電池用正極活物質、非水電解質二次電池用電極、非水電解質二次電池及び蓄電装置 |
JP2020184472A (ja) * | 2019-05-09 | 2020-11-12 | 株式会社Gsユアサ | 非水電解質蓄電素子用正極、及びこれを備えた非水電解質蓄電素子 |
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JP6274536B2 (ja) | 2018-02-07 |
CN105359311B (zh) | 2017-10-31 |
CN105359311A (zh) | 2016-02-24 |
US20160190551A1 (en) | 2016-06-30 |
JPWO2015004856A1 (ja) | 2017-03-02 |
DE112014003191T5 (de) | 2016-03-24 |
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