JP2009224305A - LITHIUM SECONDARY BATTERY WITH Li-Sn-Mn COMPOUND POSITIVE ELECTRODE THIN FILM, MANUFACTURING METHOD OF Li-Sn-Mn COMPOUND TARGET AND POSITIVE ELECTRODE THIN FILM DEPOSITION METHOD USING THIS - Google Patents
LITHIUM SECONDARY BATTERY WITH Li-Sn-Mn COMPOUND POSITIVE ELECTRODE THIN FILM, MANUFACTURING METHOD OF Li-Sn-Mn COMPOUND TARGET AND POSITIVE ELECTRODE THIN FILM DEPOSITION METHOD USING THIS Download PDFInfo
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- H01M4/50—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of manganese
- H01M4/505—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of manganese of mixed oxides or hydroxides containing manganese for inserting or intercalating light metals, e.g. LiMn2O4 or LiMn2OxFy
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- H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
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Abstract
Description
本発明は、Li−Sn−Mn化合物正極薄膜を備えるリチウム二次電池、並びにLi−Sn−Mn化合物ターゲットの製造方法及びこれを用いた正極薄膜形成方法に関する。 The present invention relates to a lithium secondary battery including a Li—Sn—Mn compound positive electrode thin film, a method for producing a Li—Sn—Mn compound target, and a method for forming a positive electrode thin film using the same.
リチウム二次電池の正極材料として既に実用化されているリチウムコバルト酸化物(LiCoO2)は高価であり、環境問題、安全性問題などを抱えていることから、リチウムマンガン酸化物はリチウムニッケル酸化物(LiNiO2)と共に、これらの問題を解決する代替物質として多くの研究が行われている物質である。リチウムコバルト酸化物及びリチウムニッケル酸化物は、過充電時に酸素が発生し爆発の危険性があるが、リチウムマンガン酸化物は、過充電時にも酸素が発生せず、コバルト(Co)に比べて相対的に豊富な元素であるマンガン(Mn)を用いることによって、価格が低廉であるという長所がある。 Lithium cobalt oxide (LiCoO 2 ), which has already been put into practical use as a positive electrode material for lithium secondary batteries, is expensive and has environmental and safety problems. Therefore, lithium manganese oxide is lithium nickel oxide. Along with (LiNiO 2 ), many materials have been studied as an alternative material to solve these problems. Lithium cobalt oxide and lithium nickel oxide generate oxygen when overcharged and there is a danger of explosion. However, lithium manganese oxide does not generate oxygen even when overcharged, and it is relative to cobalt (Co). By using manganese (Mn), which is an abundant element, there is an advantage that the price is low.
しかし、リチウムマンガン酸化物の理論充電容量(148mAh/g)は、リチウムコバルト酸化物の理論充電容量(274mAh/g)よりも小さく、充放電サイクルが繰り返されるに伴い、放電容量が急激に減少するという短所を有している。W. Liuら(J. Electronchem. Soc.、Vol. 143, No. 11,pp. 3590-3596, 1996)、及びR. J. Gummowら(Solid State Ionics, Vol. 69, No. pp. 59-67, 1994)は、充放電が繰り返される際に、リチウムイオンの挿入により正極でリチウムマンガン酸化物(Li2Mn2O4)が形成されることによる正方晶(tetragonal)への相転移が充放電サイクル不良の原因であると説明する。 However, the theoretical charge capacity (148 mAh / g) of lithium manganese oxide is smaller than the theoretical charge capacity (274 mAh / g) of lithium cobalt oxide, and the discharge capacity rapidly decreases as the charge / discharge cycle is repeated. It has the disadvantages. W. Liu et al. (J. Electronchem. Soc., Vol. 143, No. 11, pp. 3590-3596, 1996) and RJ Gummow et al. (Solid State Ionics, Vol. 69, No. pp. 59-67, 1994), when charge and discharge are repeated, the phase transition to tetragonal due to the formation of lithium manganese oxide (Li 2 Mn 2 O 4 ) at the positive electrode by the insertion of lithium ions is the charge and discharge cycle. Explain that it is the cause of the defect.
リチウムイオンの挿入によってマンガン(Mn)イオンの平均原子価が3.5以下に減少し、強いJahn-Teller変形が発生して(G. Pistoiaら、Solid State Ionics, Vol. 78, pp. 115-122, 1995)、結晶構造が立方晶(cubic)から正方晶に変化し、その結果、これ以上のリチウム脱挿入が難しくなる。すなわち、スピネル構造で3価のマンガンイオンの配列(t32g・e1g, high spin)が変化し、八面体が強く伸長し、c/a比率が単位セル当り16%増加するのに伴い、充放電が繰り返される間に正極の構造的平衡を維持することができなくなる。また、リチウム離脱時にマンガンの平均原子価(valence)が再び3.5に戻りながら生じるMn3+(3d4)の原子価の変化により、放電が困難になり、充放電容量が急激に減少するものと考えられている。 Insertion of lithium ion reduces the average valence of manganese (Mn) ion to 3.5 or less, and strong Jahn-Teller deformation occurs (G. Pistoia et al., Solid State Ionics, Vol. 78, pp. 115- 122, 1995), the crystal structure changes from cubic to tetragonal, and as a result, further lithium desorption is difficult. That is, as the arrangement of trivalent manganese ions (t32g · e1g, high spin) changes in the spinel structure, the octahedron stretches strongly, and the c / a ratio increases by 16% per unit cell. It becomes impossible to maintain the structural equilibrium of the positive electrode during the repetition. Moreover, due to the change in the valence of Mn 3+ (3d4) that occurs while the average valence of manganese returns to 3.5 again when lithium leaves, the discharge becomes difficult and the charge / discharge capacity decreases rapidly. It is considered.
本発明は、Li−Sn−Mn化合物正極薄膜を備えるリチウム二次電池、Li−Sn−Mn化合物ターゲットの製造方法及びこれを用いた正極薄膜の形成方法を提供することを目的とする。 An object of this invention is to provide the manufacturing method of a lithium secondary battery provided with a Li-Sn-Mn compound positive electrode thin film, a Li-Sn-Mn compound target, and a positive electrode thin film using the same.
本発明のリチウム二次電池用薄膜正極の形成方法は、Li2CO3、MnO2及びSnO粉末を混合して混合粉末を設ける段階と、前記混合粉末を1次粉砕する段階と、前記1次粉砕された混合粉末を仮焼する段階と、前記仮焼された混合粉末を2次粉砕する段階と、前記2次粉砕された混合粉末を加圧成形する段階と、前記加圧成形された混合物を焼結してLi、Sn、Mn及びOを備えるターゲットを製造する段階と、前記ターゲットにレーザを照射して基板に前記Li、Sn、Mn及びOを備える正極薄膜を局所蒸着する段階とを備える。 The method of forming a thin film positive electrode for a lithium secondary battery according to the present invention includes a step of mixing Li 2 CO 3 , MnO 2 and SnO powder to provide a mixed powder, a step of primary pulverizing the mixed powder, and a step of the primary A step of calcining the pulverized mixed powder, a step of secondary pulverizing the calcined mixed powder, a step of pressure-molding the secondary pulverized mixed powder, and the pressure-molded mixture A step of producing a target comprising Li, Sn, Mn, and O, and a step of locally depositing a positive electrode thin film comprising Li, Sn, Mn, and O on a substrate by irradiating the target with a laser. Prepare.
また、本発明のLiSnx/2Mn2−xO4(0<x≦0.05)ターゲットの製造方法は、Li2CO3、MnO2及びSnO粉末を混合して混合粉末を設ける段階と、前記混合粉末を1次粉砕する段階と、前記1次粉砕された混合粉末を仮焼する段階と、前記仮焼された混合粉末を2次粉砕する段階と、前記2次粉砕された混合粉末を加圧成形する段階と、前記加圧成形された混合物を焼結してLiSnx/2Mn2−xO4(0<x≦0.05)ターゲットを製造する段階とを備える。 Moreover, the manufacturing method of the LiSn x / 2 Mn 2-x O 4 (0 <x ≦ 0.05) target of the present invention includes a step of mixing Li 2 CO 3 , MnO 2 and SnO powder to provide a mixed powder. A step of primary pulverizing the mixed powder, a step of calcining the primary pulverized mixed powder, a step of secondary pulverizing the calcined mixed powder, and the secondary pulverized mixed powder. And a step of sintering the pressure-molded mixture to produce a LiSn x / 2 Mn 2-x O 4 (0 <x ≦ 0.05) target.
また、本発明のリチウム二次電池は、Li、Sn、Mn及びOの化合物正極の組成物を備える。 The lithium secondary battery of the present invention includes a composition of a compound positive electrode of Li, Sn, Mn, and O.
以下に本発明の実施態様を、添付図面を用いて詳細に説明するが、本発明はこれらの実施態様に限定されるものではない。 Embodiments of the present invention will be described below in detail with reference to the accompanying drawings, but the present invention is not limited to these embodiments.
本発明のリチウム二次電池正極薄膜は、スピネル構造を有するリチウムマンガン酸化物(LiMn2O4)に少量のスズ化合物を添加して形成し、次の化学式(1)の組成を有する。 The lithium secondary battery positive electrode thin film of the present invention is formed by adding a small amount of a tin compound to lithium manganese oxide (LiMn 2 O 4 ) having a spinel structure, and has the following chemical formula (1).
LiSnx/2Mn2−xO4 (1)
(式中、xは0<x≦0.05である)。
LiSn x / 2 Mn 2-x O 4 (1)
(Wherein x is 0 <x ≦ 0.05).
本発明の実施例では、LiSnx/2Mn2−xO4(0<x≦0.05)のターゲットを製造し、レーザ局所蒸着法を用いて、ターゲット組成成分の組成を有する正極薄膜を容易に形成することができる。 In an embodiment of the present invention, a target of LiSn x / 2 Mn 2-x O 4 (0 <x ≦ 0.05) was manufactured, and a positive electrode thin film having a composition of target composition components was prepared using a laser local vapor deposition method. It can be formed easily.
第1実施例(ターゲットの製造)
LiSnx/2Mn2−xO4(x=0、0.025、0.05)ターゲットの製造のために、Li2CO3,MnO2及びSnO粉末を、重量%でそれぞれが、19.0〜19.1:79.3〜80.7:0.3〜1.6になるように正確に秤量する。ここで、Li2CO3の重量%は、熱処理時にリチウムが損失するのを勘案して、その適切量よりも10%ほど多い量としている。 秤量した粉末を無水アルコール及びイットリア安定化ジルコニア(yttria stabilized zirconia)と共に24時間ボールミリング(ball-milling)した後、120℃で24時間乾燥させて混合粉末を準備し、アルミナ擂り鉢で1次粉砕した後、空気雰囲気中で400℃〜800℃で1〜5時間の間仮焼する。仮焼した粉末の中の一部を再びアルミナ擂り鉢で2次粉砕してPVA(polyvinyl alcohol)バインダと混ぜた後、1〜5ton/cm2の圧力でペレット状に一軸加圧成形した後、仮焼された粉末の中の加圧成形されていない残りと共に空気雰囲気中800℃〜1200℃で1〜24時間の間焼結(最終焼結)を実施する。
First embodiment (target production)
For the production of LiSn x / 2 Mn 2-x O 4 (x = 0, 0.025, 0.05) target, Li 2 CO 3 , MnO 2 and SnO powder, each in weight percent, 19. Weigh accurately to be 0-19.1: 79.3-80.7: 0.3-1.6. Here, the weight percentage of Li 2 CO 3 is set to an amount that is about 10% larger than the appropriate amount in consideration of the loss of lithium during heat treatment. The weighed powder is ball-milled with anhydrous alcohol and yttria stabilized zirconia for 24 hours, then dried at 120 ° C. for 24 hours to prepare a mixed powder, and first ground in an alumina mortar And calcining at 400 ° C. to 800 ° C. for 1 to 5 hours in an air atmosphere. A part of the calcined powder is secondarily ground in an alumina mortar and mixed with a PVA (polyvinyl alcohol) binder, and then uniaxially pressed into a pellet at a pressure of 1 to 5 ton / cm 2 . Sintering (final sintering) is carried out in the air atmosphere at 800 ° C. to 1200 ° C. for 1 to 24 hours together with the remaining non-press-molded powder in the calcined powder.
図1aは、仮焼後、焼結前の粉末のX線回折分析結果を示し、Li2MnO3,γ−Mn2O3及びSnO2などの不純物相が存在することを示している。図1bに示すように、最終的に焼結した後の粉末のX線回折分析結果では、もっぱらLiMn2O4型のスピネル相のみが示されることが分かる。このことは、最終焼結の後に不純物相が消失し、特にスズ元素はスピネル構造内に固溶して置換されたことを意味する。また、製造されたターゲットの密度は3.5g/cm3程度であり、この数値は理論密度(4.4g/cm3)の80%程度であり、これまで報告された他のターゲットの密度の数値よりも大きい。 FIG. 1a shows the result of X-ray diffraction analysis of the powder after calcination and before sintering, and shows that there are impurity phases such as Li 2 MnO 3 , γ-Mn 2 O 3 and SnO 2 . As shown in FIG. 1b, the X-ray diffraction analysis result of the powder after final sintering shows that only the LiMn 2 O 4 type spinel phase is shown. This means that the impurity phase disappeared after the final sintering, and in particular, the tin element was replaced by being dissolved in the spinel structure. Moreover, the density of the manufactured target is about 3.5 g / cm 3 , and this value is about 80% of the theoretical density (4.4 g / cm 3 ). Greater than the number.
第2実施例(レーザ局所蒸着法による薄膜製造)
前述した第1実施例によって製造したターゲットをホルダに固定し、次いで洗浄した基板を基板ホルダに固定して、レーザ局所蒸着を実施する。この時、電気化学特性の測定のための電極の位置に該当する基板の一部分をマスクで分ける。基板とターゲット間の距離は3〜5cmにする。真空チャンバ内の基本圧力は1×10−5Torr以下に調節する。基板の温度は350〜550℃、作用ガスである酸素の圧力は0.05〜0.25Torrに調節する。波長の範囲が248nmであり、20ns持続時間を有するKrFエキシマレーザを用い、レーザビームの大きさを2〜5mm2に、PLD(pulsed laser deposition)出力密度を1〜4J/cm2、スポット反復率を3〜10Hz、照射時間を3〜120分間として、ターゲットの構成成分であるLiSnx/2Mn2−xO4を基板上に蒸着する。
Second Example (Manufacturing Thin Film by Laser Local Vapor Deposition)
The target manufactured by the first embodiment described above is fixed to the holder, and then the cleaned substrate is fixed to the substrate holder, and laser local vapor deposition is performed. At this time, a part of the substrate corresponding to the position of the electrode for measuring the electrochemical characteristics is divided with a mask. The distance between the substrate and the target is 3 to 5 cm. The basic pressure in the vacuum chamber is adjusted to 1 × 10 −5 Torr or less. The temperature of the substrate is adjusted to 350 to 550 ° C., and the pressure of oxygen as the working gas is adjusted to 0.05 to 0.25 Torr. Using a KrF excimer laser with a wavelength range of 248 nm and a 20 ns duration, the laser beam size is 2 to 5 mm 2 , the PLD (pulsed laser deposition) output density is 1 to 4 J / cm 2 , and the spot repetition rate Is set to 3 to 10 Hz and the irradiation time is set to 3 to 120 minutes, and LiSn x / 2 Mn 2-x O 4 which is a component of the target is deposited on the substrate.
実施例1によって得られた厚さ0.1〜1μmの一部がスズで置換されたリチウムマンガン酸化物薄膜を正極に用い、負極としてリチウムを、電解質としてリチウムヘキサフルオロフォスフェート(LiPF6)をエチレンカルボネート:ジエチルカルボネート=1:1(体積比)の有機溶媒に溶解した電解液を用いた試験電池を製造し、この電池に対して充放電実験を行った。 The lithium manganese oxide thin film partially substituted with tin of 0.1 to 1 μm thick obtained in Example 1 was used as the positive electrode, lithium as the negative electrode, and lithium hexafluorophosphate (LiPF 6 ) as the electrolyte. A test battery using an electrolytic solution dissolved in an organic solvent of ethylene carbonate: diethyl carbonate = 1: 1 (volume ratio) was manufactured, and a charge / discharge experiment was performed on this battery.
LiSnx/2Mn2−xO4薄膜での初期充放電容量は、x=0.05で最も高かった。遮断(cut-off)電圧を3.0Vから4.5Vに変更した時のLiSnx/2Mn2−xO4の充放電特性を図2に示す。初期充放電容量は、図2a、b、cの各々が、97.9,120.0,133.0mAh/gであり、これは理論容量の66%、81%、90%程度となる。一般に、スピネル型リチウムマンガン酸化物正極の容量に決定的な役割を果たすMn3+イオンの量は、LiSnx/2Mn2−xO4において、xが増加するにつれて減少し、同時に初期充放電容量も減少する。しかし、本発明においては、x値の増加に伴い初期放電容量が増加したが、この理由は、マンガンの不完全な(Mn deficient)結晶構造により、より多くのリチウムイオンが正極結晶構造内に脱挿入できるからである。また、正極容量に決定的な因子である電子伝導度(electronic conductivity)がスズ(Sn)の添加によって向上し、充放電効率のみならず、初期充放電容量も増加したからである(G. M. Ehrlichら:Sens. Actuators A, Vol. 51, pp. 17-19, 1995, X. Wuら:Surf. Coat. Technol.、Vol. 186, pp. 412-415 (2004)、K. S. Parkら:Solid State Commun.、Vol. 129, pp. 311-314, 2004)。 The initial charge / discharge capacity of the LiSn x / 2 Mn 2-x O 4 thin film was highest at x = 0.05. FIG. 2 shows the charge / discharge characteristics of LiSn x / 2 Mn 2-x O 4 when the cut-off voltage is changed from 3.0 V to 4.5 V. The initial charge / discharge capacities are 97.9, 120.0, and 133.0 mAh / g in FIGS. 2A, 2B, and 2C, respectively, which are about 66%, 81%, and 90% of the theoretical capacity. In general, the amount of Mn 3+ ions that play a decisive role in the capacity of the spinel-type lithium manganese oxide positive electrode decreases with increasing x in LiSn x / 2 Mn 2−x O 4 , and at the same time the initial charge / discharge capacity. Also decreases. However, in the present invention, the initial discharge capacity increased as the x value increased. This is because more lithium ions are desorbed into the positive electrode crystal structure due to the Mn deficient crystal structure of manganese. This is because it can be inserted. In addition, the electronic conductivity which is a decisive factor for the positive electrode capacity is improved by the addition of tin (Sn), and not only the charge / discharge efficiency but also the initial charge / discharge capacity is increased (GM Ehrlich et al. : Sens. Actuators A, Vol. 51, pp. 17-19, 1995, X. Wu et al .: Surf. Coat. Technol., Vol. 186, pp. 412-415 (2004), KS Park et al .: Solid State Commun Vol. 129, pp. 311-314, 2004).
図3は、試験電池における充放電実験おいて、遮断電圧を3.0Vから4.5Vに増加して充放電実験を行ったときの充放電回数による放電容量の変化を示す。純粋なLiMn2O4は不安定な放電容量を示すのに対し、本発明によって形成された正極薄膜LiSn0.0125Mn1.975O4を備える電池の充放電効率特性は、飛び抜けて高いことが分かる。LiSnx/2Mn2−xO4正極薄膜の容量及び充放電効率の向上は、既存の様々な薄膜製造法で作製した異種元素によってドーピング及び置換されたLiMn2O4系リチウム二次電池用正極薄膜の容量及び充放電性能向上値よりも優れている。さらに高い電流密度(4C)でも優れた容量及び充放電特性を示す。 FIG. 3 shows a change in discharge capacity depending on the number of times of charge / discharge when the interruption voltage is increased from 3.0V to 4.5V in a charge / discharge experiment in a test battery. While pure LiMn 2 O 4 exhibits an unstable discharge capacity, the charge / discharge efficiency characteristics of the battery comprising the positive electrode thin film LiSn 0.0125 Mn 1.975 O 4 formed according to the present invention are remarkably high. I understand. The capacity and charge / discharge efficiency of the LiSn x / 2 Mn 2-x O 4 positive electrode thin film are improved for LiMn 2 O 4 based lithium secondary batteries doped and replaced by different elements produced by various existing thin film manufacturing methods. It is superior to the capacity and charge / discharge performance improvement value of the positive electrode thin film. Furthermore, even at a high current density (4C), excellent capacity and charge / discharge characteristics are exhibited.
図4に示すように、マンガンが不十分な組成であるLiSn0.0125Mn1.975O4及びLiSn0.025Mn1.95O4においても、LiMn2O4組成と同様に、(111)、(311)及び(400)面の回折ピークがそれぞれ現れ、空間群が
(立方晶、no.227)でスピネル構造を有することが示された。
As shown in FIG. 4, LiSn 0.0125 Mn 1.975 O 4 and LiSn 0.025 Mn 1.95 O 4 , which have an insufficient manganese composition, are similar to the LiMn 2 O 4 composition (111 ), (311) and (400) plane diffraction peaks respectively,
(Cubic crystal, no. 227) was shown to have a spinel structure.
図5に示すように、LiSnx/2Mn2−xO4組成においてx値を変化させたときのラマンスペクトル結果を分析することにより、スズで一部が置換されたスピネル構造のマンガン(Mn)と酸素(O)との間の伸縮振動(stretching vibration)を示すA1gピーク(630〜650cm−1領域の主ピーク)が低いラマンシフト値へ移動したことが分かる。これはマンガン−酸素結合の距離が減少したためであり、充放電時に相変化を起こさず、さらに多くのリチウムイオンが空いた八面体位置に脱挿入されることができ、スピネルの構造的安定性が向上したことを意味する。スズ置換の肯定的効果はx=0.025とx=0.05との間のラマンピークの変化がないことからみると、x=0.05以下に制限されることが分かる。 As shown in FIG. 5, by analyzing the Raman spectrum result when the x value was changed in the LiSn x / 2 Mn 2-x O 4 composition, manganese having a spinel structure partially substituted with tin (Mn It can be seen that the A1g peak (the main peak in the 630 to 650 cm −1 region) indicating the stretching vibration between oxygen) and oxygen (O) has shifted to a lower Raman shift value. This is because the distance between manganese-oxygen bonds has decreased, and phase change does not occur during charging / discharging, and more lithium ions can be inserted and removed into the vacant octahedron position, thereby improving the structural stability of the spinel. Means improved. It can be seen that the positive effect of tin substitution is limited to x = 0.05 or less, given that there is no change in the Raman peak between x = 0.025 and x = 0.05.
前記リチウム二次電池用正極薄膜は、マンガンが不十分なLiSnx/2Mn2−xO4(0<x≦0.05)組成の場合、マンガンが不十分ではないLiMδMn2−δO4(“M”は金属元素)組成に比べて、充放電時にさらに多くのリチウムイオンを含有することができ、金属元素が置換されていない原組成のLiMn2O4に比べてより大きい充放電容量を示す(R. J. Gummowら:solid State Ionics, Vol. 69, pp. 59-67, 1994、D. Singhら:Electrochem. Solid-State Letter, Vol. 5, Issue 9, pp. A198-A201, 2002)。また、マンガン−酸素結合の距離の減少は、リチウムイオンが4V領域で8a四面体の位置に脱挿入される経路として作用し、リチウムイオンが8a四面体位置に全て挿入された後、3V領域でリチウムが挿入される、スピネルの16cの八面体位置の空間をさらに広くし(K. Kangら:Science, Vol. 311, pp. 977-980, 2006、K. Tateishiら:Appl. Phys. Letter, Vol. 84, Issue 4, pp. 529-531, 2004、J. B. Batesら:J. Electrochem. Soc., Vol. 142, Issue 9, pp. L149-L151, 1995)、スズ置換によってリチウムイオンの移動及び伝導性が向上され得ることを意味する(S. Chitraら:J. Electrochem., Vol. 3, pp. 433-441, 1999、C. M. Julienら:Mater. Sci. Eng. B, Vol. 100, pp. 69-78, 2003)。
When the positive electrode thin film for a lithium secondary battery has a LiSn x / 2 Mn 2-x O 4 (0 <x ≦ 0.05) composition with insufficient manganese, LiM δ Mn 2-δ with insufficient manganese. Compared with the composition of O 4 (“M” is a metal element), more lithium ions can be contained during charging / discharging, and the charge / discharge is larger than that of LiMn 2 O 4 of the original composition in which the metal element is not substituted. Indicates discharge capacity (RJ Gummow et al .: Solid State Ionics, Vol. 69, pp. 59-67, 1994, D. Singh et al .: Electrochem. Solid-State Letter, Vol. 5, Issue 9, pp. A198-A201, 2002). Further, the decrease in the manganese-oxygen bond distance acts as a path for lithium ions to be deinserted into the 8a tetrahedron position in the 4V region, and after all the lithium ions have been inserted into the 8a tetrahedron position, in the 3V region. The space of the octahedral position of spinel 16c into which lithium is inserted is further expanded (K. Kang et al .: Science, Vol. 311, pp. 977-980, 2006, K. Tateishi et al .: Appl. Phys. Letter, Vol. 84,
本発明の属する技術分野の当業者は、本発明がその技術的思想や必須の特徴を設定せず、他の具体的な形態で実施できたということを理解することができる。従って、以上で記述した実施例は全ての面で例示的なものであり、限定的ではないものと理解しなければならない。本発明の範囲は前記詳細な説明よりは後述する特許請求の範囲によって示され、特許請求の範囲の意味及び範囲そしてその等価概念から導き出される全ての設定または変形された形態が本発明の範囲に含まれると解釈されなければならない。 Those skilled in the art to which the present invention pertains can understand that the present invention has been implemented in other specific forms without setting the technical idea or essential features thereof. Accordingly, it should be understood that the embodiments described above are illustrative in all aspects and not limiting. The scope of the present invention is defined by the following claims rather than the above detailed description, and all the settings or modified forms derived from the meaning and scope of the claims and equivalents thereof are within the scope of the present invention. Must be interpreted as included.
[発明の効果]
本発明は、リチウムマンガン酸化物(LiMn2O4)のマンガンを少量のスズ(Sn)で置換させることによって、Jahn-Teller変形を抑制し、相転移を防止してマンガン(Mn)イオンの平均原子価を3.5以上に維持させ、充放電容量を増加させることができる。
本発明の正極薄膜は、純粋なリチウムマンガン酸化物組成物を含む正極薄膜に比べて充放電容量が高く、薄膜を用いた電池の寿命を向上させることができ、高い電流密度でも優れた容量及び充放電サイクル特性を示すので、安定性に優れて高エネルギー、高電力の密度を要求する次世代マイクロ素子の具現を可能にする。
[The invention's effect]
The present invention replaces manganese of lithium manganese oxide (LiMn 2 O 4 ) with a small amount of tin (Sn), thereby suppressing Jahn-Teller deformation, preventing phase transition, and averaging manganese (Mn) ions. The valence can be maintained at 3.5 or more, and the charge / discharge capacity can be increased.
The positive electrode thin film of the present invention has a higher charge / discharge capacity than a positive electrode thin film containing a pure lithium manganese oxide composition, can improve the life of a battery using the thin film, and has an excellent capacity and high current density. Because it exhibits charge / discharge cycle characteristics, it enables the realization of next-generation micro devices that have excellent stability and require high energy and high power density.
Claims (15)
a)Li2CO3、MnO2及びSnO粉末を混合して混合粉末を設ける段階と、
b)前記混合粉末を1次粉砕する段階と、
c)前記1次粉砕された混合粉末を仮焼する段階と、
d)前記仮焼された混合粉末を2次粉砕する段階と、
e)前記2次粉砕された混合粉末を加圧成形する段階と、
f)前記加圧成形された混合物を焼結してLi、Sn、Mn及びOを備えるターゲットを製造する段階と、
g)前記ターゲットにレーザを照射して、基板に前記Li、Sn、Mn及びOを備える正極薄膜を局所蒸着する段階と、
を備えることを特徴とするリチウム二次電池正極薄膜形成方法。 A method for forming a lithium secondary battery positive electrode thin film,
a) mixing Li 2 CO 3 , MnO 2 and SnO powder to provide a mixed powder;
b) primary pulverizing the mixed powder;
c) calcination of the primary pulverized mixed powder;
d) secondary pulverizing the calcined mixed powder;
e) pressure-molding the secondary pulverized mixed powder;
f) sintering the pressure-molded mixture to produce a target comprising Li, Sn, Mn and O;
g) irradiating the target with laser and locally depositing a positive electrode thin film comprising the Li, Sn, Mn and O on the substrate;
A method for forming a positive electrode thin film for a lithium secondary battery, comprising:
a)Li2CO3、MnO2及びSnO粉末を混合して混合粉末を設ける段階と、
b)前記混合粉末を1次粉砕する段階と、
c)前記1次粉砕された混合粉末を仮焼する段階と、
d)前記仮焼された混合粉末を2次粉砕する段階と、
e)前記2次粉砕された混合粉末を加圧成形する段階と、
f)前記加圧成形された混合物を焼結してLiSnx/2Mn2−xO4(0<x≦0.05)ターゲットを製造する段階と、
を備えることを特徴とするLi−Sn−Mn化合物ターゲットの製造方法。 A method for producing a Li-Sn-Mn compound target,
a) mixing Li 2 CO 3 , MnO 2 and SnO powder to provide a mixed powder;
b) primary pulverizing the mixed powder;
c) calcination of the primary pulverized mixed powder;
d) secondary pulverizing the calcined mixed powder;
e) pressure-molding the secondary pulverized mixed powder;
f) sintering the pressure-molded mixture to produce a LiSn x / 2 Mn 2-x O 4 (0 <x ≦ 0.05) target;
A method for producing a Li—Sn—Mn compound target, comprising:
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JP2017522253A (en) * | 2014-05-22 | 2017-08-10 | シャープ株式会社 | Tin-containing compounds |
CN109065858A (en) * | 2018-07-25 | 2018-12-21 | 国联汽车动力电池研究院有限责任公司 | Modified tertiary cathode material in a kind of surface and preparation method thereof and its manufactured battery |
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KR101389774B1 (en) * | 2011-02-25 | 2014-04-28 | 세종대학교산학협력단 | Target for forming lithium-cotaning thin film for thin film bettery and preparing method of the same |
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CN102332575A (en) * | 2011-09-22 | 2012-01-25 | 西北工业大学 | Preparation method for carbon-doped lithium stannate cathodal material for lithium batteries |
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CN109065858A (en) * | 2018-07-25 | 2018-12-21 | 国联汽车动力电池研究院有限责任公司 | Modified tertiary cathode material in a kind of surface and preparation method thereof and its manufactured battery |
CN109065858B (en) * | 2018-07-25 | 2020-08-04 | 国联汽车动力电池研究院有限责任公司 | Surface modified ternary positive electrode material, preparation method thereof and battery prepared from surface modified ternary positive electrode material |
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