TW201226354A - Precursor glass for anode material of lithium ionic secondary cell and crystalline glass for anode material of lithium ionic secondary cell - Google Patents
Precursor glass for anode material of lithium ionic secondary cell and crystalline glass for anode material of lithium ionic secondary cell Download PDFInfo
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- TW201226354A TW201226354A TW100146243A TW100146243A TW201226354A TW 201226354 A TW201226354 A TW 201226354A TW 100146243 A TW100146243 A TW 100146243A TW 100146243 A TW100146243 A TW 100146243A TW 201226354 A TW201226354 A TW 201226354A
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C3/00—Glass compositions
- C03C3/04—Glass compositions containing silica
- C03C3/062—Glass compositions containing silica with less than 40% silica by weight
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C10/00—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition
- C03C10/0072—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition having a ferro-electric crystal phase
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C3/00—Glass compositions
- C03C3/12—Silica-free oxide glass compositions
- C03C3/16—Silica-free oxide glass compositions containing phosphorus
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C4/00—Compositions for glass with special properties
- C03C4/14—Compositions for glass with special properties for electro-conductive glass
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/02—Electrodes composed of, or comprising, active material
- H01M4/36—Selection of substances as active materials, active masses, active liquids
- H01M4/58—Selection of substances as active materials, active masses, active liquids of inorganic compounds other than oxides or hydroxides, e.g. sulfides, selenides, tellurides, halogenides or LiCoFy; of polyanionic structures, e.g. phosphates, silicates or borates
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/05—Accumulators with non-aqueous electrolyte
- H01M10/052—Li-accumulators
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/10—Energy storage using batteries
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Abstract
Description
201226354 六、發明說明: 【發明所屬之技術領域】 本發明是有關於一種可攜式電子機器或電動汽車等中 所使用之鐘離子二次電池正極材料用前驅體玻璃以及鐘離 子二次電池正極材料用結晶化玻璃。 【先前技術】 鋰離子二次電池確立了作為可攜式電子終端或電動汽 車所不可欠缺的高容量、輕量的電源的地位。鋰離子二次 電池之正極材料中,迄今為止使用的是鈷酸鋰(Lic〇〇2) 或錳酸鋰(LiMn〇2)等無機金屬氧化物。然而,隨著近年 來電子機器之高性能化所造成之電力消耗的增大,要求進 -步之娜子二次電池之高容量化。而且,自環境保全問 題或能源問題之觀點考慮,要求自〇> 4 Mn等環境負擔 大的材料轉換為更加環境協調型的材料。另外,於近年來, ^資源枯關題受到關注,自此種觀點考慮,亦期望轉換 為取代鈷酸鋰或錳酸鋰之廉價的正極材料。 近年來 、珉本以及資源等方面而言有利考虞, 21 Ϊ m晶石型結晶、職⑽ ^ ϋ 以及撤禮石型結晶(LiF叫)受 關庄’並進订了種種研究以及開發( 開平9-m725號公報)。苴中,_ 1彳如—日本專利 溫卢穩定性俱S 撖欖石型結晶較鈷酸鋰 恤度穩疋f生更加優異,可期待於高溫下 由於是以猶為骨架之結構 動作。而卫 所造成之域魏㈣纽^由於充放電反201226354 VI. [Technical Field] The present invention relates to a precursor glass for a positive electrode material for a clock ion secondary battery used in a portable electronic device or an electric automobile, and a positive electrode for a plasma ion secondary battery. The material is made of crystallized glass. [Prior Art] A lithium ion secondary battery has established a position as a high-capacity, lightweight power source that is indispensable for portable electronic terminals or electric vehicles. Among the positive electrode materials for lithium ion secondary batteries, inorganic metal oxides such as lithium cobaltate (Lic® 2) or lithium manganate (LiMn〇 2) have heretofore been used. However, with the increase in power consumption caused by the high performance of electronic equipment in recent years, it is required to increase the capacity of the secondary battery of the step-by-step. Furthermore, from the viewpoint of environmental protection issues or energy issues, it is required to convert materials with a large environmental burden such as 〇4 Mn into more environmentally compatible materials. In addition, in recent years, the resource has been paid attention to, and from this point of view, it is also expected to be converted into an inexpensive cathode material that replaces lithium cobaltate or lithium manganate. In recent years, transcripts and resources are considered to be good, 21 Ϊ m spar crystal, occupation (10) ^ ϋ and demolition stone crystal (LiF called) by Guan Zhuang' and have made various research and development (Kaiping) Bulletin 9-m725).苴中, _ 1彳如—Japanese Patent Wenlu Stability S 撖 石 型 型 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 结晶 钴 钴 钴 钴 钴 钴 钴 钴 钴 钴 钴 钴 钴 钴 钴 钴And Wei Wei (four) New Zealand caused by Wei Wei
4 201226354 Λ. 另外’已知錳系尖晶石型、NASICON型以及橄欖石 型之各結晶中之鐵部位可被各種過渡金屬離子置換。例如 將鐵完全置換為錳或釩之Li3Mn2(p〇4)3、LiMnP〇4、Livp〇4 專’將鐵部分性地置換為鐘或飢之 Li3(MnxFeyVl(x+y))2(P〇4)3、LiMnxFe(1.x)P04 (0<X<1、〇 <y<i、〇<x+y<1)等亦具有作為正極材料之功能。 其中,已知若於正極材料中混合碳粉末等導電活性物 質’則使電子導電性提高。㉟而,若於«酸鐵鐘正極材料 中混,導電活性物質而進行職,則由於自伽鐵鐘所產 生之氣體的影響,存在無法於磷酸鐵鋰粒子表面使導電活 性物質效率良好地活化,電子導電度降低之問題。 因此,作為於煅燒時氣體之產生少的正極材料,提出 了包含結晶化玻璃之磷酸鐵鋰材料(例如參照日本專利 2009-87933號公報)。該前驅體玻璃與碳粉末_ 物質混合而煅燒時基本上不產生氣體。因此,可於正極材 料粒子表面效率良好地使導電活性物質活化,且容易達成 優異之電子導電性。而且’藉由對該前驅體玻璃進行锻燒, 可製作具有均質之組成的析丨有晶粒尺寸小之磷酸鐵鐘处 晶或磷酸鐵_溶體結晶的結晶化朗粉末,可: 導電性優異之雜子二次電池正極材料。如上所^, 用日本專利麵·8?933號公報巾所記載之磷酸鐵 料’則變得可麟料導·以及f子導雜這 2 均優異之正極材料。 奇& 日本專利2_·87933號公報中所記載之正極材料由 201226354 於玻璃組成而造成充放電時之電池容量有大的變化。然 而,於曰本專利20〇9·87933號公報中,關於電池容量之最' 佳組成的研究料充分,現狀是尚錢㈣有高的電池容 量之正極材料。 【發明内容】 本發明是鑒於此種狀況而成的,其目的在於提供可庐 得高的電池容#的_子二次電池正極材_前驅體玻^ 以及鋰離子二次電池正極材料用結晶化玻璃。 本,明是關於-種_子二次電池正極材料用前驅體 玻璃Ί徵在於··作為朗組成,以莫耳百分比計含 Ll2〇 20%〜观、p2〇5 2G%〜概、q%〜慨、μ 〇%〜60%、Nb2〇5 〇·1%〜2 4%,且以莫耳 Μη02/2) /Ρ2〇52〇.85。 丨、2u3 + 若使,具有上述組成之前驅體玻璃,則可製作具 的電池容量之轉子二次電池正極材料。 :「二 =璃」是指藉由進行熱處理而結晶化,析出目 第二,較佳的是本發明之鐘離 前驅體玻軌料百分tb収含有q%〜電24%== V2〇5l™?^2+Al2〇3+Ga^ °2 上述成刀疋使玻璃形成能力提高之成分。 ΐΐΐ1變:容易獲得玻璃化穩定、難以析出;不 異種^量高的 佳的是於本發明之鐘離子二次電池正極材料 2012263544 201226354 Λ. In addition, the iron sites in the crystals of the known manganese-based spinel type, NASICON type, and olivine type can be replaced by various transition metal ions. For example, Li3Mn2(p〇4)3, LiMnP〇4, Livp〇4, which completely replaces iron with manganese or vanadium, partially replaces iron with bell or hunger Li3 (MnxFeyVl(x+y))2 (P 〇4)3, LiMnxFe(1.x)P04 (0<X<1, 〇<y<i, 〇<x+y<1) and the like also have a function as a positive electrode material. Among them, it is known that when a conductive active material such as carbon powder is mixed in a positive electrode material, electron conductivity is improved. 35. If the conductive active material is mixed in the acid-electrode positive electrode material, the conductive active material may not be efficiently activated on the surface of the lithium iron phosphate particle due to the influence of the gas generated from the iron-iron clock. , the problem of reduced electronic conductivity. Therefore, as a positive electrode material having a small amount of gas generated during firing, a lithium iron phosphate material containing crystallized glass has been proposed (for example, refer to Japanese Patent Laid-Open Publication No. 2009-87933). The precursor glass is substantially free of gas when it is mixed with the carbon powder _ substance to be calcined. Therefore, the conductive active material can be efficiently activated on the surface of the positive electrode material particles, and excellent electron conductivity can be easily achieved. Moreover, by calcining the precursor glass, it is possible to produce a crystallized powder having a homogeneous composition and having a small crystal grain size of iron phosphate clock crystal or iron phosphate-solution crystal, which can be: Conductive Excellent miscellaneous secondary battery cathode material. As described above, the iron phosphate "described in the Japanese Patent No. 8-933 (Japanese Patent Publication No. 8933) has become a positive electrode material which is excellent in both of the materials and the f-conducting. The positive electrode material described in Japanese Patent Publication No. 2-87933 is composed of 201226354 and has a large change in battery capacity at the time of charge and discharge. However, in the publication of Japanese Patent Laid-Open Publication No. Hei. No. 20,879,937, the research on the most preferable composition of the battery capacity is sufficient, and the current situation is that the positive electrode material having a high battery capacity is still available. SUMMARY OF THE INVENTION The present invention has been made in view of such circumstances, and an object of the present invention is to provide a battery for a battery having a high battery capacity, a positive electrode material for a secondary battery, a precursor glass, and a crystal for a positive electrode material for a lithium ion secondary battery. Glass. Ben, Ming is about the _ sub-secondary battery positive electrode material for the precursor glass Ί 在于 在于 · · 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 朗 百分比 百分比 百分比 百分比 百分比 百分比 百分比 百分比 含 百分比 含 含 含 含~ gene, μ 〇%~60%, Nb2〇5 〇·1%~2 4%, and 莫02η02/2) /Ρ2〇52〇.85.丨, 2u3 + If the precursor glass having the above composition is used, a positive electrode material for a rotor secondary battery having a battery capacity can be produced. "二=璃" means crystallization by heat treatment, and precipitation is second. Preferably, the clock of the present invention is separated from the precursor glass rail by t% and contains 24% = 24% == V2 〇 5l TM?^2+Al2〇3+Ga^ °2 The composition of the above-mentioned knives to improve the glass forming ability. Ϊ́ΐΐ1 change: It is easy to obtain stable vitrification and is difficult to precipitate; it is preferable to use a positive electrode material of the clock ion secondary battery of the present invention 201226354
Li2〇/ ( P2〇5 + Fe2〇3 + 用别驅體玻璃中,以莫耳比計Li2〇/ ( P2〇5 + Fe2〇3 + in the body glass, in molar ratio
Mn02/2) 20.5。 藉由該構成’㈣容易獲得麵化穩定、難 ^望之異種結晶、電池容量高的轉子二次電池正極材 第四,較佳的是於本發明之鋰離子二 用前驅體玻射,以料輯,Ll2〇/P2〇5_5正^料Mn02/2) 20.5. According to the configuration of (4), it is easy to obtain a rotor secondary battery positive electrode material having stable surface formation, difficult to be treated, and high battery capacity. Fourth, it is preferable to use the lithium ion dual-purpose precursor glass of the present invention. Material series, Ll2〇/P2〇5_5 正料
Li20/ (Fe203 + Mn02/2) g〇.85。 ’ 及,或、 藉由該構成,變得容易獲得玻璃化穩定 :期望之異種結晶、電池容量高驗離子二次電池正極材 第五,本發明之其他形態是關於一種鐘離子 正極材料用前驅體玻璃’其特徵在於:作為朗組成,以 莫耳百分輯対Li2Q 〜5〇%、ρ2()5 2〇%〜4〇%、Li20/ (Fe203 + Mn02/2) g〇.85. With or with this configuration, it is easy to obtain vitrification stability: desired heterogeneous crystal, high battery capacity, and secondary battery positive electrode material. The other aspect of the present invention relates to a precursor for a clock ion positive electrode material. The body glass is characterized in that, as a lang composition, the percentage of the moles is 対Li2Q 〜5〇%, ρ2()5 2〇%~4〇%,
Fe203 〇%〜40%、Μη02 〇%〜60%、Nb2〇5 〇%〜2 4%,且 以莫耳比計,Li20/P2〇5g 1.01。 第六,本發明是關於一種鋰離子二次電池正極材料用 結晶化玻璃,其特徵在於:作為玻璃組成,以莫耳百分比 計含有 Li20 20%〜50%、P2〇5 20%〜40%、Fe203 〇%〜 40%、Mn020%〜60%、Nb205 〇.l%〜2.4%,a(Fe203 +Fe203 〇%~40%, Μη02 〇%~60%, Nb2〇5 〇%~2 4%, and Li20/P2〇5g 1.01 in terms of molar ratio. Sixth, the present invention relates to a crystallized glass for a positive electrode material for a lithium ion secondary battery, which is characterized in that, as a glass composition, Li20 is contained in a percentage of 20% to 50%, P2〇5 20% to 40%, Fe203 〇%~ 40%, Mn020%~60%, Nb205 〇.l%~2.4%, a(Fe203 +
Mn02/2) /P2〇5^0.85 〇 第七,較佳的是本發明之鋰離子二次電池正極材料用 結晶化玻璃以莫耳百分比計更含有〇%〜2.4%之Si〇2 + V205 + B2〇3 + Ge02 + Al2〇3 + Ga2〇3 + Sb2〇3 + Bi203。 201226354 第八,較佳的是於本發明之鐘離子二次電池正 用結晶化玻射,以莫耳比計,Li2Q/( jMn02/2) /P2〇5^0.85 〇7, preferably, the crystallized glass for the positive electrode material of the lithium ion secondary battery of the present invention further contains 〇% to 2.4% of Si〇2 + V205 in terms of mole percentage + B2〇3 + Ge02 + Al2〇3 + Ga2〇3 + Sb2〇3 + Bi203. 201226354 Eighth, it is preferred that the clock ion secondary battery of the present invention is using crystallized glass, in molar ratio, Li2Q/(j
Mn02/2) 20.5。 3 十 第九’較佳的是於本發明之鐘離子二次電池正極 用結晶化玻璃巾,以莫耳比計,Li2〇/P2Q5^ 85、及1 u20/ (Fe2〇3 + Mn02/2) ^0.85 ° " 第十,本發明之其他形態是關於一種鐘離子二 正極材料用結晶化玻璃,其舰在於:作為玻璃組成,以 莫耳百分比計含有Li2〇 2G%〜5G%、!>2()5 ·〜4〇%、 Fe2〇3 〇%〜40%、Μη02 〇%〜6〇%、Nb2〇5 〇%〜2 4%,〇Mn02/2) 20.5. 3 ninth' is preferably a crystallized glass towel for a positive electrode of a clock ion secondary battery of the present invention, in terms of a molar ratio, Li2〇/P2Q5^85, and 1 u20/(Fe2〇3 + Mn02/2 ^0.85 ° " Tenth, another aspect of the present invention relates to a crystallized glass for a clock ion two positive electrode material, the ship of which is: as a glass composition, containing Li2〇2G%~5G% in percentage of moles! >2()5 ·~4〇%, Fe2〇3 〇%~40%, Μη02 〇%~6〇%, Nb2〇5 〇%~2 4%,〇
Li2〇/P2〇5gl.〇l。 〇’ 且 第十-’較佳的是本發明之鐘離子二次電池正極材料 用結晶化玻璃含有LiMnxFeyl^^PO4結晶(〇$xgl、 〇$%卜 0<x + y9、Μ 是選自 Nb、Ti、V、Cr、^:。、Li2〇/P2〇5gl.〇l. 〇' and the tenth-'preferably, the crystallized glass for the positive electrode material of the clock ion secondary battery of the present invention contains LiMnxFeyl^PO4 crystals (〇$xgl, 〇$% οοο lt; x + y9, Μ is selected from Nb, Ti, V, Cr, ^:,
Ni之至少1種)作為主結晶。 第十一’較佳的疋本發明之經離子二次電池正極材料 用結晶化玻璃中LiMnxFeyMWx+y)P〇4結晶之含量為5〇对% 以上。 〇 第十三,本發明是關於一種鋰離子二次電池正極材料 之製造方法’其特徵在於包含··以玻璃組成成為如下之方 式而调整原料粉末之步驟’以莫耳百分比計含有Li2〇 20% 〜50%、P205 20%〜40%、Fe203 〇%〜40%、Μη02 〇〇/0〜 60%、Nb205 〇. 1 %〜2.4%,且以莫耳比計,(Fe2〇3 + Mn〇2/2 ) /P2〇5^〇.85 ;使原料粉末熔融而獲得熔融玻璃之步驟;以At least one of Ni is used as a main crystal. The eleventh preferred embodiment of the ion secondary battery positive electrode material of the present invention has a crystal content of LiMnxFeyMWx+y)P〇4 in the crystallized glass of 5 〇% or more. According to a thirteenth aspect, the present invention relates to a method for producing a positive electrode material for a lithium ion secondary battery, which is characterized in that the step of adjusting the raw material powder by the glass composition is as follows: 'Li2〇20 is included as a percentage of moles %~50%, P205 20%~40%, Fe203 〇%~40%, Μη02 〇〇/0~ 60%, Nb205 〇. 1%~2.4%, and in terms of molar ratio, (Fe2〇3 + Mn 〇2/2 ) /P2〇5^〇.85; a step of melting the raw material powder to obtain molten glass;
S 8 201226354 及使溶融玻璃驟冷而獲得前驅體破璃之步驟。 第十四,較佳的是本發明之鐘二次電池正極材料之製 造方法更包含對如驅體玻璃進行熱處理而獲得結晶化破璃 之步驟。 .【實施方式】 本發明之鋰離子二次電池正極材料用前驅體玻璃之特 徵在於:作為玻璃組成,以莫耳百分比計含有Li2〇 20%〜 50%、P2〇5 20%〜40%、Fe203 〇%〜4〇%、Μη02 0%〜60%、 Nb205 0.1%〜2.4% ’ 且以莫耳比計,(Fe2〇3 + ]v[n〇2/2) /P205 2 〇· 8 5。將玻璃組成限定成如上所述之理由說明如下。S 8 201226354 and a step of quenching the molten glass to obtain a precursor glass break. According to a fourteenth aspect, preferably, the method for producing a positive electrode material for a secondary battery of the present invention further comprises the step of heat-treating a glass such as a drive glass to obtain a crystallized glass. [Embodiment] The precursor glass for a positive electrode material for a lithium ion secondary battery of the present invention is characterized in that, as a glass composition, Li2〇20% to 50%, P2〇5 20% to 40%, in terms of a percentage of moles, Fe203 〇%~4〇%, Μη02 0%~60%, Nb205 0.1%~2.4% ' and in terms of molar ratio, (Fe2〇3 + ]v[n〇2/2) /P205 2 〇· 8 5 . The reason why the glass composition is limited to the above is explained below.
Li2〇疋LiMnxFeyMi_(x+y)P〇4結晶之主成分。較佳的是 Li20 之含量為 20%〜50%、25%〜45%、30%〜40%、33% 〜37%、特別是33.5%〜37%。若Li20之含量過少,則使 前驅體玻璃結晶化時LiMi^FeyMi-^+^PC^結晶之析出量變 少,難以獲得高的電池容量。另一方面,若Li20之含量過 多,則變得容易析出所不期望之異種結晶(Li3P04、 [“(ΜηΜ-χΜΡΟΛ 等)。其結果,LiMnxFeyMHx+y)P〇4 結 晶之析出量變少,難以獲得高的電池容量。 P2〇5亦為LiMnxFeyMHx+y)P〇4結晶之主成分。較佳的 是 P205 之含量為 20%〜40%、5%〜35%、28%〜35°/。、29% 〜33%、特佳是29.5%〜32.5%。於P2〇5之含量為該範圍 外之情形時,於使前驅體玻璃結晶化時變得容易析出不期 望之異種結晶。其結果,LiMi^FeyM^x+joPO4結晶之析出 量變少,難以獲得高的電池容量。 201226354The main component of Li2〇疋LiMnxFeyMi_(x+y)P〇4 crystal. Preferably, the content of Li20 is 20% to 50%, 25% to 45%, 30% to 40%, 33% to 37%, particularly 33.5% to 37%. When the content of Li20 is too small, the amount of precipitation of LiMi^FeyMi-^+^PC^ crystals becomes small when the precursor glass is crystallized, and it is difficult to obtain a high battery capacity. On the other hand, when the content of Li20 is too large, it is easy to precipitate undesired heterogeneous crystals (Li3P04, ["(ΜηΜ-χΜΡΟΛ, etc.). As a result, the precipitation amount of LiMnxFeyMHx+y)P〇4 crystals is small, and it is difficult. A high battery capacity is obtained. P2〇5 is also a main component of LiMnxFeyMHx+y)P〇4 crystal. It is preferred that the content of P205 is 20% to 40%, 5% to 35%, and 28% to 35°/. 29% to 33%, particularly preferably 29.5% to 32.5%. When the content of P2〇5 is outside the range, undesired heterogeneous crystals are easily precipitated when the precursor glass is crystallized. The amount of precipitation of LiMi^FeyM^x+joPO4 crystals is small, and it is difficult to obtain a high battery capacity.
Fe203是LiMnxFeyMux+y/C^結晶之構成成分。較佳的 是Fe203之含量為0%〜40%、10%〜40%、20%〜35%、特 別是30%〜35%。若Fe2〇3之含量過多,則變得容易於使 前驅體玻璃結晶時析出不期望之異種結晶。其結果, LiMnxFeyMwx+yPO4結晶之析出量變少,難以獲得高的電 池容量。另外’亦可使用FeO或Fe3〇4等作為原料,於此 情形時’換算為Fe2〇3之量滿足所述範圍即可。Fe203 is a constituent of LiMnxFeyMux+y/C^ crystal. Preferably, the content of Fe203 is 0% to 40%, 10% to 40%, 20% to 35%, particularly 30% to 35%. When the content of Fe2〇3 is too large, it becomes easy to precipitate undesired heterogeneous crystals when the precursor glass is crystallized. As a result, the amount of precipitation of LiMnxFeyMwx+yPO4 crystals is small, and it is difficult to obtain a high battery capacity. Further, FeO or Fe3〇4 may be used as a raw material, and in this case, the amount converted to Fe2〇3 may satisfy the above range.
Mn〇2亦和Fe2〇3同樣地是LiMnxFeyMi-HPCU結晶之 構成成分。較佳的是Μη02之含量為〇%〜6〇%、20%〜 55〇/〇、30%〜55%、40%〜55¾、特別是 45%〜5〇%。若 Mn〇2之含量過多,則變得容易於使前驅體玻璃結晶時析Similarly to Fe2〇3, Mn〇2 is a constituent of the crystal of LiMnxFeyMi-HPCU. Preferably, the content of Μη02 is 〇%~6〇%, 20%~55〇/〇, 30%~55%, 40%~553⁄4, especially 45%~5〇%. If the content of Mn〇2 is too large, it becomes easy to crystallize the precursor glass.
述範圍即可。The scope is sufficient.
3 + Μη〇2/2)/Ρ2〇5 為 〇.85 匕。若(Fe203 + Mn02/2) 較佳的是以莫耳比計,(Fe2〇3 + 以上、〇·9以上、特別是〇·95以上。 201226354 之Γ容易於使前驅體玻璃結晶時析出不期望 特別:獲得高的電池容量。另外’對上限並無 較佳的是2 ί ;出充分量之LiMnxFeyMl-(X+y)P〇4結晶, 1佳的疋2以下、特別是1.5以下。 以外,可六璃形成能力提高之成分,除了 Nb2〇5 SiO、Υ〇*、十量為〇%〜2·4%、特別是〇.1%〜2 3%之 =些,一― 時析出不期望之里^士 1則變传容易於使前驅體玻璃結晶 y望之異種結晶,難以獲得高的電池容量。 體玻璃中的明之鋰離子二次電池正極材料用前驅 T〇fl ,Γ ^ } ^ (P^ + ^〇3 + Mn〇2/2) Γ〇/2ΐ:特別是:·52以上如 期望之日1料易於㈣賴綱結晶時析出不 並獲得高的電池容量。另外,對上限 ^:i^i^iLlMn^W04# 权住的疋1以下、特別是0.8以下。 趙破子。t❶電池正極材料用前驅 1以上、特別是 易於使前IS體玻璃結晶時析出不期二5; a則:: 另外,對上限並無特:二= 別3 nxFeyMl_(x+y)P〇4結晶,較佳的是2以下、特 別疋1.5以下。 ^ 較佳的是於本發明之_子二次電池正極材料用前驅 201226354 體玻璃中,以莫耳比計,祕/㈤处僅啦/2)為〇.85 以上、特別疋0.9以上。若秘/…处+他⑽)過小, 則變付容易於使前驅體玻璃結晶時析出不期望之異種結 ,,難以獲得高的電池容量。另外,耻限並麟別限定, 為了析出充分量之LiMnxFeyMi例ρ〇4結晶,較 以下、特別是1.5以下。 發明之H離子二次電池正極材料用前驅體玻璃之其 他形態的舰在於:作為玻敝成,以莫耳百分比計含有3 + Μη〇2/2)/Ρ2〇5 is 〇.85 匕. (Fe203 + Mn02/2) is preferably a molar ratio (Fe2〇3 + or more, 〇·9 or more, especially 〇·95 or more. 201226354 is more likely to precipitate the precursor glass when it is crystallized. It is desirable to obtain a high battery capacity. In addition, it is not preferable that the upper limit is 2 ί; a sufficient amount of LiMnxFeyMl-(X+y)P〇4 crystal is formed, and 1 is preferably 疋2 or less, particularly 1.5 or less. In addition to the composition of the six glass forming ability, except Nb2〇5 SiO, Υ〇*, ten is 〇%~2·4%, especially 〇.1%~2 3%= some, one-time precipitation Unexpectedly, it is easy to make the precursor crystal crystallization of the precursor crystal, and it is difficult to obtain high battery capacity. The precursor of the positive electrode material for lithium ion secondary battery in the body glass is T〇fl , Γ ^ } ^ (P^ + ^〇3 + Mn〇2/2) Γ〇/2ΐ: In particular: ·52 or more, as expected, 1 material is easy (4) Lai's crystallization does not lead to high battery capacity. For the upper limit ^:i^i^iLlMn^W04#, the weight of 疋1 is below, especially below 0.8. Zhao Chuanzi. The positive electrode material of t❶ battery uses more than 1 precursor, especially for the former IS body. When the glass crystallizes, it may not be two or five; a:: In addition, there is no special upper limit: two = 3 xxFeyMl_(x+y)P〇4 crystals, preferably 2 or less, especially 1.5 or less. It is preferable that in the precursor glass of the secondary battery positive electrode material of the present invention, 201226354, in the molar ratio, the secret / (five) is only /2 or more, especially 疋 0.9 or more. If the secret / ... + (10) is too small, the change is easy to precipitate an undesired heterogeneous knot when the precursor glass crystallizes, and it is difficult to obtain a high battery capacity. Further, the shame is not limited, and in order to precipitate a sufficient amount of LiMnxFeyMi, the ρ〇4 crystal is, in particular, 1.5 or less. The other form of the precursor glass for the positive electrode material of the H ion secondary battery of the invention is: as a glass mash, containing in percentage of mole
Ll2〇 20%〜5G%、P2〇5 2G%〜4G%、Fe2〇3 〇%〜4G%、Μη02 〇%〜6〇%、Nb2〇5 〇%〜24%,且以莫耳比計, Ll2〇/P2Ogl.(H。於該形態中,關於各成分之含量之較佳 之範圍以及限定理由等,可適用已述者。 本發明之轉子二次電池正極材湘結晶化玻璃可藉 對所述雜子二:欠電池正極材料用前驅體賴進行锻燒 使其結晶化而製作。 本發明之鐘離子二次電池正極材料用結晶化玻璃之特 徵f於:作為玻璃組成,以莫耳百分比計含有Li2020〇/。〜 50/〇 P2〇5 20%〜4〇〇/0、Fe2〇3 〇〇/〇〜4〇%、Mn〇2 〇%〜6〇%、Ll2〇20%~5G%, P2〇5 2G%~4G%, Fe2〇3 〇%~4G%, Μη02 〇%~6〇%, Nb2〇5 〇%~24%, and in terms of molar ratio, Ll2〇/P2Ogl. (H. In this form, the preferred range of the content of each component and the reason for limitation can be applied. The rotor secondary battery of the present invention can be used as a crystallized glass. In the second embodiment, the negative electrode material is prepared by calcining the precursor with a precursor. The characteristics of the crystallized glass for the positive electrode material of the clock ion secondary battery of the present invention are as follows: It contains Li2020〇/.~50/〇P2〇5 20%~4〇〇/0, Fe2〇3 〇〇/〇~4〇%, Mn〇2 〇%~6〇%,
Nb205 〇.1/0〜2.4〇/〇,且(Fe2〇3 + Mn〇2/2) /p2〇5^〇 85。 車又佳的是本發明之鋰離子二次電池正極材料用結晶化 玻璃以莫耳百分比収含有Si02 + V2〇5 +秘+ Ge〇2 +Nb205 〇.1/0~2.4〇/〇, and (Fe2〇3 + Mn〇2/2) /p2〇5^〇 85. It is also preferred that the crystallized glass for the positive electrode material of the lithium ion secondary battery of the present invention contains SiO 2 + V 2 〇 5 + secret + Ge 〇 2 + in a molar percentage.
Al2〇3 + Ga2〇3 + Sb2〇3 + Bi2〇3 0%〜2.4%。 車乂佳的是於本發明之鋰離子二次電池正極材料用結晶 化玻璃中’以莫耳比計’[砂(P2〇5 + Fe2G3 + Mn02/2) S, 12 201226354 為0.5莫耳以上。 化玻Ξϊ的τ疋:本發明之鋰離子二次電池正極材料用結晶 化玻璃中,Ll2〇/P2〇5為0.85以上。 化玻St的疋ΐ本發明之鋰離子二次電池正極材料用結晶 ^璃中,料耳比計,Ll2〇/(Fe2〇3 + Mn〇2/2)為 0.85 =於,發明之鐘離子二次電池正極材料用結晶化玻璃 Ϊ 成範圍以及其限定理由,可適用與前述之鋰離 料用前驅體玻璃之較佳⑽ 他护is之鐘離子二次電池正極材料用結晶化玻璃之其 r 2:r5〇%' ^^ Fe2〇f〇n;0: zt =〇%'Nb2〇5〇%〜2.4%,且 Li2〇/P2〇5Sioi。於該 $ I'中’關於各成分之含量之I交伯 3» ^ 等,可適用已述者。 MW®以及限定理由 是雜子"次電池正極材料㈣晶化玻璃含有 ν< Γ =Hx+y)P〇4 結晶(〇把1、〇¥1、0 < X + 作為主結晶。 ‘奶之至少!種) 較^的是UMnxFeyMl例P〇4結晶之含量為5〇讓以 二F λΓ%以上、特別是9〇 _以上。若 不充nf^1灿)Ρ〇4、结晶之含量過少,則離子導電性變得. 不充刀’難以獲得高的電池容量。另外,對上限並無特別 13 201226354 限定,現實上而言為99.9 wt%以下,特別是99 wt%以下。Al2〇3 + Ga2〇3 + Sb2〇3 + Bi2〇3 0%~2.4%.车乂佳 is in the crystallized glass for the positive electrode material of the lithium ion secondary battery of the present invention in the 'mole ratio' [sand (P2〇5 + Fe2G3 + Mn02/2) S, 12 201226354 is 0.5 m or more . In the crystallized glass for a positive electrode material for a lithium ion secondary battery of the present invention, Ll2〇/P2〇5 is 0.85 or more. In the crystal material of the positive electrode material for lithium ion secondary battery of the present invention, Lr2〇/(Fe2〇3 + Mn〇2/2) is 0.85 =, the clock ion of the invention The range of the crystallized glass crucible for the secondary battery positive electrode material and the reason for the limitation thereof can be suitably applied to the above-mentioned lithium ion-exclusive precursor glass (10), which is the crystallized glass for the positive electrode material for the ion secondary battery. r 2:r5〇%' ^^ Fe2〇f〇n; 0: zt =〇%'Nb2〇5〇%~2.4%, and Li2〇/P2〇5Sioi. In the $I', the content of each component, I, 3, ^, etc., can be applied to the above. MW® and the reason for limitation are heterozygous "secondary battery positive electrode material (4) crystallized glass containing ν < Γ = Hx + y) P 〇 4 crystal (〇 1, 〇 ¥ 1, 0 < X + as the main crystal. At least the type of milk is more than UMnxFeyMl. The content of P〇4 crystal is 5〇, and it is more than 2 F λΓ%, especially 9〇_. If the content of the crystal is too small, the ionic conductivity becomes too small. It is difficult to obtain a high battery capacity. In addition, the upper limit is not particularly limited to 201226354, and is actually 99.9 wt% or less, particularly 99 wt% or less.
LiMnxFeyMi-a+ePO4結晶之晶粒尺寸越小,則可使將 結晶化玻璃製成粉末狀而使用時之粒徑變得更小,從而可 使導電性提高L言,較麵是LiMnxFeyMi_(^)p〇4 結晶之晶粒尺寸為1〇〇 nm以下、特別是8〇 nm以下。關 於下限,並無特別限定,現實上而言為1 nm以上、特別 j U)二以上。另外,LlMnxFeyMi (x+y)p〇4結晶之晶粒尺 寸可根據結晶化玻璃粉末之粉末χ射線繞射之解析結果, 依照Scherrer公式而求出。 σ 較^是雜子二次電池正極材結晶化玻璃為粉 士狀。糟此而使作為正極材料整體之表面積變大 容易進行離子或電子之交換。較佳的是鐘離子二次電池正 極材料用結晶化玻璃粉末之平_徑為5Q师以下^ 二,是20 μιη以下。關於下限,並無 貫的是0.05 μιη以上。 兄 =/,已知有SI相反應法或水熱合成法,於該些方法中 子在如下問題:容易混入金屬鐵等磁性粒子作 $覆之充放電而形成樹枝狀結晶,成為短路之原因。另 至^ ’藉由玻璃熔融法,變得可使金屬卿熔解而嵌入 之正極=rMX+y)PQ4街,嶋嶋均質且緻密 體玻:=2明之_子二次電池正極材料用前驅 體玻璃1藉由包含如下步驟之製造方法而製作:以破璃組 201226354 成成為如下之方式而調整原料粉末之步驟,以莫耳百分比 計含有 U2〇 20%〜50%、P2〇5 20%〜40%、Fe2〇3 〇〇/。〜 40%、Μιι02 〇%〜60%、Nb2〇5 0.1%^〜2.4% ’ 且以莫耳比 &十’(Fe2〇3 + Mn〇2/2) /Ρ2〇5 2〇·85 ;使原料粉末溶融而獲 得熔融玻璃之步驟;以及使熔融玻璃驟冷之步驟。 而且,亦可進一步對鋰離子二次電池正極材料用前驅 體玻璃進行熱處理而使其結晶化,藉此而獲得鋰離子二次 電池正極材料用結晶化玻璃。 另外,撖欖石型LiMr^FeyM^^PO4結晶中之Fe與 Μη之原子價為+2價,因此如果於大氣開放中長時間熔 融’則自氧化還原平衡之關係考慮,分別容易被氧化為Η 價以及+4價。因此,為了控制原子價狀態,較佳的是於掣 作前驅體玻璃時之原料中添加草酸鐵等+2價之試劑,或^ 於前驅體玻璃熔融中添加葡萄糖等含有碳之還原劑·;而 且,於充滿還原性氣體之氣密性優異之反應容器 融之方法亦較佳。 可藉由於可控制溫度以及環境之電爐中對前驅體玻 製作結晶化玻璃。熱處理溫度因前驅體玻璃 =成或目標之晶粒尺相異,因此並無特別Μ,較佳 =疋至少玻璃轉移溫度以上、特別是結晶化溫度以上。呈 體而吕,較佳的是熱處理溫度為5〇〇t以上、 以上。若熱處理溫度過低,則存在 枚疋The smaller the crystal grain size of the LiMnxFeyMi-a+ePO4 crystal, the smaller the particle size when the crystallized glass is powdered, and the conductivity can be improved, and the surface is LiMnxFeyMi_(^ The crystal grain size of the p〇4 crystal is 1 〇〇 nm or less, particularly 8 Å or less. The lower limit is not particularly limited, and is actually 1 nm or more, particularly j U) two or more. Further, the crystal size of the LlMnxFeyMi (x+y)p〇4 crystal can be determined according to the Scherrer's formula based on the analysis result of the powdered ray diffraction of the crystallized glass powder. σ is a powdered glass of a positive electrode secondary battery. On the other hand, the surface area as a whole of the positive electrode material becomes large, and exchange of ions or electrons is facilitated. It is preferable that the flattened diameter of the crystallized glass powder for the positive electrode material of the clock ion secondary battery is 5 or less, which is 20 μm or less. Regarding the lower limit, the inconsistency is 0.05 μm or more. Brother = /, there are known SI phase reaction methods or hydrothermal synthesis methods. In these methods, neutrons have the following problems: it is easy to mix magnetic particles such as metal iron to form a dendritic crystal by charging and discharging, which is a cause of short circuit. . In addition, by the glass melting method, the positive electrode = rMX + y) PQ4 street which can be melted and melted by metal smelting, 嶋嶋 homogeneous and dense body glass: = 2 _ _ _ sub-secondary battery positive electrode material precursor The glass 1 is produced by a manufacturing method including the following steps: a step of adjusting the raw material powder by the method of breaking the glass group 201226354, and containing U2 〇 20% 〜 50%, P2 〇 5 20% by the percentage of the mole % 40%, Fe2〇3 〇〇/. ~ 40%, Μιι02 〇%~60%, Nb2〇5 0.1%^~2.4% ' and Mohr ratio & ten' (Fe2〇3 + Mn〇2/2) /Ρ2〇5 2〇·85; a step of melting the raw material powder to obtain molten glass; and a step of quenching the molten glass. Further, the precursor glass for a positive electrode material for a lithium ion secondary battery can be further subjected to heat treatment to be crystallized, whereby a crystallized glass for a positive electrode material for a lithium ion secondary battery can be obtained. In addition, the valence of Fe and Μη in the crystal of LiMr^FeyM^^PO4 is +2, so if it is melted for a long time in the open atmosphere, then the relationship between the self-oxidation-reduction equilibrium is easily oxidized to Η price and +4 price. Therefore, in order to control the valence state, it is preferred to add a reagent of +2 valence such as iron oxalate to the raw material when the precursor glass is used, or to add a reducing agent containing carbon such as glucose to the melting of the precursor glass; Further, a method of melting a reaction vessel which is excellent in airtightness of a reducing gas is also preferable. The crystallized glass can be made from the precursor glass by means of an electric furnace capable of controlling temperature and environment. Since the heat treatment temperature differs depending on the precursor glass = the target or the target grain size, it is not particularly flawed, and preferably = at least the glass transition temperature or higher, particularly the crystallization temperature. In the form of a film, it is preferred that the heat treatment temperature is 5 〇〇t or more. If the heat treatment temperature is too low, there is a enthalpy
Si電性差之傾向。另一方面,對上限並無特別限定, 右熱處理溫度過高,則存在結晶_之虞,因此是 15 201226354 1000〇C以下、特別是950。〇以下。 移、-产附近進:二又般燒,亦即將前驅體玻璃於轉 移,皿度附近進仃一定時間之熱處理 , 進-步進行熱處理的2段階锻燒,由此變㈡ 均勻之結晶粒經之結晶化玻璃。 獲付具有 可適宜地調整熱處理時間以使前驅體玻璃之妹曰化充 分進打。具體而言,熱處理時間較佳為 'σΒΘ 特別是20分鐘〜40分鐘。佳為10分鐘〜60分鐘、 熱處理之環境較佳是氫、氨、一江 藉此變得容易獲得橄禮石型LiMnxF 1還,^ ° x yM“(x+y)P〇4 結晶。 ▲右於刖驅體玻璃之熱處理時添加有機黏合劑,則由於 遠有機黏合劑之縣仙,於結晶化之前,玻射之鐵的 價數變化為+2,因此可以高的含有率獲得 LiMnxFeyMi-(x+y)P〇4 結晶。 另外’為了使導電性提高,較佳的是相對於結晶化玻 璃而混合電子導·高且穩定之導電活性㈣。導電活性 物質可列舉石墨、乙炔黑、非晶形碳等碳系導電活性物質 或金屬粉末等金屬系導電活性物質等。非晶形碳較佳的是 於FTIR分析中,f質上檢測不到成為正極材料《導電性 降低之原因的C-O鍵峰值或C-H鍵峰值的非晶形碳。 例如,較佳的是於結晶化玻璃粉末之界面承載有導電 活性物質之狀態下進行燒結。作為於結晶化玻璃粉末之界 面承載導電活性物質之方法,可列舉將葡萄糖;脂肪族羧 酸、芳香族羧酸等羧酸;有機黏合劑等有機化合物等導電 201226354 性環前驅粉末中力-混合,於氮氣等惰 前驅體玻·_化,中進行熱處理’使 殘留導;活性物質之非晶形 达匕處’脂肪族叛酸可列與 乙樹脂、聚乙二醇、聚碳酸伸 2基丙触丁§|、聚甲基丙烯酸乙6旨、聚甲基丙稀酸甲 導雷方法’可於結晶化玻雜末界面均勻地承載 ' 貝。而且,有機黏合劑有助於正極材料之成型 =與導電性這2種特性。亦即,變得可容㈣成形為片狀, Μ可於锻燒後不進行再度粉碎而為電池之正極材料。 較佳的是本發明之鐘離子二次電池用正極材料之導電 度為1.0Χ10·8 S · cm]以上、i 〇χ1〇·6 s ·咖]以上、特別 是 l,〇xl〇-4 S · cm·1 以上。 [實例] 以下,基於貫例對本發明加以詳細說明,但本發明並 不限定於該些實例。 表1〜表3表示本發明之實例(試樣N〇1〜試樣 No.19)以及比較例(試樣n〇 2〇〜試樣n〇 22)。 17 201226354 [表i] 1 2 3 4 5 6 7 8 9 10 Li2〇 33.2 34.2 35.2 36.2 37.2 38.2 32.2 34.8 34.4 30.4 P2〇5 33.2 32.7 32.2 31.7 31.2 30.7 33.7 34.8 34.4 30.4 Fe2〇3 Mn〇2 33.2 32.7 32.2 31.7 31.2 30.7 33.7 29.9 30.7 38.7 Nb203 Si02 Al2〇3 0.5 0.5 0.5 0.5 0.5 0.5 0.5 0.5 0.5 0.5 (Fe+Mn/2) /P 1.00 1.00 1.00 1.00 1.00 1.00 1.00 0.86 0.89 1.27 Li/ ( P+Fe+Mn/2 ) 0.50 0.52 0.55 0.57 0.60 0.62 0.48 0.54 0.53 0.44 Li/P 1.00 1.05 1.09 1.14 1.19 1.24 0.96 1.00 1.00 1.00 Li/ (Fe+Mn/2) 1.00 1.05 1.09 1.14 1.19 1.24 0.96 1.17 1.12 0.79 玻璃化 ο ο ο ο ο ο ο ο ο ο 結晶量(%) 94.0 96.3 96.9 94.7 94.0 91.6 88.0 96.0 93.0 86.0 放電容量(mwh/g) 130 137 141 138 135 130 120 137 128 100 18 s 201226351 [表2] 11 12 13 14 15 16 17 18 19 Li20 34.5 34.5 34.5 24.8 26.8 32.4 30.4 29.1 28.8 P2〇5 31.6 31.6 31.6 24.8 23.8 30.9 28.9 28.1 27.3 Fe203 31.6 31.6 31.6 24.7 17.1 13,7 10.6 Mn02 49.8 48.8 11.7 23.6 28.6 33.3 Nb2〇3 2.4 0.9 0.9 0.5 0.5 0.5 0.5 0.5 0.5 Si02 1.5 Al2〇3 1.5 (Fe+Mn/2) /P 1.00 1.00 1.00 1.00 1.03 0.99 1.00 1.00 1.00 Li/ ( P+Fe+Mn/2 ) 0.55 0.55 0.55 0.50 0.56 0.53 0.53 0.52 0.53 Li/P 1.09 1.09 1.09 1.00 1.13 1.05 1.05 1.04 1.05 Li/ ( Fe+Mn/2 ) 1.09 1.09 1.09 1.00 1.10 1.06 1.05 1.04 1.06 玻璃化 0 0 0 0 0 0 0 0 0 結晶量(%) 93.0 93.5 92.8 92.0 96.0 92.0 91.0 90.0 88.0 放電容量(mwh/g ) 128 131 126 120 135 125 119 115 110 19 201226354 [表3] 20 21 22 Li20 30.3 26.9 29.0 p2〇5 38.3 38.6 29.0 Fe203 30.8 31.9 37.0 Μη02 Nb203 0.5 2.6 5.0 Si02 ai2〇3 (Fe+Mn/2) /P 0.80 0.83 1.28 Li/ ( P+Fe+Mn/2 ) 0.44 0.38 0.44 Li/P 0.79 0.70 1.00 Li/ ( Fe+Mn/2 ) 0.98 0.84 0.78 玻璃化 0 X 0 結晶量(%) 70.0 80.0 放電容量(mwh/g) 40 - 88 首先,以成為表1〜表3中所示之各組成的方式調合 玻璃原料,使用鉑坩堝而於ll〇〇°C〜1400°C下進行1小時 之炫融。使熔融玻璃流入至一對成形親中,一面驟冷一面 成形為膜狀,藉此而製作前驅體玻璃。 其後,將前驅體玻璃以球磨機加以粉碎,獲得平均粒 徑為2 μιη之前驅體玻璃粉末。相對於前驅體玻璃粉末100 201226354. 重®份而&,混合酚樹脂5重量份(以石墨換算古相當 於組量份)、作為溶劑之15重量份之乙醇鼻 樂料化’利用公知之刮刀成形法而成形為厚度為5〇〇哗 之片狀之後,於80。(:下使其乾燥約丨小時。其次,將所得 之片狀成形體切斷為預定之大小,於氮氣環境中、8〇〇£)(:下 進行30分鐘之熱處理而使其結晶化,藉此獲得正極材料 (結晶化玻璃粉末之燒結體)。藉由粉末χ射線繞射法而 測定正極材料中之LiMnxFeyMl如y)P〇4結晶之含量。 其次,對於所得之正極材料,藉由以下方式而評價 0.1C倍率之放電容量。 以正極材料:黏合劑:導電性物質 ^之方式稱量正極材料、作柄合劑之7、y化求匕二 2 >、作為導電性物質之科琴黑,將該些材料分散於N_ ii=r(NMP)中之後,藉由自轉、公轉混合機充 =订攪拌而使其漿料化。其次,使關隙為15G _之 將料=為正轉1體之厚2()μιη之純上塗佈所得之 轉觀之$ 中、28(rc下進行乾燥後,使其通過一對旋 衝壓機^u lt/em進行壓⑼獲得電極片材。藉由電極 =機3片材衝㈣直經llmm,於14。。〇下乾燥6 J呀’獲得圓形之工作電極。 之下:差作電極之18面朝下而載置於钮扣型電池 得之其上積層於机下進行8小時之減壓乾燥而所 公司ΪΓ6 _之包含聚丙歸多孔質膜(H— celanese ^之Celgard#2400)之分隔件、以及作為相對電極 21 201226354The tendency of Si to be poor in electrical conductivity. On the other hand, the upper limit is not particularly limited, and if the right heat treatment temperature is too high, there is a crystallization of 结晶, so it is 15 201226354 1000 〇 C or less, particularly 950. 〇The following. Move, - near the production: two and other burns, that is, the precursor glass is transferred, the heat treatment is carried out for a certain period of time near the dish, and the second-stage calcination is carried out by heat treatment, thereby changing (2) uniform crystal grain Crystallized glass. It is paid to have a suitable heat treatment time to make the precursor glass of the precursor glass fully charged. Specifically, the heat treatment time is preferably 'σΒΘ, particularly 20 minutes to 40 minutes. Preferably, the environment is from 10 minutes to 60 minutes, and the heat treatment environment is preferably hydrogen, ammonia, and a river, thereby making it easy to obtain the olivine-type LiMnxF 1 and ^ ° x yM "(x + y) P 〇 4 crystal. ▲ When the organic binder is added to the heat treatment of the enamel glass, the valence of the molten iron is changed to +2 before the crystallization before the crystallization of the far-organic binder, so LiMnxFeyMi- can be obtained at a high content rate. (x+y) P〇4 crystals. Further, in order to improve conductivity, it is preferable to mix electrons with high conductivity and stable electrical conductivity with respect to the crystallized glass (IV). The conductive active material may, for example, be graphite or acetylene black. A carbon-based conductive active material such as amorphous carbon or a metal-based conductive active material such as metal powder. The amorphous carbon is preferably not detected in the FTIR analysis as a CO bond which causes a decrease in conductivity of the positive electrode material. Amorphous carbon having a peak or a peak of a CH bond. For example, it is preferred to carry out sintering in a state in which an interface of a crystallized glass powder is carried with a conductive active material. As a method of carrying a conductive active material at an interface of the crystallized glass powder, Column Conductive 201226354 ring precursor powder, such as glucose, carboxylic acid such as aliphatic carboxylic acid or aromatic carboxylic acid, or organic compound such as organic binder, is mixed and mixed, and is heat-treated in an inert precursor such as nitrogen. Residual conduction; the amorphous form of the active substance is 'an aliphatic tetamine can be listed with ethyl resin, polyethylene glycol, polycarbonate extension 2 base C-butyl §|, polymethacrylic acid B6, polymethyl propyl The dilute acid-guided thunder method can uniformly carry 'Bei' at the interface of the crystallized vitreous end. Moreover, the organic binder contributes to the two characteristics of the formation of the positive electrode material and the conductivity. That is, it becomes acceptable (4) It is formed into a sheet shape, and the crucible can be used as a positive electrode material for a battery without being pulverized again after calcination. It is preferable that the positive electrode material for a clock ion secondary battery of the present invention has a conductivity of 1.0 Χ 10·8 S · cm or more. i, 〇1〇·6 s · coffee] or more, particularly l, 〇xl 〇 -4 S · cm·1 or more. [Examples] Hereinafter, the present invention will be described in detail based on examples, but the present invention is not limited thereto. These examples. Table 1 to Table 3 show examples of the present invention (sample N〇1~ Sample No. 19) and Comparative Example (sample n〇2〇 to sample n〇22) 17 201226354 [Table i] 1 2 3 4 5 6 7 8 9 10 Li2〇33.2 34.2 35.2 36.2 37.2 38.2 32.2 34.8 34.4 30.4 P2〇5 33.2 32.7 32.2 31.7 31.2 30.7 33.7 34.8 34.4 30.4 Fe2〇3 Mn〇2 33.2 32.7 32.2 31.7 31.2 30.7 33.7 29.9 30.7 38.7 Nb203 Si02 Al2〇3 0.5 0.5 0.5 0.5 0.5 0.5 0.5 0.5 0.5 0.5 (Fe+Mn /2) /P 1.00 1.00 1.00 1.00 1.00 1.00 1.00 0.86 0.89 1.27 Li/ ( P+Fe+Mn/2 ) 0.50 0.52 0.55 0.57 0.60 0.62 0.48 0.54 0.53 0.44 Li/P 1.00 1.05 1.09 1.14 1.19 1.24 0.96 1.00 1.00 1.00 Li / (Fe+Mn/2) 1.00 1.05 1.09 1.14 1.19 1.24 0.96 1.17 1.12 0.79 Vitrification ο ο ο ο ο ο ο ο ο ο crystallization amount (%) 94.0 96.3 96.9 94.7 94.0 91.6 88.0 96.0 93.0 86.0 Discharge capacity (mwh/ g) 130 137 141 138 135 130 120 137 128 100 18 s 201226351 [Table 2] 11 12 13 14 15 16 17 18 19 Li20 34.5 34.5 34.5 24.8 26.8 32.4 30.4 29.1 28.8 P2〇5 31.6 31.6 31.6 24.8 23.8 30.9 28.9 28.1 27.3 Fe203 31.6 31.6 31.6 24.7 17.1 13,7 10.6 Mn02 49.8 48.8 11.7 23. 6 28.6 33.3 Nb2〇3 2.4 0.9 0.9 0.5 0.5 0.5 0.5 0.5 0.5 Si02 1.5 Al2〇3 1.5 (Fe+Mn/2) /P 1.00 1.00 1.00 1.00 1.03 0.99 1.00 1.00 1.00 Li/ ( P+Fe+Mn/2 ) 0.55 0.55 0.55 0.50 0.56 0.53 0.53 0.52 0.53 Li/P 1.09 1.09 1.09 1.00 1.13 1.05 1.05 1.04 1.05 Li/ ( Fe+Mn/2 ) 1.09 1.09 1.09 1.00 1.10 1.06 1.05 1.04 1.06 Vitrification 0 0 0 0 0 0 0 0 0 Crystallization amount (%) 93.0 93.5 92.8 92.0 96.0 92.0 91.0 90.0 88.0 Discharge capacity (mwh/g) 128 131 126 120 135 125 119 115 110 19 201226354 [Table 3] 20 21 22 Li20 30.3 26.9 29.0 p2〇5 38.3 38.6 29.0 Fe203 30.8 31.9 37.0 Μη02 Nb203 0.5 2.6 5.0 Si02 ai2〇3 (Fe+Mn/2) /P 0.80 0.83 1.28 Li/ ( P+Fe+Mn/2 ) 0.44 0.38 0.44 Li/P 0.79 0.70 1.00 Li/ ( Fe+Mn /2 ) 0.98 0.84 0.78 Vitrification 0 X 0 Crystallization amount (%) 70.0 80.0 Discharge capacity (mwh/g) 40 - 88 First, the glass raw materials are blended so as to have the respective compositions shown in Tables 1 to 3. Platinum is carried out for 1 hour at ll 〇〇 ° C to 1400 ° C. The molten glass is poured into a pair of forming members, and is formed into a film shape by quenching, whereby a precursor glass is produced. Thereafter, the precursor glass was pulverized in a ball mill to obtain a precursor glass powder having an average particle diameter of 2 μm. With respect to the precursor glass powder 100 201226354. 5 parts by weight of the mixed phenol resin (an equivalent amount in terms of graphite) and 15 parts by weight of ethanol as a solvent After forming into a sheet having a thickness of 5 Å by a doctor blade forming method, it was 80. (The following drying was carried out for about several hours. Next, the obtained sheet-like formed body was cut into a predetermined size, and subjected to heat treatment for 30 minutes in a nitrogen atmosphere to be crystallized. Thereby, a positive electrode material (sintered body of crystallized glass powder) was obtained. The content of LiMnxFeyM1 such as y)P〇4 crystal in the positive electrode material was measured by powder ray diffraction. Next, with respect to the obtained positive electrode material, the discharge capacity at a 0.1 C rate was evaluated by the following manner. The positive electrode material: the binder: the conductive material ^ is used to weigh the positive electrode material, the handle mixture is 7, the y chemical solution 2 2 >, as the conductive substance of the Ketjen black, the materials are dispersed in N_ ii = After r (NMP), the mixture was slurried by auto-rotation and revolutionary mixer charging. Secondly, the closing gap is 15G _. The material = the thickness of the positive body 1 body 2 () μιη purely coated by the coating of the middle, 28 (dry under rc, through a pair of spin The press machine ^u lt/em is pressed (9) to obtain the electrode sheet. By electrode = machine 3 sheet punching (four) straight through llmm, at 14. 〇 under the drying 6 J 呀 'get a round working electrode. The 18th surface of the differential electrode is placed on the button-type battery and placed under the machine for 8 hours under reduced pressure drying. The company ΪΓ6 _ contains polypropylene to the porous membrane (H-celanese ^Celgard) #2400) The separator, and as the opposite electrode 21 201226354
之金屬鐘,製作§式驗電池。祐田^ μ T 伸乙# DEC (碳酸乙二6溶液/EC (碳酸 於路點溫度為1C以下之環境下進行試驗電池之组裝。 使用試驗電池,藉由2VM2VUC(值定電流) 充電進行充電(自正極材料中放練離子),進—步使其自 4.2 V放電至2 V而進行放電(於正極材料巾吸藏裡離 子),測定放電谷置。將結果示於表1〜表3中。 由表1〜表3可知.作為實例之試樣N〇 1〜試樣n〇 19 之正極材料用玻璃顯示出1〇〇 mwh/g以上之良好的放電容 量。另一方面,作為比較例之試樣No.20以及試樣No 22 之正極材料用玻璃並不滿足預定之玻璃組成,放電容量低 至88mwh/g以下。另外,關於試樣No.21,並未玻璃化, 因此並未進行放電容量之測定。 【圖式簡單說明】 益〇 【主要元件符號說明】 择〇The metal clock is used to make a §-type battery. You Tian ^ μ T 伸乙# DEC (Ethylene carbonate 2 6 solution / EC (carbonation is carried out in the environment where the junction temperature is below 1C. The test battery is used, and the battery is charged by 2VM2VUC (value constant current). Charging (reducing ions from the positive electrode material), discharging it from 4.2 V to 2 V and discharging (dissolving ions in the positive electrode material), and measuring the discharge valley. The results are shown in Table 1 to Table 3. It can be seen from Table 1 to Table 3. The positive electrode material of the sample N〇1 to sample n〇19 as an example shows a good discharge capacity of 1 〇〇 mwh/g or more. The glass for the positive electrode material of the sample No. 20 and the sample No. 22 of the comparative example did not satisfy the predetermined glass composition, and the discharge capacity was as low as 88 mwh/g or less. Further, the sample No. 21 was not vitrified, so The discharge capacity is not measured. [Simple description of the diagram] Yiyi [main component symbol description]
S 22S 22
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