JP2005093416A - Negative electrode material for nonaqueous electrolyte battery, negative electrode, and the nonaqueous electrolyte battery - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a negative electrode material for nonaqueous electrolyte battery, capable of realizing a nonaqueous electrolyte battery superior in both the discharge capacity and charging and discharging cycle life. <P>SOLUTION: The negative electrode material for nonaqueous electrolyte battery has a composition expressed by general Formula (1): R<SB>a</SB>Sn<SB>b</SB>M<SB>c</SB>T<SB>d</SB>X<SB>e</SB>A<SB>f</SB>and contains a crystalline alloy having R-Sn-M phase as the main phase. <P>COPYRIGHT: (C)2005,JPO&NCIPI

Description

  The present invention relates to a negative electrode material for a nonaqueous electrolyte battery, a negative electrode including the negative electrode material for a nonaqueous electrolyte battery, and a nonaqueous electrolyte battery including the negative electrode.

Nonaqueous electrolyte secondary batteries using lithium metal, lithium alloys, lithium compounds, carbon materials, and the like as negative electrode active materials are expected to be high energy density batteries, and are actively researched and developed. To date, lithium ion secondary batteries in which LiCoO ₂ or LiMn ₂ O ₄ or the like is used as the positive electrode active material and a carbon material that absorbs or releases lithium is used as the negative electrode active material have been widely put into practical use.

  On the other hand, a secondary battery using lithium metal, a lithium alloy, or a lithium compound as a negative electrode has not been put into practical use yet. The main reason for this is that when lithium metal is used, lithium degradation due to the reaction between the non-aqueous electrolyte and the lithium metal and dendritic (dendritic) lithium generation due to repeated charge and discharge occur, The problem is that the internal short circuit and the cycle life are short.

  In order to solve such problems, studies have been made to use lithium alloys and lithium compounds for the negative electrode. Especially in an alloy such as a lithium-aluminum alloy, the reactivity with the non-aqueous electrolyte is suppressed and the charge / discharge efficiency is improved. However, repeated deep charge / discharge causes pulverization of the electrode, which causes a problem in cycle characteristics. there were.

  By the way, in JP 2001-68112 A (Patent Document 1), it is composed of particles containing at least three phases, of which at least two phases occlude lithium and at least one phase is a phase that does not occlude lithium. It is described that, by using a negative electrode active material for a water electrolyte secondary battery, expansion / contraction associated with lithium occlusion / release is alleviated and cycle life is improved. In addition, in JP 2001-93524 A (Patent Document 2), by using a negative electrode active material having an A phase and a B phase with a small difference in expansion stress during lithium occlusion, the expansion stress in the entire active material is reduced. It is described that it relaxes uniformly and improves the cycle life.

  However, since all of the negative electrode active materials described in these publications are inferior in lithium diffusibility, a sufficient charge / discharge cycle life cannot be obtained.

On the other hand, in Japanese Patent Application Laid-Open No. 2000-311681 (Patent Document 3), a negative electrode material for a lithium secondary battery containing particles mainly composed of an amorphous Sn.A.X alloy having a non-stoichiometric composition. (A represents at least one of transition metals, X represents O, F, N, Mg, Ba, Sr, Ca, La, Ce, Si, Ge, C, P, B, Bi, Sb, Al, In, It represents at least one selected from the group consisting of S, Se, Te and Zn, and describes Sn / (Sn + A + X) = 20 to 80 atomic% in the number of atoms of each atom in the above formula. In the amorphous alloy described in Patent Document 3, as described in paragraph [0078], lithium is occluded / released by an alloying reaction with lithium, and therefore, irreversible capacity is generated by repeated charge / discharge cycles. It is easy to shorten the charge / discharge cycle life.
JP 2001-68112 A JP 2001-93524 A JP 2000-311681 A

  The present invention relates to a negative electrode material for a nonaqueous electrolyte battery capable of realizing a nonaqueous electrolyte battery excellent in both discharge capacity and charge / discharge cycle life, a negative electrode including the negative electrode material, and a nonaqueous solution including the negative electrode. An electrolyte battery is to be provided.

  A negative electrode material for a non-aqueous electrolyte battery according to the present invention includes a crystalline alloy having a composition represented by the following general formula (1) and having an R-Sn-M phase as a main phase. is there.

R _a Sn _{b Mc} T _d X _e A _f (1)
Where R is at least one element selected from rare earth elements, M is at least one element selected from the group consisting of Co, Ni, Fe, Cu, Mn, V and Cr, and T is Ti, Zr , Hf, Nb, Ta, Mo and W, X is at least one element selected from the group consisting of Si, Al, Sb and In, and A is Mg, Ca , Sr, and Ba, a, b, c, d, e, and f are a + b + c + d + e + f = 100 atomic%, 0 <a ≦ 40, 45 ≦ b ≦ 70, 0 <, respectively. c ≦ 30, 0 ≦ d ≦ 10, 0 ≦ e ≦ 20, and 0 ≦ f ≦ 30.

  The electrode material for a nonaqueous electrolyte battery of the present invention may be an intermetallic compound phase consisting of a single phase or an alloy phase consisting of at least two crystal phases. The former is excellent in charge / discharge cycle life characteristics, and the latter is excellent in high capacity and excellent in initial charge / discharge efficiency. The average crystal grain size of the crystal phase is not particularly defined, but the average crystal grain size is preferably in the range of 100 nm to 10 μm.

  The negative electrode according to the present invention includes the negative electrode material for a non-aqueous electrolyte battery. The nonaqueous electrolyte battery according to the present invention comprises a negative electrode including the negative electrode material for a nonaqueous electrolyte battery, a positive electrode, and a nonaqueous electrolyte.

  According to the present invention, a negative electrode material for a nonaqueous electrolyte battery capable of realizing a nonaqueous electrolyte battery excellent in both discharge capacity and charge / discharge cycle life, a negative electrode including the negative electrode material, and the negative electrode are provided. A non-aqueous electrolyte battery can be provided.

  The negative electrode material for a non-aqueous electrolyte battery according to the present invention is characterized by containing a crystalline alloy represented by the following general formula (1).

R _a Sn _{b Mc} T _d X _e A _f (1)
Where R is at least one element selected from rare earth elements, M is at least one element selected from the group consisting of Co, Ni, Fe, Cu, Mn, V and Cr, and T is Ti, Zr , Hf, Nb, Ta, Mo, W, at least one element selected from the group consisting of W, X is at least one element selected from the group consisting of Si, Al, Sb, and In, and A is Mg, Ca , Sr, and Ba, and a, b, c, d, e, and f are a + b + c + d + e + f = 100 atomic%, 0 <a ≦ 40, 45 ≦ b ≦ 70, and 0 <, respectively. c ≦ 30, 0 ≦ d ≦ 10, 0 ≦ e ≦ 20, and 0 ≦ f ≦ 30.

  A nonaqueous electrolyte secondary battery including a negative electrode containing the negative electrode material described above as a negative electrode active material can improve volume energy density and charge / discharge cycle life.

That is, the crystalline alloy represented by the formula (1) described above has (a) the presence of lithium in the negative electrode, specifically, for example, in the crystal grain boundary or crystal grain of the negative electrode alloy, or (b) in the crystal lattice. Charging and discharging can be performed by generating at least one of (a) and (b), for example, when lithium is intercalated, and charging and discharging by so-called alloying reaction (for example, reaction shown in the following chemical formula 1) Therefore, an increase in irreversible capacity accompanying the progress of the charge / discharge cycle can be suppressed, and the charge / discharge cycle life of the secondary battery can be improved. In addition, since the alloy has a high Sn weight ratio, the amount of lithium occlusion can be increased, and the energy density of the secondary battery can be increased.

  The alloy represented by the formula (1) may be composed of an intermetallic compound composed of a single phase or at least two crystalline phases. The basic phase is an R-Sn-M phase, to which an R-Sn-M phase having a different composition ratio, or at least one phase selected from the R-Sn phase, Sn-M phase, and RM phase is added. Become a phase. In the case of a single phase, an extremely stable charge / discharge cycle can be realized.

  Since the R-Sn-M phase can repeat, for example, a charge / discharge cycle of Li by an intercalation reaction, it can contribute to a long life. In the R-Sn-M phase, a phase other than the main phase is formed due to a slight deviation in the composition ratio, and the alloying reaction shown in (C) below is parallel to the above-described intercalation reaction, for example. May occur. On the other hand, the RM phase does not have a reaction capacity with Li, but the other phases have a reaction capacity with a difference in reaction speed with Li, and can contribute to a high capacity. In the R-Sn phase and the Sn-M phase, alloying reactions shown in the following (A) and (B) are possible, respectively.

R-Sn + xLi → R + Li _x Sn Li _x Sn → xLi + Sn (A)
^{Sn-M + xLi → M +} Li x Sn Li x Sn → xLi + Sn (B)
R-Sn-M + xLi → RM + Li x Sn Li x Sn → xLi + Sn (C)
Accordingly, the phase structure in the negative electrode during use gradually includes M phase, RM phase, and R phase, and the R-Sn phase or M-Sn phase disappears depending on the number of charge / discharge cycles. There is also. Moreover, in the reversible reaction in which Sn and Li are bonded and separated in the above-described (A) to (C), partial alloying may occur and a Li—Sn alloy may exist.

  The crystal structure of the main phase of the present invention is not clear. However, when X-ray diffraction measurement is performed using Cukα, the main diffraction peak (diffractive line with the highest diffraction intensity) is between 2.75 and 2.90 で in plane spacing d. ) Is desirable. Depending on the composition, the second highest diffraction intensity peak may exist between 2.45 and 2.55 Å in terms of surface spacing or 2.7 to 2.85 の on the high angle side of the main diffraction peak. desirable. Further, it is desirable that a peak appears on the low angle side, specifically, it is desirable to detect peaks at 2θ of about 10 ° and about 20 °, respectively, and when this peak appears, it is preferable in terms of capacity.

  Examples of the main phase crystal structure include hexagonal crystals, tetragonal crystals, and orthorhombic crystals. Moreover, although the kind of the crystal phase contained in an alloy can be made into 1 type or 2 types or more, a single phase is preferable from a viewpoint of charging / discharging cycle life.

  The average crystal grain size of the crystal phase of the present invention is desirably in the range of 100 nm or more and 10 μm (10000 nm) or less. This is due to the reason explained below. If the average crystal grain size is less than 100 nm, the rise of the discharge capacity may be significantly delayed. In addition, when the crystal grains are fine, the mechanical strength of the material is increased, so that pulverization and deterioration due to lattice expansion and contraction due to charge and discharge are suppressed, which is thought to lead to an improvement in life. On the other hand, the larger crystal grain size may be the average powder grain size when pulverized to the size of the alloy powder necessary for producing the negative electrode, that is, about 10 μm. This is thought to lead to an improvement in life characteristics because strain due to expansion and contraction of the lattice caused by the intercalation reaction during charging and discharging can be reduced and pulverization degradation is difficult to occur.

  The basic element of the alloy represented by the formula (1) is Sn-R, and by adding M to this, the structure control and the phase control are performed, thereby obtaining the characteristics that achieve both high capacity and long life. . The reason for the existence of each constituent element is as follows.

1) Sn (tin)
Sn is an element capable of forming an alloy with lithium, and is a basic element that produces charge / discharge characteristics. In combination with R and M, the structure composed of a single phase or multiple phases having excellent charge / discharge characteristics can be controlled in the range of 45 to 70 atomic%. If it is less than 45 atomic%, the melting point of the material of the R—Sn _binary alloy becomes too high, the structure control becomes difficult, and it becomes difficult to obtain a high capacity or a long life. On the other hand, if it exceeds 70 atomic%, the Sn phase begins to precipitate, so that a long life cannot be obtained in the charge / discharge cycle. A more preferable range is 50 to 60 atomic%.

2) R (rare earth element)
R is at least one element selected from rare earth elements. Examples of rare earth elements include Y, La, Ge, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, and Yb. , Lu and the like. R is an element that hardly undergoes alloying with lithium, and this element contributes particularly to the discharge of the charge / discharge reaction. It is possible to control the structure composed of multiple phases with Sn and 40 atomic% or less. When R exceeds 40 atomic%, the melting point of the material of the R—Sn base alloy becomes too high, the structure control becomes difficult, and it becomes difficult to obtain a high capacity or a long life. On the other hand, at 0%, the Sn phase begins to precipitate, so a long life cannot be obtained in the charge / discharge cycle. A more preferable range is 12 ≦ a ≦ 40. In particular, when the A element is included in the alloy, the total atomic% of the A element and the R element may be 12 atomic% or more.

Examples of the R-Sn phase include RSn ₃ , R ₃ Sn ₅ , R ₂ Sn ₃ , RSn, R ₂ Sn ₅ , R ₃ Sn ₇ , and R ₁₁ Sn ₁₀ phase.

Further, by adding M described later, a phase composed of R-Sn-M, for example, R ₃ Sn ₇ M ₂ phase, R ₁ Sn ₁ M ₁ phase is obtained. In particular, since La, Ce, Pr, and Nd have a eutectic composition with Sn, it is easy to control the structure and crystal grain size by the ultra-quenching method, and is preferable for extending the life. The R ₃ Sn ₇ M ₂ phase has an orthorhombic crystal structure according to 51-645 (Co ₂ La ₃ Sn ₇ ) of the Powder Diffraction File PDF Set 51 Inorganic and Organic Data Book (issued in 2001). . The R ₁ Sn ₁ M ₁ phase also has an orthorhombic crystal structure.

3) M element Like R, M is an element that is difficult to alloy with Li, and when added to the R-Sn alloy, crystal grains can be refined and phase controlled, and the life can be extended. The amount is 30 atomic% or less in atomic%. When it exceeds 30 atomic%, the capacity decreases. If the content is too small, the effect is not sufficient, so the content is preferably 5 to 25 atom% or less, more preferably 10 to 25 atom%. From the viewpoint of extending the life, Co, Ni, Cu, Fe, and Mn are preferable among the M elements. Therefore, the c value indicating the amount of M element is more than 0 and not more than 30 atomic%, preferably 5 to 25 atomic%. By adding M element, R-Sn-M phase, for example, R ₃ Sn ₇ M ₂ phase, R ₃ Sn ₆ M ₂ phase, R ₁ Sn ₁ M ₁ phase can be formed. A compound having an integer ratio or a compound deviating from the integer ratio does not depart from the present invention.

4) T element T element forms R-Sn phase, R-Sn-M phase, Sn-M phase, RM phase as a solid solution or formation of a new phase (for example, XT phase by compound addition with X) The cycle life characteristics can be improved by such effects. The T element content in the alloy is preferably 0 ≦ d ≦ 10 in atomic percent. This is because if it exceeds 10 atomic%, a high capacity cannot be obtained. More preferably, it is 8 atomic% or less. Moreover, as a lower limit, 0.1 atomic% or more is preferable. Among T elements, Ti, Nb, and Mo are preferable in terms of improving characteristics.

5) X element X element is also an element capable of forming an alloy with Li, and the presence of this element can extend the life without significantly reducing the discharge capacity. The amount is 0 ≦ e ≦ 20 in atomic%. When it exceeds 20 atomic%, the capacity gradually decreases. One cause of this decrease in capacity is a decrease in discharge capacity per unit volume due to a decrease in density of the negative electrode active material. Further, the lower limit is preferably 0.1 atomic%. Preferably, it is 15 atomic% or less. Of the X elements, Si, Al, and In are preferable.

6) Element A The element A occupies the position of the element R in the crystal structure, and the amount thereof is 30 atomic% or less. A more preferable range is 0 ≦ f ≦ 20. Moreover, as a lower limit, 0.1 atomic% or more is preferable. From the viewpoint of improving the characteristics, Mg and Ca are more preferable. The atomic ratios of Sn, R element (rare earth element) and A element (for example, Ca), and transition metal should be in the order of Sn> R element (rare earth element) and A element (for example, Ca)> transition metal. desirable. Thereby, since the Sn weight ratio in an alloy can be made high, a high capacity | capacitance can be obtained.

  In particular, the R element is at least one element selected from the group consisting of La, Ce, Pr and Nd, the A element contains at least one element of Ca and Mg, and 12 ≦ a + f ≦ 40 It is preferable in terms of capacity and cycle life. Among them, it is more preferable that Ca is selected as the A element and the sum of a and f is 15 ≦ a + f ≦ 35, and in this case, it is more preferable that a ≧ f.

  The d value, e value, and f value indicating the contents of the element X, element T, and element A all include 0 (zero). When the d value and / or the e value are 0, the initial capacity can be increased. On the other hand, when the d value and / or e value are within a predetermined range, the initial capacity is slightly reduced, but the cycle life is improved. Therefore, it is preferable to set the d value and the e value to predetermined values depending on whether the initial capacity or the cycle life is focused. Further, when the f value is larger than 0, the capacity can be increased while maintaining the charge / discharge cycle life.

  Among the compositions represented by the formula (1) described above, a composition containing an R element, an M element and Sn composed of La is preferable because a long charge / discharge cycle life can be obtained.

  Examples of the method for producing the negative electrode material for a non-aqueous electrolyte battery described above include, for example, a high-frequency melting method, an arc melting method, a sintering method, a rapid quenching method, a strip casting method, an atomizing method, a plating method, a CVD method, a sputtering method, and rolling. Law. Particularly preferred are a rapid quenching method, a strip casting method, a high frequency dissolution method, an atomizing method, and a centrifugal spraying method.

  In each of these methods, each material weighed in advance is dissolved in a crucible in an inert atmosphere, and the subsequent cooling process is changed. That is, in the ultra rapid cooling method, a molten alloy is injected onto a cooling body that rotates at high speed to obtain a flake sample having a thickness of 10 to 50 μm. In the strip casting method, the amount of molten metal supplied per unit time to the cooling body is increased as compared with the ultra rapid cooling method to obtain a flake sample having a plate thickness of 100 to 500 μm. Depending on the conditions, plate thicknesses of up to 100 μm can be obtained by the ultra-quenching method. In the strip casting method, the molten metal may be poured onto a rotating cooling plate during casting, and the thickness of the material is controlled by the amount of molten metal supplied and the moving speed of the cooling plate. As a result, the cooling rate can be controlled. These obtained samples can be homogenized in structure and composition by heat treatment, and this is particularly noticeable in cast samples. Samples obtained by strip casting or ultra-quenching method can be processed without heat treatment. Good. In particular, in the sample obtained by the strip cast method, a columnar crystal structure is easily obtained, and this structure is preferable from the viewpoint of life.

  The negative electrode material according to the present invention is preferably a spherical powder. Thereby, since the specific surface area of negative electrode material can be made small, the oxygen content of negative electrode material can be decreased and high initial efficiency can be obtained. Moreover, the coatability of the slurry can be improved. Furthermore, it is possible to simplify the production method of the negative electrode material by eliminating the pulverization step. In order to obtain a spherical powder, there are an atomizing method, a centrifugal spraying method, and the like.

  In the gas atomization method, a raw material prepared to have a predetermined composition is put in a crucible, dissolved in a vacuum or in an inert atmosphere (eg, Ar gas, He gas, nitrogen gas) by a high frequency induction heating furnace, and alloyed through a hot water supply pipe. The molten metal is dropped into the atomizing tank. A gas atomizing nozzle is disposed in the vicinity of the hot water supply pipe, and an atomizing gas is ejected from the nozzle hole or slit toward the molten metal being dropped. The molten metal is scattered, solidified and powdered by the energy of the jet gas. The inside of this tank is an inert atmosphere, and oxidation of the generated atomized powder is prevented. The produced powdery alloy is guided to the powder storage device from the lower part of the atomizing tank and stored.

  The alloy shape obtained by gas atomization can be changed from a spherical shape to a flat shape by changing the conditions, but in the case of the present invention, it is preferably as spherical as possible. The particle size of the powder produced by the gas atomizing method generally decreases as the energy of the jet gas applied to the molten metal being dropped increases. The energy of the ejected gas can be adjusted by, for example, the pressure of the gas and the size and arrangement of the nozzle holes or slits. Moreover, if the energy of the jet gas is constant, the smaller the amount of molten metal dropped per unit time, the smaller the powder diameter. The dropping amount of the molten metal can be adjusted by the inner diameter of the hot water supply pipe or the pressure applied to the molten metal in the hot water supply pipe. The gas atomization method is characterized in that rapid cooling and pulverization are performed simultaneously.

  On the other hand, in the centrifugal spray method, a molten alloy adjusted to a predetermined composition on a high-speed rotating disk is dropped in an inert atmosphere (eg, Ar gas, He gas, nitrogen gas), and finely dispersed from the disk by centrifugal force. The spherical powder is formed by surface tension. In this case, if the wetness between the molten alloy and the disk is good, it will be difficult to scatter. Therefore, it is preferable to use a ceramic or metal material having a relatively low wettability with respect to the molten metal. The inert atmosphere is preferably He gas from the viewpoint of heat conduction, but Ar gas can also be used. The diameter of the spherical powder can be controlled by the amount of molten metal dripped, the rotational speed of the disk, the molten metal temperature, and the like.

  The particle size of the obtained spherical powder is preferably 10 to 200 μm, and particularly preferably 10 to 60 μm as the negative electrode material. Those having a large particle size can be further pulverized. This pulverization is preferably performed in an inert atmosphere. Further, the spherical powder may be crushed with a press after being applied at the time of electrode preparation.

  Here, the spherical powder means that the ratio of the major axis to the minor axis of the powder is 5 or less, but the weight of the spherical powder is 50% or more.

  Atomized powder can generally be used without heat treatment, but it can also be heat-treated for the purpose of alleviating internal strain generated during rapid cooling. In that case, it is preferable to carry out in an inert atmosphere. The heat treatment temperature is preferably 50 ° C. or more lower than the solidus temperature. More preferably, it is 100 degrees C or less.

  The crystalline alloy represented by the formula (1) described above can be subjected to a surface treatment in order to improve the initial efficiency. The decrease in the initial efficiency of the nonaqueous electrolyte battery is caused by the fact that oxygen or dissolved oxygen adsorbed on the surface of the crystalline alloy having the composition represented by the above formula (1) reacts with lithium to generate an oxide, or a catalyst. It is presumed that this causes an increase in irreversible capacity and an increase in negative electrode resistance by promoting the film formation reaction on the negative electrode surface. Examples of the surface treatment include acid treatment, heat treatment in a hydrogen atmosphere, hydrogen pulverization, and formation of a coating layer. The oxygen content in the alloy can be reduced by acid treatment, heat treatment in a hydrogen atmosphere or hydrogen pulverization. On the other hand, by forming a coating layer such as a carbon layer on the alloy surface, the behavior with respect to the nonaqueous electrolyte can be made close to that of the carbonaceous material.

  By the acid treatment, the oxide layer on the surface can be removed. The acid used is preferably hydrochloric acid or hydrofluoric acid. Acid treatment conditions can be optimized by treatment time, treatment temperature, and acid concentration, but it is preferable to use hydrochloric acid in an alloy system containing Sn.

  Further, heat treatment in a hydrogen atmosphere or hydrogen pulverization is also effective. Heat treatment in a hydrogen atmosphere is effective for reducing the oxide layer on the surface, and hydrogen pulverization can newly generate a non-oxidized surface, thereby forming a large number of surfaces effective for improving the initial efficiency.

  On the other hand, it is also possible to form a coating layer on the surface. For example, carbon can be deposited with a thickness of 20 μm or less. This carbon layer is not particularly limited, other than graphite, and may be, for example, GLC (graphite-like carbon). The deposition process is not particularly limited, such as a gas phase reaction or a solid phase reaction, and the carbon source at that time may be any of a gas (for example, a hydrocarbon type), a liquid, and a solid.

  Inevitable impurities other than the constituent elements may be contained in an amount of 1000 ppm or less. Inevitable impurities include oxygen and carbon. The amount of oxygen after pulverization is preferably 3000 ppm or less including the adsorbed content.

  Further, in the case of an alloy obtained by a normal casting method, excellent electrode characteristics are easily obtained when heat treatment is performed as compared with a cast state.

  In addition, in a non-aqueous electrolyte secondary battery including a negative electrode including a negative electrode material as a negative electrode active material, when an irreversible capacity occurs due to charge / discharge, an R phase, an RM phase, a Sn phase, or a LiSn phase is formed in the negative electrode. There is a case.

  Next, the negative electrode and the nonaqueous electrolyte battery provided with the negative electrode material for a nonaqueous electrolyte battery according to the present invention will be described.

  The nonaqueous electrolyte battery according to the present invention includes a nonaqueous electrolyte, a positive electrode, and a negative electrode including the negative electrode material for a nonaqueous electrolyte battery of the present invention as a negative electrode active material.

1) Positive electrode For the positive electrode, for example, a positive electrode active material, a conductive agent, and a binder are suspended in an appropriate solvent, and the suspension is applied to a current collector such as an aluminum foil, dried, pressed, and strip-shaped. It is produced by making an electrode.

Examples of the positive electrode active material include various oxides and sulfides. For example, manganese dioxide (MnO ₂ ), lithium manganese composite oxide (eg LiMn ₂ O ₄ or LiMnO ₂ ), lithium nickel composite oxide (eg LiNiO ₂ ), lithium cobalt composite oxide (LiCoO ₂ ), lithium nickel cobalt composite Examples thereof include oxides (for example, LiNi _1-x Co _x O ₂ ), lithium manganese cobalt composite oxides (for example, LiMn _x Co _1-x O ₂ ), vanadium oxides (for example, V ₂ O ₅ ), and the like. Moreover, organic materials, such as a conductive polymer material and a disulfide-type polymer material, are also mentioned. More preferable positive electrodes include lithium manganese composite oxide (LiMn ₂ O ₄ ), lithium nickel composite oxide (LiNiO ₂ ), lithium cobalt composite oxide (LiCoO ₂ ), and lithium nickel cobalt composite oxide (LiNi _0.8 ) having a high battery voltage. Co _0.2 O ₂ ) and lithium manganese cobalt composite oxide (LiMn _x Co _1-x O ₂ ).

  Examples of the conductive agent include acetylene black, carbon black, and graphite.

  Examples of the binder include polytetrafluoroethylene (PTFE), polyvinylidene fluoride (PVdF), and fluorine-based rubber.

  The compounding ratio of the positive electrode active material, the conductive agent and the binder is preferably in the range of 80 to 95% by weight of the positive electrode active material, 3 to 20% by weight of the conductive agent, and 2 to 7% by weight of the binder.

2) Negative electrode The negative electrode is prepared by, for example, suspending and mixing a negative electrode mixture composed of a negative electrode active material containing a negative electrode material for a nonaqueous electrolyte battery of the present invention, a conductive agent and a binder in a suitable solvent to obtain a coating solution. It is produced by applying a product to one or both sides of a current collector and drying.

  Moreover, the amount of alkali metal occlusion can be improved by adding a carbon material having a high alkali metal occlusion ability as a negative electrode active material to obtain a mixture of the above-described negative electrode material and this carbon material. As the carbon material used for such a negative electrode active material, a graphite-based carbon material is preferable, and more specifically, mesophase pitch carbon fiber (MCF) is preferable.

  Further, as the conductive agent used for the negative electrode, a carbon material is usually used. If the carbon material used for the negative electrode active material described above has high alkali metal occlusion and conductivity, the carbon material used as the negative electrode active material can also be used as a conductive agent. However, since the conductivity is low only with graphite having high carbon storage properties such as the exemplified mesophase pitch carbon fiber, it is possible to use, for example, acetylene black, carbon black or the like as the negative electrode as the carbon material used as the conductive agent. preferable.

  Examples of the binder include polytetrafluoroethylene (PTFE), polyvinylidene fluoride (PVdF), fluorine rubber, ethylene-butadiene rubber (SBR), carboxymethyl cellulose (CMC), and the like.

  The compounding ratio of the negative electrode active material, the conductive agent and the binder is preferably in the range of 70 to 95% by weight of the negative electrode active material, 0 to 25% by weight of the conductive agent, and 2 to 10% by weight of the binder.

3) Non-aqueous electrolyte The non-aqueous electrolyte contains a liquid non-aqueous electrolyte (non-aqueous electrolyte) prepared by dissolving an electrolyte in a non-aqueous solvent, and the non-aqueous solvent and the electrolyte in a polymer material. Examples thereof include a polymer gel electrolyte, a polymer solid electrolyte containing the electrolyte in a polymer material, and an inorganic solid electrolyte having lithium ion conductivity.

  As the non-aqueous solvent used in the liquid non-aqueous electrolyte, a known non-aqueous solvent can be used in a lithium battery, for example, a cyclic carbonate such as ethylene carbonate (EC) or propylene carbonate (PC), or a cyclic carbonate and a cyclic carbonate. Examples thereof include a nonaqueous solvent mainly composed of a mixed solvent with a nonaqueous solvent (hereinafter referred to as a second solvent) having a viscosity lower than that of carbonate.

  Examples of the second solvent include chain carbonates such as dimethyl carbonate, methyl ethyl carbonate, and diethyl carbonate, γ-butyrolactone, acetonitrile, methyl propionate, ethyl propionate, cyclic ether such as tetrahydrofuran, 2-methyltetrahydrofuran, and the like. Examples of the ethers include dimethoxyethane and diethoxyethane.

Examples of the electrolyte include alkali salts, and particularly lithium salts. As lithium salts, lithium hexafluorophosphate (LiPF ₆ ), lithium tetrafluoroborate (LiBF ₄ ), lithium hexafluoroarsenide (LiAsF ₆ ), lithium perchlorate (LiClO ₄ ), lithium trifluorometasulfonate (LiCF ₃ SO ₃ ) and the like. In particular, lithium hexafluorophosphate (LiPF ₆ ) and lithium tetrafluoroborate (LiBF ₄ ) are preferable. The amount of the electrolyte dissolved in the non-aqueous solvent is preferably 0.5 to 2 mol / L.

  A gel electrolyte is obtained by dissolving the solvent and the electrolyte in a polymer material to form a gel. The polymer material is a single amount of polyacrylonitrile, polyacrylate, polyvinylidene fluoride (PVdF), polyethylene oxide (PECO), or the like. And polymers with other monomers.

As the solid electrolyte, the electrolyte is dissolved in a polymer material and solidified. Examples of the polymer material include polymers of monomers such as polyacrylonitrile, polyvinylidene fluoride (PVdF), polyethylene oxide (PEO), and copolymers with other monomers. Moreover, the ceramic material containing lithium is mentioned as an inorganic solid electrolyte. Of these Li ₃ N, etc. _{Li 3 PO 4 -Li 2 S-} SiS 2 glass.

  A separator can be disposed between the positive electrode and the negative electrode. In addition, a gel-like or solid nonaqueous electrolyte layer may be used in combination with this separator, or a gel-like or solid nonaqueous electrolyte layer may be used instead of the separator.

  The separator is for preventing contact between the positive electrode and the negative electrode, and is made of an insulating material. Furthermore, a shape in which the electrolyte can move between the positive electrode and the negative electrode is used. Specific examples include a synthetic resin nonwoven fabric, a polyethylene porous film, and a polypropylene porous film.

  FIG. 1 shows an example of a cross-sectional view of a thin nonaqueous electrolyte secondary battery which is an embodiment of the nonaqueous electrolyte battery according to the present invention. FIG. 2 is an enlarged cross-sectional view of a portion A in FIG.

  For example, an electrode group 2 is accommodated in a thin container 1 made of stainless steel or a laminate film. The electrode group 2 has a structure in which a belt-like material in which a positive electrode 6, a separator 3, and a negative electrode 9 are laminated is wound in a flat shape. The positive electrode 6 has a structure in which the positive electrode layer 4 and the positive electrode current collector 5 are laminated, and the negative electrode 9 has a structure in which the negative electrode layer 7 and the negative electrode current collector 8 are laminated. One end of the positive electrode terminal 10 is electrically connected to the positive electrode current collector 5 of the electrode group 2, and the other end is extended from the container 1. On the other hand, one end of the negative electrode terminal 11 is electrically connected to the negative electrode current collector 8 of the electrode group 2 and the other end is extended from the container 1.

[Example]
Examples of the present invention will be described below.

(Examples 1-30)
<Preparation of positive electrode>
First, 91% by weight of lithium cobalt oxide (LiCoO ₂ ) powder as a positive electrode active material, 2.5% by weight of acetylene black, 3% by weight of graphite, 3.5% by weight of polyvinylidene fluoride (PVdF), N-methyl Pyrrolidone was added and mixed, applied to an aluminum foil current collector with a thickness of 15 μm, dried, and pressed to prepare a positive electrode having an electrode density of 3.0 g / cm ³ .

<Production of negative electrode>
As the negative electrode active material, a material prepared by the method described in the following (A) to (C) was used by mixing a predetermined amount of elements at the composition ratios shown in Tables 1 and 2 below.

(A) Single roll method The elements mixed in the composition ratios shown in Tables 1 and 2 below are melted by high-frequency dissolution and then injected onto a cooling roll (30 m / s) that rotates at high speed to produce flakes having a thickness of 20 to 60 μm. As a result, a negative electrode material was obtained.

(B) Strip casting method After the elements mixed in the composition ratios shown in Tables 1 and 2 below are melted by high frequency melting, the molten metal is poured onto a slowly moving cooling roll (1 m / s), and flakes having a thickness of 200 to 500 μm Was used to obtain a negative electrode material.

(C) High-frequency melting method The elements mixed in the composition ratios shown in Tables 1 and 2 below were melted by high-frequency melting, and then cast on a water-cooled disk mold with a thickness of about 10 mm to obtain an alloy ingot. The obtained alloy ingot was heat-treated in an inert atmosphere at 600 ° C. for 20 hours to obtain a negative electrode material.

  In any of the examples, it was confirmed from the results of X-ray diffractometry, SEM, and EPMA evaluation that the alloy was a crystalline alloy composed of multiple phases (having two or more crystal phases).

  Each negative electrode material was pulverized by a jet mill so as to have an average powder particle size of 8 to 10 μm to obtain a powdered negative electrode material. The obtained negative electrode material powder was added to 85% by weight of graphite as a conductive agent, 5% by weight of graphite as a conductive agent, 3% by weight of acetylene black as a conductive agent, 7% by weight of PVdF, and NMP. The negative electrode was produced by applying to a current collector made of copper foil, drying, and pressing.

<Production of electrode group>
The positive electrode, a separator made of a polyethylene porous film, the negative electrode, and the separator were each laminated in this order, and then wound in a spiral shape so that the negative electrode was located on the outermost periphery, thereby producing an electrode group.

<Preparation of non-aqueous electrolyte>
Further, non-aqueous electrolysis is performed by dissolving 1.0 mol / L of lithium hexafluorophosphate (LiPF ₆ ) in a mixed solvent of ethylene carbonate (EC) and methyl ethyl carbonate (MEC) (mixing volume ratio 1: 2). A liquid was prepared.

  The electrode group and the electrolytic solution were respectively stored in a bottomed cylindrical container made of stainless steel to assemble a cylindrical nonaqueous electrolyte secondary battery.

(Comparative Example 1)
Carbonaceous mesophase pitch-based carbon fiber (average fiber diameter 10 μm, average fiber length 25 μm, face spacing d ₀₀₂ is 0.3355 nm, specific surface area by BET method is 3 m ² / g) heat-treated at 3250 ° C. instead of alloy powder A cylindrical non-aqueous electrolyte secondary battery was assembled in the same manner as in Example 1 described above except that powder was used.

(Comparative Example 2)
The composition represented by Si ₂ Ni (= Si ₆₇ Ni ₃₃ ) was dissolved in a high frequency induction heating furnace, heat-treated at 800 ° C. for 10 hours, and then pulverized to obtain an alloy for a negative electrode. A cylindrical nonaqueous electrolyte secondary battery was assembled in the same manner as in Example 1 except that this alloy was used.

(Comparative Example 3)
A composition represented by LaSnNi ₂ (= La ₂₅ Ni ₅₀ Sn ₂₅ ) was dissolved in a high-frequency induction heating furnace, heat-treated at 800 ° C. for 10 hours, and then pulverized to obtain an alloy for a negative electrode. A cylindrical nonaqueous electrolyte secondary battery was assembled in the same manner as in Example 1 except that this alloy was used.

<Initial capacity and charge / discharge cycle life>
For each secondary battery, in the test in which the measurement environmental temperature is set to 60 ° C. and the battery is charged at 1.5 A to 2.8 V at a charging current of 1.5 A for 3 hours, the initial capacity (negative electrode material unit) The discharge capacity per volume) and the capacity retention rate (capacity at the 400th cycle when the initial capacity is 1) when this charge / discharge was repeated 400 times were measured to evaluate the charge / discharge cycle characteristics. The results are shown in Tables 1-2 below.

  As can be seen from Tables 1 and 2, the battery using the electrode material according to this example was found to have excellent discharge capacity and capacity retention.

(Examples 31-36)
Next, with respect to the alloy represented by La ₁₇ Mg ₅ Ni ₂₀ Co ₂ Sn ₅₆ , the production methods (A) to (C) were applied, the conditions were adjusted, and the average crystal grain size is shown in Table 3. What was changed was produced. From X-ray diffraction, SEM and EPMA, it was confirmed to be substantially single phase. Using these alloys as negative electrode materials, batteries were produced in the same manner as in Example 1, and the same battery characteristics were evaluated. The discharge capacity value is compared with the value of Comparative Example 1. The results are shown in Table 3.

  In Examples 1 to 36, the average crystal grain size of the crystal phase was measured by the method described below.

That is, a transmission electron microscope (TEM) photograph was taken, the maximum diameter of each crystal grain was measured for 50 crystal grains adjacent to each other, and the average was taken as the average crystal grain diameter.

  As can be seen from Table 3, it was found that the average crystal grain size is preferably in the range of 100 to 10,000 nm. In particular, it was found that when the average crystal grain size is in the range of 100 to 8000 nm, the discharge capacity can be improved while maintaining the capacity retention rate.

(Examples 37 to 62)
<Production of negative electrode>
As the negative electrode active material, a material prepared by the method described in the following (I) to (II) was used by mixing a predetermined amount of elements at the composition ratios shown in Tables 4 to 5 below.

(I) Gas atomization method The elements mixed in the composition ratios shown in Tables 4 to 5 below are melted by high-frequency dissolution, then dropped into a gas atomization chamber through a nozzle, and high-pressure Ar gas is applied to the element to cool it down. A spherical powder having an average particle size shown in Tables 4 to 5 was obtained.

  The average particle size was controlled by the amount of molten metal dropped and the gas pressure. The average particle diameter was measured as D50 (50% by weight diameter) by the microtrack method.

As an example, a transmission electron micrograph (TEM photograph) of the La ₂₆ Ni ₂₁ Sn ₅₃ alloy powder of Example 37 (average particle size is 30 μm) is shown in FIG. 3, and the La ₁₃ Ca ₁₃ Ni ₂₁ Sn ₅₃ alloy of Example 40 is shown in FIG. 4 and 7 show transmission electron micrographs (TEM photographs) of the powder (average particle size is 50 μm). From FIG. 3 to Example 37, it is a single phase, and from FIG. 4 and FIG. 7 (a TEM photograph that shows the same content as FIG. 4 and indicates the presence of the second phase), It can be confirmed that the two-phase (12) is formed.

(II) Centrifugal spray method After the elements mixed in the composition ratios shown in Tables 4 to 5 below are melted by high-frequency dissolution, the elements are scattered from the disk by dropping them onto a disk made of ceramics that rotates at high speed in a He atmosphere through a nozzle. Thus, spherical powders having average particle sizes shown in Tables 4 to 5 were obtained. The average particle size was controlled by the number of revolutions of the disk and the amount of molten metal dropped.

  From the results of X-ray diffractometry and SEM and EPMA evaluation for each example, it was confirmed that the above example contained an alloy composed of a single phase. Depending on the substitution element or the cooling rate, in other words, the diameter of the spherical powder, a slight second phase precipitation may be observed.

Moreover, the X-ray-diffraction pattern of Example 37 among the X-ray-diffraction results about Examples 37-62 is shown in FIG. As is apparent from FIG. 5, in the alloy of Example 37, the main diffraction peak P ₁ is in the range of 2.75 to 2.90 mm in terms of the interplanar spacing d, and the second strongest diffraction peak P ₂ is in the interplanar spacing d. It was confirmed that it was between 2.45 and 2.55 mm. Further, in the alloy of Example 37, a peak appears on the low angle side, and specifically, peaks P ₃ and P ₄ appear at 2θ at about 10 ° (P ₃ ) and about 20 ° (P ₄ ), respectively. . When these peaks P ₃ and P ₄ appear, it is preferable in terms of capacity and cycle life.

  The alloys of Examples 37 to 62 were subjected to differential scanning calorimetry by the method described below. Differential scanning calorimetry was measured using a differential scanning calorimeter (DSC) at a heating rate of 10 ° C./min under an inert atmosphere. In any of the examples, an exothermic peak due to crystallization of the amorphous phase was measured. Was not observed, and only an endothermic peak transitioning from the low-temperature stable phase to the high-temperature stable phase was observed, confirming that the crystalline material does not contain an amorphous phase. The DSC curve for the alloy of Example 39 is shown in FIG. From FIG. 6, it can be understood that in the alloy of Example 39, endothermic peaks appear at 735.4 ° C., 751.3 ° C., 772.4 ° C., 801.2 ° C., 837.9 ° C., and 1183.1 ° C.

  For each of the obtained negative electrode materials of Examples 37 to 62, 90% by weight of the powder of each negative electrode material, 2% by weight of graphite as a conductive agent, 3% by weight of acetylene black as a conductive agent, and 5% by weight of PVdF NMP The solution was added and mixed to prepare a slurry. The obtained slurry was applied to a current collector made of a copper foil having a thickness of 11 μm, dried and pressed to produce a negative electrode.

<Production of electrode group>
A positive electrode similar to that described in Example 1, a separator similar to that described in Example 1, the negative electrode, and the separator are stacked in this order, and then spirally arranged so that the negative electrode is positioned on the outermost periphery. The electrode group was produced by winding in a shape.

  A nonaqueous electrolyte similar to that described in the electrode group and Example 1 was housed in a stainless steel bottomed cylindrical container, and a cylindrical nonaqueous electrolyte secondary battery was assembled.

(Comparative Example 4)
An element mixed at a composition ratio shown in Si ₂ Ni (= Si ₆₇ Ni ₃₃ ) is melted by high-frequency melting, and then dropped into a gas atomizing chamber through a nozzle, and then high-pressure Ar gas is applied to the element to cool it by scattering. A spherical powder having an average particle size of 5 was obtained. A cylindrical nonaqueous electrolyte secondary battery was assembled in the same manner as in Example 37 described above, except that this alloy was used.

(Comparative Example 5)
After the elements mixed at the composition ratio shown in LaSnNi ₂ (= La ₂₅ Ni ₅₀ Sn ₂₅ ) are melted by high-frequency dissolution, they are dropped into a gas atomizing chamber through a nozzle, and high-pressure Ar gas is applied to the elements and cooled by scattering. A spherical powder having an average particle size shown in Table 5 was obtained. A cylindrical nonaqueous electrolyte secondary battery was assembled in the same manner as in Example 37 described above, except that this alloy was used.

(Comparative Example 6)
After mixing metal tin powder, cobalt powder and nickel powder so as to have the composition shown in Table 5 below, this mixture (raw material) and chromium hard spheres were put in a container of a vibration mill device, and the inside of the container was replaced with argon gas. An alloy having the composition shown in Table 5 was obtained by applying vibration. When the obtained alloy was subjected to differential scanning calorimetry under the conditions described above, an exothermic peak transitioning from the metastable phase to the stable phase was observed, and it was confirmed that the alloy was an amorphous material.

  A cylindrical nonaqueous electrolyte secondary battery was assembled in the same manner as in Example 37 described above except that this amorphous alloy was used.

<Initial capacity and charge / discharge cycle life>
For each secondary battery, in the test in which the measurement environmental temperature is set to 30 ° C., the battery is charged at a charging current of 1.5 A to 3.8 V for 3 hours and then discharged to 2.8 V at 1.5 A, the initial capacity (negative electrode material unit The discharge capacity per volume) and the capacity retention rate when the charge / discharge was repeated 400 times (the capacity at the 400th cycle when the initial capacity was 1) were measured to evaluate the charge / discharge cycle characteristics. The results are shown in Tables 4 to 5 below.

  As apparent from Tables 4 to 5, the secondary batteries of Examples 37 to 62 including the crystalline alloy having the composition represented by the formula (1) described above had a discharge capacity per unit volume of the negative electrode material and 400 cycles. It can be seen that the capacity retention rate of the eye is higher than the secondary batteries of Comparative Examples 1 and 4-6.

(Examples 63 to 88)
Alloys having the compositions shown in Tables 6 to 7 below were produced by (A) single roll method, (B) strip cast method or (C) high frequency melting method under the same conditions as described in Example 1 above. .

  The obtained alloy was pulverized by a hammer mill so as to have an average particle size of 15 to 20 μm. About the pulverized powder, surface treatment was performed by each method shown in the following (1) to (5). Only in the case of the treatment (4), pulverization with a hammer mill was not performed, but pulverization was performed by expansion and contraction of the crystal lattice caused by absorption and desorption of hydrogen.

  (1) Hydrochloric acid treatment: The pulverized powder was immersed in a 10% strength hydrochloric acid solution at room temperature for 10 minutes, washed and dried.

  (2) Hydrofluoric acid treatment: The pulverized powder was immersed in a 10% strength hydrofluoric acid solution at room temperature for 10 minutes, washed and dried.

  (3) Heat treatment in hydrogen: Heat treatment was performed at 300 ° C. in a hydrogen flow for 1 hour.

(4) Hydrogen pulverization: A high-pressure hydrogen gas pressure (10 kg / cm ² ) was applied at 60 ° C., and after the hydrogen gas was occluded in the powder, the hydrogen pressure was lowered and devolatilized from the powder. .

(5) Carbon coating: A carbon layer of about 0.5 μm was formed on the powder surface using CH ₄ by the plasma CVD method.

  A cylindrical nonaqueous electrolyte secondary battery was assembled in the same manner as in Example 37 described above except that the obtained surface-treated alloy was used.

<Initial capacity, charge / discharge cycle life and initial discharge efficiency>
For each secondary battery, in the test in which the measurement environmental temperature is set to 30 ° C., the battery is charged at a charging current of 1.5 A to 3.8 V for 3 hours and then discharged to 2.8 V at 1.5 A, the initial capacity (negative electrode material unit) Discharge capacity per volume), initial discharge efficiency (ratio of discharge amount to first charge amount), and capacity retention rate when this charge / discharge is repeated 400 times (the 400th cycle when initial capacity is 1) The charge / discharge cycle characteristics were evaluated. The results are shown in Tables 6 to 7 below. Tables 6 to 7 also show the results of Comparative Examples 1 and 4 to 6 described above.

  As is apparent from Tables 6 to 7, the secondary batteries of Examples 63 to 88 provided with the surface treatment of the crystalline alloy having the composition represented by the formula (1) described above are negative electrode material unit volumes. It can be seen that the discharge capacity per unit and the capacity retention rate at the 400th cycle are higher than those of the secondary batteries of Comparative Examples 1 and 4-6. Moreover, in any of the examples, the initial discharge efficiency was 85% or more, and good results were obtained.

The constituent phases of the main phase (R-Sn-M phase) of the intermetallic compound used in Examples 1 to 30 were determined from the X-ray diffraction method, SEM, and EPMA evaluation, and the results are shown in Table 8 below. In this evaluation, it was found that the alloy was mainly composed of the R ₃ M ₂ Sn ₇ phase or the R ₃ M ₂ Sn ₆ phase. The R-Sn-M phase includes not only those having a crystal structure based on three types of element groups of R, Sn, and M, but also various elements (for example, essential elements) different from the basic elements of R, Sn, and M In the case where the crystal structure is maintained even if T element, A element, and X element) are substituted, it is regarded as the R—Sn—M phase.

  The main phase can be confirmed by the following method.

  10 fields of scanning electron microscope (SEM) photographs were taken, the area ratio occupied by the R-Sn-M phase was determined for each field, and the average value was larger than the average area ratio for the other phases. -It can be confirmed that the M phase is the main phase.

Further, also in Examples 1 to 30, in the X-ray diffraction pattern, the main diffraction peak is in the range of 2.75 to 2.90 mm in terms of the interplanar spacing d. From this also, the R—Sn—M phase (for example, R ₃ It was confirmed that (M ₂ Sn ₇ phase) was the main phase.

  In the above-described embodiment, the example in which the present invention is applied to a cylindrical nonaqueous electrolyte secondary battery has been described. However, the present invention can be similarly applied to a prismatic nonaqueous electrolyte secondary battery, a thin nonaqueous electrolyte secondary battery, and the like. The electrode group housed in the battery container is not limited to the spiral shape, and a plurality of positive electrodes, separators, and negative electrodes may be stacked in this order.

  Moreover, although the example mentioned above demonstrated the example applied to the nonaqueous electrolyte secondary battery, when applied to a nonaqueous electrolyte primary battery, discharge capacity can be improved.

  Note that the present invention is not limited to the above-described embodiment as it is, and can be embodied by modifying the constituent elements without departing from the scope of the invention in the implementation stage. In addition, various inventions can be formed by appropriately combining a plurality of components disclosed in the embodiment. For example, some components may be deleted from all the components shown in the embodiment. Furthermore, constituent elements over different embodiments may be appropriately combined.

It is sectional drawing which shows an example of the nonaqueous electrolyte battery of this invention. It is sectional drawing to which the A section of FIG. 1 was expanded. The transmission electron micrograph about the alloy of Example 37. FIG. 40 is a transmission electron micrograph of the alloy of Example 40. FIG. The characteristic view which shows the X-ray-diffraction pattern about the alloy of Example 37. FIG. The characteristic view which shows the DSC curve by the differential scanning calorimetry about the alloy of Example 39. FIG. 5 is a transmission electron micrograph showing the same content as in FIG. 4 and explaining the presence of the second phase in this photo.

Explanation of symbols

  DESCRIPTION OF SYMBOLS 1 ... Container, 2 ... Electrode group, 3 ... Separator, 4 ... Positive electrode layer, 5 ... Positive electrode collector, 6 ... Positive electrode, 7 ... Negative electrode layer, 8 ... Negative electrode collector, 9 ... Negative electrode, 10 ... Positive electrode terminal, 11: negative terminal, 12: second phase.

Claims (8)

A negative electrode material for a non-aqueous electrolyte battery comprising a crystalline alloy having a composition represented by the following general formula (1) and having an R-Sn-M phase as a main phase.
R _a Sn _{b Mc} T _d X _e A _f (1)
Where R is at least one element selected from rare earth elements, M is at least one element selected from the group consisting of Co, Ni, Fe, Cu, Mn, V and Cr, and T is Ti, Zr , Hf, Nb, Ta, Mo and W, X is at least one element selected from the group consisting of Si, Al, Sb and In, and A is Mg, Ca , Sr, and Ba, a, b, c, d, e, and f are a + b + c + d + e + f = 100 atomic%, 0 <a ≦ 40, 45 ≦ b ≦ 70, 0 <, respectively. c ≦ 30, 0 ≦ d ≦ 10, 0 ≦ e ≦ 20, and 0 ≦ f ≦ 30.   The R element is at least one selected from the group consisting of La, Ce, Pr and Nd, the A element includes at least one element of Ca and Mg, and 12 ≦ a + f ≦ 40. The negative electrode material for nonaqueous electrolyte batteries according to claim 1.   2. The negative electrode for a non-aqueous electrolyte battery according to claim 1, wherein the crystalline alloy is subjected to any surface treatment among acid treatment, heat treatment in a hydrogen gas atmosphere, hydrogen pulverization, and carbon coating. material.   The electrode material for a non-aqueous electrolyte battery according to claim 1 has an average crystal grain size of 100 nm to 10 μm, and a negative electrode material for a non-aqueous electrolyte battery.   The negative electrode material for a non-aqueous electrolyte battery according to claim 1, wherein the crystalline alloy does not exhibit an exothermic peak in differential scanning calorimetry.   2. The negative electrode for a non-aqueous electrolyte battery according to claim 1, wherein a main diffraction peak appears between 2.75 and 2.90 で at an interplanar spacing d in the X-ray diffraction measurement using Cukα. material.   A negative electrode comprising the negative electrode material for a nonaqueous electrolyte battery according to any one of claims 1 to 6.   A nonaqueous electrolyte battery comprising: a negative electrode including the negative electrode material for a nonaqueous electrolyte battery according to claim 1; a positive electrode; and a nonaqueous electrolyte.

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