JP4281055B2 - Nonaqueous electrolyte, nonaqueous electrolyte battery, and method for producing nonaqueous electrolyte battery - Google Patents

Description

  The present invention relates to a non-aqueous electrolyte battery using a silicon material for a negative electrode, and more particularly to a non-aqueous electrolyte used for this.

  In recent years, various non-aqueous electrolyte batteries that can obtain high energy density have attracted attention for power supplies for electronic devices, power storage power supplies, and electric vehicle power supplies that are becoming higher performance and smaller.

Currently, commercially available lithium ion batteries use lithium cobaltate (LiCoO ₂ ) for the positive electrode, use a carbon material capable of occluding and releasing lithium ions for the negative electrode, and use organic materials such as ethylene carbonate and diethyl carbonate as nonaqueous electrolytes. A solution in which an electrolyte salt such as LiPF ₆ is dissolved in a solvent is used. When LiPF ₆ is used as the electrolyte salt, the ion conductivity of the non-aqueous electrolyte can be increased and the battery performance can be improved. Therefore, LiPF ₆ is frequently used as the electrolyte salt.

  In a lithium ion battery using a carbon material for the negative electrode, it is necessary to moderately suppress the decomposition of the nonaqueous electrolyte that occurs on the negative electrode surface. When the nonaqueous electrolyte decomposes on the negative electrode surface, a coating film is formed on the negative electrode surface by the reaction product generated by the decomposition reaction. If the coating film is too rough, further decomposition reaction of the nonaqueous electrolyte is suppressed. However, if the coating is too dense, the resistance of the negative electrode becomes too high, and in any case adversely affects the various characteristics of the battery. Therefore, it has been a problem to form a good coating on the negative electrode surface. In order to cope with this problem, a technique of adding vinylene carbonate, propane sultone, or the like to the nonaqueous electrolyte is known (see, for example, Patent Documents 1 to 3). These additives contributed to the formation of a stable protective film on the surface of the negative electrode carbon material (see, for example, Patent Document 3, paragraphs 0025 to 0026).

On the other hand, the use of silicon as a negative electrode material for nonaqueous electrolyte batteries has been proposed. Since silicon can be alloyed with a composition up to lithium and Li ₂₂ Si _5, it has attracted attention because it may have a weight energy density that is an order of magnitude higher than that of carbon materials. (For example, refer nonpatent literature 1). In addition, since silicon is abundant in resources and has low toxicity, it can be said that it is one of inexpensive and safe battery materials. For example, Patent Document 4 proposes using a silicon single crystal for the negative electrode of a lithium battery. In addition, it has been proposed to use an ultrafine silicon material as a negative electrode material and to produce a silicon electrode by a sputtering method (see, for example, Patent Document 5).
JP-A-11-67266 JP-A-11-162511 JP 2002-83632 A JP-A-5-74463 JP-A-11-185744 Japanese Patent Laid-Open No. 3-105854 JP-A-4-43556 Edited by T. B. Massalski, “Binary Alloy Phase Diagrams”, 3rd edition, Materials Information Society, 1990 ,. 2465-2469 (ISBN 0-87170-403-X)

However, the non-aqueous electrolyte battery using silicon as the negative electrode has a problem that the charge / discharge cycle performance is not sufficient. Furthermore, the present inventors made remarkable use of the characteristics of LiPF ₆ which is excellent in ion conductivity and oxidation resistance, particularly when LiPF ₆ is used as the electrolyte salt, and the capacity decrease due to repeated charge and discharge becomes remarkable. I found that there was a problem that it could not be used as a battery.

The present invention has been made in view of the above problems, and an object of the present invention is to ensure sufficient charge / discharge cycle performance of a battery using a silicon material capable of occluding and releasing lithium as a negative electrode. It is further desirable to provide a non-aqueous electrolyte battery having sufficient charge / discharge cycle performance even when LiPF ₆ having excellent ion conductivity is used as the electrolyte salt.

In the nonaqueous electrolyte battery using silicon as the negative electrode material, the present inventors have insufficient charge / discharge cycle performance, and when LiPF ₆ is used as the electrolyte salt, the discharge capacity decreases with repeated charge / discharge cycles. In view of the fact that the degree of this is particularly large, it was considered that the deterioration mechanism of the negative electrode performance was greatly influenced by extraneous factors that did not exist in the case of the negative electrode using the carbon material. And in the battery which used silicon for the negative electrode and the performance fell, it discovered that the silicon oxide which originally existed on the silicon surface was removed to some extent. Therefore, the present inventors consider that suppressing the process of removing silicon oxide present on the silicon surface will lead to improving the performance of a non-aqueous electrolyte battery using silicon as a negative electrode, and further studies are made. Proceeded.

  As a result of the above studies, the inventors of the present invention have surprisingly improved the performance of the nonaqueous electrolyte battery using silicon as the negative electrode by assuming that the nonaqueous electrolyte contains a specific structure. As a result, the present invention has been found.

  That is, the configuration of the present invention and its operation and effects are as follows. However, the action mechanism includes estimation, and the success or failure of the action mechanism does not limit the present invention.

The present invention comprises a positive electrode and a negative electrode using a silicon material capable of occluding and releasing lithium, and 1,3-propane sultone as a cyclic organic compound having an S═O bond is 0.1% by mass or more and 10% by mass or less. It is the nonaqueous electrolyte battery assembled using the nonaqueous electrolyte characterized by containing.

The nonaqueous electrolyte battery of the present invention is characterized in that the nonaqueous electrolyte contains a hexafluorophosphate anion.

Moreover, the nonaqueous electrolyte battery of the present invention is characterized in that the nonaqueous electrolyte further contains vinylene carbonate.

  The nonaqueous electrolyte battery of the present invention is characterized in that the silicon material used for the negative electrode is a microcrystalline body.

  The negative electrode of the nonaqueous electrolyte battery of the present invention is characterized in that a silicon material is formed on a material having electronic conductivity.

  The negative electrode of the nonaqueous electrolyte battery according to the present invention is a method for producing a nonaqueous electrolyte battery including a step of forming microcrystalline silicon on a material having electron conductivity by a sputtering method.

  In addition, the nonaqueous electrolyte battery manufacturing method of the present invention is characterized in that crystalline silicon is used as a target used in the sputtering method.

  Since the present invention is configured as described above, the charge / discharge cycle performance of a battery using a silicon material capable of occluding and releasing lithium as a negative electrode can be remarkably improved.

By making the non-aqueous electrolyte used in the non-aqueous electrolyte battery using a silicon material capable of occluding and releasing lithium into the negative electrode contains a cyclic organic compound having an S═O bond, Although it is not necessarily clear about the effect | action which exhibits a sufficient effect, the present inventors guess as follows. The surface of the negative electrode silicon material is usually covered with silicon oxide (SiO ₂ ). When charging / discharging the battery, lithium ions pass through the silicon oxide layer. On the other hand, many non-aqueous electrolytes contain a small amount of hydrogen fluoride. In particular, an electrolyte containing a hexafluorophosphate anion tends to react with the mixing of moisture in the air and the like to easily contain hydrogen fluoride. However, since hydrogen fluoride reacts remarkably with silicon oxide, when a non-aqueous electrolyte containing hydrogen fluoride is used, the silicon oxide covering the surface of the negative electrode silicon material is removed. And since the silicon negative electrode material from which the silicon oxide was removed is a thing which is not excellent in charge / discharge performance repeatedly for some reason, the fall of battery performance is remarkable. Here, since the electrolyte contains a cyclic organic compound having an S═O bond, hydrogen fluoride reacts with the cyclic organic compound having an S═O bond and disappears. Reaction with hydrogen fluoride is suppressed. Therefore, when the non-aqueous electrolyte of the present invention is used in a non-aqueous electrolyte battery using a silicon material capable of occluding and releasing lithium as a negative electrode, the presence of a silicon oxide layer on the surface of the silicon negative electrode material is maintained, and the non-aqueous electrolyte battery The charge / discharge cycle performance can be significantly improved.

The reaction between the hydrogen fluoride and the cyclic organic compound having an S═O bond is represented by the following formula when the cyclic organic compound having an S═O bond is 1,3-propane sultone, for example.

The content of 1,3-propane sultone , which is a cyclic organic compound having an S═O bond, contained in the nonaqueous electrolyte is 0.1% with respect to the total mass of the nonaqueous solvent and the electrolyte constituting the nonaqueous electrolyte. It is preferably 10% or less. By setting the content to be 0.1% or more, the effect of the present invention that improves the charge / discharge cycle performance can be reliably exhibited. Further, by setting the content to 10% or less, it is possible to reduce the possibility that the internal resistance of the battery increases due to a side reaction (decomposition reaction) of the cyclic organic compound having an S═O bond. However, since the cyclic organic compound having S═O bond is opened as shown in the above formula by reaction with hydrogen fluoride, the cyclic compound having S═O bond initially added based on the nonaqueous electrolyte collected from the battery is used. Such reaction products must also be taken into account when estimating the amount of organic compounds.

  By using a silicon material capable of occluding and releasing lithium as the negative electrode active material in the nonaqueous electrolyte battery, lithium ions can be occluded and released in a range of at least 0 to 2 V with respect to metallic lithium.

  Next, the best mode of the silicon material used for the negative electrode will be described. In general, regarding the crystallinity of a substance, when the crystallites are arranged in order from small to large, they become amorphous, microcrystalline, polycrystalline, and single crystalline.

  The silicon material used for the negative electrode of the battery of the present invention is not particularly limited, and single crystal silicon, polycrystalline silicon, microcrystalline silicon, amorphous silicon, or the like can be used. The negative electrode may be formed by forming a silicon material on a material having electronic conductivity.

Among these, the crystal form of the silicon material used for the negative electrode of the battery of the present invention is preferably a microcrystalline body. A single crystal is not preferable because the crystal collapses and becomes extremely fine due to the volume change accompanying the occlusion and release of lithium ions. If it is a polycrystal, each crystal undergoes a volume change associated with insertion and extraction of lithium ions. As a result, the negative electrode as a whole cannot absorb the volume change, resulting in a large capacity reduction due to repeated charge / discharge cycles. On the other hand, in the case of amorphous, since it does not have crystals, the composition of Li ₂₂ Si ₅ cannot be taken, and a large charge / discharge capacity cannot be obtained. On the other hand, by using microcrystalline silicon for the negative electrode, it is possible to basically take the composition of Li ₂₂ Si ₅ by occlusion / release of lithium, and the volume change of each crystal generated at that time is absorbed. Therefore, the volume change of the negative electrode as a whole is drastically reduced, so there is no occurrence of fine pulverization or partial isolation of the negative electrode active material during charging / discharging, as seen in conventional general alloys. Charge / discharge cycle performance is improved. In addition, since a large interface between the microcrystalline silicon and the electrolytic solution is obtained, various discharge performances of the battery are improved.

  By the way, when samples of various crystal forms are measured by X-ray diffractometry, clear peaks are not observed for amorphous and microcrystals, but clear crystallinity peaks for polycrystals and single crystals. Is observed. On the other hand, when an electron beam diffraction measurement is performed by a transmission electron microscope (TEM) to obtain a diffraction image, a halo is observed for the amorphous body, and a Debye-Scherrer ring is observed for the microcrystalline body and the polycrystalline body, For a single crystal, a two-dimensional point array single crystal pattern is observed. From this, a microcrystal and a polycrystal can be distinguished by combining the X-ray diffraction method and the electron diffraction method using a transmission electron microscope (TEM). That is, the microcrystalline material suitable for the battery of the present invention refers to a crystal in which a clear peak is not observed by X-ray diffraction measurement and a Debye-Scherrer ring is observed by electron diffraction using a transmission electron microscope (TEM). .

  A method for obtaining microcrystalline silicon is not particularly limited, but a sputtering method is preferably used. “Sputter” originally means “jumping and popping”. Sputtering refers to a phenomenon in which a material used for a target in discharge or the like is knocked out of the target by ion impact and adheres to the surface of a nearby object. Here, the sputtering method is a method of making a thin film by striking ions against a target material, which is a raw material, in a vacuum, and carrying atoms knocked from the target material on a nearby substrate. Thin film production by sputtering has the characteristics that there is little compositional deviation from the raw material, film production of a high melting point material is possible, and industrial continuous operation is possible.

  Preferred examples of the sputtering method include RF sputtering, DC sputtering, magnetron sputtering, and ion beam sputtering. Here, microcrystalline silicon can be obtained by using silicon as a target.

  The silicon material used for the target is not particularly limited, but it is desirable to use crystalline silicon. That is, by using crystalline silicon as a target, a part of the crystal structure of silicon used for the target is reflected, so that microcrystalline silicon can be obtained more reliably. From this point of view, it is not easy to obtain a microcrystal because silicon passes through a gaseous state in the CVD method or the vapor deposition method.

  In addition, if an electron conductive material that can be used as a current collector is directly supported by a sputtering method, etc., the electron contact between the microcrystalline silicon and the current collector is ensured, and the reversibility and rate characteristics are improved. To do. Further, it is preferable in that a binder, a conductive material, and a coating operation are not necessary.

For the negative electrode that can be used in the present invention, a silicon material capable of occluding and releasing lithium is used, but it is also possible to simultaneously sputter elements other than silicon. For example, alkaline earth metals, transition metals, and non-metals, which are elements that can be alloyed with lithium, and oxides, nitrides, sulfides, phosphates, and the like are included as compounds. Preferably, elements such as arsenic, aluminum, tin, antimony and lead are preferably used. Further, it is preferable to perform sputtering at the same time as a metal having excellent conductivity, such as nickel and copper, which is difficult to alloy with lithium, in order to improve the conductivity of the sputtered thin film. Further, an element that improves the conductivity of the microcrystalline silicon by doping silicon may be sputtered simultaneously. In particular, the microcrystalline silicon material has an electron conductivity of 10 ⁻⁵ Scm ⁻¹ or more, preferably ¹ Scm ⁻¹ or more at room temperature.

Silicon is a semiconductor, but when it is used as the main constituent material of the negative electrode active material, the flow of electrons between the active material and the current collector is important. That is, by doping impurities into silicon, which is an intrinsic semiconductor, a foreign semiconductor, in particular, a p-type semiconductor, an n-type semiconductor, and a semiconductor having a pn junction can be obtained. As the negative electrode active material, a material having better charge / discharge cycle performance can be obtained. The impurities referred to here are those that can become donor atoms and acceptor atoms among all the elements of the periodic table, preferably P, Al, As, Sb, B, Ga, In, etc., most preferably Although it is B, it is not limited to these. In addition, the presence of lattice defects may contribute to the improvement of electron conduction. As the impurity doping method, a method in which silicon in which impurities are mixed in advance is used as an argon sputtering target, a method in which sputtering is performed simultaneously, and a sputtered thin film is doped by an alloy method, a diffusion method, an ion implantation method, or the like. Examples include, but are not limited to, methods. The concentration of such impurity addition is usually a ratio of one donor atom or one acceptor atom to 10 ⁷ to 10 ⁶ silicon atoms, but high concentration doping is preferable, and 10 ⁴ silicon atoms are suitable. It is desirable that the concentration be one donor atom or one acceptor atom or higher.

In addition to silicon materials capable of occluding and releasing lithium, the negative electrode includes lithium metal, lithium alloys, etc., calcined carbonaceous compounds capable of occluding and releasing lithium ions or lithium metal, chalcogen compounds, and organic compounds containing lithium such as methyllithium. Etc. may be used together. By using these together, lithium can be occluded in advance in the silicon negative electrode material, which is effective when combined with a positive electrode active material that does not have lithium at the time of the raw material, such as TiS ₂ .

  The current collector may be anything as long as it is an electronic conductor that does not adversely affect the constructed battery. For example, as a current collector material, in addition to copper, stainless steel, nickel, aluminum, titanium, calcined carbon, carbon fiber, conductive polymer, conductive glass, Al-Cd alloy, etc., adhesion, conductivity, resistance For the purpose of improving reducibility, the surface of copper or carbon fiber group treated with carbon, nickel, titanium, silver or the like can be used. Moreover, what formed by vapor deposition of copper, platinum, gold | metal | money, silver, etc. on films, such as olefinic polymers, such as polyethylene and a polypropylene, and a polyimide, can be used. The surface of these materials can be oxidized. For these shapes, films, sheets, nets, punches, expanded ones, lath bodies, porous bodies, foams, formed bodies of fiber groups, and the like are used in addition to foils produced by rolling or electrolysis. The thickness is not particularly limited, but a thickness of 1 to 500 μm is used. Furthermore, a foil having a rough surface surface roughness of 0.2 μmRa or more is preferable, whereby the adhesion between the negative electrode active material and the current collector is excellent. Therefore, it is preferable to use an electrolytic foil because it has such a rough surface. In particular, an electrolytic foil that has been subjected to a cracking treatment is most preferable.

On the other hand, examples of the positive electrode active material include V ₂ O ₅ , MnO ₂ , Li _x MO ₂ having a layered structure (M is a transition metal such as Co, Ni, and Mn), Li _x Mn ₂ O ₄ having a spinel structure, and the like. It absorbs transition metal oxides, metal chalcogenides such as TiS ₂ , MoS ₂ and NbSe ₃ , graphite intercalation compounds such as polyacene, polyparaphenylene, polypyrrole and polyaniline, and alkali metal ions and anions such as conductive polymers. A variety of releasable materials can be utilized. In particular, when the microcrystalline silicon material of the present invention is used as a negative electrode active material, a material having a 4V class potential such as Li _x CoO ₂ , Li _x NiO ₂ , or Li _x Mn ₂ O ₄ is desirable from the viewpoint of high energy density. In particular, lithium-containing transition metal oxides such as Li _x CoO ₂ , Li _x NiO ₂ , and Li _x Mn ₂ O ₄ are preferable.

  As the non-aqueous electrolyte, for example, a liquid electrolyte (electrolytic solution), a gel electrolyte, a polymer solid electrolyte, an inorganic solid electrolyte, a molten salt, and the like can be preferably used. As the organic solvent of the organic electrolyte, a self-evident one can be used in a self-evident prescription.

On the other hand, as the solid electrolyte, for example, an inorganic solid electrolyte, an organic solid electrolyte, an inorganic organic solid electrolyte, a molten salt, or the like can be used. As the inorganic solid electrolyte, lithium nitride, halide, oxyacid salt, phosphorus sulfide compound, and the like are well known, and one or more of these can be used in combination. Among _{them, Li 3 N, LiI, Li} 5 NI 2, Li 3 N-LiI-LiOH, Li 4 SiO 4, Li 4 SiO 4 -LiI-LiOH, xLi 3 PO 4 - (1-x) Li 4 SiO 4 Li ₂ SiS _{3 and the} like are effective. On the other hand, in an organic solid electrolyte, a polyethylene oxide derivative, a polymer containing at least the derivative, a polypropylene oxide derivative, a polymer containing at least the derivative, a polyphosphazene or the derivative, a polymer containing an ion dissociating group, a phosphate ester polymer derivative Furthermore, a polymer matrix material (gel electrolyte) in which a non-aqueous electrolyte is contained in a polyvinylpyridine derivative, a bisphenol A derivative, polyacrylonitrile, polyvinylidene fluoride, fluororubber, or the like is effective.

  As the separator, an insulating thin film having excellent ion permeability and mechanical strength can be used. From the viewpoint of organic solvent resistance and hydrophobicity, sheets made of olefin polymers such as polypropylene and polyethylene, glass fibers, polyvinylidene fluoride, polytetrafluoroethylene, and the like, microporous films, nonwoven fabrics, cloths, and the like are used. The pore diameter of the separator is in a range generally used for batteries, for example, 0.01 to 10 μm. The thickness is also the same, generally in the range used for batteries, for example, 5 to 300 μm.

(Example 1)
A negative electrode was produced as follows. A silicon single crystal, which is a p-type semiconductor doped at a ratio of one boron (B) atom to 10 ⁴ silicon atoms, is used as a target. On an electrolytic copper foil (manufactured by Nippon Electrolytic Co., Ltd .: GP15), argon sputtering was performed at an output of 200 W for 30 minutes to form a silicon layer of about 5 mg, which was used as a negative electrode.

As a result of X-ray diffraction measurement, no crystalline peak was observed. When an electron beam diffraction image was obtained using a transmission electron microscope (TEM), a ring was observed. From this, it was confirmed that the formed silicon layer was made of microcrystalline silicon. on the other hand,
Moreover, the negative electrode surface part was cut | disconnected with the focused ion beam apparatus (FIB), and the cross section was similarly observed with FIB. The observation image by FIB is shown in FIG. This observation image is an observation of the surface of the negative electrode with an accuracy of 45 degrees. In FIG. 1, a mushroom umbrella-like portion can be seen in the approximate center of the screen. This reflects the cross-sectional shape of the copper portion of the electrolytic copper foil cut by the FIB, and the component of the white portion that occupies the center of the portion is copper. Copper metal crystals are observed as if they were observed with a polarizing microscope. Next, a dark portion covering the periphery of the Hana shape is a silicon layer. The periphery of the silicon layer is covered with a slightly lighter layer, which is platinum deposited on the surface before cutting by FIB. The edge of the silicon layer is clearly defined and the thickness is observed. It was given to make it easier to do. From this observation result, it was confirmed that a silicon layer having a thickness of 0.4 μm to 0.5 μm was formed on the electrolytic copper foil. In addition, the shape of the negative electrode surface which is not cut | disconnected in cross section is observed around the white part which occupies the screen center part demonstrated by the above. The large granular shape is a reflection of the Hana shape, but it can be seen that the surface of the granular shape is covered with fine irregularities. The irregularities are considered to reflect silicon microcrystals.

A positive electrode was produced by a known method as follows. LiCoO ₂ was used as the active material, acetylene black was used as the conductive agent, and polyvinylidene fluoride was used as the binder. These materials were made into a paste using N-methylpyrrolidone, applied onto a 15 μm aluminum foil, dried, and pressed by a roll press to obtain a positive electrode.

The volume ratio of ethylene carbonate and diethyl carbonate 6: LiPF ₆ in a mixed solvent of 4 was dissolved 1mol / liter, more 1,3-propane sultone 2 wt%, vinylene carbonate was added 2 wt%, and a non-aqueous electrolyte did.

  A polyethylene microporous film (25 μm, 1 sheet) was sandwiched between the positive electrode and the negative electrode to form a pole group 4. This pole group 4 was covered with an outer package 5 made of a metal resin composite film, the nonaqueous electrolyte was poured, and the periphery of the outer package was sealed by thermal fusion to produce a nonaqueous electrolyte battery. This is the battery 1 of the present invention. An external view of the battery according to this example is shown in FIG. 6 is a terminal.

(Example 2)
Except for using 1 mol / liter of LiPF ₆ dissolved in a mixed solvent of ethylene carbonate and diethyl carbonate in a volume ratio of 6: 4 as a nonaqueous electrolyte and further adding 2% by mass of 1,3-propane sultone. Produced a nonaqueous electrolyte battery in the same manner as in Example 1. This is referred to as the battery 2 of the present invention.

(Example 3)
A negative electrode was produced as follows. Silicon powder which is polycrystalline silicon (manufactured by Kojundo Chemical Laboratory Co., Ltd .: about 10 μm or less), acetylene black as a conductive agent and polyvinylidene fluoride as a binder are made into a paste using N-methylpyrrolidone, and 15 μm It apply | coated and dried on copper foil, it pressed with the roll press, and it was set as the negative electrode.

  A polyethylene microporous film (25 μm, 1 sheet) was sandwiched between the positive electrode and the negative electrode as a separator to form a pole group. Except for these, a nonaqueous electrolyte battery similar to that of Example 1 was produced. This is referred to as the present invention battery 3.

(Comparative Example 1)
Except that 1 mol / liter of LiPF ₆ was dissolved in a mixed solvent of ethylene carbonate and diethyl carbonate in a volume ratio of 6: 4 as a non-aqueous electrolyte, and 2% by mass of vinylene carbonate was added. In the same manner as in Example 1, a nonaqueous electrolyte battery was produced. This is referred to as comparative battery 1.

(Comparative Example 2)
Except that 1 mol / liter of LiPF ₆ was dissolved in a mixed solvent of ethylene carbonate and diethyl carbonate in a volume ratio of 6: 4 and 0.4% by mass of succinic anhydride was added as a non-aqueous electrolyte. A nonaqueous electrolyte battery was produced in the same manner as in Example 1. This is referred to as comparative battery 2.

(Comparative Example 3)
A non-aqueous electrolyte battery was prepared in the same manner as in Example 1 except that a non-aqueous electrolyte was prepared by dissolving 1 mol / liter of LiPF _{6 in} a mixed solvent of ethylene carbonate and diethyl carbonate in a volume ratio of 6: 4. Produced. This is referred to as comparative battery 3.

(Comparative Example 4)
Aqueous volume ratio of ethylene carbonate and diethyl carbonate as an electrolyte 6: except that used was prepared by dissolving 1mol / liter of LiPF ₆ in a mixed solvent of 4, a non-aqueous electrolyte battery in the same manner as in Example 3 Produced. This is referred to as a comparative battery 4.

  A large number of each of the batteries of the present invention and comparative batteries were prepared and subjected to a charge / discharge test. The charging condition was a constant current / constant voltage charging of current 0.2 ItA, 4.2 V, 5 hours, and the discharging condition was a constant current discharge of current 0.2 ItA, final voltage 3.0 V. Here, the discharge capacity at the second cycle was defined as “initial discharge capacity”. Charging / discharging was repeated 30 cycles, and the value of the discharge capacity at the 30th cycle when the “initial discharge capacity” was set to 100 for each battery was determined as the “charge / discharge cycle performance value”. The results are shown in Table 1.

  As is clear from the results in Table 1, the batteries 1 and 2 of the present invention using the nonaqueous electrolyte containing 1,3-propane sultone significantly improved the charge / discharge cycle performance as compared with the comparative battery 3. The improvement rate has actually reached about 160%. On the other hand, in Comparative Examples 1 and 2, the effect of improving the charge / discharge cycle performance was small.

  For reference, the charge / discharge cycle performance of the battery of the present invention 1 and the battery of Comparative Example 3 is shown in FIG. From this, it can be seen that the effect of using the non-aqueous electrolyte of the present invention is so remarkable that it is unimaginable.

  On the other hand, in a battery using a carbon material as a negative electrode, it is said that cycle performance can be improved by adding vinylene carbonate or the like, as in the case of adding 1,3-propane sultone. However, in the above embodiment, in the comparative battery 1 using vinylene carbonate instead of 1,3-propane sultone and the comparative battery 2 using succinic anhydride instead of 1,3-propane sultone, the charge / discharge cycle is changed. The degree of improvement was not noticeable. From this, it can be seen that the concept of a preferable negative electrode surface state in the silicon negative electrode material cannot be considered in the same manner as when the negative electrode carbon material is used. That is, when a negative electrode carbon material is used, a film formed on the carbon negative electrode by the action of an additive such as 1,3-propane sultone or vinylene carbonate plays an important role in charge / discharge cycle performance. Even when a silicon negative electrode material is used, there will certainly be a film formed by the action of 1,3-propane sultone or vinylene carbonate as described above. However, although the degree of the effect is sufficient, it is considered that it is extremely important to ensure that the silicon oxide on the surface of the silicon negative electrode is not removed in order to obtain sufficient charge / discharge cycle performance. It is presumed that this is related to the fact that a specific effect was exhibited with respect to charge / discharge cycle performance only when a cyclic organic compound having an S═O bond was added.

  Further, as is apparent from comparison between the present invention battery 1 and the present invention battery 2, the charge / discharge cycle performance is further improved by further containing vinylene carbonate in addition to 1,3-propane sultone in the nonaqueous electrolyte. be able to.

Further, as is clear from comparison between the present invention battery 1 and the present invention battery 3, by using microcrystalline silicon, the charge / discharge cycle is remarkably compared with the case of using polycrystalline silicon (commercially available silicon powder). It turns out that it is excellent in performance. As is clear from comparison between the battery 3 of the present invention and the comparative battery 4, a charge / discharge cycle is obtained when 1,3-propane sultone is added as a cyclic organic compound having an S═O bond even in polycrystalline silicon. It can be seen that the performance has improved. However, the extent of the effect is not name be such dramatic as in the case of using a microcrystalline silicon.

It is a FIB observation image of the cross section in the negative electrode surface part of this invention battery. It is an external view of the nonaqueous electrolyte battery which concerns on an Example. It is a figure which shows the charging / discharging cycling performance of this invention battery and a comparison battery.

Explanation of symbols

DESCRIPTION OF SYMBOLS 1 Positive electrode 2 Negative electrode 3 Separator 4 Positive electrode collector 5 Negative electrode collector 6 Exterior material

Claims (7)

A non-aqueous electrolyte comprising a positive electrode and a negative electrode using a silicon material capable of occluding and releasing lithium, and containing 0.1 to 10% by mass of 1,3-propane sultone Non-aqueous electrolyte battery assembled. The non-aqueous electrolyte, a non-aqueous electrolyte battery according to claim 1, wherein comprising a hexafluorophosphate anion. The non-aqueous electrolyte, a non-aqueous electrolyte battery according to claim 1 or 2, characterized in that additionally contain vinylene carbonate. The non-aqueous electrolyte battery according to claim 1, wherein the silicon material used for the negative electrode is a microcrystalline body. The negative electrode, the nonaqueous electrolyte battery according to claim 1, the material having electron conductivity silicon material is formed. The said negative electrode is a manufacturing method of the nonaqueous electrolyte battery in any one of Claims 1-5 including the process of forming microcrystal silicon by the sputtering method in the material which has electronic conductivity. The method for manufacturing a nonaqueous electrolyte battery according to claim 6 , wherein crystalline silicon is used as a target used in the sputtering method.