• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    The present invention relates to an anode compartment for rechargeable lithium or sodium batteries comprising: a solid electrolyte; a collector deposited on the solid electrolyte; and a lithium metal or sodium metal active material which has been grown between the solid electrolyte and the collector to form with the collector a lithium metal or sodium metal electrode, in which the collector is in one amorphous alloy. It also relates to a method of manufacturing such an anode compartment and a battery comprising this anode compartment.
    公开号:FR3015118A1
    申请号:FR1362919
    申请日:2013-12-18
    公开日:2015-06-19
    发明作者:Philippe Stevens；Gwenaelle Toussaint；Laurent Puech；Philippe Vinatier
    申请人:Electricite de France SA；Centre National de la Recherche Scientifique CNRS；
    IPC主号:
    专利说明:

    [0001] FIELD OF THE INVENTION The present invention relates to the technical field of rechargeable lithium and sodium batteries and more particularly to an anode compartment for such batteries as well as to processes for their manufacture. STATE OF THE ART The relatively low specific energy density is today the main limitation for the use of rechargeable lithium or sodium batteries in portable equipment such as portable electronics or electric vehicles. This is largely related to the performance of the materials that make up the batteries. At present, the available negative electrode materials have a specific capacity of between 300 and 350 Ah / kg. The higher the specific capacity of a material, the higher the specific energy density can be increased. Lithium metal having a theoretical specific capacity greater than 3800 Ah / kg, its use as a material for negative electrodes seems promising. Unfortunately, this material used as an active material in a negative electrode has the unfortunate tendency to grow as dendrites during charge phases. By growing, these dendrites pass through the liquid electrolyte and can therefore cause a short circuit by electrically connecting the positive electrode to the negative electrode. In order to avoid the growth of lithium metal in the form of dendrites during charge phases, lithium-ion batteries use a negative electrode material in which the lithium ion can be inserted during the charge phase and from which it can to be released during the discharge phase. Graphite is an example. An illustration of the use of graphite as a negative electrode material is given in US5053297.
    [0002] Nevertheless, graphite has the disadvantage of having a very low specific capacity (theoretically 376 Ah / kg for LiC6 for example) to that of lithium metal. Alternatively, the lithium metal may be used in combination with a polymer electrolyte composed of a neutral matrix such as polyethylene oxide (also referred to as PEO) in which a lithium salt such as bis (trifluoromethanesulfonyl) imide of lithium (also referred to as LiTFSI) is dissolved.
    [0003] This is the case in lithium-metal-polymer batteries (LMP batteries). In order to limit the risk of growth of lithium metal in the form of dendrites, the thickness of the lithium metal is limited, generally between 30 and 100 [Inn, in the negative electrodes of the LMP batteries. Thus, the lithium metal is rolled in ribbon form on a sheet of polymer electrolyte to obtain an anode compartment whose payload density per unit area is relatively low, typically between 1 and 10 rnAh / cne. Moreover, in such a polymer electrolyte, the ionic conductivity of the electrolyte is obtained by adding the LiTFSI salt. The mobility of this salt, in particular the anion, in the neutral matrix generates a salt concentration gradient during the passage of an ionic current, in fact, the number of transport (that is to say the fraction of the current carried by the ion) for the cation is less than 1. This concentration gradient is even higher than the current density will be strong. However, the formation of lithium metal in the form of dendrites is favored by the strong gradients in concentration. A final solution to avoid the growth of lithium metal in the form of dendrite which will be described here is the use of a very hard solid electrolyte. The high hardness of these solid electrolytes has the advantage of preventing the formed dendrites from passing through the solid electrolyte and generating a short circuit. In the article - Lithium metal stability in batteries with block copolymer electrolytes "(in French: - The stability of lithium metal in batteries with electrolytes in block copolymer), D. Hallinan et al. have calculated that a polymer electrolyte with a hardness of about 6 GPa is needed to avoid dendrite formation (Journal of the Electrochemical Society, 160 (3) A464-A470 (2013).
    [0004] Ceramic materials such as Lisicon (Li super ionic conductor) or Nasicon (super ionic conductor Na), which can be used as solid electrolytes have a hardness of about 6 GPa. In addition, these ceramic materials do not depend on any salt dissolved in their matrix to exhibit ion conduction properties since they are intrinsically ion-conducting: the ionic conduction is obtained solely by cation transport through the structure crystal of these ceramic materials and the conduction of electrons is negligible. Therefore, their transport number is equal to 1, which further disadvantages the growth of lithium metal in the form of dendrites.
    [0005] The use of a ceramic electrolyte therefore opens the way to the use of a negative electrode with a much greater thickness because the problem of the formation of dendrites does not arise. Thus, a negative electrode with a much higher surface capacitance can be obtained. The combination of a negative electrode with a very high surface capacitance with a high capacitance positive electrode such as an air electrode (using oxygen from the air) or a sulfur electrode can therefore lead to obtaining a battery with a very high density of mass and volume energy. In such a battery, metal, for example steel, is deposited on the ceramic electrolyte, for example by sputtering, in a thin layer to form a current collector. Subsequently, the lithium metal is grown between the collector and the ceramic electrolyte. In such a battery with a very high density of mass and volume energy, the reduction of the cations during the charging phase occurs at the interface between the ceramic electrolyte and the active material lithium metal. Thus, the growth of lithium metal is made from this interface in a single dimension. Nevertheless, the lithium metal can grow in the form of a dense and uniform layer (see Figure 7) or in the form of a filamentous or porous deposit (see Figure 6). The inventors have observed that a stringy or porous lithium metal negative electrode exhibits a resistance that increases rapidly with the number of charge and discharge cycles compared to a dense and uniform lithium metal negative electrode. They attribute this increase to a decrease in the active surface of the negative electrode which is determined by the interface between the lithium metal and the solid electrolyte. The decrease of this surface causes that of the capacity of the negative electrode and the increase of the resistance thereof. When the lithium layer created during the charging phase is dense and uniform, there is no increase in the resistance of the negative electrode and this can be used for a number of charging and charging cycles. higher discharge.
    [0006] In addition, the inventors have observed that the growth of lithium in stringy or porous form (low density form) reduced the capacity of the negative electrode by making part of the lithium metal inaccessible during the discharge phase: this part of lithium metal is not oxidized. For example, the inventors analyzed a totally discharged negative electrode and observed that 30% of the lithium metal formed during the charging phase was not accessible during the discharge phase and was present in stringy or porous form. This is due to the fact that the lithium metal is no longer in effective contact with the solid electrolyte and therefore can not oxidize Li + cation during the discharge phase at the interface. On the same negative electrode, all the parts which were present in dense and uniform form with a good interface with the solid electrolyte were accessible during the discharge phase and could be completely consumed. In seeking a solution to this problem, the inventors have discovered that the use of an amorphous metal to form the current collector avoids the formation of low density lithium and only dense lithium is produced. The present invention is based on this discovery. Presentation of the invention Therefore, the present invention provides a solution to overcome the problems encountered in the prior art described above. For this, the present invention provides an anode compartment for rechargeable lithium or sodium batteries comprising: a solid electrolyte; a collector deposited on the solid electrolyte; and a lithium metal or sodium metal active material which has been grown between the solid electrolyte and the collector to form with the collector a lithium metal or sodium metal electrode, in which the collector is in one amorphous alloy. In such an anode compartment, the active material of lithium metal or sodium metal grows in dense form. Thus, the negative electrode formed by the collector and the active material has a high specific capacity between 10 and 500 nnAh / cne. Other optional and non-limiting features are as follows. The amorphous alloy preferably has a maximum relative elongation coefficient greater than 1.8%. The amorphous alloy advantageously contains less than 10% by number of Si, Sn or Ag atoms in total. The amorphous alloy is preferably CuxZri.x, with x ranging from 0.25 to 0.75.
    [0007] The collector may be in the form of a thin layer of thickness less than 1 [Inn. The solid electrolyte is advantageously made of a ceramic material. The present invention also provides a method for manufacturing an anode compartment for rechargeable lithium batteries comprising: - a solid electrolyte; an amorphous alloy collector; and - a lithium metal or sodium metal active material between the solid electrolyte and the collector; the method comprising the steps of: depositing an amorphous alloy on the solid electrolyte to form the collector; - Growth of a lithium metal or sodium metal active material between the solid electrolyte and the collector thus obtaining the anode compartment. The amorphous alloy can be deposited on the solid electrolyte by sputtering or ion beam sputtering. The amorphous alloy is preferably CuxZri.x, with x being between 0.25 and 0.75. The active material is advantageously grown between the solid electrolyte and the collector by electrochemical deposition.
    [0008] The solid electrolyte is advantageously made of a ceramic material. The invention also proposes a battery comprising an anode compartment as described above and a cathode. Drawings Other objectives, features and advantages will appear on reading the following illustrative description, with reference to the drawings given by way of nonlimiting example, among which: FIG. 1 is a schematic illustration of an anode compartment according to the invention without coating; - Figure 2 is a schematic illustration of an anode compartment according to the invention with coating; - Figure 3 is a schematic illustration of an anode compartment according to the invention without coating and comprising a housing; - Figure 4 is a schematic illustration of an anode compartment according to the invention with coating and comprising a housing; - Figure 5 is a diagram illustrating schematically the various steps of the method of manufacturing an anode compartment according to the invention, the optional steps being indicated in dashed lines; - Figure 6 is a photograph showing the state of the surface of a steel collector after a charging phase; and FIG. 7 is a photograph showing the asped of a lithium metal active material.
    [0009] Description With reference to FIGS. 1 to 4, an anode compartment for rechargeable lithium or sodium batteries according to the invention will be described below.
    [0010] This anode compartment 1 comprises a solid electrolyte 2, a collector 3 on the solid electrolyte 2, and an active material 4 made of lithium metal or sodium metal between the solid electrolyte 2 and the collector 3. The active ingredient 4 results from the growth of lithium metal or sodium metal between these two elements and form with the collector 3 a lithium metal electrode or sodium metal.
    [0011] The anode compartment 1 has its originality in that the collector 3 is an amorphous alloy. Indeed, as already indicated above, the inventors have discovered that such a collector prevented the growth of active ingredient in sparse form. Subsequently, the inventors wanted to identify the cause of this growth in the sparse form of the active ingredient in the collectors of the prior art. Thus, the inventors have observed that this growth of the lithium metal in sparse form occurs particularly where the collector, generally made of steel, deposited on the solid electrolyte, and under which the lithium metal grows, has cracks ( see Figure 6).
    [0012] The inventors assume that this growth in sparse form is due to the fact that in these zones of cracks, the lithium metal is not constrained and therefore tends to form in a more anarchic manner. To explain the appearance of cracks, the inventors propose the hypothesis according to which, during the growth of the lithium metal between the collector and the solid electrolyte, a voltage is created on the surface of the collector oriented collinearly therewith and leading to its break. An amorphous alloy, as opposed to a crystalline alloy, has an irregular arrangement of atoms at medium and great distances. The amorphous alloy collector 3 of the invention does not crack during the charging phase of a battery comprising the anode compartment, which makes it possible to prevent the growth of the active material in a sparse form (stringy or porous). It is able to deform in a reversible way (elastic deformation) for important constraints by compressing the active ingredient. Indeed, the maximum relative elongation coefficient (Ey) of an amorphous alloy, equal to the stress (Gy) divided by the Young's modulus (E), is higher than that of a crystalline metal or alloy. . The amorphous alloy chosen advantageously has a maximum relative elongation coefficient (Ey) greater than 1.8%.
    [0013] The amorphous alloy is preferably composed of metals that do not form an alloy with the lithium metal during an electrochemical deposition of lithium metal from the collector 3 in such an alloy. Thus, the amorphous alloy preferably contains in total less than 10% by weight of silicon, tin and silver atoms. Advantageously, the amorphous alloy is CuxZri.x, where x is between 0.25 and 0.75, preferably x is about 0.4. The collector 3 is in the form of a thin layer, preferably less than 1 [Inn. Thus the manifold 3 is flexible. The collector 3 is electrically connected to a flexible electronic conductor formed by a grid or a flexible metal sheet, preferably a flexible steel grid. This flexible metal grid covers at least a portion, preferably all, of the surface of the current collector. In order to improve the electrical contact between the current collector and the electronic conductor, a silver lacquer is preferably applied at their contact zone. The electronic conductor makes it possible to electrically connect the collector 3 to an element outside the anode compartment. The solid electrolyte 2 is made of an alkaline cation-conducting ceramic material, for example lithium or sodium, preferably lithium. Such lithium conductive ceramic materials are known, for example LIC-GC (for Lithium Ion Conducting Glass Ceramic from Ohara Inc. Japan). These are, for example, ceramics of the formula Lii.x (M, Ga, Al) x (Ge1.yTiy) 2.x (PO4) 3 where M represents one or more metals selected from Nd, Sm, Eu, Gd , Tb, Dy, Ho, Er, Tm and Yb, and where 0 <xs0.8 and 0sys1.0. Other materials of this type are also known in the literature, such as the LATP of the formula Li 1, Al x Ti 2 .x (PO 4) 3 and described in the article The effects of crystallization parameters on the ionic conductivity of a lithium aluminum germanium phosphate glass- ceramics "by JS Thokchom, and B. Kumar, in J. Power Sources, vol.195, p.2870, 2010, or the LLZ of formula Li2La3Zr2012 and described in the article - Fast Lithium Ion Conduction in Garnet-Type Li2La3Zr2012 "by R. Murugan, V. Thangadurai, and W. Weppner, in Angew. Chem. Int. Ed., 46 (2007), p. 7778.
    [0014] Sodium conductive ceramic materials are for example materials of formula Na1.xZr2SixP3,012 where Osxs3. They are described in particular in the US6485622 patent and in the article - Comparison of Different Synthesis Methods for Nasicon Cerannics "by N. Gasmi et al., J. of Sol-Gel Science and Technology 4 (3) (1995) p. 231-237, and known in the literature under the name Nasicon.
    [0015] The solid electrolyte 2 is preferably in the form of a membrane. Its thickness depends on its two other dimensions. The larger the surface of the membrane, the greater the thickness must be to resist mechanical stress. In addition, the electrical efficiency of a battery is partly governed by the specific resistance of the electrolyte, and this specific resistance R is expressed by the formula: R = (re) / A, where r denotes the resistivity of the electrolyte. electrolyte, the thickness of the membrane and the area of its surface. Thus, it will generally be sought to use, as far as possible, solid electrolytes of small thickness. The thickness of the membrane is advantageously between [Inn and 500 [Inn, preferably between 50 [Inn and 160 [Inn. These thicknesses are suitable for surfaces of greater than 1 nnnn2, preferably between 1 nnnn2 and 400 cnn2, still preferably between 4 cnn2 and 100 cnn2. The ceramic electrolyte 2 may be coated on at least one of its surfaces from which the active material will grow, especially when the latter is made of lithium metal. Examples of such coatings are Li3N, Li3P, LiI, LiBr, LiF or lithium / phosphonium oxynitride (LiPON) coatings (see, for example, X. Yu et al., J. Electrochem Soc. (1997) 144 (2), page 524) for conduction of lithium, and for example borosilicate glass with the addition of Na 2 O or of sodium and phosphorus oxynitride (NaPON) (see, for example, S. Chun et al. Proc 124th Meeting Electrochem Soc. (2008) 195) for sodium conduction. The active material 4 advantageously has a maximum thickness of between 50 [Inn and 5 mm, preferably between 100 [Inn and 500 [Inn, at the end of the charging phase.
    [0016] The anode compartment 1 may comprise a sealed and rigid housing 6 in which are the solid electrolyte 2, the collector 3 and the active material 2. The surface of the solid electrolyte 2 opposite to that facing the collector 3 forms at least in part an outer surface of the housing 6. The housing 6 may have any suitable form for integration into a battery, for example a cylindrical or parallelepiped shape. Thus, the housing 6 and the solid electrolyte 2 delimit a sealed interior space. The housing 6 may be made of synthetic resin, preferably a thermoset resin or cold hardened. The chemical nature of this resin is not critical provided that it does not disadvantageously interact with the components contained inside the anode compartment 1, and the elements of the battery in which the anode compartment 1 will be used. For example, epoxy resins, unsaturated polyesters, phenolics and polyimides are suitable. In this case, and advantageously, the collector 3 covers almost the entire face of the solid electrolyte 2 but not entirely, especially to prevent it from coming into contact with the walls of the sealed housing 6. Indeed, if the active material has a relatively large thickness at the end of the charging phase, and if the collector 3 is in contact with the inner walls of the housing 6, the collector 3 may deform and / or rupture as it moves away from the solid electrolyte 2 when the active material 4 increases during the charging phase.
    [0017] The extent of the collector 3 on the solid electrolyte 2 is chosen so that the distance between the edges of the collector 3 and the walls of the housing 6 is preferably at most equal to a few hundred microns. Still in this case, the anode compartment 1 can then also include a resilient element acting on the collector 3 so that it is forced towards the solid electrolyte 2 thus allowing the continuous compression of the active material 4. The element resilient may be one or more walls of the housing 6 itself or a block 7 of resilient material such as a foam. In the second case, the block of resilient material occupies all the space left free in the cassette when the active ingredient is completely consumed, that is to say at the end of the discharge phase.
    [0018] Block 7 made of resilient material is, for example, made of poly (chloroprene) foams (also known as Neoprene®, preferably neoprene foams sold under the name Bulatex®, in particular Bulatex C166 by the company Hutchinson). Sylomer® G, a polyether polyurethane foam sold by Plastiform's A battery comprising the anode compartment described above will be described below This battery comprises, in addition to the anode compartment, a positive electrode, optionally a liquid electrolyte.
    [0019] The positive electrode may be for example an air electrode or an electrode using sulfur. When the positive electrode is an air electrode, it is preferably a porous electron-conducting material. This porous material is for example a carbon black compound, a catalyst based on manganese oxide or cobalt, a hydrophobic binder such as HFP (hexafluoropropylene) or PTFE (polytetrafluoroethylene), and a current collector as a collector in the form of a nickel grid. An anion-conductive polymer may be added to the electrode as described in patent WO 2010/128242 A1, especially when the electrolyte is aqueous. This polymer has the function of preventing the carbonation of the aqueous electrolyte by the CO2 contained in the air. The hydrophobic binder has the dual function of producing a porous structure mechanically integrates from a powder whose electronic percolation is provided by contact between the carbon grains, and of being sufficiently hydrophobic to prevent the electrolyte from passing through the electrode. when it is liquid.
    [0020] This battery is for example a lithium-air or sodium-air or lithium-sulfur battery. Or any battery using a lithium metal or sodium metal anode With reference to FIG. 5, a process for the manufacture of an anode compartment as presented above is described below.
    [0021] This method comprises depositing an amorphous alloy on the solid electrolyte to form the collector and the growth of a lithium metal or sodium metal active material between the solid electrolyte and the collector thereby obtaining the anode compartment. The amorphous alloy can be deposited on the solid electrolyte by sputtering or ion beam sputtering.
    [0022] In the case of sputtering, the material of the target used may be directly the alloy that is desired to be deposited on the solid electrolyte, the material may be crystalline or already amorphous. In a variant, several targets may be used whose maximum number is the number of metal elements that make up the amorphous alloy that is to be deposited on the solid electrolyte. In the case where the number of targets is less than the number of metal elements making up the amorphous alloy, at least one of the targets is an alloy. The definition of metal element is understood to include all transition chemical elements as well as steel. For example, the target material is an amorphous or crystalline CuZr alloy. Another example, two targets are used, one in Cu and the other in Zr. The amorphous alloy is deposited on the solid electrolyte to a thickness of less than 2 [Inn, preferably between 200 and 400 nm. The growth of the active material between the solid electrolyte and the collector can be carried out as follows. The face of the solid electrolyte not facing the collector is brought into contact, at least in part, with a liquid electrolyte containing the alkali metal cations which will form the active material. A reducing potential is then applied between the collector and a positive electrode immersed in the liquid electrolyte containing the alkali metal cations. The reducing potential is maintained between the collector and the positive electrode for a time sufficient for the active material to grow between the solid electrolyte and the collector to a desired thickness. The liquid electrolyte may for example be LiOH for a lithium metal active material, or NaOH for a sodium metal active material. The concentration of LiOH or NaOH is preferably at least equal to 1 mol / L and can go to saturation or even beyond. The positive electrode used for the growth of lithium metal or sodium metal may be a stable metal or alloy electrode in the liquid electrolyte used and the ion oxidation potentials of the liquid electrolyte.
    [0023] The applied reduction potential is preferably maintained at a value between -3.1 V and -3.6 V relative to a reference electrode Hg / HgO / 1M KOH in the liquid electrolyte. This potential must indeed be sufficiently high in absolute value for the alkali ion to be reduced to alkali metal. Preferably, the intensity of the current is between 0.1 mAh / cm 2 and 100 nnAh / cnn2.
    [0024] In the case where a coating is provided on the solid electrolyte, it is deposited on the solid electrolyte before the deposition of the amorphous alloy by sputtering, for example. In the case where the anode compartment is in the form of a housing, the housing is cast around the assembly constituted by the solid electrolyte, optionally the coating, the active material, the collector and possibly the block made of resilient material. .10
    权利要求:
    Claims (12)
    [0001]
    REVENDICATIONS1. Anode compartment for rechargeable lithium or sodium batteries comprising: - a solid electrolyte; a collector deposited on the solid electrolyte; and a lithium metal or sodium metal active material which has been grown between the solid electrolyte and the collector to form with the collector a lithium metal or sodium metal electrode, in which the collector is in one amorphous alloy.
    [0002]
    Anode compartment according to claim 1, wherein the amorphous alloy has a maximum relative elongation coefficient greater than 1.8%
    [0003]
    Anode compartment according to claim 1 or claim 2, wherein the amorphous alloy contains in total less than 10% by number of Si, Sn and Ag atoms.
    [0004]
    4. Anode compartment according to one of claims 1 to 3, wherein the amorphous alloy is CuxZri_x, with x between 0.25 and 0.75.
    [0005]
    5. Anode compartment according to one of claims 1 to 4, wherein the collector is in the form of a thin layer less than 1 μm thick.
    [0006]
    6. Anode compartment according to one of claims 1 to 5, wherein the solid electrolyte is a ceramic material.
    [0007]
    7. Process for the manufacture of an anode compartment for rechargeable lithium or sodium batteries comprising: a solid electrolyte; an amorphous alloy collector; and a lithium metal or sodium metal active material between the solid electrolyte and the collector, the method comprising the steps of: depositing an amorphous alloy on the solid electrolyte to form the collector; - Growth of a lithium metal or sodium metal active material between the solid electrolyte and the collector thus obtaining the anode compartment.
    [0008]
    8. The method of claim 7, wherein the amorphous alloy is deposited on the solid electrolyte by sputtering or ion beam sputtering.
    [0009]
    9. The method of claim 7 or claim 8, wherein the amorphous alloy is CuxZri.x, with x ranging from 0.25 to 0.75.
    [0010]
    10. Method according to one of claims 7 to 9, wherein the active material is grown between the solid electrolyte and the collector by electrochemical deposition.
    [0011]
    11. Method according to one of claims 7 to 10, wherein the solid electrolyte is a ceramic material.
    [0012]
    12. Battery comprising a cathode, a liquid electrolyte and an anode compartment according to one of claims 1 to 6.20
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    优先权:
    申请号 | 申请日 | 专利标题
    FR1362919A|FR3015118B1|2013-12-18|2013-12-18|ANODIC COMPARTMENT WITH AMORPHOUS ALLOY MANIFOLD|FR1362919A| FR3015118B1|2013-12-18|2013-12-18|ANODIC COMPARTMENT WITH AMORPHOUS ALLOY MANIFOLD|
    PL14828226T| PL3084866T3|2013-12-18|2014-12-17|Anode compartment having an amorphous-alloy collector|
    KR1020167019050A| KR101905777B1|2013-12-18|2014-12-17|Anode Compartment Having an Amorphous-Alloy Collector|
    DK14828226.2T| DK3084866T3|2013-12-18|2014-12-17|ANODE CHAMBER WITH COLLECTOR OF AN AMORF ALLOY|
    ES14828226T| ES2708995T3|2013-12-18|2014-12-17|Anodic compartment with amorphous alloy collector|
    US15/105,392| US10177368B2|2013-12-18|2014-12-17|Anode compartment with a collector made of amorphous-alloy|
    PCT/FR2014/053380| WO2015092267A1|2013-12-18|2014-12-17|Anode compartment having an amorphous-alloy collector|
    JP2016541437A| JP6395839B2|2013-12-18|2014-12-17|Anode compartment with collector made of amorphous alloy|
    KR1020187018448A| KR20180077320A|2013-12-18|2014-12-17|Anode Compartment Having an Amorphous-Alloy Collector|
    EP14828226.2A| EP3084866B1|2013-12-18|2014-12-17|Anode compartment having an amorphous-alloy collector|
    HUE14828226A| HUE041360T2|2013-12-18|2014-12-17|Anode compartment having an amorphous-alloy collector|
    CN201480071294.5A| CN106063007B|2013-12-18|2014-12-17|Anode chamber with collector made of amorphous alloy|
    JP2018111264A| JP2018163885A|2013-12-18|2018-06-11|Anode compartment with collector made of amorphous alloy|
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