Patent Application
20120134871
The technical field to which relates the invention is that of hydridable alloys for a negative electrode of an accumulator with an alkaline electrolyte of the nickel-metal hydride type as well as that of methods for preparing such alloys.
Applications such as electric vehicles (EV for Electric Vehicle), hybrid vehicles (HEV for Hybrid Electric Vehicle), rechargeable hybrid vehicles (PHEV for Plug-in Hybrid Electric Vehicle), safety lighting (ELU for Emergency Lighting Unit) or PhotoVoltaic applications (PV) require increasing needs in terms of bulk energy. An accumulator with an alkaline electrolyte of the nickel metal hydride (Ni-MH) type comprising a negative electrode based on a hydridable alloy of the type AB5 (wherein A represents one or more elements forming stable hydrides under normal conditions of temperature and of pressure, such as for example rare earths, and B one or more elements, for which the hydrides are unstable under the same conditions, such as for example nickel) and a positive electrode based on nickel hydroxide does not satisfactorily meet the development of this energy need.
In an Ni-MH accumulator, the initial capacity is limited by construction (or design) by the capacity of the positive electrode. Thus, increasing the initial capacity of the accumulator requires an increase in the capacity of the positive electrode, therefore of its active material volume, since optimization of the technology of this electrode is at a development stage where the performances are now equivalent to the theoretical yields. Further, the lifetime of an Ni-MH accumulator is limited by the corrosion of the alloy and its consequences, i.e. the reduction in the capacity of the negative electrode and the drying of the bundle consecutive to consumption of water by the corrosion reaction inducing an increase in the impedance of the accumulator. The increase in the initial capacity of the accumulator is therefore accomplished to the detriment of its lifetime since this leads to a limitation either of the volume of the electrolyte, or of that of the alloy. Thus, an increase in the initial capacity of the accumulator can only be obtained to the detriment of its lifetime. Conversely, it is possible to achieve an increase in the lifetime of the accumulator but to the detriment of its initial capacity. Research work is therefore conducted in order to obtain an active material of the negative electrode providing both high capacity and a long lifetime.
In order to increase the bulk capacity, novel negative electrode materials have been contemplated. Mention may be made of alloy families with a stoichiometry of the AB2 type. However, although their initial capacity is much greater than that of a AB5 stoichiometry alloy, their power and lifetime are considerably reduced. Recently, the use of an alloy of composition (R, Mg)Bx was proposed, wherein R represents one or more elements selected from rare earths, yttrium, Zr and Ti and B represents the nickel element partly substituted with other elements such as Co, Mn, Al or Fe, with x comprised between 3 and 4. These alloys may consist of one or more crystalline phases, such as:
the phase of composition AB5 crystallizing in the hexagonal system of the CaCu5 type;
the phases of composition AB2, so-called Laves phases, either crystallizing in the cubic system: a so-called “C15” phase of the MgCu2 type, or in the hexagonal system: so-called “C14” phase of the MgZn2 type or so-called “C36” phase of the MgNi2 type;
the phases of composition AB3 either crystallizing in the hexagonal system (H—CeNi3 type) or in the rhombohedral system (R—PuNi3 type);
the phases of composition A2B7 either crystallizing in the hexagonal system (H—Ce2Ni7 type), or in the rhombohedral system (R—Gd2Co7 type);
the phases of composition A5B19 either crystallizing in the hexagonal system (H—Pr5Co19 type), or in the rhombohedral system (R—Ce5Co19 type);
the phase of composition AB4.
Each of these crystalline phases, except for the phases AB5 and AB2 may be considered as consisting of one or more patterns of the type C of formula AB5 associated with a pattern of type L of composition A2B4 corresponding to 2 formulae AB2.
For example:
a crystalline phase of composition AB3 consists of a pattern of the type C and of a pattern of the type L;
a crystalline phase of composition A2B7 consists of a pattern of type C and of two consecutive patterns of type L;
a crystalline phase of composition A5B19 consists of a pattern of type C and of three consecutive patterns of type L;
a crystalline phase of composition AB4 consists of a pattern of type C and of four consecutive patterns of type L.
The following documents describe hydridable alloys having a good lifetime under charging-discharging cycle conditions.
Document JP 2001-316744 describes a hydridable alloy of formula Ln1-xMgx(Ni1-yTy)z wherein:
0.05≦x<0.20, 0≦y≦0.5 and 2.8≦z≦3.9.
Document JP 2002-069554 describes a hydridable alloy of formula R1-aMgaNibCOcMd wherein
R represents at least two elements selected from rare earths and Y;
M represents at least one element selected from Mn, Fe, V, Cr, Nb, Al, Ga, Zn, Sn, Cu, Si, P and B; 0.15<a<0.35; 0≦c≦1.5; 0≦d≦0.2 and 2.9<b+c+d<3.5. It is stated that crystalline phases of the AB2, AB3, A2B7, AB5, Mg2Ni and MgNi2 type may be obtained.
Document EP-A-1 026 764 describes a hydridable alloy of formula AMx wherein A may be a rare earth, optionally substituted with magnesium; and M may be selected from Cr, Mn, Fe, Co and Ni. x is comprised between 2.7 and 3.8. The average atomic radius r of the atoms of the alloy is comprised between 1.36 and 1.39 Å. x and r satisfy the relationship 1.42≦0.017x+r≦1.44.
Document U.S. Pat. No. 6,214,492 describes a hydridable alloy comprising a crystalline phase comprising at least one unit cell which is a stack of at least one structure of the A2B4 type and of at least one structure of AB5 type, the ratio between the number of structures of the A2B4 type and the number of structures of AB5 is comprised between 0.5 and 1. Preferably the unit cell is an ordered stack of the LCLCC type, wherein L represents the structure of type A2B4 and C represents a structure of type AB5. The crystalline phase comprises a repetition of stacks of the LCLCC type.
Document US 2004/0134569 describes a hydridable alloy of formula Ln1-xMgxNiy-aAla wherein Ln is at least one rare earth; 0.05≦x<0.20; 2.8≦y≦3.9 and 0.10≦a≦0.25.
Document US 2004/0146782 describes the hydridable alloy of formula Ln1-xMgxNiy-aMa wherein Ln is at least one rare earth, M is at least one element selected from Al, V, Nb, Ta, Cr, Mo, Mn, Fe, Co, Ga, Zn, Sn, In, Cu, Si et P and 0.05≦x<0.20. 2.8≦y≦3.9 and 0.10≦a≦0.50.
Document US 2005/0100789 describes a negative electrode of a nickel metal hydride accumulator, comprising:
a) a hydridable alloy of formula Ln1-xMgxNiyAlzMa wherein Ln is at least one rare earth, M is an element other than a rare earth, Mg, Ni or Al, and 0.10≦x<0.30. 2.8≦y≦3.6. 0≦z≦0.30 and 3.0≦y+z+a≦3.6 and
b) an amount of manganese of less than 1% based on the weight of the hydridable alloy. This document describes that an alloy which crystallizes in the AB5 structure is easily oxidized. Therefore, with it is not possible to obtain a good lifetime of the electrode during cycling.
Documents US 2005/0175896 and US 2005/0164083 describe a hydridable alloy comprising at least one rare earth, magnesium, nickel and aluminium and mainly crystallizing in a structure of the Ce2Ni7 type.
Document EP-A-2 096 691 describes a hydridable alloy of formula Ln1-xMgxNiy-a-bAlaMb wherein Ln represents at least two elements including lanthanum, M represents at least one element selected from Co, Mn and Zn, 0.1≦x≦0.20, 3.6≦y≦3.9, 0.1≦a≦0.2 and 0≦b≦0.1. This alloy comprises in majority a crystalline phase of the A5B19 type and may comprise A2B7 and/or AB5 phases. The equilibrium hydrogen pressure at 40° C. is comprised between 0.3 and 1.7 bars for an absorbed hydrogen amount equal to 0.5 H/M.
Document US 2008/0085209 describes a hydridable alloy of formula R1-uMguNit-vMv wherein R represents at least one element selected from La, Ce, Nd and Pr; M represents one or more elements selected from Mn, Fe, Al, Co, Cu, Zr, Sn and M does not contain Cr; 0≦u≦0.25, v≦0.5 and 3.5≦t≦4.5. This alloy comprises in majority a crystalline phase of the A5B19 type and optionally the A2B7 and/or AB5 phases. The equilibrium hydrogen pressure at 40° C. is less than 1.5 bars for an amount of absorbed hydrogen amount of less than 1%.
Document JP 2010-073424 describes a hydridable alloy containing a rare earth, magnesium and nickel. It comprises a stack of crystalline phases crystallizing in the AB3, A2B7, A5B19, AB4 and AB5 systems. The phases AB3, A2B7, A5B19, AB4 each consist of a stack of a pattern of the A2B4 type with n patterns of the AB5 type, n ranging from 1 to 4. The stacking of the crystalline phases is carried out in an ordered way, i.e., with a gradual variation of the parameter n, therefore of the number of patterns of the AB5 type in the direction of the stacking The following stacking order is indicated AB3, A2B7, A5B19, AB4, i.e. a B/A ratio of 3; 3,5; 3,8 and 4 respectively. This gradual increase in the B/A ratio indicates a gradual increase in the amount of nickel based on the total amount of rare earths and of magnesium in the direction of the stacking The number n of patterns of the AB5 type gradually increases in the direction of the stacking
Document JP 09-194971 describes a hydridable alloy of formula R2(Ni7-x-y-zMnxAyBz)n wherein R represents at least one rare earth, A represents at least one element selected from Co, Cr, Fe, Al, Zr, W, Mo, Ti; and B represents at least one element selected from Cu, Nb, V; 0.3≦x≦1.5; 0≦y≦1.0; 0≦z≦1.0; y+z≦1.0 and 0.96≦n≦1.1. This alloy comprises a crystalline phase of the hexagonal Ce2Ni7 type.
Document EP-A-0 783 040 describes a hydridable alloy of formula (R1-xLx)(Ni1-yMy)z wherein R represents La, Ce, Pr or Nd, M represents Co, Al, Mn, Fe, Cu, Zr, Ti, Mo, Si, V, Cr, Nb, Hf, Ta, W, B or C; with 0.05≦x≦0.4; 0≦y≦0.5 and 3.0≦z≦4.5.
Document JP 2004-115870 describes a hydridable alloy of formula Ln1-xMgxNiyMz wherein Ln represents at least one element selected from Y, Sc and rare earths; M represents one or more elements selected from Co, Mn, Al, Fe, V, Cr, Nb, Ga, Zn, Sn, Cu, Si, P or B; 0.1≦x≦0.5; 2.5≦y≦3.5; 0≦z≦0.5 and 3.0≦y+z≦3.5.
An electrode active material is sought which has a high initial mass capacity as well as a good lifetime during cycling. Such an active material is characterized by an initial mass capacity of at least 310 mAh/g and with a capacity degradation of less than 15% after 100 cycles. A method for preparing such an active material is also sought.
For this purpose, the object of the invention is a hydridable alloy, of formula R1-x-yMgxMyNis-aBa wherein
R is selected from the group consisting in rare earths, yttrium and a mixture thereof;
M represents Zr and/or Ti;
B is selected from the group consisting Mn, Al, Co, Fe and a mixture thereof;
0.1≦x≦0.4; 0≦y<0.1; 3<s<4.5 and 0≦a<1;
wherein at least 5% of the volume consists of a stack of sequences of a pattern of the A2B4 type and n patterns of the CaCu5 type randomly distributed along a direction, n being an integer comprised between 1 and 10 and representing the number of patterns of the CaCu5 type per pattern of the A2B4 type.
According to an embodiment, the volume consisting of the stack of sequences of a pattern of the A2B4 type and of n patterns of the CaCu5 type randomly distributed, represents at least 10% of the volume of the alloy, preferably at least 20%.
According to an embodiment, the volume consisting of the stack of sequences of a pattern of the A2B4 type and of n patterns of the CaCu5 type randomly distributed, represents less than 90% of the volume of the alloy, preferably less than 70%.
According to an embodiment, n is less than or equal to 8, preferably less than or equal to 6, still preferably less than or equal to 4.
According to an embodiment x is comprised between 0.1 and 0.3, preferably between 0.15 and 0.25.
According to an embodiment, a is less than 0.3, preferably less than 0.15.
According to an embodiment, s is comprised between 3 and 4, preferably between 3.5 and 4.
According to an embodiment, the alloy comprises Nd and Pr, and the R″/R′ molar ratio is less than 0.5, R″ designating the sum of the number of moles of Nd and of Pr and R′ designating the sum of the numbers of moles of rare earths Y, Zr and Ti.
The invention also relates to a method for making a hydridable alloy comprising the steps:
According to an embodiment, step c) is achieved by the flash sintering technique.
According to an embodiment, the compound of step a) has the formula R′Niy with y comprised between 4 and 5, R′ designating the sum of the numbers of moles of rare earths, Y, Zr and Ti.
According to an embodiment, the compression of step c) is carried out under a pressure comprised between 40 and 80 MPa.
According to an embodiment, step c) is carried out at a temperature comprised between 700 and 900° C.
According to an embodiment, the hydridable alloy has the formula R1-x-yMgxMyNis-aBa wherein
R is selected from the group consisting in rare earths, yttrium and a mixture thereof;
M represents Zr and/or Ti;
B is selected from the group consisting in Mn, Al, Co, Fe and a mixture thereof;
0.1<x<0.4; 0≦y<0.1; 3<s<4.5 and 0≦a<1.
This method may be used for making the alloy according to the invention.
This alloy may be used as a negative electrode active material of an alkaline accumulator of the nickel metal hydride type. The invention therefore also relates to an electrode comprising said alloy as well as to an accumulator of the nickel metal hydride type comprising this electrode.
According to an embodiment, the electrode comprises from 0.4 to 1% by weight of yttrium oxide and/or from 1 to 2% by weight of manganese oxide.
The alloy according to the invention has the formula R1-x-yMgxMyNis-aBa wherein:
R is selected from the group consisting in rare earths, yttrium and a mixture thereof;
M represents Zr and/or Ti;
B is selected from the group consisting in Mn, Al, Co, Fe and a mixture thereof;
0.1<x<0.4; 0≦y<0.1; 3<s<4.5 and 0≦a<1.
In an embodiment, R comprises La, Nd, Pr and Sm.
In an embodiment, R consists of La, Nd, Pr and Sm; B is one or more elements selected from Mn, Al and Co; x is comprised between 0.1 and 0.3; s is comprised between 3 and 4 and a is less than 0.5. The stoichiometry is greater than AB3 since this corresponds to an AB5 pattern for an A2B4 pattern. The upper limit corresponds to the AB4 phase, which was detected by Ozaki [T. Ozaki and al., J. Alloys and Comp., Vol. 446-447, pp 620-624, 2007] and which corresponds to 4 patterns of the AB5 type for one pattern of the A2B4 type. Moreover, the Mg level is greater than 0.1 in order to obtain a sufficient capacity. An increase in the Mg level beyond 0.3 tends to promote a mixture of AB3 (or AB2) and AB5 phases to the detriment of the other phases of the An+2B5n+4 type. With partial substitutions of Ni with Mn and Al, it is possible to lower the equilibrium hydrogen pressure while Co and Al promote the stability of the alloy during cycling.
In an embodiment, R consists of La, Nd, Pr and Sm; the R″/R′ ratio is less than 0.5; R″ designating the sum of the numbers of moles of Nd and of Pr; B is one or more elements selected from Al and Co; x is comprised between 0.1 and 0.3; s is comprised between 3.5 and 4; and a is less than 0.5. For values of s of less than 3.5, the AB3 phase proportion, which decomposes during cycling, increases and causes accelerated reduction of the capacity during the cycling. In order to avoid this, the use of stoichiometries greater than or equal to 3.5 and the use of aluminium and cobalt which promote cycling stability are preferred, rather than manganese as substituants for nickel. However, these modifications cause an increase in the equilibrium hydrogen pressure. In order to maintain this pressure within acceptable limits for the application to Ni-MH batteries, the Nd+Pr level is reduced to the benefit of La.
In an embodiment, R consists of La, Nd, Pr, Sm; the R″/R′ ratio is less than 0.5; B is one or more elements selected from Al and Co; x is comprised between 0.15 and 0.25; s is comprised between 3.5 and 4; and a is less than 0.3. Aluminium and cobalt have the effect of improving the cycling stability of the alloy. However, the capacity of the alloy decreases when their level increases beyond a threshold which depends on the magnesium level. This decrease in capacity is limited if the magnesium level is restricted between 0.15 and 0.25 and if the Al+Co level is less than 0.3.
In an embodiment, R consists of La, Nd, Pr, Sm; the R″/R′ ratio is less than 0.5; B is Al; x is comprised between 0.15 and 0.25; s is comprised between 3.5 and 4, and a is less than 0.15. As cobalt is an expensive and speculative element, it seems to be preferable to use an alloy without cobalt and only retain aluminium as a substituent for nickel. However, an aluminium level of more than 0.15 causes a decrease in the equilibrium pressure and therefore in the voltage of the element.
The composition of the alloy may be determined by elementary chemical analysis by the plasma emission spectroscopy method (ICP for Inductively Coupled Plasma), atomic spectroscopy or X-ray fluorescence spectroscopy.
The alloy comprises one or more crystalline phases selected from:
a) the phase AB5 crystallizing in the hexagonal system of the CaCu5 type;
b) the phases AB2, so-called Laves phases, either crystallizing in the cubic system: a so-called “C15” phase of the MgCu2 type, or in the hexagonal system; so-called “C14” phase of the MgZn2 type or “C36” phase of the MgNi2 type.
c) the phases of the Rm+1MgNi5m+4 type consisting of a periodic stack of sequences including m C patterns (identical with the lattice cell of the CaCu5 type structure) and of one pattern L (a pattern forming AB2 Laves phases), with hexagonal (H) or rhombohedral (R) symmetry with m ranging from 1 to 10.
m=1 corresponds to the AB3 phases either crystallizing in the hexagonal system (H—CeNi3 type), or in the rhombohedral system (R—PuNi3 type);
m=2 corresponds to the A2B7 phases either crystallizing in the hexagonal system (H—Ce2Ni7 type), or in the rhombohedral system (R—Gd2CO7 type);
m=3 corresponds to the A5B19 phases either crystallizing in the hexagonal system (H—Pr5Co19 type), or in the rhombohedral system (R—Ce5Co19 type);
m=4 corresponds to the phase of composition AB4.
These crystalline phases may be detected by analyzing an X-ray diffraction diagram.
At least 5% by volume of the alloy consists of a so-called ‘crystalline phase with random stacking’, characterized by a stacking of sequences of a pattern of the A2B4 type and of n patterns of the CaCu5 type randomly distributed along a direction, n being an integer comprised between 1 and 10 and representing the number of patterns of the CaCu5 type per pattern of A2B4 type.
By “random variation” is meant the variation in which the value assumed by the parameter n for a given sequence is independent of the values assumed by this parameter in adjacent sequences. The so-called ‘random stacking crystalline’ structure may be observed in high resolution transmission electron microscopy (HRTEM). This structure will be better understood by referring to the examples illustrated in
According to an embodiment, n varies randomly and not periodically.
According to an embodiment, the value of n in the different sequences is less than or equal to 8, preferably less than or equal to 6, still preferably less than or equal to 4.
According to an embodiment, the volume of said ‘random stacking crystalline’ phase is greater than 10%, still preferably greater than 20% and less than 70% based on the alloy.
According to an embodiment, the alloy has a hydrogen absorption capacity greater than 1% by mass, preferably greater than 1.3%, still preferably greater than 1.45%.
According to an embodiment, the alloy has a hydrogen equilibrium pressure comprised between 0.01 and 5 bars at 40° C. for a hydrogen mass concentration in the alloy of 0.5%. The capacity of hydrogen absorption by the alloy and the equilibrium pressure with hydrogen for a hydrogen mass concentration in the alloy of 0.5% may be determined from an isothermal pressure-composition curve representing the dihydrogen pressure in equilibrium with a hydrogen concentration inserted into the alloy (in % by mass or by moles of H inserted per mole of metal). The H/Metal ratio is the ratio between the number of moles of hydrogen atoms inserted into the alloy and the number of moles of metal atoms of the alloy. By “Metal” is meant the whole of the metals contained in the alloy, i.e. R, Mg, M, Ni and B.
The curve of
In a second portion, the curve has the shape of a slightly tilted plateau. The onset of this plateau marks the onset of the formation of the hydride (in the hydride, atomic hydrogen occupies the insertion sites of the alloy in an ordered way). During the plateau phase, atomic hydrogen gradually occupies all the insertion sites of the alloy. The end of the plateau corresponds to the situation in which practically all the insertion sites of the alloy are occupied by hydrogen.
In a third portion, the hydrogen pressure again increases rapidly with the hydrogen concentration and the amount of hydrogen which the alloy may still insert does not increase very much. The alloy is then only found in the form of the hydride in which excess atomic hydrogen is inserted in a disordered way. Desorption of hydrogen occurs at a plateau pressure below the absorption pressure.
It is possible to determine on the axis of the abscissas of the PCT curve, the position of the H/metal ratio equal to 0.5 and to infer therefrom the value of the equilibrium pressure by reading the ordinate of the corresponding point of the desorption curve. It is also possible to determine the position of the axis of the abscissas of the PCT curve corresponding to a hydrogen mass concentration of 0.5%, by knowing the 1 g molar mass of atomic hydrogen and the molar mass of the alloy used. The value of the equilibrium pressure is inferred therefrom by reading the ordinate of the corresponding point.
The hydrogen plateau pressure is not inherent to the composition of the hydridable alloy but to the composition of the phase which absorbs hydrogen. Now, for a same alloy composition, different elaboration methods, notably different heat treatments, may lead to obtaining a single phase alloy or a multiphase alloy, none of the phases of which having a composition identical with that of the alloy.
In an embodiment, the alloy has an equilibrium pressure with hydrogen H2 at 40° C. for an atomic hydrogen mass concentration in the alloy of 0.5%, comprised between 0.01 and 5 bars, preferably between 0.01 and 1 bar, still preferably between 0.05 and 0.7 bars. It is necessary to adapt the conditions for synthesis of the alloy in a range of temperatures comprised between 700 and 900° C. under a pressure comprised between 40 and 80 MPa according to its composition in order to obtain the desired characteristics.
According to a preferred embodiment, the maximum hydrogen mass concentration in the alloy under pressure of 10 bars is greater than 1.3%, preferably greater than 1.45%. It is necessary to adapt the conditions for synthesis of the alloy in a range of temperatures comprised between 700 and 900° C. under a pressure comprised between 40 and 80 MPa according to its composition in order to obtain the desired characteristics.
The invention also relates to a method for preparing a hydridable alloy with a fast sintering method. This manufacturing method comprises the steps:
Step c) may be carried out by using the rapid sintering technique (SPS Spark Plasma Sintering), which is also known under the acronym of FAST (Field Activated Sintering Technique). By simultaneous application of a compression force and of a square-wave shaped DC current of great intensity, this technique allows complete sintering of powders within only a few minutes. A mixture is milled, comprising Mg2Ni and a compound comprising nickel and one or more elements selected from the group consisting in rare earths and yttrium. It is optionally possible to add to the mixture, titanium and/or zirconium as well as one or more elements selected from Mn, Al, Co, Fe. The mixture is placed between an anvil and a piston. The mixture is compressed under a force preferably comprised between 40 and 80 MPa and heated by the Joule effect, which causes sintering. Temperatures comprised between 750 and 1,000° C. may be obtained.
It was discovered that the structure of the ‘random stacking crystalline’ phase of the alloy according to the invention was able to be obtained by applying the method as described to a mixture comprising nickel and one or more elements selected from the group consisting in rare earths and yttrium.
The invention also relates to an anode (negative electrode) comprising the alloy as an electrochemically active material. The anode is made by pasting an electrically conducting support with a paste consisting of an aqueous mixture of the alloy according to the invention with additives and optionally with conductive agents.
The support may be of the foam, felt, planar or three-dimensional perforated sheet type, in nickel or in nickel-plated steel.
The additives are intended to facilitate application or the performances of the anode. They may be thickeners such as carboxymethylcellulose (CMC), hydroxypropylmethylcellulose (HPMC), polyacrylic acid (PAAc), poly(ethylene oxide) (PEO). They may also be binders such as copolymers of butadiene-styrene (SBR), polystyrene acrylate (PSA), polytetrafluoroethylene (PTFE). They may also be polymeric fibers such as polyamide, polypropylene, polyethylene, etc., for improving the mechanical properties of the electrode.
The conductive agents may be nickel powder, carbon powder or fibers, nanotubes.
The alloy may be mixed with an yttrium compound in order to increase the capacity of the anode. In particular, this effect arises in the case of discharges with a strong current (discharges under 5C rating conditions). The mixture of the alloy with an yttrium compound also has the effect of increasing the cycling lifetime of the anode.
The yttrium compound is selected from a non-exhaustive list comprising an yttrium oxide such as Y2O3, and yttrium hydroxide such as Y(OH)3 or an yttrium salt. Preferably the yttrium compound is the yttrium oxide Y2O3.
The yttrium compound is mixed with the alloy in such a proportion that the yttrium mass represents from 0.1 to 2% of the mass of the alloy, preferably from 0.2 to 1% of the mass of the alloy, preferably from 0.2 to 0.7% of the mass of the alloy.
According to a preferred embodiment, the alloy is mixed with a compound based on manganese selected from a non-exhaustive list comprising oxides such as MnO, MnO2, or a hydroxide or salt based on manganese. Preferably, the manganese-based compound is the oxide MnO. The mixture of the alloy with a manganese compound has the effect of preventing or delaying the occurrence of micro short-circuits ascribed to cobalt deposits from the positive electrode or from the negative electrode, in the separator during the cycling of the accumulator. These micro short-circuits actually generate exacerbated self-discharge which is expressed by an acceleration in the reduction of the restored capacity during discharge. The mass proportion of manganese in the negative electrode is comprised between 1.5 and 2.5% of the hydridable alloy mass.
The invention also relates to an accumulator with an alkaline electrolyte comprising at least one anode according to the invention, at least one cathode (positive electrode) in nickel, at least one separator and one alkaline electrolyte.
The cathode consists of the cathode active mass deposited on a support which may be a sintered support, a nickel foam, a planar or three-dimensional perforated sheet in nickel or in nickel-plated steel.
The cathode active mass comprises the cathode active material and additives intended to facilitate its application or its performances. The cathode active material is a nickel hydroxide Ni(OH)2 which may be partly substituted with Co, Mg and Zn. This hydroxide may be partly oxidized and may be coated with a surface layer based on cobalt compounds.
Among the additives, mention may be made, without this list being exhaustive, of carboxymethylcellulose (CMC) hydroxypropylmethylcellulose (HPMC), hydroxypropylcellulose (HPC), hydroxyethylcellulose (HEC), polyacrylic acid (PAAc), polystyrene maleic anhydrides (SMA), copolymers of butadiene-styrene (SBR), optionally carboxylated, a copolymer of acrylonitrile and butadiene (NBR), a copolymer of styrene, ethylene, butylene and styrene (SEBS), a terpolymer of styrene, of butadiene and of vinylpyridine (SBVR), polystyrene acrylate (PSA), polytetrafluoroethylene (PTFE), a fluorinated copolymer of ethylene and propylene (FEP), polyhexafluoropropylene (PPHF), ethylvinyl alcohol (EVA), zinc oxide ZnO, fibers (Ni, C, polymers), powders of cobalt-based compounds such as Co, Co(OH)2, CoO, LixCoO2, HxCoO2, NaxCoO2, as well as additives intended to improve the charging efficiency such as Y2O3, Yb2O3 or Nb2O5.
The separator generally consists of polyolefin (for example polypropylene) fibers or of non-woven porous polyamide.
The electrolyte is a concentrated alkaline aqueous solution comprising at least one hydroxide (KOH, NaOH, LiOH), in a concentration generally of the order of several times normality.
Conventionally, the pastes are prepared for electrodes, the electrodes are made and then at least one cathode, separator and an anode are superposed in order to form the electrochemical bundle. The electrochemical bundle is introduced into a container cup and is impregnated with the aqueous alkaline electrolyte. The accumulator is then closed.
The invention relates to any format of accumulators: a prismatic format (planar electrodes) or a cylindrical format (spiral or concentric electrodes).
The accumulator of the Ni-MH type according to the invention may be of the open (either open or half-open) type or of the sealed type.
The accumulator according to the invention is particularly well adapted as a source of energy for an electric vehicle or a portable appliance.
Other features and advantages of the present invention will become apparent upon reading the examples.
An alloy 1 according to the invention with a composition of La0.8Mg0.2Ni3.67 was prepared by the flash sintering technique (SPS for Spark Plasma Sintering) from two precursors: Mg2Ni elaborated by powder metallurgy and LaNiy (y=4.3875) elaborated by melting a mixture of the simple elements in an induction oven. These powders were ground into powder for two hours in a planetary milling machine Fritsch Pulverisette 4 with a speed of rotation of 400 revolutions per minute and a Ball/Powder mass ratio equal to 10:1. Subsequently the mixture was sintered with SPS under pressure of 50 MPa for one hour at a temperature of 820° C.
An alloy 2 used as a counter-example, with the same composition as the alloy 1, was prepared with a fast cooling technique (melt spinning), at a speed of 106 K/s, from two precursors used for elaborating the alloy 1. The thereby prepared alloy was then annealed for 10 days at a temperature of 800° C. under an inert atmosphere.
An alloy 3 of the prior art with a composition of La0.57Ce0.27Nd0.12Pr0.04Ni3.95Mn0.40Al0.30CO0.55 was prepared by melting together simple elements in a segmented copper crucible cooled with water and by slow cooling. This alloy was then annealed for 4 days at 1,050° C. under an inert atmosphere.
Table 1 below recalls these compositions.
The thereby obtained alloys were characterized by x-ray diffraction (XRD) by means of a Bruker AXS D8 θ-θ diffractometer (Bragg-Brentano geometry, Cu Kα radiation, 2θ angular domain=20 to 90°, step 0.04°). The analysis of the phases and the structural determination were carried out by means of the program for fitting the whole of the FULLPROF profile, based on Rietveld's method. Local chemical analysis was carried out by means of an electronic microprobe in Wavelength Dispersive Spectroscopy (WDS-EPMA Wavelength Dispersive Spectroscopy-Electron Probe Micro Analysis) CAMEBAX SX-100.
The isothermal hydrogen absorption and desorption curves (PCT) were established at 40° C. by the Sievert volumetric method.
Table 2 recalls the composition of the alloys in terms of phases as well as their PCT characteristics.
The samples for examinations with high resolution transmission electron microscopy (HRTEM) were prepared by mechanical polishing and thinning with an ion beam before being immediately transferred into the microscope in order to avoid oxidation of the surface. The observations were carried out by means of an FEI Tecnai microscope under an acceleration voltage of 200 kV. The high resolution transmission electron microscopy photographs show grey vertical lines which appear raised (these are patterns of the type L or Laves phase) relatively to a background consisting of vertical lines which appear brighter (patterns of type C).
In the case of the alloy 2 of the counter-example, made by melt spinning, the observed microstructures are characterized by a number of bright lines (and a gap) between two dark lines which is constant over a long distance. This structure is characteristic of a crystalline phase of the A5B19 type for a number of bright lines between two dark lines equal to 3. On the other hand, in the case of the alloy according to the invention, it is observed that the number of bright lines between two dark lines is not constant and varies randomly.
For making the electrodes, the alloy is mechanically powdered down to a grain size of 60 μm (Dv50=60 μm, Dv50 is the median volume diameter of the sample). The thereby obtained powder is mixed with 1% of styrene-butadiene polymer (SBR styrene-butadiene rubber) and 0.5% of CMC in an aqueous solution in order to make a paste which was deposited in a nickel foam. The thereby obtained strip was laminated and dried, and then cut out in order to produce negative electrodes.
A bundle consisting of a negative electrode framed with two positive electrodes containing nickel hydroxide with excess capacity and separated from each other by a separator consisting of a membrane impervious to oxygen and of two non-woven webs of polyolefin, was mounted and clamped between wedges in a polyethylene tub in order to form an open accumulator, for which the capacity equal to 1 Ah, is limited by the negative electrode. The bundle was then impregnated in vacuo with an aqueous KOH solution with an excess concentration of 8.7 N. The capacity of the alloy was measured in open elements limited by the negative electrode, in foam technology, under the following conditions:
After a formation cycle, the accumulator underwent about 10 activation cycles consisting of:
charging with a current of 35 mA/g for 16 h,
a resting period of 1 h and
discharging carried out with a current of 70 mA/g down to a cut-off voltage of 0.9V.
Next, the accumulator underwent fast cycling ageing consisting of a 48 min discharge with holding at 0.9V and 52 min charging at a rate of 350 mA/g. A cycle for performance measurement is carried out intermittently under the conditions of the activation cycles. The results are shown in Table 3.
The alloy 1 according to the invention, in the activated state, has a capacity of 322 mAh/g, 47 mAh/g greater than that of the alloy 2 (counter-example) and 40 mAh/g greater than that of the alloy 3 of the prior art. This table also shows the available capacity under the same conditions as above (16 h charging at 35 mA/g, rest period 1 h, discharging at 70 mA/g, cut-off voltage of 0.9V) by these elements in cycle 100, i.e. after 90 cycles of ageing during fast cycling under C conditions. The stability of the alloy is estimated by the index S100 calculated as follows:
S
100=(Capacity measured at cycle 100/Capacity at cycle 1)×100.
These results show that the alloy 3 of the prior art has a low initial capacity of 272 mAh/g and a very good cycling stability (S100=88.6%). On the other hand, the alloy of the counter-example 2, with the same composition as the alloy 1 according to the invention, but made by the melt spinning technique, has a high initial capacity of 313 mAh/g but a poor cycling stability (S100=78.3%). The alloy 1 according to the invention has the advantage of combining a high initial capacity of 318 mAh/g and a cycling stability, the level of which remains high (86.6%), and close to that of the alloy 3 of the prior art.
| Number | Date | Country | Kind |
|---|---|---|---|
| 1059878 | Nov 2010 | FR | national |
