There is provided a positive electrode for an alkaline secondary battery and an alkaline secondary battery having good output properties and cycle life. To that end, a positive electrode (10) for alkaline secondary battery is obtained by laminating a flexible metal substrate (11) having flexibility; a primer layer (12) having conductivity provided on one or both surfaces of the substrate (11); and a positive electrode composite material layer (13) provided on the primer layer (12) and containing a positive electrode active material, a binder resin, and a first conductive material.

A method of producing electrodes includes selecting a palladium alloy, annealing the palladium alloy at a first temperature above 350° C., cold working the palladium alloy into a desired electrode shape, and annealing the palladium alloy at a second temperatures and for a time sufficient to produce a grain size between about 5 microns and about 100 microns. The method further includes etching the palladium alloy, rinsing the palladium alloy with at least one of water and heavy water, and storing the palladium alloy in an inert environment.

A high-capacity and long-life negative electrode hydrogen storage material of La—Mg—Ni type for secondary rechargeable nickel-metal hydride battery and a method for preparing the same are provided in the present invention. A chemical formula of the negative electrode hydrogen storage material of La—Mg—Ni type is La.sub.1-x-yRe.sub.xMg.sub.y(Ni.sub.1-a-bAl.sub.aM.sub.b).sub.z, wherein Re is at least one of Ce, Pr, Nd, Sm, Y, and M is at least one of Ti, Cr, Mo, Nb, Ga, V, Si, Zn, Sn; 0≤x≤0.10, 0.3≤y≤0.5, 0<a≤0.05, 0≤b≤0.02, 2.3≤z<3.0. The negative electrode hydrogen storage material of La—Mg—Ni type in the present invention has excellent charge-discharge capacity and cycle life. The negative electrode hydrogen storage material of La—Mg—Ni type can be applied in both common secondary rechargeable nickel-metal hydride battery and secondary rechargeable nickel-metal hydride battery with ultra-low self-discharge and long-term storage performance.

Electrodes for a metal-hydrogen battery are described. The electrodes include one or more porous layers, each of the porous layers including a porous substrate and a catalyst layer covering the porous substrate, the catalyst layer including a transition metal, wherein at least one of the at least one porous layer includes a surface with features that facilitate hydrogen gas transport. In some embodiments, an anode electrode includes a first porous layer having a first surface; and a second porous layer adjacent the first porous layer having a second surface, wherein the first surface of the first porous layer and the second surface of the second porous layer form hydrogen gas transport channels.

Provided is an aqueous battery configured to use hydroxide ions (OH.sup.−) as carrier ions. The aqueous battery is an aqueous battery comprising a cathode layer, an anode layer and an aqueous liquid electrolyte, wherein the cathode layer contains, as a cathode active material, a graphite having a rhombohedral crystal structure; wherein the anode layer contains, as an anode active material, at least one selected from the group consisting of an elemental Zn, an elemental Cd, an elemental Fe, a Zn alloy, a Cd alloy, an Fe alloy, ZnO, Cd(OH).sub.2, Fe(OH).sub.2 and a hydrogen storage alloy; and wherein, as an electrolyte, at least one selected from the group consisting of KOH and NaOH is dissolved in the aqueous liquid electrolyte.

A hydrogen absorbing alloy negative electrode is provided. The hydrogen absorbing alloy negative electrode has a hydrogen absorbing alloy, and an additive including yttrium fluoride. A mass of the yttrium fluoride is 0.1 parts by mass or more and 0.2 parts by mass or less based on a hydrogen absorbing alloy powder of 100 parts by mass.

A main object of the present disclosure is to provide an anode active material with excellent capacity properties. The present disclosure achieves the object by providing an anode active material to be used in an alkaline storage battery, the anode active material including: a base material containing Ti and Cr, and including a BCC structure as a metastable phase; and a coating layer that coats the base material, and contains a catalyst metal and a metal with oxygen affinity that is more than oxygen affinity of Ti; wherein an oxide film is present in an interface between the coating layer and the base material; and when a first thickness T.sub.A (nm) and a second thickness T.sub.B(nm) of the oxide film are determined by Auger electron spectroscopy, a rate of the T.sub.A with respect to the T.sub.B, which is T.sub.A/T.sub.B is, for example, 1.50 or more.

An alkaline secondary battery negative electrode and a composition forming the negative electrode, containing an active material, a binder resin, and an electrically conductive agent containing an electrically conductive carbon material. When a value of D50 is defined to be an average particle size X and a value of D20 is defined to be a particle size Y in a cumulative particle size distribution obtained by measuring the active material using a laser diffractometry particle size distribution meter, the average particle size X is 10 μm or less, and the particle size Y is in the range of 30% to 70% of the average particle size X.

This disclosure provides a hydrogen storing alloy and a production method thereof. The hydrogen storing alloy has a chemical composition of a general formula R.sub.(1-x)Mg.sub.xNi.sub.y, wherein R is one or more elements selected from rare earth elements comprising Y, x satisfies 0.05≦x≦0.3, and y satisfies 2.8≦y≦3.8. The ratio of the maximal peak intensity present in a range of 2θ=31°-33° to the maximal peak intensity present in a range of 2θ=41°-44° is 0.1 or less (including 0), as measured by X-ray diffraction in which a Cu-Kα ray is set as an X-ray source.

Laves phase-related BCC metal hydride alloys historically have limited electrochemical capabilities. Provided are processes of activating these alloys to produce hydrogen storage materials with greater than 200 mAh/g capacities and commonly much greater than 300 mAh/g capacities. The processes include cooling the alloy during hydrogenation to reduced temperatures or by subjecting the materials to significantly increased hydrogen pressures. Temperatures in many embodiments do not exceed 300° C. By decreasing the temperature or increasing the hydrogen pressure the phase structure of the material is optimized to increase a synergistic effect between multiple phases in the resulting alloy thereby greatly improving the electrochemical capacities.