Mg2Ni Phase Research Articles

Phase, microstructure and hydrogen storage properties of Mg–Ni materials synthesized from metal nanoparticles

After Mg and Ni nanoparticles were fabricated by hydrogen plasma metal reaction, Mg-rich MgxNi100−x(75 < x < 90) materials were synthesized from these metal nanoparticles to study the synergistic effects for hydrogen storage in these samples to show both good kinetics and high capacity. These MgxNi100−x materials may absorb hydrogen with a capacity of around 3.3–5.1 wt% in 1 min at 573 K. The Mg90Ni10 sample shows a hydrogen capacity of 6.1 wt%. The significant kinetic enhancement is thought to be due to the unique nanostructure from the special synthesis route, the catalytic effect of the Mg2Ni nano phase, and the synergistic effects between the Mg2Ni and Mg phases in the materials. An interesting phenomenon which has never been reported before was observed during pressure composition isotherm (PCT) measurements. One steep step in the absorption process and two obviously separated steps in the desorption process during PCT measurements of Mg80Ni20 and Mg90Ni10 samples were observed and a possible reason from the kinetic performance of the Mg2Ni and Mg phases in absorption and desorption processes was explained. These MgxNi100−x materials synthesized from Mg and Ni nanoparticles show high capacity and good kinetics, which makes these materials very promising candidates for thermal storage or energy storage and utilization for renewable power.

An investigation of the microstructure and hydrogenation/dehydrogenation properties of ball-milled CeMg12 alloys with Ni powders

Abstract CeMg12 + 100 wt.% Ni composite hydrogen storage alloys were prepared using ball-milling. The phase structure, morphologies, and hydrogen absorption and desorption kinetics of these alloys were systematically investigated. The results show that the milled CeMg12 + 100 wt.% Ni alloys consisted of Mg2Ni and Ni phase with nanocrystalline and amorphous structures. Additionally, the volume fractions of the phase increased with prolonged ball-milling times, which improved the hydrogenation rates and the hydrogen storage capacities of the alloy samples. However, the dehydrogenation kinetics of the alloy samples were also impaired by the increased milling times. The poor dehydriding kinetics of the alloy samples milled for 80 h and 100 h were primarily attributed to grain size effects.

Advanced study of hydrogen storage by substitutional doping of Mn and Ti in Mg2Ni phase

The substitutional doping of Mn and Ti in Mg2Ni phase has been investigated by first principles density functional theory calculations. The calculation of enthalpy of formation shows that among the four different lattice sites of Mg(6f), Mg(6i), Ni(3b) and Ni(3d) in Mg2Ni unit cell, the most preferable site of substitution of Mn in Mg2Ni lattice has been confirmed to be Mg(6i) lattice site. The most preferable site of Ti substitution in Mg2Ni lattice is Mg(6i) position and the stability of Ti-doped Mg2Ni decreases with the increase of substitution quantity of Ti for Mg.

Effects of ultra-high pressure on phase compositions, phase configurations and hydrogen storage properties of LaMg4Ni alloys

The influences of ultrahigh pressure (UHP, under 5 GPa) on phase compositions, phase morphologies and hydrogen storage properties of LaMg4Ni alloys were studied. The X-ray diffraction patterns show that the as-cast alloy consists of La2Mg17, LaMg2Ni and Mg2Ni phases, whereas a new LaMg3 phase is observed in the UHP samples in addition to LaMg2Ni and Mg2Ni phases. The scanning electron microscopy graphs indicate that the phase distribution is more homogenous in the UHP alloys than in the as-cast one. Additionally, the microstructure of the UHP alloy heat-treated at 973 K is finer than that at 823 K. Both the reversible hydrogen storage capacity and the plateau of hydrogen pressure of the UHP alloys are close to those of the as-cast one. Of particular interest is that both UHP alloys exhibit better activation properties compared with the as-cast alloy. Moreover, the dehydriding onset temperature of the UHP alloys (5 GPa at 973 K) is about 490 K, which is obviously lower than that of the as-cast alloy. The amount of hydrogen desorption in the UHP alloy (5 GPa at 973 K) is 2.69 wt.% at 573 K, which corresponds to 89.6% of the saturated capacity. However, the corresponding values change to 1.75 wt.% and 58.3% in the as-cast alloy, respectively. It is confirmed the UHP treatment is one of effective approaches to tune the hydrogen storage performances of those rare earth–magnesium–nickel alloys.

Phase structure and hydrogen storage properties of REMg8.35Ni2.18Al0.21 (RE=La, Ce, Pr, and Nd) hydrogen storage alloys

REMg8.35Ni2.18Al0.21 (RE=La, Ce, Pr, and Nd) alloys were prepared by induction melting and following annealing. X-ray diffraction (XRD) and scanning electron microscopy (SEM) results showed that the alloys were composed of Mg2Ni, (La, Pr, Nd)Mg2Ni, (La, Ce)2Mg17, (Ce, Pr, Nd)Mg12 and Ce2Ni7 phases. The above phases were disproportioned into Mg2NiH4, MgH2 and REHx (x=2.51 or 3) phases in hydriding. CeH2.51 phase transformed into CeH2.29 phase in dehydriding, whereas LaH3, PrH3 and NdH3 phases remained unchanged. The PrMg8.41Ni2.14Al0.20 alloy had the fastest hydriding kinetics and the highest dehydriding plateau pressure while the CeMg8.35Ni2.18Al0.21 alloy presented the best hydriding/dehydriding reversibility. The onset hydrogen desorption temperature of the CeMg8.35Ni2.18Al0.21 hydride decreased remarkably owing to the phase transformation between the CeH2.51 and the CeH2.29.

Hydrogen storage properties of Mg–Ni nanoparticles

The aim of this work is to investigate metal–hydride transformation in Magnesium (Mg) nanoparticles decorated by Nickel (Ni). The samples were synthesized by Inert Gas Condensation: Mg single crystal nanoparticles were deposited on a metal substrate and subsequently their surface was exposed to evaporation of Ni. Structural analysis was made by Synchrotron Radiation Powder X-ray Diffraction and thermodynamic measurements by Sieverts apparatus. Ni decoration significantly improves the hydrogen release and uptake kinetics of the nanoparticles. The results connect the formation of Mg2Ni and Mg2NiH4 phases to the enhancement of hydrogen sorption properties.

Gaseous and electrochemical hydrogen storage kinetics of as-quenched nanocrystalline and amorphous Mg2Ni-type alloys

The nanocrystalline and amorphous Mg2Ni-type Mg2Ni1−xCox (x = 0, 0.1, 0.2, 0.3, 0.4) alloys were synthesized by melt quenching technology. The structures of the as-cast and quenched alloys were characterized by XRD, SEM and HRTEM. The gaseous hydrogen storage kinetics of the alloys was measured using an automatically controlled Sieverts apparatus. The alloy electrodes were charged and discharged with a constant current density in order to investigate the electrochemical hydrogen storage kinetics of the alloys. The results demonstrate that the substitution of Co for Ni results in the formation of secondary phases MgCo2 and Mg instead of altering the major phase Mg2Ni. No amorphous phase is detected in the as-quenched Cofree alloy, however, a certain amount of amorphous phase is clearly found in the as-quenched alloys substituted by Co. Furthermore, both the rapid quenching and the Co substitution significantly improve the gaseous and electrochemical hydrogen storage kinetics of the alloys, for which the notable increase of the hydrogen diffusion coefficient (D) along with the limiting current density (IL) and the obvious decline of the electrochemical impedance generated by both the Co substitution and the rapid quenching are basically responsible.

Hydrogenation-induced microstructure evolution in as cast and severely deformed Mg-10 wt.% Ni alloy

We determined the kinetics of hydrogen absorption of the hypoeutectic Mg-10 wt.% Ni alloy in the as-cast state and after processing by four passes of equal channel angular pressing (ECAP). While during the first hydrogenation cycle the ECAP-modified alloy exhibited faster absorption than its as-cast counterpart, this advantage was lost after the second hydrogenation cycle; parity was regained after six cycles. We attributed these differences in the hydrogen absorption kinetics to the formation of large (tens of micrometers) faceted Mg crystals observed during the first hydrogenation cycle. These crystals were significantly larger in the ECAP-modified alloy than in its as-cast counterpart. We discussed the growth of large Mg crystals during hydrogenation in terms of self-diffusion of Mg atoms driven by the metal-hydride transformation stress. The larger size of these crystals in the ECAP-processed alloy was attributed to the acceleration of diffusion by ECAP. Our metallographic studies revealed a number of microstructural changes in the alloys upon hydrogenation, such as cracking, accumulation of plastic strain in large Mg crystals, and re-distribution of the dispersed particles of Mg2Ni phase in the partly hydrogenated alloys.

Hydrogenation reaction of Mg-Based alloys fabricated by rapid solidification

Mg-23.5wt%Ni-xwt%Cu (x=2.5, 5 and 7.5) alloys for hydrogen storage were prepared by melt spinning and crystallization heat treatment. The alloys were ground by a planetary ball mill for 2 h in order to obtain a fine powder. The Mg-23.5Ni-5Cu alloy had crystalline Mg and Mg2Ni phases. Mg-23.5Ni-5Cu had an effective hydrogen capacity of near 5 wt%. The activated Mg-23.5Ni-5Cu alloy absorbed 4.50 and 4.84 wt%H at 573K under 12 bar H2 for 10 and 60 min, respectively, and desorbed 3. 21 and 4.81 wt%H at 573K under 1.0 bar H2 for 10 and 30 min, respectively. The activated Mg-23.5Ni-5Cu alloy showed a quite high hydriding rate like Mg-10Fe2O3, and higher dehydriding rates than the activated Mg-xFe2O3−yNi. This likely resulted because the melting before melt spinning process has led to the homogeneous distribution of Ni and Cu in the melted Mg, and the Mg-23.5Ni-5Cu alloy has a larger amount of the Mg2Ni phase than the Mg-xFe2O3−yNi alloy.

Phase transformations and hydrogen-storage characteristics of Mg-transition metal-oxide alloys

Samples with the compositions of 76.5 wt%Mg-23.5 wt%Ni (Mg-Ni), 71.5 wt%Mg-23.5 wt%Ni-5 wt% Fe2O3 (Mg-Ni-Fe2O3) and 71.5 wt%Mg-23.5 wt%Ni-5 wt% Fe2O3 (spray conversion) (Mg-Ni-scFe2O3), 71.5 wt%Mg-23.5 wt%Ni-5 wt% Fe (Mg-Ni-Fe) and 80 wt%Mg-13.33 wt%Ni-6.67 wt%Fe (Mg-13Ni-7Fe) were prepared by reactive mechanical grinding. Mg-13Ni-7Fe has the highest hydriding and dehydriding rates. After hydriding-dehydriding cycling, all the samples contain the Mg2Ni phase. The samples with Fe2O3 and Fe2O3(spray conversion) as starting materials contain the Mg(OH)2 phase after hydriding-dehydriding cycling as well as after reactive mechanical grinding. Mg-Ni-Fe and Mg-13Ni-7Fe contain the MgH2 phase after reactive mechanical grinding. Phases, space groups, cell parameters, contents and crystallite sizes were analyzed by Full Pattern Matching Refinement program, one of the Rietveld analysis programs, from the XRD powder patterns of Mg-Ni-scFe2O3 after reactive mechanical grinding and after hydriding-dehydriding cycling. The MgH2 phase formed in the Mg-Ni-Fe and Mg-13Ni-7Fe mixtures after reactive mechanical grinding is considered to help the pulverization of the materials during reactive mechanical grinding, leading to the high hydriding and dehydriding rates of these mixtures.

Study of hydrogen absorption kinetics of Mg2Ni-based powders produced by high-injected shock power mechanical alloying and subsequent annealing

Mg2Ni-based compounds were prepared using a high-energy milling technique, with a planetary ball mill, and subsequent annealing at 350 °C. X-ray diffraction analyses revealed that Mg2Ni phase was obtained after 10 milling hours, in addition to Ni phase. Increasing the ball-milling duration from 10 to 17 h causes a decrease in the crystal size of particles from 93 to 76 nm. However, the subsequent annealing of all Mg2Ni-based materials highly increases their crystallite sizes with calculated values in the range of 261–235 nm. In the same way, X-ray diffraction patterns of annealed compounds show the presence of highly crystallized Mg2Ni phases. The particle size of Mg2Ni/Ni particles is estimated at 25 µm after 10 milling hours and drops to 5 µm at longer times. The scanning electron microscopy images of Mg2Ni/Ni particles demonstrated a drastic increase of their sizes up to 100 µm upon annealing. The hydrogenation reactivity and kinetic of Mg2Ni/Ni were both characterized by solid–gas reactions. The hydrogen absorption capacity value was about 3.5 H/f.u for milled and annealed Mg2Ni/Ni compound. The highest hydrogen absorption kinetic was obtained during the first 5 h of absorption time, where 95 % of the maximum absorption capacity was reached.

Investigations on hydrogen storage properties of LaMg8.52Ni2.23M0.15 (M=Ni, Cu, Cr) alloys

LaMg8.52Ni2.23M0.15 (M=Ni, Cu, Cr) alloys were prepared by induction melting. X-ray diffraction showed that all the three alloys had a multiphase structure, consisting of La2Mg17, LaMg2Ni and Mg2Ni phases. Energy dispersive X-ray spectrometer results revealed that most of Cu and Cr distributed in Mg2Ni phase. La2Mg17 and LaMg2Ni phases decomposed into MgH2, Mg2NiH4 and LaH3 phases during the hydrogenation process. Hydriding/dehydriding measurements indicated that the reversible hydrogen storage capacities of Mg2Ni phase in LaMg8.52Ni2.23M0.15 (M=Cu, Cr) alloys increased to 1.05 wt.% and 0.97 wt.% from 0.79 wt.% of Mg2Ni phase in LaMg8.52Ni2.38 alloy at 523 K. Partial substitution of Cu and Cr for Ni decreased the onset dehydrogenation temperature of the alloy hydrides and the temperature lowered by 18.20 and 5.50 K, respectively. The improvement in the dehydrogenation property of the alloys was attributed to that Cu and Cr decreased the stability of Mg2NiH4 phase.

Effect of ball milling time on microstructure and electrochemical properties of CeMg12+100%Ni hydrogen storage alloy

In order to improve hydrogen storage performances of CeMg12 type alloys, ball milling technology was used for preparing nanocrystalline/amorphous CeMg12+100%Ni composite hydrogen storage alloys. The microstructures and morphologies of alloy samples were characterised by X-ray diffraction, scanning electron microscopy and high resolution transmission electron microscopy. The electrochemical hydrogen storage characteristics of as milled alloys were tested by an automatic galvanostatic system. The electrochemical impedance spectra were plotted by an electrochemical workstation (PARSTAT2273). The hydrogen diffusion coefficients D in the alloys were calculated by virtue of potential step method. The results show that the amount of nanocrystalline/amorphous Mg2Ni phase and Ni phase within alloy samples increase with prolonging milling time. Prolonging of ball milled duration markedly improves the electrochemical discharge properties and cyclic stability of alloy samples. The amorphisation degree of the milling alloys increases with rising milling duration. Furthermore, the high rate dischargeability, electrochemical impedance spectra and potential step measurement all indicate that electrochemical kinetics of alloy electrodes first increases and then decreases with increasing ball milling.

Comparative study of electrochemical performances of the as-melt Mg20Ni10−xMx (M = None, Cu, Co, Mn; x = 0, 4) alloys applied to Ni/metal hydride (MH) battery

The partial substitution of M (M=Cu, Co, Mn) for Ni has been performed in order to ameliorate the electrochemical hydrogen storage performances of Mg2Ni-type electrode alloys. The melt spinning technology was used to prepare the Mg20Ni10−xMx (M=None, Cu, Co, Mn; x=0, 4) electrode alloys. The impacts of the melt spinning and the M (M=Cu, Co, Mn) substitution on the structures and electrochemical hydrogen storage characteristics of the alloys were investigated systemically. The analysis of XRD and TEM reveals that the as-spun (M=None, Cu) alloys display an entire nanocrystalline structure, whereas the as-spun (M=Co, Mn) alloys hold a nanocrystalline/amorphous structure, indicating that the substitution of M (M=Co, Mn) for Ni facilitates the glass formation in the Mg2Ni-type alloys. Besides, all the as-cast alloys have a major phase Mg2Ni, whereas the M (M=Co, Mn) substitution brings on the formation of some secondary phases, MgCo2 and Mg for the (M=Co) alloy, and MnNi and Mg for the (M=Mn) alloy. Based upon the electrochemical measurements, an evident impact engendered by melt spinning on the electrochemical performances of the alloys appears. The cycle stability of the alloys augments monotonously with the growing of the spinning rate. The discharge capacity and high rate discharge ability (HRD), however, act differently. Melt spinning enhances the cycle stability of the (M=Co, Mn) alloys dramatically, but exerts an adverse impact on the (M=None, Cu) alloys. The high rate discharge ability (HRD) of all the alloys grow considerably with the rising of the spinning rate except for (M=Mn) alloy, whose HRD has a maximum value with the variation of the spinning rate. Furthermore, the substitution of M (M=Cu, Co, Mn) for Ni enhances the electrochemical performances of the as-cast and spun Mg2Ni alloys evidently, but the M (M=Mn) substitution gives rise to a decline of HRD when the spinning rate reaches 20m/s.

Influence of magnesium on electrochemical properties of RE3–xMgx(Ni0.7Co0.2Mn0.1)9 (x=0.5–1.25) alloy electrodes

RE3–xMgx(Ni0.7Co0.2Mn0.1)9 (x=0.5–1.25) alloys were prepared by induction melting and the influence of the partial substitution of RE (where RE stands for La-rich mischmetal) by Mg on the hydrogen storage and electrochemical properties of the alloys were investigated systematically. These alloys mainly consisted of three phases, La(Ni,Mn,Co)5 phase, La2Ni7 phase and Mg2Ni phase. The P-C-T isotherms showed that with Mg content increasing in the alloys, the hydrogen storage capacity first increased and reached the maximum capacity of 1.36 wt.% when x=1.0, and then decreased with x increasing further. Electrochemical studies revealed that the discharge capacity reached the maximum value of 380 mAh/g and the alloy electrode presented better cyclic stability when RE/Mg=2. The high rate discharge ability of the alloy electrodes was also improved by the substitution of Mg for RE. The RE2Mg(Ni0.7Co0.2Mn0.1)9 alloy exhibited better hydrogen absorption kinetics (x=1.0).

Mg2−xTixNi (x = 0, 0.5) alloys prepared by mechanical alloying for electrochemical hydrogen storage: Experiments and first-principles calculations

Mg2−xTixNi (x = 0, 0.5) electrode alloys have been prepared by mechanical alloying (MA) under argon atmosphere at room temperature using a planetary high-energy ball mill. The microstructures of synthesized alloys are characterized by X-ray diffraction (XRD), scanning electron microscopy (SEM) and transmission electron microscopy (TEM). The effects of substitutional doping of Ti in Mg2Ni phase have been investigated by first-principles density functional theory calculations. XRD analysis results indicate that Ti substitution for Mg in Mg2Ni-type alloys results in the formation of TiNi (Pm-3m) and TiNi3 intermetallics. With the increase of milling time, the TiNi phase captures Ni from Mg2Ni to further form TiNi3 phase and the MgO phase increases. The calculated results of enthalpy of formation indicate that the most preferable site of Ti substitution in Mg2Ni lattice is Mg(6i) position and the stability of phase gradually decreases along the sequence TiNi3 phase > TiNi phase > Mg9Ti3Mg(6i)Ni6 Ti-doped phase > Mg2Ni phase. SEM observations show that the average particle sizes of Mg2Ni and Mg1.5Ti0.5Ni milled alloys decrease and increase, respectively with increasing the milling time. The TEM analysis results reveal that TiNi and Mg2Ni coexist as nanocrystallites in the Mg1.5Ti0.5Ni alloy milled for 20 h. Electrochemical measurements indicate that the maximum discharge capacities of Mg2Ni and Mg1.5Ti0.5Ni alloys rise and decline, respectively with the prolongation of milling time. The Mg1.5Ti0.5Ni alloy milled for 20 h shows the highest discharge capacity among all milled alloys. The capacity retaining rate of Mg1.5Ti0.5Ni milled alloys is better than that of Mg2Ni milled alloys.

An investigation on diffusion bonding of aluminum and magnesium using a Ni interlayer

Diffusion bonding aluminum and magnesium using a Ni interlayer was investigated for the first time. The bonding trials were carried out at 440°C for different time under 1MPa in a vacuum of 6×10−3Pa. The interfaces were investigated by means of SEM, EPMA, XRD and Vickers hardness test. The results showed that dissimilar metals of Mg/Al could be successfully joined by diffusion bonding with a Ni interlayer and the Mg–Al intermetallic compounds were impeded. From Al side to Mg side, there was Al substrate, Al–Ni reaction layer, Ni interlayer, Mg–Ni reaction layer, Mg substrate. The microhardness in the Al–Ni reaction layer and Mg–Ni reaction layer increased sharply, which were 201.5Hv and 244.1Hv. The fracture occurred in the intermetallic compound layer of the Mg–Ni reaction layer, where the Mg2Ni phase appeared on both Al and Mg surfaces.

Reaction Kinetics with Hydrogen and Temperature Dependence of the Hydriding Rate for a Magnesium-Based Nickel Iron Oxide Alloy

A 71.5 wt%Mg-23.5 wt%Ni-5 wt%Fe2O3 (Mg-23.5Ni-5Fe2O3) sample was prepared by a quite simple process, reactive mechanical grinding, and its hydriding and dehydriding properties were then investigated. The reactive mechanical grinding of Mg with Ni and Fe2O3 is considered to facilitate nucleation and shorten the diffusion distances of the hydrogen atoms. After the hydriding-dehydriding cycling, the Mg- 23.5Ni-5Fe2O3 sample contained Mg2Ni phase. Expansion and contraction of the hydride-forming materials (Mg and Mg2Ni) with the hydriding and dehydriding reactions are also considered to increase the hydriding and dehydriding rates of the mixture by forming defects and cracks leading to the fragmentation of the particles. The temperature dependence of the hydriding rate of the sample is discussed.

Phase structure and hydrogen storage properties of LaMg3.93Ni0.21 alloy

The phase structure and hydrogen storage property of LaMg3.93Ni0.21 alloy were studied. XRD and SEM results exhibited that LaMg3.93Ni0.21 alloy consisted mainly of LaMg3, La2Mg17 and LaMg2Ni phases; after hydriding/dehydriding process, all the three phases transformed, La3H7 phase existed and the actual hydrogen absorption phases were Mg and Mg2Ni phases. Pressure-composition-temperature (P-C-T) measurement showed that the reversible hydrogen storage capacity of LaMg3.93Ni0.21 alloy was 2.63 wt.%, and the absorption time for reaching 90% of the storage capacity was 124 s at 523 K, and it was 1850 s for deabsorbing 90% of the maximum dehydrogen capacity. The hydriding process of LaMg3.93Ni0.21 alloy followed the nucleation and growth mechanisms. The enthalpy and entropy for hydriding and dehydriding reactions of the Mg phase in LaMg3.93Ni0.21 alloy were calculated to be −66.381.10 kJ/mol H2, −100.961.96 J/(K·mol) H2 and 68.503.87 kJ/mol H2, 98.28 5.48 J/(K·mol) H2, respectively. A comparison of these data with those of MgH2 (−74.50 kJ/mol H2, −132.30 J/Kmol H2) suggested that the hydride of LaMg3.93Ni0.21 alloy was less stable than MgH2. The existence of La hydride and synergetic effect of multiphase led to higher reversible hydrogen storage capacity and better kinetic property at lower temperature for LaMg3.93Ni0.21 alloy.

Hydriding and Dehydriding Kinetics of Nanocrystalline and Amorphous Mg&lt;sub&gt;20&lt;/sub&gt;Ni&lt;sub&gt;10-x&lt;/sub&gt;M&lt;sub&gt;x&lt;/sub&gt; (M=Cu, Mn; x = 0-4) Alloys Prepared by Melt Spinning

The partial substitution of M (M=Cu, Mn) for Ni has been performed in order to ameliorate the hydriding and dehydriding kinetics of Mg2Ni-type hydrogen storage alloys. The melt spinning technology was used to prepare the Mg20Ni10-xMx (M=Cu, Mn; x=0, 1, 2, 3, 4) alloys. The structures of the as-spun alloys were characterized by XRD and TEM. The hydriding and dehydriding kinetics of the alloys were measured by an automatically controlled Sieverts apparatus. The results show that the as-spun (M=Cu) alloys hold a typical nanocrystalline structure, whereas the as-spun (M=Mn) alloys display a nanocrystalline and amorphous structure, confirming that the substitution of Mn for Ni facilitates the glass formation in the Mg2Ni-type alloy. Furthermore, Mn substitution results in the formation of the secondary phases MnNi and Mg instead of changing the major phase of Mg2Ni. The substitution of M (M=Cu, Mn) for Ni exerts an insignificant effect on the hydriding kinetics, but it ameliorates the hydrogen desorption kinetics of the alloys dramatically. The hydrogen desorption ratio ( ) is enhanced form 20.84% to 52.88% for the (M=Cu) alloy spun at 20 m/s, and from 20.84% to 53.87% for the (M=Mn) alloy spun at 20 m/s by increasing the M (M=Cu, Mn) content from 0 to 4.