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 456.38±1.10 kJ/mol H2, -100.96±1.96 J/（K·mol） H2 and 68.50-x3.87 kJ/mol H2, 98.28 ±5.48 J/（K-mol） H2, respectively. A comparison of these data with those of MgHz （-74.50 kJ/mol H2, -132.30 J/K.mol H2） suggested that the hydride of LaMg3.93Nio.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 LaMg3mNi0.21 alloy.
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 MgzNi phase. La2Mg17 and LaMg2Ni phases decomposed into MgHz, Mg2NiH4 and LaH3 phases during the hydrogenation process. Hydriding/dehydriding measurements indicated that the reversible hydrogen storage capacities of Mg2Ni phase in LaMgs.52Ni2.23M0.15 （M=Cu, Cr） alloys increased to 1.05 wt.% and 0.97 wt.% from 0.79 wt.% of Mg2Ni phase in LaMgs.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.
