Characterization of Mg–20wt% Ni–Y hydrogen storage composite prepared by reactive mechanical alloying

Li, Zhinian; Liu, Xiaopeng; Jiang, Lijun; Wang, Shumao

doi:10.1016/j.ijhydene.2006.09.022

Cited by 95 publications

(30 citation statements)

References 19 publications

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“…For the 2LiNH 2 -1.1MgH 2 -0.04Ti 3 Cr 3 V 4 composite, fine Ti-Cr-V particles homogenously distributed in the matrix can decrease the diffusion distance and increase the H diffusion paths at the same time, which improve the dehydrogenation properties of the composite. Furthermore, for the dehydrogenation process, the Ti 3 Cr 3 V 4 BCC alloy homogeneously distributed in the substrate desorbs hydrogen first and makes significant volume contraction, causing significant contraction strain on Li-Mg-N-H particles around it, which could decrease the activating energy of hydrogen molecules to H atoms (the same effect has been proved by Li et al for Mg-based hydrogen storage materials [16]). Therefore, the dehydrogenation kinetics properties of the Li-Mg-N-H system are significantly enhanced.…”

Section: Catalytic Mechanismsmentioning

confidence: 62%

Enhancement of Ti-Cr-V BCC alloys on the dehydrogenation kinetics of Li-Mg-N-H hydrogen storage materials

Wang

et al. 2010

Rare Metals

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The hydrogen storage properties of a Li-Mg-N-H material doped by a 4 mol.% Ti 3 Cr 3 V 4 body centre cubic (BCC) alloy hydride and prepared with a ball-milling method were investigated by X-ray diffraction, scanning electron microscopy, transmission electron microscopy and Sievert's technology test. The results show that the Ti 3 Cr 3 V 4 BCC alloy hydride/Li-Mg-N-H composite has good reversible hydrogen storage properties. The dehydrogenation kinetics of the Li-Mg-N-H system can be greatly improved by doping the Ti 3 Cr 3 V 4 BCC alloy hydride. The composite desorbed 4.1 wt.% hydrogen in the first 60 min at 473 K under 0.1 MPa pressure, but when without the BCC alloy addition, only 3.0 wt.% hydrogen was desorbed under the same dehydrogenation condition. It can be deduced that the Ti 3 Cr 3 V 4 BCC alloy uniformly distributed in the Li-Mg-N-H substrate could decrease the activating energy of hydrogen molecules to H atoms and increase H diffusion paths in the composite, enhancing the dehydrogenation kinetics of the Li-Mg-N-H system.

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Section: Catalytic Mechanismsmentioning

confidence: 62%

Enhancement of Ti-Cr-V BCC alloys on the dehydrogenation kinetics of Li-Mg-N-H hydrogen storage materials

Wang

et al. 2010

Rare Metals

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“…A lot of work to improve the hydriding and dehydriding rates of magnesium has been performed by alloying with magnesium metals 5,6) such as Cu, 7) Ni, 8,9) In, 10) Sn, 11) V, 12) and Ni and Y, 13) by synthesizing compounds such as CeMg 12 14) and As shown in these examples, the hydrogen absorption and desorption behaviors of Mg have been studied by using pure Mg or pure MgH 2 as a starting material. The pure MgH 2 is more difficult to synthesize and more expensive than the pure Mg. By comparing the hydrogen absorption and desorption behaviors and the prices, it is necessary to determine which is appropriate to be used as a starting material.…”

Section: )mentioning

confidence: 99%

Hydrogen Storage Properties of Pure MgH2

Kwak¹,

Lee²,

Park³

et al. 2013

Korean. J. Mater. Res.

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The hydrogen storage properties of pure MgH 2 were studied and compared with those of pure Mg. At the first cycle, pure MgH 2 absorbed hydrogen very slowly at 573 K under 12 bar H 2 . The activation of pure MgH 2 was completed after three hydriding-dehydriding cycles. At the 4 th cycle, the pure MgH 2 absorbed 1.55 wt% H for 5 min, 2.04 wt% H for 10 min, and 3.59 wt% H for 60 min, showing that the activated MgH 2 had a much higher initial hydriding rate and much larger H a (60 min), quantity of hydrogen absorbed for 60 min, than did activated pure Mg. The activated pure Mg, whose activation was completed after four hydriding-dehydriding cycles, absorbed 0.80 wt% H for 5 min, 1.25 wt% H for 10 min, and 2.34 wt% H for 60 min. The particle sizes of the MgH 2 were much smaller than those of the pure Mg before and after hydridingdehydriding cycling. The pure Mg had larger hydrogen quantities absorbed at 573K under 12 bar H 2 for 60 min, H a (60 min), than did the pure MgH 2 from the number of cycles n = 1 to n = 3; however, the pure MgH 2 had larger H a (60 min) than did the pure Mg from n = 4 to n = 6.

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“…A lot of work to improve the hydriding and dehydriding rates of magnesium has been performed by alloying with magnesium metals 2,3) such as Cu, 4) Ni, 5,6) In, 7) Sn, 8) V, 9) and Ni and Y, 10) by synthesizing compounds such as CeMg 12 11) and Mg 76 Ti 12 Fe 12-x Ni x (x = 4, 8), 12) and by making composites such as Mg -20 wt% Fe 23 Y 8 . 13) Aminorroaya et al 14) added Nb and multi-walled carbon nanotubes to Mg-Ni alloys, and Cho et al 15) added transition metals to cast Mg-Ni alloys for the improvement of the reaction rates of Mg with H 2 .…”

Section: Introductionmentioning

confidence: 99%

Hydrogen Absorption at a Low Temperature by MgH2 after Reactive Mechanical Grinding

Song¹,

Lee²,

Kwak³

et al. 2014

Korean. J. Mater. Res.

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Pure MgH 2 was milled under a hydrogen atmosphere (reactive mechanical grinding, RMG). The hydrogen storage properties of the prepared samples were studied at a relatively low temperature of 423 K and were compared with those of pure Mg. The hydriding rate of the Mg was extremely low (0.0008 wt% H/min at n = 4), and the MgH 2 after RMG had higher hydriding rates than that of Mg at 423 K under 12 bar H 2 . The initial hydriding rate of MgH 2 after RMG at 423 K under 12 bar H 2 was the highest (0.08 wt% H/min) at n = 2. At n = 2, the MgH 2 after RMG absorbed 0.39 wt% H for 5 min, and 1.21 wt% H for 60 min at 423K under 12 bar H 2 . At 573 K under 12 bar H 2 , the MgH 2 after RMG absorbed 4.86 wt% H for 5 min, and 5.52 wt% H for 60 min at n = 2. At 573 K and 423 K under 1.0 bar H 2 , the MgH 2 after RMG and the Mg did not release hydrogen. The decrease in particle size and creation of defects by reactive mechanical grinding are believed to have led to the increase in the hydriding rate of the MgH 2 after RMG at a relatively low temperature of 423 K.

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Characterization of Mg–20wt% Ni–Y hydrogen storage composite prepared by reactive mechanical alloying

Cited by 95 publications

References 19 publications

Enhancement of Ti-Cr-V BCC alloys on the dehydrogenation kinetics of Li-Mg-N-H hydrogen storage materials

Enhancement of Ti-Cr-V BCC alloys on the dehydrogenation kinetics of Li-Mg-N-H hydrogen storage materials

Hydrogen Storage Properties of Pure MgH2

Hydrogen Absorption at a Low Temperature by MgH2 after Reactive Mechanical Grinding

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