Hydrogen storage properties and microstructure of melt-spun Mg90Ni8RE2 (RE = Y, Nd, Gd)

Kalinichenka, Siarhei; Röntzsch, Lars; Riedl, Thomas; Weißgärber, Thomas; Kieback, Bernd

doi:10.1016/j.ijhydene.2011.05.147

Cited by 99 publications

(25 citation statements)

References 33 publications

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“…The positive contribution of Y substitution with Mg to hydrogen diffusion is ascribed to the following two aspects. Kalinichenka et al [25] found that the partial substitution of rare-earth elements for Mg (La, Ce, Pr, Nd, Y, and Sm) and for Ni in Mg 2 Ni alloy (Cu, Fe, Al, Cr, Co, and Mn) could weaken the bond between Mg and H atoms, thereby promoting hydrogen diffusion. Furthermore, Cui et al confirmed that increasing of the lattice constants and that of the cell volume facilitate a decrease in the diffusion activation energy of hydrogen atoms, thereby also enhancing hydrogen diffusion [26].…”

Section: Electrochemical Kineticsmentioning

confidence: 99%

Electrochemical hydrogen-storage performance of Mg20−x Y x Ni10 (x = 0–4) alloys prepared by mechanical milling

et al. 2015

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Mg in Mg 2 Ni-type alloy was partially substituted with Y to improve the electrochemical performance of the alloy. The as-cast Mg 2 Ni-type Mg 20-x Y x Ni 10 (x = 0, 1, 2, 3, 4) electrode alloys were prepared by vacuum induction melting under the protection of highpurity helium atmosphere and subsequent mechanical milling for different time points. Effects of Y substitution with Mg on the microstructures and electrochemical performance of the as-cast and milled alloys were investigated in detail by X-ray diffraction, transmission electron microscopy, scanning electron microscopy coupled with energy-dispersive spectrometry, and automatic galvanostatic system. Results revealed that the substitution of Y with Mg evidently changed the phase composition of alloys. At a Y content of x B 1, the major phase in alloys was Mg 2 Ni, but the phase changed to YMgNi 4 ? YMg 3 with further addition of Y content. Electrochemical measurement showed that variations in the discharge capacity of alloys with Y content were closely related to the milling time. At B 10-h milling time, the discharge capacity of alloy invariably increased with the increasing Y content; at [ 10-h milling time, the discharge capacity initially increased, and then decreased with the increasing Y content. The substitution of Y with Mg dramatically ameliorated the cycle stability of the as-cast and milled alloys. Furthermore, high rate of discharge ability, electrochemical impedance spectrum, Tafel polarization curves, and potential-step measurements indicated that the electrochemical kinetic properties of the as-cast and milled alloys initially increased and then decreased with the increasing Y content.

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Section: Electrochemical Kineticsmentioning

confidence: 99%

Electrochemical hydrogen-storage performance of Mg20−x Y x Ni10 (x = 0–4) alloys prepared by mechanical milling

et al. 2015

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“…15,16 Furthermore, it was documented that the microstructures of Mg-based alloys inuenced their hydriding and dehydriding kinetics. 17 The hydrogenation/dehydrogenation performances of Mg-based alloys can be signicantly enhanced by reducing their grain sizes far below the micrometer scale.…”

Section: Introductionmentioning

confidence: 99%

Improved hydrogen storage kinetics of nanocrystalline and amorphous Ce–Mg–Ni-based CeMg₁₂-type alloys synthesized by mechanical milling

Zhang

Wang

et al. 2018

RSC Adv.

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In this paper, ball milling was used to prepare CeMg 11 Ni + x wt% Ni (x ¼ 100, 200) alloys having nanocrystalline and amorphous structures. The structures of the alloys and their electrochemical and gaseous kinetic performances were systematically investigated. It was shown that the increase in Ni content was beneficial to the formation of nanocrystalline and amorphous structures, and it significantly enhanced the electrochemical and gaseous hydrogen storage performances of as-milled alloys. In addition, the hydrogen storage capacities of the alloys fluctuated greatly with variation in milling duration. The maximum values of hydrogen capacity detected by varying the milling durations were 5.949 wt% and 6.157 wt% for x ¼ 100 and 200 alloys, respectively. Similar results were observed for the hydriding rates and high-rate discharge abilities (HRD) of the as-milled alloys. The dehydriding rate increased with the increase in milling duration. The reduction in hydrogen desorption activation was the reason for enhanced gaseous hydrogen storage kinetics.

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“…Metallic glasses (MGs), also known as amorphous alloys, possess more excellent mechanical and functional properties than conventional crystalline alloys in many practical fields [7][8][9][10][11][12][13][14], and are also expected to be candidates for hydrogen storage due to their unique structural and physical properties [8]. In 1980, Mealand et al [9] reported that amorphous TiCu alloy could absorb 35% more hydrogen than that of crystalline TiCu alloy.…”

Section: Introductionmentioning

confidence: 99%

“…Friedlmeier et al [11] prepared a series of amorphous or nano-crystalline Mg-Ni alloys by melt spinning, and achieved very high storage capacity of nearly 6.0 wt.%-H, while the hydrogen activation for the melt-spun Mg-Ni alloys required high temperatures and pressures above 663 K and 1.5 MPa. Very recently, Kalinichenka et al [12] produced an nano-crystalline Mg 90 Ni 8 RE 2 (RE = Y, Nd, Gd) alloy by melt spinning, and the activated alloy could reach a reversible hydrogen storage density of up to 5.6 wt.% with fast dehydrogenation rates at 528 K under initial pressure of vacuum. However, the surface activation of the alloys mentioned on amorphous or nano-crystalline Mg-based alloys is all carried out at temperatures higher than 573 K, which is far above the crystallization temperatures of Mg-based MGs.…”

Section: Introductionmentioning

confidence: 99%

Room temperature gaseous hydrogen storage properties of Mg-based metallic glasses with ultrahigh Mg contents

Lin

Wang

Zhu

2012

Journal of Non-Crystalline Solids

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Hydrogen storage properties and microstructure of melt-spun Mg90Ni8RE2 (RE = Y, Nd, Gd)

Cited by 99 publications

References 33 publications

Electrochemical hydrogen-storage performance of Mg20−x Y x Ni10 (x = 0–4) alloys prepared by mechanical milling

Electrochemical hydrogen-storage performance of Mg20−x Y x Ni10 (x = 0–4) alloys prepared by mechanical milling

Improved hydrogen storage kinetics of nanocrystalline and amorphous Ce–Mg–Ni-based CeMg₁₂-type alloys synthesized by mechanical milling

Room temperature gaseous hydrogen storage properties of Mg-based metallic glasses with ultrahigh Mg contents

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Hydrogen storage properties and microstructure of melt-spun Mg90Ni8RE2 (RE = Y, Nd, Gd)

Cited by 99 publications

References 33 publications

Electrochemical hydrogen-storage performance of Mg20−x Y x Ni10 (x = 0–4) alloys prepared by mechanical milling

Electrochemical hydrogen-storage performance of Mg20−x Y x Ni10 (x = 0–4) alloys prepared by mechanical milling

Improved hydrogen storage kinetics of nanocrystalline and amorphous Ce–Mg–Ni-based CeMg12-type alloys synthesized by mechanical milling

Room temperature gaseous hydrogen storage properties of Mg-based metallic glasses with ultrahigh Mg contents

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Improved hydrogen storage kinetics of nanocrystalline and amorphous Ce–Mg–Ni-based CeMg₁₂-type alloys synthesized by mechanical milling