Activity-Tuning of Supported Co–Ni Nanocatalysts via Composition and Morphology for Hydrogen Storage in MgH2

Introduction

Magnesium (Mg)-hydrides are considered promising hydrogen-storage materials due to their high theoretical hydrogen capacity of ~7.6 wt%, low-cost, and good reversibility (Cao et al., 2015; Liu X. et al., 2015; Ding et al., 2017; Møller et al., 2017; Schneemann et al., 2018), even as compared to other high H-content complex hydrides (Zheng et al., 2008; Li et al., 2011, 2014a; Liu D. M. et al., 2015). As solid-state hydrogen storage media, their application is still hampered by a large reaction enthalpy of ~76 kJ· mol⁻¹ H₂ for desorption (Si et al., 2018), high activation barrier, and slow hydrogen atom diffusion (Paskevicius et al., 2010), which result in higher desorption temperature and sluggish kinetics. Many strategies such as catalytic doping (Liu et al., 2019; Wang et al., 2019), nanosizing (Xia et al., 2015; Fang et al., 2019), alloying (Li et al., 2014b; Wei et al., 2018), and ionic substitution (Ouyang et al., 2014) have been proposed to overcome these challenges.

Catalytic doping was demonstrated to be an effective approach for making hydrogen desorption from MgH₂ easier at relatively lower temperature (Shen et al., 2018; Wang et al., 2018). More importantly, unlike alloying, which introduces more non-absorbed elements (Ouyang et al., 2014), the content of doped catalysts is very limited and does not decrease the effective hydrogen storage capacity. In the last two decades, various catalysts such as transition metals (Humphries et al., 2013; German and Gebauer, 2016), oxides (Lin et al., 2014), carbon (Yao et al., 2007), fluorides (Kalantzopoulos et al., 2014), metallic glasses (El-Eskandarany, 2016), and 2D MXenes (Liu et al., 2016) have thus been developed. Recently, carbon-supported transition metals, especially Ni, were found to possess a superior catalysis effect for promoting hydrogen storage in MgH₂ (Ma et al., 2018), most of which focused on the type, amounts, and particle size of catalysts (Shevlin and Guo, 2013). However, so far, the dependence of the hydrogen sorption properties of MgH₂ on the morphology, composition, and activity of supported nanocatalysts has not been established. The science behind it remains unclear, particular in terms of their intrinsic mechanisms for enhancement. It is therefore important to attempt to promote hydrogen storage of MgH₂ based on consideration of catalytic activity tuned by morphology and/or composition.

In this work, we realize the regulation of the activity of graphene-supported Co-Ni nanocatalysts by changing their morphology and compositions and further examine their catalytic effects on hydrogen storage in Mg. It is demonstrated that when Ni was partly substituted by Co, the shape of these nanocatalysts is shifted from spherical to plate-like and that the catalytic activity of these supported Co–Ni nanocatalysts depends strongly on their morphology and composition. The correlations among catalyst composition, shape, activity, and altered hydrogen sorption of Mg are also discussed. The results obtained will deepen the understanding of catalytic hydrogen storage and provide insights into the design of novel catalysts for property improvement of Mg-based materials.

Experimental Section

Preparation of Graphene-Supported Co–Ni Nanocatalysts and Their Doped MgH₂ Composites

The starting chemicals of cobalt chloride (CoCl₂·6H₂O, purity 99.99%), nickel chloride (NiCl₂·6H₂O, purity 99.3%), and hexamethylenetetramine (C₆H₁₂N₄, purity 99%) were purchased from Alfa Aesar and used without further purification. First, CoCl₂·6H₂O, NiCl₂·6H₂O, and hexamethylenetetramine were dissolved in 1,000 ml of deionized water at different weight ratios and then refluxed for 6 h under nitrogen protection with continuous magnetic stirring. The light-pink precipitate was recovered by filtration and washed with deionized water and anhydrous ethanol in turn. Finally, it was air-dried at room temperature. By changing the starting mixing ratio of CoCl₂·6H₂O and NiCl₂·6H₂O, different kinds of Co/Ni(OH)_x precursors can be obtained according to the above process.

The precursor and graphene were first mixed manually at an optimized weight ratio of 7:3, and then the mixed powders were ball-milled on a planetary ball mill at 300 rpm with a ball-to-sample weight ratio of 60:1 for 6 h under an argon atmosphere. The catalyst powders were then thermally annealed at ~800°C for 5 h. Subsequently, the catalyst obtained was used to dope MgH₂ by mixing them at a weight ratio of 95:5 for 2 h under a 0.5 MPa hydrogen atmosphere by using a planetary mill at 400 rpm with a 20:1 ball-to-powder ratio and are denoted as Ni/Co@G-doped MgH₂ composites.

Characterization and Hydrogen Sorption Measurements

To examine the microstructural evolution, scanning electron microscopy (SEM) and transmission electron microscopy (TEM) observations were carried out on a Shimadzu SUPERSCAN SSX-550 scanning electron microscope and JEOL JEM-2100 F instrument, respectively. The sample preparation was dispersed in a dried THF solvent and was then spread on a copper grid-supported holey carbon film. The high-angle annular dark-field (HAADF) image was detected by an FEI Tecnai F20 analytical scanning transmission electron microscope (STEM) operated at a 200 kV accelerating voltage. The thermogravimetric behaviors of the as-prepared samples were examined using a Netzsch STA 409 PC system with a ramping rate of 10°C/min under a flowing Ar atmosphere. The sorption properties were measured using an automated Sieverts-type apparatus, which allowed for the accurate determination of the amount of evolved hydrogen (Si et al., 2018). Typically, an ~1 g sample was loaded into a stainless-steel autoclave and was evacuated. Rapid heating in the furnace to the desired temperature was accomplished by immersing the sample chamber in it, and then the desorption was performed against a back pressure of 10 Pa, and the absorption was performed against a pressure of 5 MPa. Multi-cycling of ab-/desorption was repeated for activation until a constant value of absorbed hydrogen was obtained. After activation, the samples were placed under a vacuum to completely remove the residual hydrogen, and then the isothermal sorption kinetics and pressure–composition (P–C) isotherms were measured at various temperatures. All sample handling was carried out in an Ar-filled glove box.

Results and Discussion

Figure 1 shows a schematic diagram of the preparation of Co-Ni nanocatalysts anchored onto the graphene by two steps from the as-purchased graphene and Co/Ni(OH)_x precursors. These Co/Ni(OH)_x precursors, which were prepared by the hydrothermal method, exhibit small particle sizes and abundant active sites, which would facilitate the subsequent anchoring on graphene. Graphene and precursors with different mass ratios were first mixed by ball-milling and then heating at 800°C under an Ar atmosphere for carbon thermal reduction. By adjusting the composition of the Ni and Co ratio, different morphologies of particles and plates can be obtained for the Co-Ni metallic catalysts anchored on the graphene. Interestingly, Co incorporation does not alter the phase components of Co-Ni@G catalysts, suggesting its solid dissolution in the similar Ni lattice. With a further increase in Co content, the size of the Co-Ni based nanoplates can grow. Thus, we can realize control of the shape and size of the Co-Ni nanocatalysts prepared by this two-step method.

FIGURE 1

Figure 1. Schematic diagram of the preparation of Co-Ni nanocatalysts anchored to graphene by two steps. The morphology and size were changed significantly by adding Co into Ni catalysts.

We further examine the morphological changes during the fabrication process to support the above schematic method. Figures 2a,b shows SEM images of the hydrothermal CoNi(OH)_x precursors and the as-prepared graphene. The precursors exhibit small particles with an aggregated structure, while the graphene shows an ultra-thin sheet structure somewhat like “corrugated paper,” as further confirmed by the TEM image shown in Figure 2c. Figure 2d shows the spherical morphology of the Ni@G with a broader size distribution from 10 to 160 nm, also confirmed by the HADDF-STEM image in Figure 2e. Further magnification of the image in Figure 2f shows that smaller particles of 10–30 nm along with bigger ones are observed in the Ni@G. When introducing Co into Ni catalysts, the shape of Ni catalysts changes from spherical to plate-like, as shown in Figure 2g. Interestingly, the plates sizes grow obviously with further increase in Co content, such as with change from CoNi to 4CoNi, as compared in Figures 2g,h. These graphene-supported Co-Ni nanocatalysts have different morphologies, both in shape and size, corresponding to changes in specific surface area and metallic active sites, which strongly suggests that they would exhibit distinct catalytic effects on the hydrogen storage in MgH₂.

FIGURE 2

Figure 2. (a) SEM image of the Co/Ni(OH)_x precursor. (b,c) SEM and TEM images of as-purchased graphene. (d,f) TEM images and (e) HADDF-STEM image of the Ni nanoparticles anchored to graphene denoted as Ni@G, and the corresponding histogram for the particle size distribution (inset in d), showing an average diameter of 45 ± 7 nm. (g,h) TEM images of the CoNi nanoplates anchored to graphene denoted as CoNi@G and 4CoNi@G, respectively.

Figure 3A compares the TG curves of the non-doped and Ni@G-, CoNi@G-, and 4CoNi@G-doped MgH₂ samples. As compared to pure MgH₂, the hydrogen release from all Co-Ni@G catalyst-doped samples shifted to a lower temperature, where Ni@G shows the most significant improvement, i.e., the onset desorption temperature shifts from 325°C for MgH₂ to 250°C and 225°C for CoNi@G-doped and Ni@G-doped MgH₂, respectively. Similarly, the main peak for desorption shifts from 380°C for MgH₂ to 336, 325, and 285°C for 4CoNi@G-, CoNi@G-, and Ni@G-doped MgH₂, respectively, as shown in Figure 3B. These results strongly suggest that the Co-Ni nanocatalysts can cause a significant enhancement in desorption and that the introduction of Co deteriorates the catalytic effect of Ni. A similar phenomenon was also demonstrated by the activation testing at 300°C. As shown in Figures 3C,D, both Ni@G- and CoNi@G-doped MgH₂ can be activated by two cycles. However, the initial desorption of CoNi@G-doped MgH₂ shows relatively slow kinetics as compared to Ni@G-doped MgH₂. The above results indicate that the catalytic effects of supported Co-Ni catalysts depend strongly on their composition and that the Ni element is more favorable than the Co element.

FIGURE 3

Figure 3. (A) TG curves and (B) derivative curves for MgH₂ composites with no doping (“none”) and doped with Ni@G, CoNi@G, and 4CoNi@G catalysts. (C,D) Activation curves of the initial three desorption curves for typical Ni@G- and CoNi@G-doped MgH₂ composites, respectively.

Figures 4A,D shows the isothemal desorption curves of Ni@G- and CoNi@G-doped MgH₂ samples. The Ni@G-doped MgH₂ can release about 6.5 wt% H₂ within 45 min at 260°C, while the desorption can be finished within 25 min at 280°C. In comparison, the CoNi@G-doped MgH₂ sample exhibits relatively slow kinetics, with only 5 wt% H₂ released within 60 min at 280°C. To quantitatively examine the distinct improvements in the desorption process, kinetic studies on the hydrogen release from the Ni@G-and CoNi@G-doped MgH₂ were conducted by using the JMAK (Johnson–Mehl–Avrami–Kolmogorov) model (Li et al., 2014a). On the basis of the JMAK model, the desorption kinetics can be expressed by the following equation:

$\begin{array}{ll}ln\left[-ln(1-\alpha )\right]=\eta lnk+\eta lnt& (1)\end{array}$

where α is the reaction fraction, corresponding to the beginning and completion of the reaction, η is the Avrami exponent of reaction order, k is the rate constant, and t is time. For the experimental sample data, the plot of ln[–ln(1–α)] as a function of ln(t) was linear for each curve at the various temperatures, as shown in Figures 4B,E. After calculating the rate constant lnk, the activation energy E_a can be further determined by the Arrhenius equation:

$\begin{array}{ll}k=k_{0}exp(-E_a/RT)& (2)\end{array}$

where k₀ is the pre-exponential factor, R is the gas constant, and T is absolute temperature. From the slopes of the straight lines shown in Figures 4C,F, the activation energies E_a were calculated to be about 122 and 131 kJ mol⁻¹ for the Ni@G- and CoNi@G-doped samples, both of which are lower than the reported 158 kJ mol⁻¹ of pure MgH₂. This clearly indicates that the activation energy can be significantly reduced by doping with Co-Ni nanocatalysts and that the element Ni is better than Co.

FIGURE 4

Figure 4. (A) Isothermal desorption curves, (B) Johnson-Mehl-Avrami (JMA) model plots of ln[–ln(1–α(t))] vs. ln t, and (C) Arrhenius plot of the Ni@G-doped MgH₂ at different temperatures. (D) Isothermal desorption curves, (E) Johnson-Mehl-Avrami (JMA) model plots of ln[–ln(1–α(t))] vs. lnt, and (F) Arrhenius plot of the CoNi@G-doped MgH₂ at different temperatures.

The pressure–composition isotherms for Ni@G- and CoNi@G-doped MgH₂ at different temperatures are compared in Figures 5A,C. It can be seen that both Ni@G- and CoNi@G-doped MgH₂ samples exhibit one flat plateau at different temperatures. Interestingly, CoNi@G-doped MgH₂ shows a higher pressure of desorption plateaus than Ni@G-doped MgH₂, suggesting its unfavorable thermodynamic properties. To evaluate these enthalpy changes for the two samples quantitatively, van ‘t Hoff plots of desorption based on their equilibrium pressures at various temperatures were drawn, as shown in Figures 5B,D. The obtained ΔH_d value of CoNi@G-doped MgH₂ is about ~75 kJ mol⁻¹ H₂, higher than the Ni@G-doped sample, which has a value of ~74 kJ mol⁻¹ H₂, although both are lower than that of pure MgH₂. These results clearly indicate that the desorption thermodynamics of MgH₂ can be altered but that Ni is superior to Co for this purpose.

FIGURE 5

Figure 5. (A) P–C isotherms and (B) the van 't Hoff plots for the desorption plateaus of the Ni@G-doped MgH₂ at different temperatures. (C) P–C isotherms and (D) the van 't Hoff plots for the desorption plateaus of the CoNi@G-doped MgH₂ at different temperatures.

On the basis of the above results, we can conclude that the catalytic activity of the supported Co-Ni catalysts depends strongly on their composition and morphology, with Ni@G exhibiting the best improvement effects, which can be understood through the following two aspects: (i) the compositions are first of importance because of not only their different natural electronic structures but also their effects on the morphology of catalysts; (ii) the effects of small spherical catalysts are superior to those of nanoplates. This is because the small sphere morphology has a larger specific area, which provides more active sites and lower energy barriers for desorption, and it possesses abundant grain boundaries and defects that act as favorable channels for hydrogen diffusion. Furthermore, the introduction of Co indeed decreases the activity of Ni@G for hydrogen storage in MgH₂, which can be understood through two aspects: i) introducing Co will increase of the particle size of the catalyst and its specific surface area, and thus its activity will be decreased, and ii) the electronegativity of Ni is larger than that of Co, corresponding to electron transport being easier in Ni atoms than in Co atoms, facilitating H atom dissociation and transfer. This explains why the introduction of Co exhibits an adverse catalytic effect for hydrogen storage.

Conclusion

In conclusion, the catalytic activity of supported Co–Ni nanocatalysts is demonstrated to be highly dependent on their morphology and composition. When Ni was partly substituted by Co, the shape of these nanocatalysts changed from spheres to plates, thus corresponding to a decrease in their activity. These changes intrinsically not only result in a decreased peak desorption temperature but also positively change the initial activation for sorption, with a reduction in activation energy as compared with that of a pure sample. These results provide insights into the design of catalysts for improving the hydrogen sorption of Mg-based materials.

Data Availability Statement

All datasets generated for this study are included in the article/supplementary material.

Author Contributions

XD carried out the material preparation, analyzed the XRD, SEM, and TEM results, and co-wrote the paper. HD did the property test and wrote the paper. YS supervised all the experiments, especially the material preparation. CX discussed the results and the paper. YL and QZ attained the main financial support for the research, supervised all experiments, and revised the manuscript.

Conflict of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.

Acknowledgments

This work was financially supported by the National Natural Science Foundation of China (Nos. 51701004, 51871002, 51971002), the Guangxi Key Laboratory of Information Materials (Guilin University of Electronic Technology), P. R. China (Project No. 191002-k), and the International Science and Technology Cooperation Project of the Anhui Provincial Key Research & Development Program (No. 201904b11020028).

References

Cao, Z., Ouyang, L., Wu, Y., Wang, H., Liu, J., Fang, F., et al. (2015). Dual-tuning effects of In, Al, and Ti on the thermodynamics and kinetics of Mg₈₅In₅Al₅Ti₅ alloy synthesized by plasma milling. J. Alloys Comp. 623, 354–358. doi: 10.1016/j.jallcom.2014.10.200

CrossRef Full Text | Google Scholar

Ding, X., Li, Y., Fang, F., Sun, D., and Zhang, Q. (2017). Hydrogen-induced magnesium–zirconium interfacial coupling: enabling fast hydrogen sorption at lower temperatures. J. Mater. Chem. A 5, 5067–5076. doi: 10.1039/C7TA00460E

CrossRef Full Text | Google Scholar

El-Eskandarany, M. S. (2016). Metallic glassy Zr₇₀Ni₂₀Pd₁₀ powders for improving the hydrogenation/dehydrogenation behavior of MgH₂. Sci. Rep. 6:26936. doi: 10.1038/srep26936

PubMed Abstract | CrossRef Full Text | Google Scholar

Fang, L., Feng, J. J., Shi, X., Si, T., Song, Y., Jia, H., et al. (2019). Turning bulk materials into 0D, 1D and 2D metallic nanomaterials by selective aqueous corrosion. Chem. Commun. 55, 10476–10479. doi: 10.1039/C9CC04807C

PubMed Abstract | CrossRef Full Text | Google Scholar

German, E., and Gebauer, R. (2016). Improvement of hydrogen vacancy diffusion kinetics in MgH₂ by niobium-and zirconium-doping for hydrogen storage applications. J. Phys. Chem. C 120, 4806–4812. doi: 10.1021/acs.jpcc.5b12092

CrossRef Full Text | Google Scholar

Humphries, T. D., Kalantzopoulos, G. N., Llamas-Jansa, I., Olsen, J. E., and Hauback, B. C. (2013). Reversible hydrogenation studies of NaBH₄ milled with Ni-containing additives. J. Phys. Chem. C 117, 6060–6065. doi: 10.1021/jp312105w

CrossRef Full Text | Google Scholar

Kalantzopoulos, G. N., Guzik, M. N., Deledda, S., Heyn, R. H., Muller, J., and Hauback, B. C. (2014). Destabilization effect of transition metal fluorides on sodium borohydride. Phys. Chem. Chem. Phys. 16, 20483–20491. doi: 10.1039/C4CP02899F

PubMed Abstract | CrossRef Full Text | Google Scholar

Li, Y., Zhang, L., Zhang, Q., Fang, F., Sun, D., Li, K., et al. (2014a). In situ embedding of Mg₂NiH₄ and YH₃ nanoparticles into bimetallic hydride NaMgH₃ to inhibit phase segregation for enhanced hydrogen storage. J. Phys. Chem. C. 118, 23635–23644. doi: 10.1021/jp508395s

CrossRef Full Text | Google Scholar

Li, Y., Zhang, Q., Fang, F., Song, Y., Sun, D., Ouyang, L., et al. (2014b). Facile self-assembly of light metal borohydrides with controllable nanostructures. RSC Adv. 4, 983–986. doi: 10.1039/C3RA45867A

CrossRef Full Text | Google Scholar

Li, Y., Zhou, G., Fang, F., Yu, X., Zhang, Q., Ouyang, L., et al. (2011). De-/re- hydrogenation features of NaAlH₄ confined exclusively in nanopores. Acta Mater. 59, 1829–1838. doi: 10.1016/j.actamat.2010.11.049

CrossRef Full Text | Google Scholar

Lin, H., Tang, J., Yu, Q., Wang, H., Ouyang, L., Zhao, Y., et al. (2014). Symbiotic CeH_2.73/CeO₂ catalyst: a novel hydrogen pump. Nano Energy. 9, 80–87. doi: 10.1016/j.nanoen.2014.06.026

CrossRef Full Text | Google Scholar

Liu, D. M., Tan, Q. J., Gao, C., Sun, T., and Li, Y. T. (2015). Reversible hydrogen storage properties of LiBH₄ combined with hydrogenated Mg₁₁CeNi alloy. Int. J. Hydrog. Energ. 40, 6600–6605. doi: 10.1016/j.ijhydene.2015.03.130

CrossRef Full Text | Google Scholar

Liu, M., Zhao, S., Xiao, X., Chen, M., Sun, C., Yao, Z., et al. (2019). Novel 1D carbon nanotubes uniformly wrapped nanoscale MgH₂ for efficient hydrogen storage cycling performances with extreme high gravimetric and volumetric capacities. Nano Energy. 61, 540–549. doi: 10.1016/j.nanoen.2019.04.094

CrossRef Full Text | Google Scholar

Liu, X., Wu, N., Cui, C., Li, Y., and Bi, N. (2015). Facile preparation of carbon-coated Mg nanocapsules as light microwave absorber. Mater. Lett. 149, 12–14. doi: 10.1016/j.matlet.2015.02.095

CrossRef Full Text | Google Scholar

Liu, Y., Du, H., Zhang, X., Yang, Y., Gao, M., and Pan, H. (2016). Superior catalytic activity derived from a two-dimensional Ti₃C₂ precursor towards the hydrogen storage reaction of magnesium hydride. Chem. Commun. 52, 705–708. doi: 10.1039/C5CC08801A

PubMed Abstract | CrossRef Full Text | Google Scholar

Ma, Z., Zhang, J., Zhu, Y., Lin, H., Liu, Y., Zhang, Y., et al. (2018). Facile synthesis of carbon supported nano-Ni particles with superior catalytic effect on hydrogen storage kinetics of MgH₂. ACS Appl. Energy Mater. 1, 1158–1165. doi: 10.1021/acsaem.7b00266

CrossRef Full Text | Google Scholar

Møller, K. T., Jensen, T. R., Akiba, E., and Li, H. W. (2017). Hydrogen-A sustainable energy carrier. Prog. Nat. Sci. Mater. Int. 27, 34–40. doi: 10.1016/j.pnsc.2016.12.014

CrossRef Full Text | Google Scholar

Ouyang, L. Z., Cao, Z. J., Wang, H., Liu, J. W., Sun, D. L., Zhang, Q. A., et al. (2014). Enhanced dehydriding thermodynamics and kinetics in Mg(In)–MgF₂ composite directly synthesized by plasma milling. J. Alloys Comp. 586, 113–117. doi: 10.1016/j.jallcom.2013.10.029

CrossRef Full Text | Google Scholar

Paskevicius, M., Sheppard, D. A., and Buckley, C. E. (2010). Thermodynamic changes in mechanochemically synthesized magnesium hydride nanoparticles. J. Am. Chem. Soc. 132, 5077–5083. doi: 10.1021/ja908398u

PubMed Abstract | CrossRef Full Text | Google Scholar

Schneemann, A., White, J. L., Kang, S. Y., Jeong, S., Wan, L. F., and Cho, E. S. (2018). Nanostructured metal hydrides for hydrogen storage. Chem. Rev. 118, 10775–10839. doi: 10.1021/acs.chemrev.8b00313

PubMed Abstract | CrossRef Full Text | Google Scholar

Shen, Z., Wang, Z., Zhang, M., Gao, M., Hu, J., Du, F., et al. (2018). A novel solid-solution MXene (Ti_0.5V_0.5)₃C₂ with high catalytic activity for hydrogen storage in MgH₂. Materialia. 1, 114–120. doi: 10.1016/j.mtla.2018.04.007

CrossRef Full Text | Google Scholar

Shevlin, S. A., and Guo, Z. X. (2013). MgH₂ dehydrogenation thermodynamics: nanostructuring and transition metal doping. J. Phys. Chem. C. 117, 10883–10891. doi: 10.1021/jp3117648

CrossRef Full Text | Google Scholar

Si, T. Z., Zhang, X. Y., Feng, J. J., Ding, X. L., and Li, Y. T. (2018). Enhancing hydrogen sorption in MgH2 by controlling particle size and contact of Ni catalysts. Rare Met. 1–8. doi: 10.1007/s12598-018-1087-x

CrossRef Full Text | Google Scholar

Wang, Z., Ren, Z., Jian, N., Gao, M., Hu, J., Du, F., et al. (2018). Vanadium oxide nanoparticles supported on cubic carbon nanoboxes as highly active catalyst precursors for hydrogen storage in MgH₂. J. Mater. Chem. A. 6, 16177–16185. doi: 10.1039/C8TA05437A

CrossRef Full Text | Google Scholar

Wang, Z., Zhang, X., Ren, Z., Liu, Y., Hu, J., Li, H. W., et al. (2019). In situ formed ultrafine NbTi nanocrystals from a NbTiC solid-solution MXene for hydrogen storage in MgH₂. J. Mater. Chem. A. 7, 14244–14252. doi: 10.1039/C9TA03665B

CrossRef Full Text | Google Scholar

Wei, P., Huang, W., Ding, X., Li, Y., Liu, Z., Si, T., et al. (2018). Intrinsic alterations in the hydrogen desorption of Mg₂NiH₄ by solid dissolution of titanium. Dalton Trans. 47, 8418–8426. doi: 10.1039/C8DT01591K

PubMed Abstract | CrossRef Full Text | Google Scholar

Xia, G., Tan, Y., Chen, X., Sun, D., Guo, Z., Liu, H., et al. (2015). Monodisperse magnesium hydride nanoparticles uniformly self-assembled on graphene. Adv. Mater. 27, 5981–5988. doi: 10.1002/adma.201502005

PubMed Abstract | CrossRef Full Text | Google Scholar

Yao, X., Wu, C., Du, A., Zou, J., Zhu, Z., Wang, P., et al. (2007). Metallic and carbon nanotube-catalyzed coupling of hydrogenation in magnesium. J. Am. Chem. Soc. 129, 15650–15654. doi: 10.1021/ja0751431

PubMed Abstract | CrossRef Full Text | Google Scholar

Zheng, S., Fang, F., Zhou, G., Chen, G., and Sun, D. (2008). Hydrogen storage properties of space-confined NaAlH₄ nanoparticles in ordered mesoporous silica. Chem. Mater. 20, 3954–3958. doi: 10.1021/cm8002063

CrossRef Full Text | Google Scholar