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Materials and Technologies for Hydrogen and Fuel Cells

A topical collection in Materials (ISSN 1996-1944). This collection belongs to the section "Energy Materials".

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Editors


E-Mail Website1 Website2
Collection Editor
Istituto di Tecnologie Avanzate per l'Energia, Consiglio Nazionale delle Ricerche, 98126 Messina, Italy
Interests: materials for energy, electrochemistry, systems, fuel cells, electrolysis, photo-electrochemical cells, batteries, physico-chemical characterisation
Special Issues, Collections and Topics in MDPI journals

E-Mail Website
Collection Editor
CNR-ITAE Institute for Advanced Energy Technologies “N. Giordano”, Via Salita S. Lucia sopra Contesse 5, 98126 Messina, Italy
Interests: polymer electrolyte fuel cells; direct alcohol fuel cells; water electrolysis; metal–air batteries; dye-sensitized solar cells; photo-electrolysis; carbon dioxide electro-reduction
Special Issues, Collections and Topics in MDPI journals

E-Mail Website
Collection Editor
CNR—ITAE, Istituto di Tecnologie Avanzate per l’Energia “Nicola Giordano”, Via Salita S. Lucia sopra Contesse n. 5, 98126 S. Lucia-Messina, Italy
Interests: polymers, membranes, nano carbon materials, metal oxides and hybrid materials, fuel cells, supercapacitors, electrochemistry
Special Issues, Collections and Topics in MDPI journals

Topical Collection Information

After publishing the Special Issue “Hydrogen and Fuel Cells: From Materials to Systems”, we would like to announce the publication of a collection on “Materials and Technologies for Hydrogen and Fuel Cells”. The objective is to highlight new results and advances in materials science, processing, characterization, technology development and system testing of various types of fuel cells and hydrogen processes. As is well known, the diffusion of efficient and sustainable energy conversion technologies and zero-emission vehicles on a wide scale is largely required to address urgent environmental issues such as polluting emissions, global warming and climate change. Fuel cells can provide an effective solution and hydrogen together with electricity can become the main energy vectors in the future energy system, covering most of the energy chain. These technologies comply with the requirement of a low carbon economy by 2050, where both hydrogen and a highly efficient distributed power generation using fuel cells, providing both electrical power and heat, can significantly reduce the emission of greenhouse gases. Original papers are solicited on all types of fuel cells and hydrogen production technologies. Recent developments in advanced materials, processes, characterization, stack designs, and systems are of particular interest together with contributions addressing emerging fields and new applications of these technologies. Articles and reviews dealing with fuel cells and hydrogen for different market applications, including zero-emission vehicles, grid-balancing service, power-to-gas, portable power systems, combined heat and power (CHP) production, consumer devices and distributed energy systems are very welcome.

Dr. Antonino Salvatore Aricò
Dr. Vincenzo Baglio
Dr. Francesco Lufrano
Guest Editors

Manuscript Submission Information

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Published Papers (6 papers)

2024

Jump to: 2023, 2021, 2020, 2019

12 pages, 5852 KiB  
Article
Development of Cost-Effective Sn-Free Al-Bi-Fe Alloys for Efficient Onboard Hydrogen Production through Al–Water Reaction
by Rui Deng, Mingshuai Wang, Hao Zhang, Ruijun Yao, Kai Zhen, Yifei Liu, Xingjun Liu and Cuiping Wang
Materials 2024, 17(20), 4973; https://doi.org/10.3390/ma17204973 - 11 Oct 2024
Viewed by 883
Abstract
Leveraging the liquid-phase immiscibility effect and phase diagram calculations, a sequence of alloy powders with varying Fe content was designed and fabricated utilizing the gas atomization method. Microstructural characterizations, employing SEM, EDS, and XRD analyses, revealed the successful formation of an incomplete shell [...] Read more.
Leveraging the liquid-phase immiscibility effect and phase diagram calculations, a sequence of alloy powders with varying Fe content was designed and fabricated utilizing the gas atomization method. Microstructural characterizations, employing SEM, EDS, and XRD analyses, revealed the successful formation of an incomplete shell on the surfaces of Al-Bi-Fe powders, obviating the need for Sn doping. This study systematically investigated the microstructure, hydrolysis performance, and hydrolysis process of these alloys in deionized water. Notably, Al-10Bi-7Fe exhibited the highest hydrogen production, reaching 961.0 NmL/g, while Al-10Bi-10Fe demonstrated the peak conversion rate at 92.99%. The hydrolysis activation energy of each Al-Bi-Fe alloy powder was calculated using the Arrhenius equation, indicating that a reduction in activation energy was achieved through Fe doping. Full article
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Figure 1
<p>The schematic experimental setup for the hydrolysis test.</p>
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<p>(<b>a</b>) Calculated vertical phase diagrams of Al-10Bi-Fe (wt.%); (<b>b</b>–<b>d</b>) calculated phase fractions diagrams of Al-10Bi-(3, 7, 10) Fe (wt.%).</p>
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<p>SEM images at various magnifications of as-atomized Al-Bi-Fe alloy powders: (<b>a</b>–<b>a<sub>2</sub></b>) Al-10Bi-3Fe (wt.%); (<b>b</b>–<b>b<sub>2</sub></b>) Al-10Bi-7Fe (wt.%); and (<b>c</b>–<b>c<sub>2</sub></b>) Al-10Bi-10Fe (wt.%).</p>
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<p>EDS analysis of the cross-section of the Al-Bi-Fe alloy powders: (<b>a</b>) Al-10Bi-3Fe, with element distributions: (<b>a<sub>1</sub></b>) Al; (<b>a<sub>2</sub></b>) Bi; (<b>a<sub>3</sub></b>) Fe; (<b>b</b>) Al-10Bi-7Fe (wt.%), with element distributions: (<b>b<sub>1</sub></b>) Al; (<b>b<sub>2</sub></b>) Bi; (<b>b<sub>3</sub></b>) Fe; (<b>c</b>) Al-10Bi-10Fe (wt.%), with element distributions: (<b>c<sub>1</sub></b>) Al; (<b>c<sub>2</sub></b>) Bi; (<b>c<sub>3</sub></b>) Fe.</p>
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<p>XRD patterns of the as-atomized Al-Bi-Fe alloy powders (<b>a</b>) separated XRD patterns; (<b>b</b>) stacked patterns focusing on the Al (111) peak.</p>
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<p>Charts of the hydrolysis of Al-Bi-Fe variations using deionized water at different reaction temperatures ranging from 30 to 50 °C: (<b>a</b>) the hydrogen yield vs. time curve; (<b>b</b>) the conversion rate.</p>
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<p>Cost and hydrolysis performance for various active Al alloys: (1) red area indicates Ga, In, Sn doping alloys; (2) yellow area indicates Ga, In-free alloys; and (3) green area indicates Sn-free alloys. The data are drawn from references [<a href="#B23-materials-17-04973" class="html-bibr">23</a>,<a href="#B24-materials-17-04973" class="html-bibr">24</a>,<a href="#B26-materials-17-04973" class="html-bibr">26</a>,<a href="#B27-materials-17-04973" class="html-bibr">27</a>,<a href="#B29-materials-17-04973" class="html-bibr">29</a>,<a href="#B30-materials-17-04973" class="html-bibr">30</a>].</p>
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<p>Plots of the hydrolysis of the Al-Bi-Fe variations using deionized water at different reaction temperatures ranging from 30 to 50 °C (<b>a</b>) hydrogen yield rates vs. time curves, (<b>b</b>) the Arrhenius plots.</p>
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<p>SEM images of the hydrolysis products of Al-Bi-Fe variations using deionized water at different reaction temperatures ranging from 30 to 50 °C.</p>
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<p>The morphological changes on the surface of Al-Bi-Fe alloy powders at different stages of the hydrolysis process, along with a schematic representation of the reaction mechanism.</p>
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2023

Jump to: 2024, 2021, 2020, 2019

13 pages, 3140 KiB  
Article
A Comparative Study of CCM and CCS Membrane Electrode Assemblies for High-Temperature Proton Exchange Membrane Fuel Cells with a CsH5(PO4)2-Doped Polybenzimidazole Membrane
by Yizhe Li, Zhiyong Fu, Yifan Li and Guichen Zhang
Materials 2023, 16(11), 3925; https://doi.org/10.3390/ma16113925 - 24 May 2023
Cited by 3 | Viewed by 3146
Abstract
Membrane electrode assemblies (MEAs) are critical components in influencing the electrochemical performance of high-temperature proton exchange membrane fuel cells (HT-PEMFCs). MEA manufacturing processes are mainly divided into the catalyst-coated membrane (CCM) and the catalyst-coated substrate (CCS) methods. For conventional HT-PEMFCs based on phosphoric [...] Read more.
Membrane electrode assemblies (MEAs) are critical components in influencing the electrochemical performance of high-temperature proton exchange membrane fuel cells (HT-PEMFCs). MEA manufacturing processes are mainly divided into the catalyst-coated membrane (CCM) and the catalyst-coated substrate (CCS) methods. For conventional HT-PEMFCs based on phosphoric acid-doped polybenzimidazole (PBI) membranes, the wetting surface and extreme swelling of the PA-doped PBI membranes make the CCM method difficult to apply to the fabrication of MEAs. In this study, by taking advantage of the dry surface and low swelling of a CsH5(PO4)2-doped PBI membrane, an MEA fabricated by the CCM method was compared with an MEA made by the CCS method. Under each temperature condition, the peak power density of the CCM-MEA was higher than that of the CCS-MEA. Furthermore, under humidified gas conditions, an enhancement in the peak power densities was observed for both MEAs, which was attributed to the increase in the conductivity of the electrolyte membrane. The CCM-MEA exhibited a peak power density of 647 mW cm−2 at 200 °C, which was ~16% higher than that of the CCS-MEA. Electrochemical impedance spectroscopy results showed that the CCM-MEA had lower ohmic resistance, which implied that it had better contact between the membrane and catalyst layer. Full article
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Figure 1
<p>Schematics of preparation process of CCM-MEA and CCS-MEA.</p>
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<p>Polarization curves of CCM-MEA and CCS-MEA measured at (<b>a</b>) 160 °C, (<b>b</b>) 180 °C, and (<b>c</b>) 200 °C with dry H<sub>2</sub> and O<sub>2</sub>.</p>
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<p>Polarization curves of CCM-MEA and CCS-MEA measured at (<b>a</b>) 160 °C, (<b>b</b>) 180 °C, and (<b>c</b>) 200 °C, with humidifying H<sub>2</sub> and dry O<sub>2</sub>.</p>
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<p>Impedance curve of CCS-MEA measured at 0.6 V and 160 °C (its equivalent circuit and fitting curves are included).</p>
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<p>Impedance curves measured for CCS-MEA and CCM-MEA at 0.6 V and (<b>a</b>) 160 °C, (<b>b</b>) 180 °C, and (<b>c</b>) 200 °C under dry gas conditions (feeding with dry H<sub>2</sub> and O<sub>2</sub>) and humidifying gas conditions (feeding with 10% RH H<sub>2</sub> and dry O<sub>2</sub>).</p>
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<p>Electrochemical resistance values (R<sub>Ω</sub>, R<sub>ct</sub> and R<sub>p</sub>) of CCM-MEA and CCS-MEA measured at 0.6 V from 160 to 200 °C, feeding with (<b>a</b>) dry H<sub>2</sub> and dry O<sub>2</sub> and (<b>b</b>) 10% RH H<sub>2</sub> and dry O<sub>2</sub>, respectively.</p>
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2021

Jump to: 2024, 2023, 2020, 2019

13 pages, 1751 KiB  
Article
Waste Aluminum Application as Energy Valorization for Hydrogen Fuel Cells for Mobile Low Power Machines Applications
by Xavier Salueña-Berna, Marc Marín-Genescà, Lluís Massagués Vidal and José M. Dagà-Monmany
Materials 2021, 14(23), 7323; https://doi.org/10.3390/ma14237323 - 30 Nov 2021
Cited by 11 | Viewed by 2666
Abstract
This article proposes a new model of power supply for mobile low power machines applications, between 10 W and 30 W, such as radio-controlled (RC) electric cars. This power supply is based on general hydrogen from residual aluminum and water with NaOH, so [...] Read more.
This article proposes a new model of power supply for mobile low power machines applications, between 10 W and 30 W, such as radio-controlled (RC) electric cars. This power supply is based on general hydrogen from residual aluminum and water with NaOH, so it is proposed energy valorization of aluminum waste. In the present research, a theoretical model allows us to predict the requested aluminum surface and the required flow of hydrogen has been developed, also considering, in addition to the geometry and purity of the material, two key variables as the temperature and the molarity of the alkaline solution used in the hydrogen production process. Focusing on hydrogen production, isopropyl alcohol plays a key role in the reactor’s fuel cell vehicle as it filters out NaOH particles and maintains a constant flow of hydrogen for the operation of the machine, keeping the reactor temperature controlled. Finally, a comparison of the theoretical and experimental data has been used to validate the developed model using aluminum sheets from ring cans to generate hydrogen, which will be used as a source of hydrogen in a power fuel cell of an RC car. Finally, the manuscript shows the parts of the vehicle’s powertrain, its behavior, and mode of operation. Full article
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Figure 1
<p>Theoretical representation of corrosion rate of a sheet by the reaction of aluminum–water.</p>
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<p>Hydrogen generation, filtering, and drying areas for the fuel cell of an RC car. (Photography: Aleix Llobet).</p>
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<p>Decrease in the thickness (2<span class="html-italic">e</span>) of an aluminum foil (mm/h) at different molarities, at 25 °C, for 3 h.</p>
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<p>Comparison of the volume of hydrogen generated (in the figure <b>above</b>) from 104 sheet metal chips (chips) and a sheet (sheet), with the similar beginning active surface NaOH solution in a 7.5 M (with isopropyl alcohol), at 25 °C and its theoretical active surface as a function of time (in the figure <b>below</b>).</p>
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<p>Hydrogen flow generated comparison <span class="html-italic">Q</span><sub>(<span class="html-italic">H</span><sub>2</sub>,<span class="html-italic">t</span>)</sub> from a 7.5 M sheet, with and without isopropyl alcohol at initially 60 °C.</p>
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<p>Theoretical hydrogen flow comparison of <span class="html-italic">Q</span><sub>(<span class="html-italic">H</span><sub>2</sub>,<span class="html-italic">t</span>)</sub> produced from 15 rings and those obtained in the vehicle tank under the test conditions. The intensity generated by the fuel cell during the test is also shown.</p>
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11 pages, 2918 KiB  
Article
Flexible Supercapacitors Based on Graphene/Boron Nitride Nanosheets Electrodes and PVA/PEI Gel Electrolytes
by Chan Wang, Kuan Hu, Ying Liu, Ming-Rong Zhang, Zhiwei Wang and Zhou Li
Materials 2021, 14(8), 1955; https://doi.org/10.3390/ma14081955 - 14 Apr 2021
Cited by 23 | Viewed by 4595
Abstract
All-solid-state supercapacitors have gained increasing attention as wearable energy storage devices, partially due to their flexible, safe, and lightweight natures. However, their electrochemical performances are largely hampered by the low flexibility and durability of current polyvinyl alcohol (PVA) based electrolytes. Herein, a novel [...] Read more.
All-solid-state supercapacitors have gained increasing attention as wearable energy storage devices, partially due to their flexible, safe, and lightweight natures. However, their electrochemical performances are largely hampered by the low flexibility and durability of current polyvinyl alcohol (PVA) based electrolytes. Herein, a novel polyvinyl alcohol-polyethyleneimine (PVA-PEI) based, conductive and elastic hydrogel was devised as an all-in-one electrolyte platform for wearable supercapacitor (WSC). For proof-of-concept, we assembled all-solid-state supercapacitors based on boron nitride nanosheets (BNNS) intercalated graphene electrodes and PVA-PEI based gel electrolyte. Furthermore, by varying the electrolyte ions, we observed synergistic effects between the hydrogel and the electrode materials when KOH was used as electrolyte ions, as the Graphene/BNNS@PVA-PEI-KOH WSCs exhibited a significantly improved areal capacitance of 0.35 F/cm2 and a smaller ESR of 6.02 ohm/cm2. Moreover, due to the high flexibility and durability of the PVA-PEI hydrogel electrolyte, the developed WSCs behave excellent flexibility and cycling stability under different bending states and after 5000 cycles. Therefore, the conductive, yet elastic, PVA-PEI hydrogel represents an attractive electrolyte platform for WSC, and the Graphene/BNNS@PVA-PEI-KOH WSCs shows broad potentials in powering wearable electronic devices. Full article
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Figure 1
<p>A schematic showing the fabrication process and structure of the wearable supercapacitor (WSC). (<b>a</b>) The carbon cloth was used as a current collector. (<b>b</b>) The carbon nanotubes (CNTs) were loaded on the carbon cloth through filtration, where sodium dodecylbenzene sulfonate (SDBS) was used as a dispersant. (<b>c</b>) The graphene was mounted on the CNTs layer through filtration, where boron nitride nanosheets (BNNS) was used to prevent graphene from collapsing. (<b>d</b>) The as-fabricated WSC was assembled with hydrogel used as a solid electrolyte. (<b>e</b>) The schematic structure of the WSC. (<b>f</b>) The WSCs could be integrated into clothing to power wearable devices.</p>
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<p>Schematic showing the fabrication process and the properties of the ionic hydrogel. (<b>a</b>) The preparation process and structure of the ionic hydrogel. (<b>b</b>) The as-fabricated hydrogel exhibited superior transparency and mechanical elasticity. The SEM images of the hydrogel showed a porous structure. (<b>c</b>) The Fourier transform infrared spectroscopy (FTIR) spectra of PVA-PEI-based ionic hydrogel. (<b>d</b>) The tensile stress–strain curves of PVA and PVA-PEI-based hydrogel.</p>
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<p>SEM images of the CC/CNT/graphene electrode. (<b>a</b>) SEM image of the carbon cloth. (<b>b</b>) SEM image of the carbon cloth loaded with CNTs. (<b>c</b>) SEM image of the carbon cloth loaded with CNT and graphene. (<b>d</b>) The BNNS inserting into layered graphene sheets to prevent collapse. (<b>e</b>) SEM images and the corresponding Energy Disperse Spectroscopy (EDS) elemental mapping of (<b>C</b>,<b>B</b>) for CC/CNT/graphene electrode.</p>
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<p>The electrochemical behavior of the WSCs. (<b>a</b>) The interaction among the electrolyte, BNNS and graphene. (<b>b</b>) the optical image of the WSC. CV (<b>c</b>) and galvanic charge/discharge (GCD) (<b>d</b>) curves of the WSC based on G@H. CV (<b>e</b>) and GCD (<b>f</b>) curves of the WSC based on G/BNNS@H. (<b>g</b>) Areal capacitances of WSCs at different scan rates. (<b>h</b>) Nyquist plot for WSCs based on G/BNNS@H and G@H.</p>
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<p>The electrochemical behavior of the WSCs. (<b>a</b>) CV curves of the WSC based on G/BNNS@H/KOH. (<b>b</b>) CV curves of the WSC based on G/BNNS@H/H<sub>2</sub>SO<sub>4</sub>. (<b>c</b>) Areal capacitance of WSCs at different scan rates. (<b>d</b>) Nyquist plot of WSCs. (<b>e</b>) The conductance of WSCs. (<b>f</b>) Cycling stability of WSCs at a current density of 0.53 mA/cm<sup>2</sup>.</p>
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<p>The electrochemical performance of the WSC with G/BNNS@H/KOH. (<b>a</b>) CV curves of the SC under different bending states obtained at a scan rate of 40 mV/s. (<b>b</b>) Cycling stability of WSCs with stage bending at a current density of 0.53 mA/cm<sup>2</sup>. (<b>c</b>) GCD curves of single/two/three WSCs connected in series. (<b>d</b>) GCD curves of single/two/three WSCs connected in parallel. (<b>e</b>) The timer powered by three WSCs linked in series. (<b>f</b>) The WSCs were anchored on cloth for powering the wearable electronic devices.</p>
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2020

Jump to: 2024, 2023, 2021, 2019

13 pages, 4803 KiB  
Article
Characterization of Glass-Ceramic Sealant for Solid Oxide Fuel Cells at Operating Conditions by Electrochemical Impedance Spectroscopy
by Roberto Spotorno, Marlena Ostrowska, Simona Delsante, Ulf Dahlmann and Paolo Piccardo
Materials 2020, 13(21), 4702; https://doi.org/10.3390/ma13214702 - 22 Oct 2020
Cited by 10 | Viewed by 2659
Abstract
A commercially available glass-ceramic composition is applied on a ferritic stainless steel (FSS) substrate reproducing a type of interface present in solid oxide fuel cells (SOFCs) stacks. Electrochemical impedance spectroscopy (EIS) is used to study the electrical response of the assembly in the [...] Read more.
A commercially available glass-ceramic composition is applied on a ferritic stainless steel (FSS) substrate reproducing a type of interface present in solid oxide fuel cells (SOFCs) stacks. Electrochemical impedance spectroscopy (EIS) is used to study the electrical response of the assembly in the temperature range of 380–780 °C and during aging for 250 h at 780 °C. Post-experiment analyses, performed by means of X-ray diffraction (XRD), and along cross-sections by scanning electron microscopy (SEM) and energy dispersive X-ray (EDX) analysis, highlight the microstructural changes promoted by aging conditions over time. In particular, progressive crystallization of the glass-ceramic, high temperature corrosion of the substrate and diffusion of Fe and Cr ions from the FSS substrate into the sealant influence the electrical response of the system under investigation. The electrical measurements show an increase in conductivity to 5 × 10−6 S∙cm−1, more than one order of magnitude below the maximum recommended value. Full article
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Graphical abstract

Graphical abstract
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<p>Detail of a stack scheme showing the position of sealing and its interfaces. ① indicates the sealing portions in contact with steel at both sides; ② indicates the sealing portions in contact with steel on one side and ceramic on the other side.</p>
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<p>Nyquist plot of EIS measured at 780 °C (circles) and fit (solid line). The inset shows a schematic model of the equivalent electric circuit used for fitting.</p>
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<p>Evolution over time of (<b>a</b>) the EIS contributions; (<b>b</b>) thickness of the interaction layer; (<b>c</b>) crystallinity and (<b>d</b>) the roughness ratio. Data plotted as empty triangles in (<b>a</b>) were not taken into account for fitting the P-II trend.</p>
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<p>Evolution over time of (<b>a</b>) the EIS contributions; (<b>b</b>) thickness of the interaction layer; (<b>c</b>) crystallinity and (<b>d</b>) the roughness ratio. Data plotted as empty triangles in (<b>a</b>) were not taken into account for fitting the P-II trend.</p>
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<p>Diffraction profiles of samples after sintering (red), aged for 100 h (green) and for 250 h (blue). Peaks not related to the Ba<sub>3</sub>Si<sub>2</sub>O<sub>8</sub> phase are indicated in the spectra with (▴) for the Fe-Cr alloy and (⦁) for MgCrO<sub>4</sub>.</p>
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<p>SEM-BSE cross-section image and EDX line scans of the sample (<b>a</b>) before aging and (<b>b</b>) aged for 250 h at 780 °C.</p>
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<p>Frequency dependence of (<b>a</b>) the real part, Z’, and (<b>b</b>) the imaginary part, −Z’’, measured in the temperature range of 380–780 °C, during heating.</p>
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<p>Frequency dependence of (<b>a</b>) the real part, Z’, and (<b>b</b>) the imaginary part, −Z’’, measured in the temperature range of 280–780 °C, during cooling.</p>
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<p>Temperature dependence of the specific conductivities for the high (P-I)- and low (P-II)-frequency processes (<b>a</b>) during heating and (<b>b</b>) cooling after aging for 250 h at 780 °C. Labels report the activation energies of the corresponding segments. Dashed lines indicate the softening temperature (Ts) and the glass transition temperature (Tg).</p>
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2019

Jump to: 2024, 2023, 2021, 2020

64 pages, 13606 KiB  
Review
Alanates, a Comprehensive Review
by Karina Suárez-Alcántara, Juan Rogelio Tena-Garcia and Ricardo Guerrero-Ortiz
Materials 2019, 12(17), 2724; https://doi.org/10.3390/ma12172724 - 25 Aug 2019
Cited by 34 | Viewed by 5031
Abstract
Hydrogen storage is widely recognized as one of the biggest not solved problem within hydrogen technologies. The slow development of the materials and systems for hydrogen storage has resulted in a slow spread of hydrogen applications. There are many families of materials that [...] Read more.
Hydrogen storage is widely recognized as one of the biggest not solved problem within hydrogen technologies. The slow development of the materials and systems for hydrogen storage has resulted in a slow spread of hydrogen applications. There are many families of materials that can store hydrogen; among them, the alanate family can be of interest. Basic research papers and reviews have been focused on alanates of group 1 and 2. However, there are many alanates of transition metals, main group, and lanthanides that deserve attention in a review. This work is a comprehensive compilation of all known alanates. The approaches towards tuning the kinetics and thermodynamics of alanates are also covered in this review. These approaches are the formation of reactive composites, double cation alanates, or anion substitution. The crystallographic and X-ray diffraction characteristics of each alanate are presented along with this review. In the final sections, a discussion of the infrared, Raman, and thermodynamics was included. Full article
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Figure 1
<p>Periodic table of alanates. The reported alanates were collected in this “periodic table”.</p>
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<p>Mechanical milling main concepts.</p>
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<p>Dehydrogenation pathway of several deuterated alanes (adapted from [<a href="#B62-materials-12-02724" class="html-bibr">62</a>]).</p>
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<p>Crystal structure of several alanes and their calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
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<p>Crystal structure of lithium alanates and their calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
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<p>Phase diagram of LiH/Al/H<sub>2</sub> and Li<sub>3</sub>AlH<sub>6</sub>. The blue line represents the equilibrium. Data adapted from reference [<a href="#B86-materials-12-02724" class="html-bibr">86</a>]: <math display="inline"><semantics> <mrow> <mi>ln</mi> <mrow> <mo stretchy="false">(</mo> <mi>p</mi> <mo stretchy="false">)</mo> </mrow> <mo>=</mo> <mo>−</mo> <mfrac> <mrow> <mn>0.22</mn> </mrow> <mrow> <mi>R</mi> <mi>T</mi> </mrow> </mfrac> <mo>+</mo> <mn>13.89</mn> </mrow> </semantics></math>; where (in the original formula) <span class="html-italic">p</span> is in atm, <span class="html-italic">T</span> in Kelvin and <math display="inline"><semantics> <mrow> <mo>Δ</mo> <msub> <mi>H</mi> <mi>R</mi> </msub> <mo>=</mo> <mn>0.22</mn> <mo> </mo> <mi>eV</mi> </mrow> </semantics></math>. For visual reference (bottom and right) the equilibrium of Ti-doped Na<sub>3</sub>AlH<sub>6</sub> (blue zone) and NaH + Al (yellow zone) phases were included [<a href="#B88-materials-12-02724" class="html-bibr">88</a>].</p>
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<p>Crystal structure of sodium alanates and their calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 8
<p>Phase diagram of Ti-doped (Ti(OBu)<sub>4</sub>) NaAlH<sub>4</sub>, Na<sub>3</sub>AlH<sub>6</sub>, and NaH + Al. Na<sub>3</sub>AlH<sub>6</sub>/NaAlH<sub>4</sub>: <math display="inline"><semantics> <mrow> <mrow> <mi>ln</mi> <mrow> <mo stretchy="false">(</mo> <mrow> <mfrac> <mrow> <msub> <mi>p</mi> <mrow> <mi>e</mi> <mi>q</mi> </mrow> </msub> </mrow> <mi>p</mi> </mfrac> </mrow> <mo stretchy="false">)</mo> </mrow> <mo>=</mo> <mo>−</mo> <mfrac> <mrow> <mn>37</mn> <mo> </mo> <mi>kJ</mi> <mo>·</mo> <msup> <mi>mol</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> <mrow> <mi>R</mi> <mi>T</mi> </mrow> </mfrac> <mo>+</mo> <mfrac> <mrow> <mn>122</mn> <mo> </mo> <mi mathvariant="normal">J</mi> <mo>·</mo> <msup> <mi>mol</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> <mo> </mo> <msup> <mi mathvariant="normal">K</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> <mi>R</mi> </mfrac> </mrow> </mrow> </semantics></math>. NaH and Al/Na<sub>3</sub>AlH<sub>4</sub>: <math display="inline"><semantics> <mrow> <mrow> <mi>ln</mi> <mrow> <mo stretchy="false">(</mo> <mrow> <mfrac> <mrow> <msub> <mi>p</mi> <mrow> <mi>e</mi> <mi>q</mi> </mrow> </msub> </mrow> <mi>p</mi> </mfrac> </mrow> <mo stretchy="false">)</mo> </mrow> <mo>=</mo> <mo>−</mo> <mfrac> <mrow> <mn>47</mn> <mo> </mo> <mi>kJ</mi> <mo>·</mo> <msup> <mi>mol</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> <mrow> <mi>R</mi> <mi>T</mi> </mrow> </mfrac> <mo>+</mo> <mfrac> <mrow> <mn>126</mn> <mo> </mo> <mi mathvariant="normal">J</mi> <mo>·</mo> <msup> <mi>mol</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> <mo> </mo> <msup> <mi mathvariant="normal">K</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> <mi>R</mi> </mfrac> </mrow> </mrow> </semantics></math> [<a href="#B88-materials-12-02724" class="html-bibr">88</a>,<a href="#B133-materials-12-02724" class="html-bibr">133</a>].</p>
Full article ">Figure 9
<p>Crystal structure of potassium alanates and their calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 10
<p>Phase diagram of KAlH<sub>4</sub>, K<sub>3</sub>AlH<sub>6</sub>, and KH + Al. Constructed with data of reference [<a href="#B167-materials-12-02724" class="html-bibr">167</a>] K<sub>3</sub>AlH<sub>6</sub>/KAlH<sub>4</sub>: <math display="inline"><semantics> <mrow> <mi>ln</mi> <mrow> <mo stretchy="false">(</mo> <mrow> <mfrac> <mrow> <msub> <mi>p</mi> <mrow> <mi>e</mi> <mi>q</mi> </mrow> </msub> </mrow> <mi>p</mi> </mfrac> </mrow> <mo stretchy="false">)</mo> </mrow> <mo>=</mo> <mo>−</mo> <mfrac> <mrow> <mn>70</mn> <mo> </mo> <mi>kJ</mi> <mo>·</mo> <msup> <mi>mol</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> <mrow> <mi>R</mi> <mi>T</mi> </mrow> </mfrac> <mo>+</mo> <mfrac> <mrow> <mn>130</mn> <mo> </mo> <mi mathvariant="normal">J</mi> <mo>·</mo> <msup> <mi>mol</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> <mo> </mo> <msup> <mi mathvariant="normal">K</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> <mi>R</mi> </mfrac> </mrow> </semantics></math>. KH and Al/K<sub>3</sub>AlH<sub>4</sub>: <math display="inline"><semantics> <mrow> <mi>ln</mi> <mrow> <mo stretchy="false">(</mo> <mrow> <mfrac> <mrow> <msub> <mi>p</mi> <mrow> <mi>e</mi> <mi>q</mi> </mrow> </msub> </mrow> <mi>p</mi> </mfrac> </mrow> <mo stretchy="false">)</mo> </mrow> <mo>=</mo> <mo>−</mo> <mfrac> <mrow> <mn>81</mn> <mo> </mo> <mi>kJ</mi> <mo>·</mo> <msup> <mi>mol</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> <mrow> <mi>R</mi> <mi>T</mi> </mrow> </mfrac> <mo>+</mo> <mfrac> <mrow> <mn>130</mn> <mo> </mo> <mi mathvariant="normal">J</mi> <mo>·</mo> <msup> <mi>mol</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> <mo> </mo> <msup> <mi mathvariant="normal">K</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> <mi>R</mi> </mfrac> </mrow> </semantics></math>.</p>
Full article ">Figure 11
<p>Crystal structure of rubidium alanates and their calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 12
<p>Crystal structure of cesium alanates and their calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 13
<p>Crystal structure of beryllium alanates and their calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 14
<p>Crystal structure of magnesium alanates and their calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 15
<p>Crystal structure of calcium alanates and their calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 16
<p>Phase diagram of CaAlH<sub>5</sub>, CaH<sub>2</sub>, and Al. CaH<sub>2</sub> and Al/CaAlH<sub>5</sub>: <math display="inline"><semantics> <mrow> <mrow> <mi>ln</mi> <mrow> <mo stretchy="false">(</mo> <mrow> <mfrac> <mrow> <msub> <mi>p</mi> <mrow> <mi>e</mi> <mi>q</mi> </mrow> </msub> </mrow> <mi>p</mi> </mfrac> </mrow> <mo stretchy="false">)</mo> </mrow> <mo>=</mo> <mo>−</mo> <mfrac> <mrow> <mn>32</mn> <mo> </mo> <mi>kJ</mi> <mo>·</mo> <msup> <mi>mol</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> <mrow> <mi>R</mi> <mi>T</mi> </mrow> </mfrac> <mo>+</mo> <mfrac> <mrow> <mn>130</mn> <mo> </mo> <mi mathvariant="normal">J</mi> <mo>·</mo> <msup> <mi>mol</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> <mo> </mo> <msup> <mi mathvariant="normal">K</mi> <mrow> <mo>−</mo> <mn>1</mn> </mrow> </msup> </mrow> <mi>R</mi> </mfrac> </mrow> </mrow> </semantics></math> [<a href="#B224-materials-12-02724" class="html-bibr">224</a>].</p>
Full article ">Figure 17
<p>Crystal structure of strontium alanates and their calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 18
<p>Production of BaAlH<sub>4</sub> or B<sub>2</sub>AlH<sub>7</sub> from hydrogenation of Ba<sub>7</sub>Al<sub>13</sub> or Ba<sub>4</sub>Al<sub>5</sub>.</p>
Full article ">Figure 19
<p>Crystal structure of barium alanates and their calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 20
<p>Crystal structure of lanthanides alanates and their calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 21
<p>Crystal structure of Na-Li alanate and its calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 22
<p>Phase diagram of 2NaH + LiH + Al vs. Na<sub>2</sub>LiAlH<sub>6</sub>. Data adapted from references [<a href="#B274-materials-12-02724" class="html-bibr">274</a>,<a href="#B285-materials-12-02724" class="html-bibr">285</a>], <math display="inline"><semantics> <mrow> <mi>ln</mi> <mrow> <mo stretchy="false">(</mo> <mi>p</mi> <mo stretchy="false">)</mo> </mrow> <mo>=</mo> <mo>−</mo> <mfrac> <mrow> <mn>7685.3</mn> </mrow> <mi>T</mi> </mfrac> <mo>+</mo> <mn>18.3</mn> </mrow> </semantics></math> for un-catalyzed material, and <math display="inline"><semantics> <mrow> <mi>ln</mi> <mrow> <mo stretchy="false">(</mo> <mi>p</mi> <mo stretchy="false">)</mo> </mrow> <mo>=</mo> <mo>−</mo> <mfrac> <mrow> <mn>6894.9</mn> </mrow> <mi>T</mi> </mfrac> <mo>+</mo> <mn>17.0</mn> </mrow> </semantics></math> for material catalyzed with TiF<sub>4</sub>. In the original formulae, <span class="html-italic">p</span> is in atm, and <span class="html-italic">T</span> in Kelvin.</p>
Full article ">Figure 23
<p>Crystal structure of Li-K alanate and its calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 24
<p>Crystal structure of Li-Mg alanates and its calculated diffraction patterns (λ = Cu<sub>kα1</sub>)</p>
Full article ">Figure 25
<p>Crystal structure of Li-Ca mixted alanate and its calculated diffraction patterns (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 26
<p>Crystal structure of Na-K mixed alanate and its calculated diffraction pattern (λ = Cu<sub>kα1</sub>).</p>
Full article ">Figure 27
<p>Normal modes of vibration of tetrahedral [AlH<sub>4</sub>]<sup>−</sup>. Adapted from reference [<a href="#B302-materials-12-02724" class="html-bibr">302</a>].</p>
Full article ">Figure 28
<p>Normal modes of vibration of octahedral [AlH<sub>6</sub>]<sup>3−</sup>. Adapted from reference [<a href="#B302-materials-12-02724" class="html-bibr">302</a>].</p>
Full article ">Figure 29
<p>Most intense peak of infrared vibrations in the group 1 alanates, MAlH<sub>4</sub>. (<b>a</b>) Stretching, (<b>b</b>) Bending.</p>
Full article ">Figure 30
<p>Most intense peak of infrared vibrations in the group 1 intermediaries, M<sub>3</sub>AlH<sub>6</sub>. The red dots are an extrapolation based on the fitted curve.</p>
Full article ">Figure 31
<p>Most intense Raman peak in the group 1 alanates. (<b>a</b>) Stretching and (<b>b</b>) Bending modes. The red dots are an extrapolation based on the fitted curve.</p>
Full article ">
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