It is well know that the properties of nano-objects differ from those of their macroscopic analogs. Any system of nanometric size shows characteristics that strongly depend on its size and geometric form. It is mainly because the major part of atoms (or molecules) of nano-volume are located at the object surface and their cohesive energy is smaller than for the atoms in the bulk. As a consequence, the density of the nanoobjects is not homogeneous, and may decrease close to the object boundary. Here we show that when a fluid is confined in nano-volume, delimited by non-interacting pore walls, its density is on average smaller than the bulk density. The heterogeneous distribution of fluid density results from the nano-confinement, and progressively weakens when the pore size increases: it disappears for pores larger than 5 nm. On the other side, the fluid density approaches the ideal gas values in the limit of very small pores. This effect should be distinguished from the well know heterogeneity of density of fluids adsorbed in nanopores, driven by the difference between the strength of fluid-fluid and fluid-pore wall interactions. The reported observation has non-trivial influence on evaluation of excess/total adsorption in nanopores, as these two quantities are calculated assuming the known – and homogeneous – bulk density of gas in the pore. Additionally, the gas density in the pores depends on the definition of the pore volume which is neither straightforward nor unique. We analyze this phenomenon on an example of five gases: H2, CH4, the two intensively studied energy vectors, and N2, Ar, and Kr, commonly used for characterization of porous structures. Two model pore geometries with not adsorbing soft walls are analyzed (slit-shaped and cylindrical). For H2, the distributions of densities of gas confined in adsorbing and not adsorbing pores are compared and commented.

The adequate choice of the interaction model is essential to reproduce qualitatively and estimate quantitatively the experimentally observed characteristics of materials or phenomena in computer simulations. Here we present the results of a benchmarking of density-functional theory calculations of rigid and flexible metal-organic frameworks (MOFs). The stability of these systems depends on the dispersion interactions. We compare the performance of two functionals, Perdew-Burke-Ernzerhof (PBE) and PBE designed for solids, with and without the dispersion corrections (D2 and TS), in reproducing the high-accuracy low-temperature X-ray and neutron diffraction data for both groups of MOFs. We focus our analysis on the key structural parameters: the lattice parameters, bond lengths, and angles. We show that the dispersion long range correction is essential to stabilize the structures and, in some cases, to converge the system to a geometry that is in line with the experimentally observed structure, especially for breathing MIL-53 structures or zeolitic imidazolate frameworks. We find that for all structures and all analyzed parameters, the D2-corrected PBE functional performs the best, except for bonds involving the metal ions; however, even for these bonds the difference between the experimentally observed and calculated lengths is small. Therefore, we recommend the use of the PBE-D2 functional in further numerical analyses of rigid and flexible nanoporous MOFs.

Hydrogen is considered to be the preferred successor to gasoline due to its clean combustion, but its efficient and save storage remains the bottle-neck and one of the main challenges in hydrogen based technologies, especially those addressing mobile applications. Among different storage methods, reversible physical adsorption of molecular hydrogen in nanoporous materials is considered as the one of most attractive options. However, despite of more than 20 years of intensive experimental research no existing porous structures – from traditional activated carbons to porous polymer networks or metal organic frameworks - possess the required adsorbing properties.Therefore, we used computer simulations to explore the experimental options toward the most promising solutions. We showed that boron substituted graphene-based nanoporous structures may reach necessary storage performance if both key parameters defining the storage capacity of a sorbent (its specific surface and the energy of hydrogen adsorption) will be optimized. A potentially effective way to synthetize such optimized structures is arc-discharge procedure, successfully used in the past to synthetize fullerenes and nanotubes. We have assumed that the synthesis parameters can be modified to prepare graphene-based structures with a variety of substitution sites, shapes, sizes, and interconnections between graphene fragments.The first boron-substituted carbons prepared in this way show promising properties: they contain a variety of organized, graphene based structures decorated with boron nanoclusters, partially incorporated into graphene layers. The strongest adsorption occurs with the binding energy higher than 10 kJ/mol, and at least 10 % of adsorption sites adsorb hydrogen with the energy higher than 6.5 kJ/mol, significantly larger than in activated carbons (~4.5 kJ/mol). The specific surface of as-prepared samples is low (~ 200 m2/g). To increase it, both physical (heating in O2 reach atmosphere) and chemical (with KOH) activation are currently in progress.

Hydrogen storage is a key technology for the fuel applications. Hydrogen has the highest energy density of any fuel; however, its low ambient temperature density results in a low energy per unit volume. High density hydrogen storage is a challenge for stationary and portable applications and remains a significant challenge for transportation applications. Presently available storage options typically require large-volume systems that store hydrogen in gaseous form. On a mass basis, hydrogen has nearly three times the energy content of gasoline—120 MJ/kg for hydrogen versus 44 MJ/kg for gasoline. On a volume basis, however, the situation is reversed; liquid hydrogen has a density of 8 MJ/L whereas gasoline has a density of 32 MJ/L, as shown in the figure https://energy.gov/eere/fuelcells/hydrogen-storage) comparing energy densities of fuels based on lower heating values. Onboard hydrogen storage capacities of 5–13 kg hydrogen will be required to meet the driving range for the full range of light-duty vehicle platforms. One of alternative methods is storage by adsorption in porous materials.The numerical modeling of hydrogen adsorption has been a part of research with the goal to provide adequate hydrogen storage for onboard light-duty vehicle, material-handling equipment, and portable power. Here we discuss how this methodology has been used for the last 20 years and what is it contribution towards final solution. The discussion will be focused on three aspects. First, we will discuss why the existing high-surface porous materials are not promising hydrogen sorbents. Then, we will show how chemical modifications of the adsorbing surface may increase the binding energy between the hydrogen molecule and the surface. Finally, we will present the “universal” limits of hydrogen adsorption in porous structures and discuss the resulting problems and future research perspectives.

The search for sustainable automotive fuels has driven numerous studies of sorption-based hydrogen storage for hydrogen fuel cell vehicles. Storage by adsorption is fully reversible, achieves fast fill/discharge demands by simple pressurization/depressurization, and operates at much lower pressure than compressed hydrogen and at much less demanding temperatures than liquid hydrogen. In support of the DOE 2020 storage capacity target of 40 g hydrogen/L system, we have investigated the density of the adsorbed hydrogen films in a variety of porous carbons synthesized at the University of Missouri. The investigation decomposes storage into a high-density adsorbed film and low-density non-adsorbed gas and determines the fraction of pore volume occupied by the two phases.We find exceptionally dense H2 films at liquid nitrogen temperature, 77 K. Saturated film densities are 100-120 g/L across all samples at pressures as low as 35-70 bar. This is 1.4-1.7 times the density of liquid hydrogen at its normal boiling point, 71 g/L (20 K). Experimental film thicknesses are 0.30-0.32 nm, and fractions of total pore volume filled with high-density film are 0.25-0.53. Thus high storage capacities, well in excess of the DOE target and even in excess of liquid hydrogen, can be achieved at 77 K in appropriately engineered nanoporous carbons.The dense films occur at a temperature more than twice the liquid-gas critical temperature of hydrogen, 33 K, above which no bulk liquid exists at any pressure. The high-density film above 33 K does not contradict the non-existence of bulk liquid: the film is not a bulk, 3D phase, but a monomolecular 2D phase. Monte Carlo simulations confirm the observed high density and small film thickness. The film density and volume remain constant up to gas densities ~80% of the film density. A discussion in terms of competing forces acting on adsorbed molecules will be given.