Computational Screening of MOF-Based Mixed Matrix Membranes for CO<sub>2</sub>/N<sub>2</sub> Separations

Sumer, Zeynep; Keskin, Seda

doi:https://doi.org/10.1155/2016/6482628

Journal of Nanomaterials

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Abstract Introduction Results and Discussion Conclusion Acknowledgments Supplementary Materials References Copyright Related Articles

Research Article | Open Access

Volume 2016 | Article ID 6482628 | https://doi.org/10.1155/2016/6482628

Computational Screening of MOF-Based Mixed Matrix Membranes for CO₂/N₂ Separations

Zeynep Sumer¹and Seda Keskin¹

Academic Editor: Pushpendra Kumar

Received11 Apr 2016

Accepted09 May 2016

Published01 Jun 2016

Abstract

Atomically detailed simulations were used to examine CO₂/N₂ separation potential of metal organic framework- (MOF-) based mixed matrix membranes (MMMs) in this study. Gas permeability and selectivity of 700 new MMMs composed of 70 different MOFs and 10 different polymers were calculated for CO₂/N₂ separation. This is the largest number of MOF-based MMMs for which computational screening is done to date. Selecting the appropriate MOFs as filler particles in polymers resulted in MMMs that have higher CO₂/N₂ selectivities and higher CO₂ permeabilities compared to pure polymer membranes. We showed that, for polymers that have low CO₂ permeabilities but high CO₂ selectivities, the identity of the MOF used as filler is not important. All MOFs enhanced the CO₂ permeabilities of this type of polymers without changing their selectivities. Several MOF-based MMMs were identified to exceed the upper bound established for polymers. The methods we introduced in this study will create many opportunities to select the MOF/polymer combinations with useful properties for CO₂ separation applications.

1. Introduction

Emission of CO₂ has become a serious concern due to increased global warming. Capture of CO₂ from power plant flue gas, a mixture composed mainly of water-saturated N₂ with smaller amounts of O₂ and other species, is highly important. Effective separation technologies applied in power plants can decrease the total CO₂ emission up to 40% [1]. Compared to traditional separation technologies, membrane-based gas separation offers low cost, energy efficiency, and relatively small ecological footprint [2]. Therefore, it is preferred for CO₂/N₂ separations in power plants. Polymer membranes have been widely used for this gas separation. Unfortunately, the main disadvantage of polymer membranes is the trade-off between gas permeability and selectivity [3]. Polymer membranes’ selectivities tend to decrease as their permeabilities increase. For an efficient and economic gas separation process, both high gas selectivity and high gas permeability are required. High gas selectivity provides high purity and high gas permeability decreases the required surface area of the membrane and hence the capital cost. In order to overcome the trade-off of the polymer membranes, mixed matrix membranes (MMMs) are fabricated. MMMs are heterogeneous membranes in which nanoporous materials such as zeolites [4], carbon nanotubes [5], zeolitic imidazolate frameworks (ZIFs) [6, 7], and carbon molecular sieves [8] are incorporated as filler particles into polymer membranes. A series of hybrid inorganic-organic membranes based on polymers and various organosilica structures was also synthesized [9]. MMMs combining two different kinds of porous fillers, a MOF and a zeolite, in a polymer matrix were also synthesized and tested for gas separations [10].

In this way, the advantages of nanoporous filler particles such as high gas permeability and high gas selectivity can be combined with the advantages of polymers such as easy processability and low cost [11]. MMMs can be fabricated on large scales with relatively minor adaptation of existing commercial technology developed for polymer membranes. If the appropriate fillers are chosen, both the selectivity and permeability of the polymer membrane can be improved. Among MMM fillers, MOFs are relatively new members of crystalline nanoporous materials [12–16]. MOFs are composed of metal complexes that are linked by organic ligands to create highly porous frameworks [17]. They have fascinating physical and chemical properties, very large surface areas (500–6000 m²/g), high pore volumes (1–4 cm³/g), wide range of pore sizes from micro- to mesoscale (1–98 Å), and reasonable thermal and mechanical stabilities. Physical and chemical properties of MOFs can be tuned during synthesis and this controllable synthesis leads to a large diversity of materials with various structural properties and functionalities [18].

Incorporation of MOFs into polymers to improve the gas selectivity and permeability of the membrane has been recently investigated by several experimental and computational studies in the literature. We recently reviewed both the experimental and computational studies on MOF-based MMMs [19]. Several of these studies focused on CO₂/N₂ separations: Car et al. [20] studied the CO₂/N₂ selectivities of four different MMMs composed of CuBTC and Mn-(HCOO)₂ as filler particles incorporated into polydimethylsiloxane (PDMS) and polysulfone (PSf) polymers. They obtained slight improvements in CO₂ selectivity over N₂. Perez and coworkers [21] incorporated MOF-5 into Matrimid and showed that the permeabilities increased to 124% for CO₂ and 108% for N₂ while selectivity remains almost the same as the pure polymer. Basu et al. [22] synthesized CuBTC/Matrimid and CuBTC/Matrimid/PSf MMMs and investigated mixed-gas permeation properties for CO₂/N₂. They observed increases in both CO₂ permeability and CO₂/N₂ selectivity. The same group [23] also incorporated CuBTC, ZIF-8, and MIL-53(Al) into Matrimid and these MMMs showed higher CO₂/N₂ selectivity and higher CO₂ permeability than unfilled Matrimid. Bae and Long [13] incorporated Mg₂(dobdc) into PDMS, cross-linked polyethylene oxide (XLPEO), and polyimide (6FDA-TMPDA). While the CO₂ permeabilities of Mg₂(dobdc)/PDMS and Mg₂(dobdc)/XLPEO membranes decreased, the CO₂/N₂ selectivities were reported to slightly increase. Duan et al. [24] synthesized CuBTC/Ultem MMM with CuBTC and showed that the CO₂ permeability is increased up to 2.6 times while the CO₂/N₂ selectivity is almost unchanged. Kim et al. [25] investigated Cu-MOF as filler particle in polymer membranes, amorphous poly(2-ethyl-2-oxazoline), and semicrystalline poly(amide-6-b-ethylene oxide) and reported that ideal CO₂/N₂ selectivity of polymer membranes significantly increases with the addition of MOF particles.

As can be seen from the results of these experimental studies, MOF fillers can improve the gas separation performances of polymers. MOF-based MMMs can exhibit higher CO₂/N₂ selectivity and/or higher CO₂ permeability than the pure polymer membranes. There are thousands of available MOFs that can be used as filler particles in polymer membranes. This high number of materials represents both opportunity and challenge to select the correct MOF/polymer combinations for MMM fabrications. It is not possible to synthesize all the possible MOF/polymer MMMs and report their gas separation performances using purely experimental manners. Computational studies that can accurately predict the selectivity and permeability of MOF-based MMMs are highly useful to efficiently screen large numbers of MOFs prior to experiments. In this way, experimental efforts, time, and resources can be directed to the most promising MOF fillers among many possible candidates. We recently developed a computational approach that combines atomically detailed simulations with continuum modeling to assess gas separation performances of MOF-based MMMs [26]. The accuracy of this approach was validated by comparing the predictions of our method with the available experimental gas permeability measurements of fabricated MOF-based MMMs such as IRMOF-1/Matrimid, CuBTC/PSf, and CuBTC/PDMS [27]. This method was then used to estimate the potential of new MOF-based MMMs in CO₂/CH₄ and CH₄/H₂ separations [27, 28]. We recently studied MMMs in which ZIFs [29] and porous coordination networks, PCNs [30], were used as fillers in polymers for CO₂/N₂ separations. 80 ZIF-based and 200 PCN-based MMMs were examined using molecular simulations and our results showed that a large number of ZIF- and PCN-filled MMMs have higher CO₂ permeability and higher CO₂/N₂ selectivity than the pure polymers.

In this work, we expanded the number of studied MOFs significantly and considered 700 different MOF-based MMMs composed of 70 MOFs and 10 polymers for CO₂/N₂ separation. We first used atomically detailed simulations to calculate adsorption and diffusion of CO₂ and N₂ gases in MOFs. Using the gas adsorption and diffusion data, CO₂/N₂ selectivity and CO₂ permeability of MOFs were computed to provide the first information about the separation potential of these materials. Relations between adsorption selectivity, diffusion selectivity, and permeation selectivity of MOFs were discussed. We then predicted the CO₂/N₂ selectivity and CO₂ permeability of MOF-based MMMs and categorized the MOFs based on their effects on the separation performance of polymers. Our results showed that atomically detailed simulations can be used to select the appropriate MOF filler particles for polymers that will yield MMMs with extraordinary CO₂/N₂ separation properties.

2. Computational Details

2.1. MOFs and Polymers

In this work, 70 different MOFs and 10 different polymers were studied as components of 700 different MMMs. This is the largest number of MOF-based MMMs for which computational screening is done to date. Crystal structures of the selected MOF materials were taken from the Cambridge Crystallographic Data Centre (CCDC) [31]. The CCDC names and structural properties such as pore limiting diameter (PLD), largest cavity diameter (LCD), pore volume, and surface area of the MOFs are given in Table S1 in Supplementary Material available online at http://dx.doi.org/10.1155/2016/6482628. These structural properties were computed using Zeo++ [32] software. For surface area (pore volume) calculations, the number of trials was set to 2000 (50000) and probe size was set to 1.86 (zero) Å. For two MOFs, PODKUQ and QIFLOI, calculations were performed using Sarkisov and Harrison’s algorithm, Poreblazer [33]. We used universal force field (UFF) [34] for Poreblazer algorithm. Parameters such as He atom’s sigma, He atom’s epsilon, N atom’s sigma, temperature, cut-off distance, and number of trials were set to 2.58 Å, 10.22 K, 3.314 Å, 298 K, 12.8 Å, and 500, respectively. The largest anticipated pore diameter was set to 20 Å and the size of the bin was set to 0.25 Å.

As polymers, Ultem, Matrimid, polyimide (thianthrene-2,3,7,8-tetracarboxylic dianhydride-5,5,10,10-tetraoxide (TADATO), 3,3′,4,4′-diphenylsulfonyltetracarboxylic dianhydride (DSDA), and 3,7-diamino-2,8(6)-dimethyldibenzothiophene sulfone (DDBT)), 6FDA-2,2-bis(3,4-carboxyphenyl) hexafluoropropane dianhydride-diaminomesitylene (DAM) (6FDA-DAM), poly(bis(2-(2-methoxyethoxy)ethoxy)phosphazene) (MEEP), polymers of intrinsic microporosity (PIM-1 and PIM-7), modified PDMS, poly(trimethylgermylpropyne) (PTMGP), and poly(trimethylsilypropyne) (PTMSP) were studied [3]. Ultem, Matrimid, 6FDA-DAM, and modified PDMS were selected because they are widely used in experimental studies of MMMs. MEEP, PIM-1, PIM-7, PTMGP, and PTMSP were selected because they are close to Robeson’s upper bound. If the appropriate MOF fillers are incorporated, their CO₂ selectivities and CO₂ permeabilities can be enhanced to exceed the upper bound. The polymers that we considered in this work represent a wide range of CO₂ selectivity and permeability. For example, Ultem, Matrimid, and polyimide have low CO₂ permeabilities (1.4, 9, and 45 Barrers, resp.) but high CO₂/N₂ selectivities (25, 36, and 35.4, resp.). MEEP, 6FDA-DAM, PIM-7, modified PDMS, and PIM-1 have high CO₂ permeabilities (250, 842.4, 1100, 2000, and 2300, resp.). PTMGP and PTMSP have the highest CO₂ permeabilities (14000 and 29000 Barrers, resp.) but their CO₂/N₂ selectivities are low (14 and 10.7, resp.). Complete data for CO₂ permeabilities, N₂ permeabilities, and CO₂/N₂ selectivities of polymers are given in Table S2 in Supplementary Material.

2.2. Atomically Detailed Simulations

In order to calculate gas permeabilities of MOF-based MMMs, we need to know gas permeabilities of polymers and MOFs. Gas permeabilities of polymers were taken from the literature because there is a large amount of experimental studies related to polymers and their gas permeabilities [3]. Gas permeabilities of MOFs were computed in this work using atomically detailed simulations. Grand Canonical Monte Carlo (GCMC) and equilibrium molecular dynamics (EMD) simulations were used to compute gas adsorption and gas diffusion in MOFs, respectively [35]. Adsorption and diffusion data were then used to compute the gas permeabilities.

In GCMC and EMD simulations, UFF and Dreiding [36] force fields were used for MOFs in order to define the Lennard-Jones (LJ) potential parameters of the framework atoms. These force fields were selected based on the results of previous simulation studies that show a good agreement with the available experimental gas uptake data of MOFs [37]. The force fields used for each MOF together with the CCDC names of the MOFs are given in Table S3. The CO₂ molecule was modeled as three-site rigid molecule with LJ 12-6 potential; location of partial point charges was set as center of each side [38]. The N₂ molecule was modeled as three-site molecule, two sites were located at the N atoms, and third site was located at the center of the mass with partial point charges [39]. The LJ cross-interaction parameters for gas-gas and gas-MOF were calculated using Lorenz-Berthelot mixing rules. Electrostatic interactions were taken into consideration using the Coulomb potential. In order to compute the electrostatic interactions between gas molecules and MOFs, partial charges were assigned to MOF atoms using extended charge equilibration method (EQeq) [40]. The cut-off distance for truncation of dispersion and electrostatic interactions was set to 13 Å and 25 Å, respectively.

GCMC simulations were performed to compute single-component adsorption isotherms of CO₂ and N₂ in MOFs. The adsorbed amount of each gas was calculated by specifying the pressure and temperature. These simulations were performed at pressures of 2 bar and 10⁻⁶ bar at 298 K since most MMMs are experimentally tested for a feed pressure of 2 bar and permeate pressure of vacuum at room temperature. All simulations were done at room temperature, 298 K. Four different movement types were used in simulations, translation, rotation, insertion, and deletion of a molecule. Periodic boundary conditions were applied to simulate the bulk phase. A simulation box of 2 × 2 × 2 crystallographic unit cells was used. The number of steps was set to 1.5 × 10⁷ for equilibration and 1.5 × 10⁷ for production in simulations.

EMD simulations were performed to calculate the corrected diffusivity () of each gas. These simulations were done at average of feed and permeate pressure loadings that were obtained from the GCMC simulations. In each EMD simulation, 20 independent trajectories with 16 ns length were collected. Corrected diffusivities of gases were calculated in three directions and average diffusivity was reported. If diffusion was in one (two) direction(s), only that diffusivity (average diffusivity of these directions) was used. The Nose-Hoover thermostat algorithm was applied in NVT ensemble (constant number of molecules, constant volume, and constant temperature) [35]. The simulation volume was increased up to 6 × 6 × 6 crystallographic unit cells to ensure that it contains enough gas molecules at the lowest loadings to increase the statistical accuracy of the simulations.

Transport diffusivity () was calculated by multiplying the corrected diffusivity () obtained from EMD simulations with the thermodynamic correction factor [41], the partial derivative relating adsorbate concentration, , and the bulk phase fugacity, . If the single-component adsorption isotherm of the gas is known, the thermodynamic correction factor can be fully defined as follows:Steady-state gas fluxes () through a MOF were then calculated based on Fick’s law [41], where is the concentration gradient of the adsorbed species based on the difference between feed and permeate pressures of the membrane. Gas flux in a MOF was then converted to gas permeability (), using the pressure drop () and membrane thickness (), as shown in the following: Permeation selectivity (also referred to as membrane selectivity) of a MOF () was calculated from the ratio of gas permeability of two components:

2.3. Calculating Gas Permeability of MMMs

Gas permeabilities of MMMs were calculated using the well-known Maxwell model [42]. Erucar and Keskin [28] previously compared several theoretical permeation models, including Maxwell, modified Maxwell, Bruggeman, Lewis-Nielson, Pal, Felske, and modified Felske and showed that the Maxwell model is the best predicting model among the ones considering ideal morphology. In addition to these, we recently used the Maxwell model to predict CO₂ and N₂ permeabilities of MOF-based MMMs with a MOF volume fraction of 0.3 and showed the good agreement between simulation results and experiments for gas permeabilities of MOF-based MMMs [30]. These results suggested that it is reasonable to use the Maxwell model for estimating separation performance of new MOF-based MMMs for which experimental gas permeability data are not available. The Maxwell model predicts a MMM’s gas permeability () based on the polymer’s gas permeability (), filler particle’s permeability (), and the volume fraction of the filler particle within the polymer matrix () as follows: We used the MOF’s permeability, , calculated from (3) as the filler particle’s permeability () in (6). Gas selectivities of MMMs were computed as the ratio of gas permeabilities obtained from the Maxwell model similar to (4).

3. Results and Discussion

3.1. Permeability and Selectivity of MOFs

Before analyzing the results for MOF-based MMMs, we first examined the CO₂/N₂ separation performances of MOFs. Predicted CO₂ permeabilities, N₂ permeabilities, and CO₂/N₂ selectivities of MOFs are given in Table S4 in Supplementary Material. Figure 1 shows the CO₂/N₂ selectivities and CO₂ permeabilities of 70 different MOFs calculated from atomically detailed simulations. We also showed the selectivity and permeability data for 10 different polymers that we considered in this work together with Robeson’s upper bound established for CO₂/N₂ separation. Membrane materials that can exceed this upper bound are considered to be highly promising. The first observation from Figure 1 is that there are several MOFs that can exceed Robeson’s upper bound. 27 of the 70 MOFs are located above the upper bound. Most of these MOFs have generally similar or lower CO₂/N₂ selectivities than the polymers but significantly higher CO₂ permeabilities. MOFs, HAJKOU, LARVIL, and NUJCIE exhibit high CO₂/N₂ selectivities, 59, 54, and 49, respectively, and their CO₂ permeabilities are 7.5 × 10⁵, 7 × 10⁶, and 2.6 × 10⁵ Barrers. These values are higher than the selectivities and permeabilities of the polymers. Therefore, it is expected that if these three MOFs are used as filler particles in the polymers, they can significantly enhance both the selectivity and permeability of the polymer membranes. IDIWOH has the highest CO₂ permeability among all MOFs we considered, ~10⁷ Barrers. However, the CO₂/N₂ selectivity of this MOF (6) is lower than that of polymers. If IDIWOH is incorporated into polymers, we expect an increase in the CO₂ permeabilities of the polymers but decrease or no change in their selectivities.

One important observation from Figure 1 is that almost all MOFs that we considered in this work have higher CO₂ permeabilities than the polymers. The CO₂ permeabilities of polymers are in the range of 1–10⁴ Barrers whereas MOFs exhibit CO₂ permeabilities of 10⁴–10⁷ Barrers. These high permeabilities can be attributed to the large pore volumes of MOFs. We showed the calculated surface areas and pore volumes of all 70 MOFs in Figure S1. Surface areas of MOFs vary between 90 and 5210 m²/g and pore volumes are in the range of 0.1–3.1 cm³/g, which explains the high gas permeabilities of MOFs compared to polymers. As can be seen from Figure S1, the computed surface area in general closely correlates with the pore volume. As the pore volumes increase, surface areas also increase. The MOFs that we identified to be highly promising for CO₂/N₂ separations in Figure 1, NUJCIE, LARVIL, and HAJKOU have low surface areas (175 m²/g, 350 m²/g, and 890 m²/g, resp.) and low pore volumes (0.28 cm³/g, 0.24 cm³/g, and 0.39 cm³/g, resp.). As previously discussed by Watanabe and Sholl [43], high surface areas and pore volumes are generally preferred for materials used for adsorbent applications but are not critical for membrane materials. Overall, Figure 1 suggests that there are several promising MOFs with high CO₂/N₂ selectivities and high CO₂ permeabilities and these MOFs can be promising fillers for MMMs to enhance polymers’ separation performances.

In order to better assess gas separation performances of MOFs, we examined adsorption and diffusion selectivities of MOFs separately. Figure 2 shows adsorption, diffusion, and permeation (membrane) selectivity of MOFs as a function of their PLDs. Adsorption selectivities were computed as the ratio of adsorbed amount of CO₂ to N₂ at the average loadings of feed and permeate pressures. All MOFs are CO₂ selective in adsorption regardless of their pore sizes as shown in Figure 2(a). This is expected since CO₂ molecules have stronger energetic interactions with the MOF atoms compared to N₂ molecules as a result of higher quadrupole moment of CO₂. Strong adsorption of CO₂ molecules over weak adsorption of N₂ molecules gives rise to the CO₂ selective trend in adsorption. Adsorption selectivities of MOFs are moderate and close to each other in the range of 3–20. The best performing MOFs in adsorption are LECQEQ, EDUSUR, and LARVIL with adsorption selectivities of 17, 20, and 20.3, respectively. The MOFs that we identified to be highly promising for CO₂/N₂ separation based on permeation selectivity results, HAJKOU, NUJCIE, and LARVIL, have adsorption selectivities of 4, 15, and 20.3, respectively. This result suggests that the most promising membrane candidates for selective CO₂ separation are not necessarily the ones with the highest CO₂ adsorption selectivities.

(a)

(b)

(c)

Figure 2(b) shows diffusion selectivities of MOFs calculated as the ratio of corrected diffusivity of CO₂ over N₂ obtained from the EMD simulations. It is important to note that both CO₂ and N₂ diffusivities were greater than 10⁻⁸cm²/s in all MOFs we studied since gas diffusion can be readily characterized with EMD simulations above this limit. One important observation from Figure 2(b) is that there is no correlation between diffusion selectivity of MOFs and their PLDs. There are many MOFs having similar PLDs but different diffusion selectivities. A significant amount of MOFs, 63 out of 70, has diffusion selectivity less than 1 for CO₂ over N₂. In other words, these MOFs are N₂ selective in diffusion. This is an expected result since N₂ molecules are lighter than the CO₂ molecules leading to faster diffusion of N₂ compared to CO₂. Furthermore, CO₂ molecules are strongly adsorbed in MOFs as shown in Figure 2(a) and slow diffusion of the strongly adsorbed components is a common observation. Interestingly, there are five MOFs that favor CO₂ in diffusion. These MOFs are QIFLOI, HAJKIO, LARVIL, NUJCIE, and HAJKOU which have diffusion selectivities of 2.2, 2.5, 2.6, 3.2, and 14.8, respectively, for CO₂ over N₂. Three of these MOFs, LARVIL, NUJCIE, and HAJKOU, were identified to be highly promising materials for CO₂/N₂ separations due to their high permeation selectivities in Figure 1. The reason for their high permeation selectivities is that both adsorption and diffusion favor the same component, CO₂, in these MOFs. Therefore, these three MOFs are highly CO₂ selective materials. Although QIFLOI and HAJKIO are CO₂ selective in diffusion, their adsorption selectivities for CO₂ are low (3 and 4.5) compared to other MOFs; therefore, they are not as selective for CO₂ as the other three MOF materials in permeation. Finally, there are several MOFs with diffusion selectivities close to 1, suggesting that diffusion rates of CO₂ and N₂ are similar in the pores of these materials. As a result, permeation selectivities of these materials are determined by their adsorption selectivities.

Permeation (membrane) selectivities of MOFs are shown in Figure 2(c). Except four, all MOFs are CO₂ selective membranes. The CO₂/N₂ selectivities are in the range of 0.45–59.5. The CO₂/N₂ selectivities of FEVFUJ, GITVEL, EDUSUR, and YOZBOF are 0.5, 0.5, 0.7, and 0.7, respectively, which show that they are N₂ selective. Adsorption favors CO₂ in these MOFs with selectivities of ~12, 7, 20, and 7, but diffusion very strongly favors N₂ over CO₂ with selectivities of 24, 15, 30, and 9, respectively. Diffusion selectivities for N₂ dominate the adsorption selectivities for CO₂ and as a result these MOFs become N₂ selective membranes. FEVFUJ, GITVEL, EDUSUR, and YOZBOF can be promising adsorbent candidates for selective separation of CO₂ from N₂ and at the same time they are promising membrane materials for selective separation of N₂ from CO₂. For example, EDUSUR exhibits one of the highest adsorption selectivities for CO₂, 20, as shown in Figure 2(a) but when the kinetic properties of gases are considered, EDUSUR becomes weakly N₂ selective membrane as shown in Figure 2(c). This example signifies the importance of diffusion selectivity in governing a material’s membrane selectivity. Overall, analysis of adsorption, diffusion and permeation selectivities of MOFs obtained from atomically detailed simulations can be summarized as follows. (i) Adsorption selectivity favors CO₂ in all MOFs. (ii) If the diffusion selectivity also favors CO₂, then these MOFs become highly CO₂ selective in permeation. (iii) If the diffusion selectivity weakly favors N₂, then these MOFs become weakly CO₂ selective in permeation. (iv) If the diffusion selectivity strongly favors N₂, then these MOFs become N₂ selective in permeation.

3.2. Permeability and Selectivity of MOF-Based MMMs

In our recent work, we compared the CO₂ and N₂ permeability predictions of our atomically detailed simulations with the experimentally measured ones for various MOF- and ZIF-based MMMs [30]. We collected 98 experimental data points from the literature for CO₂ and N₂ permeability of 15 different types of MOF- and ZIF-based MMMs and showed that predictions of the Maxwell model are in good agreement with the experimental measurements of CO₂ and N₂ permeability. This good agreement validated the accuracy of our computational methodology to estimate separation performances of new MOF-based MMMs for which experimental gas permeability data are not available. In this work, we used the same computational approach to predict CO₂ and N₂ permeabilities and CO₂/N₂ selectivities of 700 different MOF-based MMMs which have not been fabricated to date. Calculated gas permeability and selectivity data for all MOF-based MMMs are reported in Tables S5–S14.

Figure 3 shows predicted CO₂/N₂ selectivity and CO₂ permeability of 560 different MMMs composed of Ultem, Matrimid, polyimide, MEEP, modified PDMS, PIM-1, PIM-7, and 6FDA-DAM polymers. The volume fraction of the MOF fillers in MMMs was set to 0.3. Predicted gas permeabilities of different MOF-based MMMs composed of 6FDA-DAM, Ultem, PIM-7, polyimide, Matrimid, and MEEP are almost the same; therefore a single symbol was used to represent different MOF-based MMMs of these polymers. In other words, the identity of the MOF used as filler particle does not affect the performance of MMMs composed of these six polymers. Ultem, Matrimid, polyimide, and 6FDA-DAM are below the upper bound due to their low CO₂ permeabilities compared to other polymers. Results showed that adding MOFs as filler particles into these polymers increases the CO₂ permeability of polymers since all the MOFs we studied have higher CO₂ permeability than these polymers. For example, CO₂ permeability increases from 1.4 to 3.2 Barrers for Ultem-based MMMs, 9 to 21 Barrers for Matrimid-based MMMs, 45 to 102.8 Barrers for polyimide-based MMMs, and 842.4 to 1908.7 Barrers for 6FDA-DAM-based MMMs. On the other hand, there is almost no change in CO₂/N₂ selectivity of these polymers.

With a CO₂/N₂ selectivity of 26.2 and CO₂ permeability of 1100 Barrers, PIM-7 is just below the upper bound. When MOFs are used as filler particles in this polymer, the MMM’s permeability increases from 1100 to 2485.9 Barrers and as a result PIM-7 can exceed the upper bound. This is an important result showing that highly permeable MOFs can significantly improve the CO₂ permeability of polymers and carry them above the upper bound. MEEP polymer is on Robeson’s upper bound and it easily exceeds the upper bound due to the improvement in CO₂ permeability by addition of MOF fillers. The CO₂ permeability of MEEP polymer increases from 250 to 570 Barrers with the incorporation of MOFs. No increase in the selectivity of MEEP was expected since it has the highest selectivity among all MOFs and polymers we considered in this work. The identity of the MOF used as filler affects the performance of MMMs composed of modified PDMS and PIM-1. These two polymers have significantly higher CO₂ permeabilities than the other polymers, 2000 and 2300 Barrers, respectively. There is a single MOF, FEVFUJ, which adversely affects the selectivity of these two polymers. FEVFUJ is N₂ selective MOF as shown in Figure 1. It has the lowest CO₂ selectivity (0.5) and the lowest CO₂ permeability (40500 Barrers) among all the MOFs we considered. If FEVFUJ is used as filler in modified PDMS and PIM-1, the CO₂ permeabilities still increase but at the expense of decreasing CO₂ selectivities as shown in Figure 3. For example, the CO₂/N₂ selectivity of modified PDMS (PIM-1) decreases from 34.2 to 30.7 (25 to 22.2) while the CO₂ permeability increases from 2000 to 4103.1 (2300 to 4650.5) Barrers. Incorporation of other MOFs into modified PDMS and PIM-1 gives similar results; permeabilities are enhanced while selectivities remain constant.

PTMGP and PTMSP are the two polymers located at the lower right end of Robeson’s upper bound as shown in Figure 1. They have high CO₂ permeabilities (14000 and 29000 Barrers, resp.), but low CO₂/N₂ selectivities (14 and 10.7, resp.). The gas permeabilities of these two polymers are much closer to the gas permeabilities of MOFs compared to the other polymers. Because of this reason, MMMs composed of PTMGP and PTMSP exhibit significantly different separation performances based on the identity of the MOF used as fillers. Figure 4(a) shows predicted CO₂/N₂ selectivity and CO₂ permeability of 70 different MOF/PTMGP MMMs. The effect of MOF fillers can be categorized into three: MOFs that increase both the CO₂ permeability and CO₂/N₂ selectivity, MOFs that increase the permeability without changing the selectivity, and MOFs that increase the permeability at the expense of decreasing selectivity. We discuss each case in detail in the following.

(a)

(b)

(a) Only 3 MOFs, NUJCIE, HAJKOU, and LARVIL, can increase both the CO₂ permeability and CO₂/N₂ selectivity of PTMGP. The selectivity of PTMGP increases from 14 to 17.3 and its permeability increases from 14000 to 28500 Barrers when NUJCIE is used as a filler particle. If HAJKOU is used to make a MMM, then the selectivity increases to 16 and permeability increases to 30650 Barrers. LARVIL also slightly increases the CO₂ selectivity of PTMGP to 14.2 and significantly increases the CO₂ permeability to 31850 Barrers. All three MMMs, NUJCIE/PTMGP, HAJKOU/PTMGP, and LARVIL/PTMGP, can exceed the upper bound established for CO₂/N₂ separation.

(b) Several MOFs (19 among 70) improve the CO₂ permeability of PTMGP but they do not significantly affect its selectivity. All these MOFs carry PTMGP above the upper bound due to large increases in the CO₂ permeability. The highest permeability observed for PTMGP-based MMMs is 31900 Barrers with IDIWOH filler while selectivity is constant at 14.

(c) A significant number of MOFs (48 among 70) increase the CO₂ permeability of PTMGP but decrease its selectivity. The reason is that the CO₂ permeabilities of these MOFs are similar to the PTMGP while their CO₂/N₂ selectivities are significantly lower than the polymer. As a result, the improvement in the CO₂ permeability of polymers occurs at the expense of a reduction in the selectivity. For example, the CO₂ permeability of PTMGP increases from 14000 to 19500 Barrers while its selectivity decreases from 14 to 8.8 with the addition of FEVFUJ filler into the polymer.

Figure 4(b) shows predicted CO₂/N₂ selectivity and CO₂ permeability of 70 different MOF-based MMMs composed of PTMSP polymer. PTMSP-based MMMs show the same trend with PTMGP-based MMMs. NUJCIE, HAJKOU, and LARVIL are the MOFs that increase both permeability and selectivity of PTMSP. NUJCIE increases permeability (selectivity) from 29000 to 53200 Barrers (from 10.7 to 15.9), HAJKOU increases to 60800 Barrers (to 14.1), and LARVIL increases to 65650 Barrers (to 11.2). MMMs in which NUJCIE, HAJKOU, and LARVIL are used as fillers exceed the upper bound established for CO₂/N₂ separation. There are 17 MOFs which improve the CO₂ permeability of PTMSP but do not significantly change the CO₂ selectivity. For example, IDIWOH increases the CO₂ permeability to 65800 Barrers but keeps the selectivity of MMM the same as that of pure polymer. Permeability increases upon addition of MOF fillers carry the PTMSP-based MMMs above the upper bound. Most of the MOFs studied (50 among 70) increased the CO₂ permeability of PTMSP but decreased the CO₂ selectivity due to the same reason as discussed for PTMGP.

We so far examined the widely studied polymers for CO₂/N₂ separation. In fact, most of these polymers are located close to the upper bound and it is easy for these polymers to exceed the upper bound with the incorporation of highly permeable MOF fillers. We now turn to the hypothetical polymers to understand which polymers can reap the largest advantages when used in combination with MOFs. Figure 5 shows 6 hypothetical polymers that lie along Robeson’s upper bound for CO₂/N₂ separation. By specifying the position of a polymer along the upper bound we defined the information required to predict MMMs’ performances. The CO₂ permeabilities of selected hypothetical polymers are in the range of 90–3 × 10⁶ Barrers and their CO₂/N₂ selectivities vary from 2 to 80. For each hypothetical polymer, we used 5 different MOFs as filler particles, NUJCIE, HAJKOU, LARVIL, IDIWOH, and FEVFUJ. These MOFs are chosen to represent highly CO₂/N₂ selective and highly permeable fillers (NUJCIE, HAJKOU, and LARVIL), a highly CO₂ permeable filler with low CO₂/N₂ selectivity (IDIWOH), and a N₂ selective filler with low CO₂ permeability (FEVFUJ). If the polymer membrane has a high selectivity for CO₂ but low permeability such as the first two hypothetical polymers, adding a MOF can enhance the membrane’s permeability with no change in the selectivity. In this limit, the identity of the MOF appears to be unimportant. The effect of MOF identity becomes important for the third polymer which has moderate selectivity and permeability. Highly permeable NUJCIE, HAJKOU, LARVIL, and IDIWOH enhance permeability of the third polymer without changing its selectivity whereas FEVFUJ enhances its CO₂ permeability but decreases the CO₂/N₂ selectivity. Except FEVFUJ, selected MOF fillers improve both the CO₂ permeability and the CO₂/N₂ selectivity of the fourth and fifth polymers. This improvement depends on the identity of the MOF. MOFs like NUJCIE and HAJKOU significantly enhance the CO₂/N₂ selectivity whereas a MOF like LARVIL significantly enhances the CO₂ permeability. The most interesting results are observed for the sixth polymer which has very high permeability but very low selectivity. Highly permeable MOFs, LARVIL and IDIWOH, enhance both the permeability and selectivity of that polymer but all the other MOFs cause a decrease in the CO₂ permeability although they increase the selectivity. These results support the idea that there is a wide range of polymers that have moderate selectivity and moderate permeability for which incorporation of an appropriate MOF can yield large separation performance enhancements. The polymers we studied in this work generally have lower CO₂ permeabilities but relatively higher CO₂/N₂ selectivities compared to MOFs. For polymers that have high permeabilities and low selectivities, separation performances of the MMMs are strongly dependent on the type of MOF.

Finally, it is important to discuss the assumptions of the computational approach that we used to screen MOF-based MMMs for CO₂/N₂ separation. Rigid MOF structures were used in our atomically detailed simulations. This assumption has been widely used in almost all molecular simulation studies of MOFs in the literature since flexible simulations require significant amount of computational time and resources. We recently investigated the effect of MOF’s flexibility on the permeability and selectivity of MOF-based MMMs and showed that flexibility of the MOFs can be neglected as a reasonable approximation if the MOF volume fraction is low and if the MOF is much more permeable than the polymer [30]. The MOFs we studied in this work were highly permeable compared to the polymers shown in Figure 1 and the volume fraction of the MOF in the MMM was set to a low value, 0.3. Therefore, neglecting the flexibility of MOFs is a reasonable approximation especially for large-scale computational screening studies. Our atomically detailed simulations do not provide any information about the stability of MOF/polymer MMMs. This issue is more likely to be investigated by experimentalists. We checked the stability information for 3 MOFs, which were identified to improve both the selectivity and permeability of polymers, from their corresponding experimental synthesis papers. HAJKOU is reported to exhibit high thermal stability and permanent porosity [44], LARVIL is reported to preserve its crystalline integrity at ambient conditions [45], and no information was found for the stability of NUJCIE [46]. We believe that results we presented in this work will motivate several experimental studies to fabricate and test both separation performance and long-term stability of these MOF-based MMMs.

At that point one may think about why not to use MOFs as pure membranes rather than using them as filler particles in polymer membranes. MOFs exhibit high gas permeabilities and high gas selectivities as shown in Figure 1. However, fabrication of MOF membranes requires synthesis of MOFs in bulk amounts at low cost. MOFs are currently synthesized in small amounts at the lab scale and commercially available MOFs are expensive. Furthermore, it is experimentally challenging to fabricate defect-free thin film MOF membranes although recent studies described routes for processing MOF membranes in polymeric hollow fibers [47, 48]. On the other hand, fabrication of MOF-based MMMs on large scales can be done with relatively minor adaptation of existing commercial technology developed for fabrication of polymer membranes at a reasonable cost. Therefore, MOF-based MMMs are expected to be more widely used in gas separation applications compared to thin film MOF membranes in the near future. We believe that results of this study will motivate experiments to fabricate the most promising MOF-based MMMs for CO₂/N₂ separations.

4. Conclusion

In this study, we combined atomically detailed simulations with the Maxwell model to make predictions for the performances of MOF-based MMMs in CO₂/N₂ separations. We first performed atomically detailed simulations to obtain adsorption and diffusion data of CO₂ and N₂ gases in MOFs. Adsorption, diffusion, and permeation selectivities of MOFs were compared to understand the potential of MOFs in CO₂/N₂ separations. Results showed that adsorption selectivity favors CO₂ in all MOFs whereas diffusion selectivity can favor either CO₂ or N₂. As a result, permeation selectivities of MOFs are governed by the diffusion selectivity preference of the materials. Several promising MOFs with high CO₂/N₂ selectivities and high CO₂ permeabilities were identified. A large number of MOFs were found to be located above the upper bound established for polymers.

Motivated from this result, we examined the separation performances of 700 different MOF-based MMMs composed of 70 MOFs and 10 polymers. This is the largest number of MOF-based MMMs for which computational screening is done to date. Using MOFs as filler particles increased the CO₂ permeability of all 10 polymers but the change in selectivity varied with respect to position of the polymer on the upper bound. We showed that, for polymers that have low CO₂ permeabilities but high CO₂ selectivities, the identity of the MOF used as filler is not important. All MOFs enhanced the CO₂ permeabilities of this type of polymers without changing their selectivities. On the other hand, for polymers that have high CO₂ permeabilities but low CO₂ selectivities, separation properties of the MMMs strongly depend on the identity of the filler particle. Highly selective MOFs were able to increase both the CO₂ permeabilities and the CO₂/N₂ selectivities of PTMGP and PTMSP. At that point, it is important to note that we only examined a fraction of the MOFs that are reported in CCDC. There are thousands of MOFs in the database that might show better separation properties than the MOFs we studied. It is also important to note that computational methods that we used in this work do not provide any information about the stability of MOF-based MMMs, MOF-polymer interactions, and possible filler agglomeration. Large-scale computational screening approach that we used here will fasten the design and development of new MOF-based MMMs and motivate experimental studies.

Competing Interests

The authors declare that they have no competing interests.

Acknowledgments

Financial support provided by the Scientific and Technological Research Council of Turkey (TUBITAK) Grant MAG-213M401 is gratefully acknowledged.

Supplementary Materials

Supplementary Material consists of structural properties of MOFs, permeability and selectivity of polymers, forcefields used in molecular simulations of MOFs, simulation results for permeability and selectivity of MOFs, calculated permeability and selectivity data for MMMs, and calculated accessible surface area vs. pore volume of the MOFs.

Supplementary Material

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Copyright © 2016 Zeynep Sumer and Seda Keskin. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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