EP3820593A1 - Hybrid membranes for energy-efficient carbon capture - Google Patents
Hybrid membranes for energy-efficient carbon captureInfo
- Publication number
- EP3820593A1 EP3820593A1 EP19737544.7A EP19737544A EP3820593A1 EP 3820593 A1 EP3820593 A1 EP 3820593A1 EP 19737544 A EP19737544 A EP 19737544A EP 3820593 A1 EP3820593 A1 EP 3820593A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- graphene
- gas separation
- separation membrane
- film
- polymer
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 title claims abstract description 99
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Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D69/00—Semi-permeable membranes for separation processes or apparatus characterised by their form, structure or properties; Manufacturing processes specially adapted therefor
- B01D69/02—Semi-permeable membranes for separation processes or apparatus characterised by their form, structure or properties; Manufacturing processes specially adapted therefor characterised by their properties
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D53/00—Separation of gases or vapours; Recovering vapours of volatile solvents from gases; Chemical or biological purification of waste gases, e.g. engine exhaust gases, smoke, fumes, flue gases, aerosols
- B01D53/22—Separation of gases or vapours; Recovering vapours of volatile solvents from gases; Chemical or biological purification of waste gases, e.g. engine exhaust gases, smoke, fumes, flue gases, aerosols by diffusion
- B01D53/228—Separation of gases or vapours; Recovering vapours of volatile solvents from gases; Chemical or biological purification of waste gases, e.g. engine exhaust gases, smoke, fumes, flue gases, aerosols by diffusion characterised by specific membranes
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D67/00—Processes specially adapted for manufacturing semi-permeable membranes for separation processes or apparatus
- B01D67/0039—Inorganic membrane manufacture
- B01D67/0053—Inorganic membrane manufacture by inducing porosity into non porous precursor membranes
- B01D67/006—Inorganic membrane manufacture by inducing porosity into non porous precursor membranes by elimination of segments of the precursor, e.g. nucleation-track membranes, lithography or laser methods
- B01D67/0062—Inorganic membrane manufacture by inducing porosity into non porous precursor membranes by elimination of segments of the precursor, e.g. nucleation-track membranes, lithography or laser methods by micromachining techniques, e.g. using masking and etching steps, photolithography
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D67/00—Processes specially adapted for manufacturing semi-permeable membranes for separation processes or apparatus
- B01D67/0039—Inorganic membrane manufacture
- B01D67/0072—Inorganic membrane manufacture by deposition from the gaseous phase, e.g. sputtering, CVD, PVD
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D67/00—Processes specially adapted for manufacturing semi-permeable membranes for separation processes or apparatus
- B01D67/0079—Manufacture of membranes comprising organic and inorganic components
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D67/00—Processes specially adapted for manufacturing semi-permeable membranes for separation processes or apparatus
- B01D67/0079—Manufacture of membranes comprising organic and inorganic components
- B01D67/00791—Different components in separate layers
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D69/00—Semi-permeable membranes for separation processes or apparatus characterised by their form, structure or properties; Manufacturing processes specially adapted therefor
- B01D69/12—Composite membranes; Ultra-thin membranes
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D71/00—Semi-permeable membranes for separation processes or apparatus characterised by the material; Manufacturing processes specially adapted therefor
- B01D71/02—Inorganic material
- B01D71/021—Carbon
- B01D71/0211—Graphene or derivates thereof
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D71/00—Semi-permeable membranes for separation processes or apparatus characterised by the material; Manufacturing processes specially adapted therefor
- B01D71/06—Organic material
- B01D71/52—Polyethers
- B01D71/521—Aliphatic polyethers
- B01D71/5211—Polyethylene glycol or polyethyleneoxide
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D71/00—Semi-permeable membranes for separation processes or apparatus characterised by the material; Manufacturing processes specially adapted therefor
- B01D71/06—Organic material
- B01D71/58—Other polymers having nitrogen in the main chain, with or without oxygen or carbon only
- B01D71/60—Polyamines
- B01D71/601—Polyethylenimine
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D2257/00—Components to be removed
- B01D2257/50—Carbon oxides
- B01D2257/504—Carbon dioxide
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D2323/00—Details relating to membrane preparation
- B01D2323/36—Introduction of specific chemical groups
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01D—SEPARATION
- B01D2325/00—Details relating to properties of membranes
- B01D2325/04—Characteristic thickness
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02C—CAPTURE, STORAGE, SEQUESTRATION OR DISPOSAL OF GREENHOUSE GASES [GHG]
- Y02C20/00—Capture or disposal of greenhouse gases
- Y02C20/40—Capture or disposal of greenhouse gases of CO2
Definitions
- the present invention pertains generally to the field of gas separation filters, especially useful to the C0 2 capture from the flue gas. More particularly, the present invention is related to filter membranes for C0 2 capture and even more particularly, the present invention relates to composite filter membranes for C0 2 capture.
- Membranes have been shown to be more energy-efficient than the commercial amine-based CO2 scrubbing technology for the postcombustion carbon capture (CO2 capture from the flue gas), especially from the power plants, petrochemical refineries, and steel and cement industries, where the CO2 concentration in the flue gas is higher than 15%.
- Single-layer graphene is the thinnest molecular barrier, and is highly promising for the gas separation if molecular-sized pores can be incorporated with a high pore-density in the graphene lattice.
- Experiments and molecular simulations have indicated that nanoporous graphene film can yield orders of magnitude higher gas permeance than that from the conventional membranes, attributing to the ultrashort diffusion path of molecules through the atom-thick membrane.
- the incorporation of molecular-selective nanopores in otherwise impermeable graphene lattice, at a reasonably high pore-density, has proven to be a major challenge.
- Multi-layered film of graphene-oxide (GO) hosting C0 2 -philic molecules into the interlayered nanochannels have demonstrated the separation of C0 2 from N 2 .
- the gas transport pathway in GO membranes is long and tortuous, resulting in a moderate C0 2 permeance of 250 GPU, lower than the capture target.
- the long-term stability of GO membrane is questionable.
- a primary object of the invention is to solve the above-mentioned problems and more particularly to develop a high-performance graphene-based membrane yielding performance that meets or exceeds the C0 2 capture target.
- the present invention relates to a single-layer graphene film chemically modified with a polymer film having a thickness of 5-100 nm, preferably 5-50 nm, more preferably 5-20 nm and even more preferably 10 nm, which yields a record performance in C0 2 /N 2 separation, and which meets the C0 2 capture target.
- the lattice of single-layer graphene was etched to incorporate porosity with pore-size (defined by electron-density-gap in the pore) in the range of 0.2-10.0 nm, preferably, 0.3-5.0 nm and even more preferably 0.3-2.0 nm.
- a layer of C0 2 -philic polymer (polymer with high permeability for C0 2 with respect to other gases) having a thickness of 5-100 nm, preferably 5-50 nm, more preferably 5-20 nm and even more preferably 10 nm, acting as a C0 2 -selective film, was chemically grafted on top of the graphene surface.
- the C0 2 -philic polymer was subsequently swollen with another low molecular-weight C0 2 -philic polymer.
- the resulting membranes yielded a high C0 2 permeance of 6100 GPU and an attractive C0 2 /N 2 separation factor of 22.5.
- This invention also provides a novel graphene transfer method allowing the synthesis of crack-free graphene film on to a porous substrate.
- Figure 1 is a schematic diagram representing the manufacturing process of the membrane of the present invention
- Figures 2a and 2b represent Raman spectra of as-synthesized graphene and graphene exposed to various plasma times, and a plot of ID/IG and / 2 D//G ratios as a function of plasma exposure time, respectively, c-h)
- TEM transmission electron microscopy
- the mean pore size corresponds to the arithmetic average of the pore diameters.
- the scale bars in the TEM images correspond to 2 nm.
- Figure 3 represent an XPS spectra of oxidized graphene by ozone treatment of 20 min at room temperature.
- Figure 4 shows SEM images of the surface morphologies of a) ONG@Si, b) PONGl@Si, c) PONG2@Si, and d) SPONG1/PTMSP on Si wafer;
- Figure 5 shows SEM images of the cross-sectional morphologies of a) bare PTMSP, b) SPONG1/PTMSP, and c) SPONG2/PTMSP on Si wafer;
- Figure 6 shows a Thickness analysis of the PONG1 samples, a) Topography, and b) the corresponding height distribution of the as-prepared sample on the Si wafer, c) Topography of the trench, and d) the corresponding line profiles across the trench;
- Figure 7 shows the gas separation performance of various membranes as a function of plasma time.
- the SPONG2 membranes under the single-gas permeation conditions. Membranes were tested at 30 °C, and the pressure in the feed side was 2 bar;
- Figure 8 shows the gas separation performance of various membranes as a function of the pore-size in graphene.
- CO2 permeance and CO2/N2 selectivities as a function of the mean pore size in graphene for (a) SPONG1 membranes (comparing single gas and mixture data), and (b) comparing single gas data for SPONG1 and SPONG2 membranes;
- Figure 9 shows the CO2/N2 mixture separation performance of SPONG membranes compared with the state-of-the-art thin-film composite membranes.
- Facilitated transport membranes are not included because of their widely-known stability issues.
- Pore size electron-density-gap in graphene pore
- C0 2 -philic polymer these are polymer chains with high permeability for C0 2 with respect to other gases (for example, in this case N 2 ).
- Solubility x Diffusivity Solubility x Diffusivity, where Solubility is defined as amount of C0 2 solubilized by the polymer chains (wt%) as a function of C0 2 concentration in the gas phase and Diffusivity is a measure of transport rate of C0 2 when it hops from one site in polymer to another site.
- a preferred range of C0 2 permeability for this application is 10 -10000 barrer with C02/N2 selectivity of 10-1000.
- Oxidative Groups specifically refer to epoxides, carbonyl, carboxylic, hydroxyl and carbonic groups.
- This expression means transfer of graphene from Cu substrate to a porous substrate in a way such that there are no microscopic cracks (defined as cracks with width greater than 0.1 micron) with a tolerance limit for smaller cracks to be 10-100 ppm.
- Low molecular weight lower than 10000 g/moles.
- PTMSP an abbreviation for a polymer name (polytrimethylsilylpropyne).
- a single-layer graphene was synthesized on a copper foil (25 pm, 99.8% purity, Sigma) using the low-pressure chemical vapor deposition (CVD). Briefly, the copper foil was annealed at 1000 °C in a C0 2 atmosphere for 30 min to get rid of organic contaminations. Subsequently, C0 2 flow was switched off and H 2 (8 mL/min) was introduced to anneal the copper. Then, CH 4 (24 mL/min) flow was open for 30 min as a precursor for graphene crystallization.
- CVD chemical vapor deposition
- this graphene was used to prepare an oxygen-functionalized nanoporous single- layer graphene (ONG).
- the nanopores on the single-layer graphene were created by an 0 2 plasma.
- a piece of the graphene/copper foil was placed in the plasma chamber in an 0 2 atmosphere. After the pressure reaches 50 mTorr, the 0 2 plasma was opened for a certain time (4-8 s) to etch the graphene lattice.
- the nanoporous graphene was oxygen-functionalized by placing graphene in an oxidizing atmosphere (21% 0 3 in 0 2 ) generated by an ozone generator (Absolute Ozone ® Atlas 30), for 20 min at room temperature.
- the ONG was modified by C0 2 -philic polymer to create a PONG. More particularly, PONG was prepared by spin coating a dilute solution of C0 2 -philic polymer on top of ONG resting on the copper foil. Aqueous solution of polyethylenimine (PEI, 10 mg/ml) or polyethylene glycol) bis(amine) (PEGBA, 20 mg/ml) was used as the coating solution. The coating solution was added dropwise within 10 s while the graphene/copper substrate was spinning at 1000 rpm. Subsequently, the spin coating was carried out at 3000 rpm for 60 s.
- PEI polyethylenimine
- PEGBA polyethylene glycol) bis(amine)
- PTMSP for graphene transfer
- ONG/PTMSP or PONG/PTMSP a coating of PTMSP for graphene transfer
- a thin PTMSP layer was coated onto the top of ONG or PONG by spin coating.
- a thin layer of 1.25 wt% of PTMSP toluene solution was spread on the substrate, followed by spinning the substrate at 1000 rpm for 30 s, and then 2000 rpm for 20 s.
- the resulting film was dried in a closed dish for 12 h, and then dried in a vacuum oven for 12 h at room temperature.
- the final step comprises a swelling of the composite film and transfer to a porous tungsten support (SPONG/PTMSP).
- SPONG/PTMSP porous tungsten support
- the copper foil acting as substrate to the ONG/PTMSP or the PONG/PTMSP film was removed by chemical etching by placing the films on a FeCU (1 M in water) bath for 30 min. Then, the underside of the floating film was rinsed with 0.1 M HCI solution for 1 h, and then on Dl water for 1 h to remove the residues.
- PEGDE polyethylene glycol dimethyl ether
- SPONG/PTMSP was scooped up using a porous tungsten support.
- the remaining water on the surface of the film was carefully removed by a bloating paper, followed by drying in a vacuum oven for 12 h.
- the film was directly scooped up using a porous tungsten support.
- the SPONG membranes were characterized by several methods including Raman spectroscopy, X-ray photoelectron spectroscopy (XPS), Scanning electron microscope (SEM), Atomic force microscope (AFM) and Gas permeation measurement.
- the Raman characterization was carried out on graphene/copper using a Renishaw micro-Raman spectroscope (457 nm, 2.33 eV, 50x objective). More than 10 spectra were obtained using the mapping method for every sample. The ID/IG and / 2 D//G ratios were calculated by analyzing the Raman data using MATLAB. The background was subtracted from the Raman data for the calculation.
- XPS graphene
- SEM was used to observe the surface or cross-sectional morphologies of ONG, ONG/PTMSP, and SPONG/PTMSP films, using FEI Teneo SEM with an operating voltage of 1-5 kV and a working distance of 2.5-6 mm.
- the sample was coated with a 10-nm-thick iridium layer. No conductive coating was used for observing surface morphologies.
- AFM was used to detect the surface topography and thickness of PEGBA or PEI layers.
- the porosity and oxygen-functionalization in graphene were generated by the similar method as described above.
- the composite graphene membrane is fabricated as follows.
- step 0 consists in synthesizing monolayer graphene on a copper foil, preferably by CVD, then the following process is carried out as illustrated in Figure 1:
- the membranes prepared using PEI are referred to as SPONGl_X, where X represents plasma time in second. Accordingly, the membranes prepared using PEGBA are referred to as SPONG2-X.
- Single-layer graphene can be synthesized on the copper foil preferably by the CVD method.
- Figure 2a and 2b show the Raman spectroscopy data which displays that the as- synthesized graphene has an ID/IG ratio of 0.08, and an / 2 D/7G ratio of 3.26, confirming that the as-synthesized graphene comprised of a low-density of the intrinsic defects, and is primarily single-layer.
- the 0 2 plasma can be utilized as an effective method to incorporate nanopores in the graphene lattice.
- the evolution of pore-density with the plasma time is characterized by the Raman spectroscopy, as shown in Figure 2a and 2b.
- the ID/IG ratio indicating the extent of disorder in graphene lattice
- the / 2 D//G ratio decreases to 0.48.
- both ratios decrease. This behaviour indicates that the graphene treated with 4 s of plasma transitions from the "nanocrystalline graphite stage" into a "sp 3 -amorphous carbon stage", where ID is proportional to the probability of finding the sp 2 carbon ring.
- the distance between defects appears to be smaller than 5 nm, and the density of defects appears to be larger than 1.27xl0 12 cm 2 .
- the size and density of the defects increases.
- the distance between defects is smaller than 3.5 nm, and the density of defects is larger than 2.6xl0 12 cm 2 .
- the nanopores had a lognormal distribution, with mean pore size (arithmetic average of the pore diameters) of 1.8 ⁇ 1.2 and 2.4 ⁇ 1.5 nm after 4 and 6 s of plasma treatment, respectively (Figure 2c-h).
- mean pore size arithmetic average of the pore diameters
- Several large nanopores up to 5 and 8 nm in the 4 and 6 s samples, respectively
- Both zigzag and armchair pore-edge configurations could be observed.
- the pore-densities were 2.1 x 10 12 and 2.3 x 10 12 cm 2 , respectively, corresponding to porosities of 6.8 and 13%, respectively.
- the order of magnitude for the pore-density obtained by electron microscopy is consistent with the defect-density from the Raman analysis. While new pores were nucleated as the etching time was increased, the mean pore size increased at a linear rate (4 L/s) with respect to the etching time. Based on this, the mean pore size in NG etched for 8 s is estimated to be around 3.2 nm.
- the nanoporous graphene is preferably further treated by ozone to functionalize it with abundant oxygen-containing groups, as indicated by the XPS data ( Figure 3).
- the oxygen-containing groups were mainly composed of epoxy, hydroxy, carbonyl, and carboxy groups.
- the functional groups grafted on graphene as a result of the 0 3 treatment, improve the interaction with the subsequent C0 2 -philic polymer layer via hydrogen-bonding and electrostatic interactions.
- the surface and the cross-sectional morphologies of ONG and ONG coated with C0 2 -philic polymer can be observed by SEM ( Figure 4). Overall, the surfaces appear to be quite uniform and smooth indicating a uniform coating of the polymer layers on the graphene.
- the cross-sectional morphologies in Figure 5 show that the thicknesses of ONG/PTMSP, PONG1/PTMSP, and PONG2/PTMSP are 400, 220, and 120 nm, respectively.
- the thickness of PONG1/PTMSP and PONG2/PTMSP are much smaller than that of ONG/PTMSP film. This can be attributed to the fact that coating of PEI or PEGBA films on graphene modifies the surface-wetting properties, leading to only a thinner PTMSP film when PTMSP is coated on top of PONG1 or PONG2, compared to when PTMSP is directly coated on
- the coating of PTMSP on top of PONG facilitates the transfer of graphene from Cu to a porous substrate, without inducing any cracks or tear.
- a 100% success rate (defined by the number of successfully transferred samples normalized by the number of attempts) can be achieved.
- the PTMSP film was selected due to the following reasons:
- PTMSP is one of the most permeable polymers.
- the standalone PTMSP film on the porous support yields a C0 2 permeance of 9097 GPU with a CO2/N2 selectivity of 10.2. This high gas permeance ensures that the CO2 permeance of composite film would not be limited by the PTMSP layer;
- PTMSP provides sufficient mechanical support (rigidity) to the floating graphene film to eliminate cracks and tear in the film.
- the topography of the PONG samples is measured with or without scratches using the atomic force microscopy (AFM).
- the PONG samples for AFM were prepared by transferring ONG to a Si wafer, followed by coating PEI or PEGBA film on top of graphene.
- Figure 6a shows that the surface of PONG1 is relatively smooth.
- Several pm-scale uncovered areas were present attributing to the fact that the ONG does not cover the Si wafer completely due to cracks and tear, and as a result, the PEI coating solution does not wet the domains devoid of ONG.
- the height distribution data revealed a bimodal height distribution, with a modal spacing of about 8 nm ( Figure 6b).
- the modal spacing indicates the thickness of the PEI layer to be around 8 nm.
- the gas separation performance is evaluated using a homemade gas permeance setup, and the data is shown in Tables 2, 3 and Figure 7.
- the gas separation performance from all SPONG1-X membranes shows a consistent trend; with increasing the time of O 2 plasma treatment from 4 to 8 s, the CO 2 permeance increases (from 1030 to 11640 GPU) while the CO 2 /N 2 and CO 2 /CH 4 selectivity decreases (41.9 to 14.7 and 18.6 to 7.5, respectively, Figure 7a). This indicates a strong role of graphene nanopores in the separation of CO 2 from N 2 and CH 4 .
- the pore-size-distribution (PSD) in plasma-treated graphene can be characterized by two kinds of pores; the pores across which the molecular transport is primarily in the temperature-activated mode and the pores across which the transport is primarily in the effusive mode.
- the former represents pores that are commensurate with the size of molecule that transverse the pores.
- C0 2 transport this corresponds to pores that have an electron-density-gap similar to or slightly smaller than the kinetic diameter of C0 2 (0.33 nm).
- the effusive transport takes place from the pores that are large enough such that molecule does not experience any activation barrier while translocating the pore.
- the permeation coefficient (permeance per pore) is higher in the effusive transport compared to that in the activated transport attributing to the activation barrier and the loss in entropy at the transition state in the case of activated transport. Therefore, a high degree of C0 2 /N 2 separation can be achieved if pores with an electron-density-gap in the range of 0.33 to 0.36 nm can be incorporated in graphene (kinetic diameter of N 2 is 0.36 nm). Also, increasing the mean-pore-size is expected to increase permeance and reduce separation selectivity. Based on this, the observed decrease in C0 2 /N 2 and C0 2 /CH 4 selectivity with increasing plasma time strongly indicates that permeance increase and selectivity loss was primarily because of the increase in the mean-pore-size in graphene.
- the carbon atoms at the pore-edge are oxygen-functionalized and highly polar attributing to a) their generation by the plasma treatment and b) subsequent graphene functionalization by ozone.
- These oxygenated polar groups strongly interact with the C0 2 - philic polymer layers (PEI, PEGBA, and PEGDE) via electrostatic and van der Waal's interaction. Such strong interaction shrinks the effective electron-density-gap, especially for the large- pores that can accommodate the polymer chains.
- the polymer-modified pore yields higher C0 2 /N 2 or C0 2 /CH 4 selectivities compared to that from the unmodified pores.
- the SPONGl-8s membrane yields a C0 2 /N 2 selectivity of 14.7, close to that from pure PTMSP membrane (10.2).
- This phenomenon indicates that the porous graphene film in the SPONGl-8s membrane contributed only slightly to the overall selectivity, attributing to that the pore size at 8 s plasma exposure is too big. In this case, it is very likely that larger pores are not fully covered with PEI film because of the relatively weaker interactions between the copper under the graphene pore and PEI.
- Another important feature of the SPONG membrane is the ultrathin functional polymer film on top of the NPG.
- the PEGDE swollen PEI film contains a high-density C0 2 -philic groups (amino and ethylene oxide), leading to the enhancement of C0 2 sorption and C0 2 separation capability.
- the branched PEI polymer possesses a strong intramolecular hydrogen bonds, resulting in a low free volume and CO2 permeability.
- the impregnation of PEGDE into the PEI network can break the intramolecular hydrogen bonds, increasing the free volume.
- the ultrathin PEGDE swollen PEI film has a high CO2 permeance and good CO2/N2 separation capacity.
- the SPONGl-6s membrane M3 shows a remarkably high CO2 permeance of 5470 GPU with a CO2/N2 ideal selectivity of 25.2.
- the mixed gas permeation measurement can be performed using a feed mixture of 20/80 mol% for CO2/N2 at 30 °C and 2 bar (Table 1 and Figure 7b). Comparing the data from the single-gas and mixture gas, we see that the selectivity is nearly the same, while the gas permeance is decreased by around 1% for the mixture gas. For the SPONGl-4s membrane, the CO2 permeance decreased from 1030 to 970 GPU while the selectivity decreased from 41.9 to 41.1 when we switched to the mixed gas feed.
- Figure 7c shows the single-gas separation performance for the SPONG2 membranes.
- these membranes yield a lower CO2 gas permeance but a higher CO2/N2 ideal selectivity (Table 2).
- the SPONG2-4s membrane yielded a CO2 permeance of 620 GPU with a CO2/N2 ideal selectivity of 57.2.
- Figure 9 shows the comparison of the SPONG membranes with the state-of-the-art membranes for the carbon capture (separation of the CO2/N2 mixture).
- the target area indicates that the desired membrane should have a high CO2 permeance (>1000 GPU) and moderate separation factor (>20) to achieve an economical CO2 capture from flue gas.
- the outstanding separation performance of the SPONG membranes is clearly established by the comparison in Figure 9.
- the SPONGl-6s membrane shows an exceptionally high CO2 permeance of 4940 GPU with a moderate CO2/N2 separation factor of 25.8 at 30 °C. At 40 °C, the CO2 permeance increased to 6100 GPU while the CO2/N2 separation factor, 22.5, remained in the target area. This CO2 permeance is nearly 60 fold higher than that from the commercial cellulose acetate membrane, while their CO2/N2 separation factors are comparable. 6
- the membrane achieved an outstanding CO2 capture performance, that is, CO2 permeance is 6100 GPU with a CO2/N2 separation factor of 22.5, mainly attributing to two reasons: (i) the single layer graphene with a high density of nanopores combined with the ultrathin polymer can afford a high gas permeance due to the short diffusion pathway; and (ii) the CC philic polymer can increase the solubility and adsorption of CO2, thus affording a high selectivity of CO2/N2.
- the approach of hybrid membranes involving single-layer graphene with another CC philic layer could pave the way for the large-scale commercialization of the membranes for carbon capture.
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