Carbon Dioxide Separation Through Polymeric Membra
Carbon Dioxide Separation Through Polymeric Membra
Carbon Dioxide Separation Through Polymeric Membra
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Carbon Dioxide Separation through Polymeric Membrane Systems for Flue Gas
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Geoff Stevens
University of Melbourne
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Received: October 27, 2007; Accepted: November 6, 2007; Revised: November 15, 2007
Abstract: The capture and storage of carbon dioxide has been identified as one potential solution to greenhouse gas
driven climate change. Efficient separation technologies are required for removal of carbon dioxide from flue gas streams
to allow this solution to be widely implemented. A developing technology is membrane gas separation, which is more
compact, energy efficient and possibly more economical than mature technologies, such as solvent absorption. This
review examines the recent patented developments in polymeric based membranes designed for carbon dioxide separation
from mixed-gas systems. Initially, the background to polymeric membrane separation is provided, with an overview of
past polymeric designs. This is followed by a discussion on the current state of the art; in particular developments in
mixed matrix polymeric membranes and facilitated transport polymeric membranes for improved carbon dioxide
permeation and selectivity. Recent developments in other membrane types, carbon and inorganic, are reviewed for
comparison purposes with polymeric developments. Finally, a brief comment on the future directions of polymeric
membrane gas separation technologies is provided.
Keywords: Polymeric membranes, gas separation, carbon dioxide, mixed matrix membranes, facilitated transport membranes.
Fig. (2). Schematic representation of three of the different possible mechanisms for membrane gas separation, Knudsen diffusion, molecular
sieving and solution-diffusion.
CO2 44 3.3
O2 32 3.46
N2 28 3.64
H2O 18 2.65
CH4 16 3.8
H2 2 2.89
C = CD + CH (5)
Where CH is the standard Langmuir relationship
Fig. (3). Schematic representation of the relationship between the
C' H b ƒ
CH = (6) polymer specific volume and temperature in an amorphous polymer
(1 + b ƒ ) (reprinted with permission from [28]).
bound to membrane performance. This upper bound can carbon dioxide flux of cellulose acetate based membranes
clearly be seen in Fig. (4), for a range of membranes invol- decreases substantially with time, due to the material being
ved in CO2/N2 separations. Overcoming this upper bound is susceptible to plasticisation and compaction under feed
the focus of many recently awarded patents in polymeric stream conditions. Therefore, later polymeric membrane
membranes, because achieving both high carbon dioxide patents focus on more robust polymers that achieve greater
permeability and selectivity is desirable. selectivity and/or permeability. Improving the performance
of the CO2-selective polymeric membrane is achieved by
two approaches; increasing the solubility of carbon dioxide
in the membrane through changes in polymeric composition,
and increasing the diffusion of carbon dioxide by altering the
polymer packing within the membrane. Diffusion is
generally enhanced by increasing the volume of free space
within the membrane and this can sometimes be achieved
through the addition of bulk substituent groups [9]. The
polymer packing in glassy membranes and thus the free
volume is also influenced by the casting method and
annealing conditions. Therefore, along with the polymeric
materials, casting methods have also been patented [35].
The combination of these approaches has produced a
wide range of polymeric membranes with reasonable
permeability and selectivity to provide good carbon dioxide
separation. Some patented polymeric membranes are based
on polyamides [36-44], polysemicarbazides [45], polycarbo-
nates [46-50], polyarylates [51, 52], poly(phenylene oxide)
[53-57], polyaniline [58-60] and polypyrrolones [61]. These
all have reasonable permeability and selectivity, with some
achieving performance around Robeson’s upper bound. The
difference between individual patents for each polymeric
system is through the addition of bulky substituent and
Fig. (4). Comparison of Robeson’s curve for CO2/N2 separation by functional groups to the polymer, as well as cast history.
carbon membranes (o) and polymeric membranes (•) [9, 33].
One of the most widely patented polymeric materials are
polysulfones [62-72]. They are regarded as among the most
Improving permeability and selectivity are not the only
membrane properties that are important. For membrane chemically and thermally durable thermoplastic polymers
available; and polysulfones have been extensively applied to
materials to be viable, they need to be thermally and chemi-
gas separation. More recently, polyimides based membranes
cally robust, resistant to plasticisation and aging affects to
have out performed polysulfones, displaying some of the
ensure continual performance over long time periods, and be
best permeability and selectivity properties for purely
cost effective to manufacture as standard membrane
polymeric membranes [73-95]. This coupled with their
modules.
thermal, chemical and plasticisation resilience, as well as
Patents have been awarded for a wide range of polymeric considerable mechanical strength makes them an attractive
based membranes that claim to meet these aims. Here, material for gas separation membranes. The performance of
original polymeric and inorganic membrane patents are these two polymers has resulted in a large number of patents.
reviewed briefly to inform the reader of past developments Differences between patents deal with substituent groups to
in the art, since the majority of these patents were awarded in change the carbon dioxide solubility, membrane packing
the 1980s and early 1990s. This review will then focus on density and free volume, as well as improving the membrane
recent novel approaches in polymeric membranes that resistance to harsh environments.
achieve separation performance above Robeson’s upper
More recent patents on purely polymeric membranes
bound and therefore are possibly more commercially com-
have focused on combining different polymers to produce
petitive than present membrane gas separation technologies.
composite polymeric membranes. The copolymers used
2. MEMBRANE TECHNOLOGY - STATE OF THE generally have a glassy (hard) polymer segment and a
ART rubbery (soft) polymer segment [9]. The hard segment forms
the structural frame and provides the mechanical support.
2.1. Polymeric Membranes
The rubbery segment generally forms continuous microdo-
The first carbon dioxide separating membranes were mains within the membrane and the flexible nature of the
based on cellulose acetate and derivatives thereof, originally structure allows the transportation of gas, hence greater
designed for reverse osmosis [14, 34]. These polymeric permeability. The idea is to combine the selectivity of one
membranes are characterized by a thin, dense selective polymer with the permeability of the other to provide a better
surface ‘skin’ on a less dense porous support that is non- performance membrane. Again, a considerable number of
selective. This is the basis of all asymmetric membrane patents have been awarded for copolymer membranes, with
materials that are readily used in industry. However, the the best performance based on blends of polyimide [77, 96-
56 Recent Patents on Chemical Engineering, 2008, Vol. 1, No. 1 Kentish et al.
100]. These copolymer blends have improved separation molecules (Table 1) dictates which molecular sieves are
performance over polyimides, while retaining high mecha- useful and provides an indication of selectivity [17]. For
nical, thermal and chemical stability. example, Zeolite 3A separates hydrogen effectively from
hydrocarbon feeds because the pore diameters are ~3 Å
2.2. Inorganic Membranes [109]. Zeolite 4A has pore sizes of ~ 4 Å, which will
Inorganic membranes represent an alternative gas separate carbon dioxide from nitrogen and methane.
separation technology; however it is not the purpose of this Molecular sieving based inorganic membranes incorpo-
review to cover these membranes in detail. There are two rate such materials into the pores of a porous support. This
major categories of inorganic membranes, porous and non- integrates the size exclusion properties of the molecular
porous. Non-porous membranes are generally used in highly sieve within the pores, providing selective gas separation
selective separation of hydrogen, where transportation is [110]. A major difficulty with this approach is to achieve an
through alloys of palladium [101] or oxygen through perovs- efficient trap of the sieve particles within the pores. Both the
kite systems [102-104]. Porous inorganic membranes are pore and sieve sizes must be well-known and sufficiently
generally cheaper but less selective. The attraction of inor- similar to ensure strong packing of the pores. Otherwise, the
ganic systems is their ability to operate at high temperatures. gaps between the sieves and the pore walls will allow bulk
A particular high temperature operation of interest is the diffusion of gas molecules, diminishing selectivity
separation of carbon dioxide from hydrogen in syngas performance [111].
processes.
3. RECENT DEVELOPMENTS IN POLYMERIC
The large size of carbon dioxide relative to hydrogen
MEMBRANE SYSTEMS
means that achieving a carbon dioxide rich permeate stream
by simple molecular sieving is not possible Table 1. The current research into polymeric membranes is
Inorganic membranes overcome this by functionalizing the focused on increasing the polymeric performance above
pores of the membrane to increase the carbon dioxide Robeson’s upper bound to become cost competitive with
loading. Permeability then becomes a function of surface solvent absorption, as well as improving the resilience of the
diffusion. Recent patents describe inorganic membranes that membrane material. McKeown et al. [112] disclose the
consist of a ceramic support, such as Al2O3, onto which a formation of microporous polymeric structures with very
porous separating layer is added, often silica, alumina or high free volumes. These polymers of intrinsic microporosity
zirconia. To this a functional layer is added, BaTiO3 by Ku et (PIMs) are rod-like randomly contorted structures which
al. [105] or MgO by Gobina [106]. These functional groups generate intrinsic cavities within the membrane. They exhibit
have a high chemical affinity for carbon dioxide and behaviour analogous to conventional molecular sieves, but
therefore the pore walls become saturated, which increases have greater solubility.
the permeability, as shown in Fig. (5). For BaTiO3 on
Young et al. [113] detail the cross-linking of polybenzi-
alumina, for 5 nm pores a CO2/H2 selectivity of 3.1 is
midazole for improved mechanical properties. Unmodified
achieved at 500oC and for 1 nm pores a selectivity of 18.4 is
polybenzimidazole has been covered in past patents and
achieved. Similarly for MgO, a CO2/N2 selectivity of 120 is provides reasonable permeability and selectivity for carbon
obtained with a carbon dioxide permeability of > 0.02 barrer
dioxide separation from methane [114, 115]. Cross-linking
at 350oC. These membrane performances approach Robe-
of the polymer improves the mechanical properties, by
son’s upper bound for carbon dioxide separation and are
increasing the yield stress of the membrane, which also
therefore compatible with polymeric membranes.
results in increased separation performance. The patented
example has a carbon dioxide permeation of 7.9 barrer with a
selectivity over nitrogen of 27, when the polymer is cross-
linked, compared to a carbon dioxide permeability of 0.3
barrer with a selectivity of 18 for unmodified linear poly-
benzimidazole, at 23oC tested by single gases. The effect of
cross-linking on performance is dependent on the linking
agent.
Wang and Yeager [116] present solvent resistant
polymeric membranes that can reduce the plasticisation
effects of hydrocarbons in the feed stream. The patent covers
Fig. (5). Schematic of inorganic membrane operation through polyketone, polyether ketone, polyarylene ethere ketone,
Knudsen and surface diffusion (adapted from [107]). polyimide, polyetherimide and polyphenylene sulphide,
which have intrinsic solvent inertness and can therefore
Molecular sieves exist in both natural and synthetic withstand organic rich operation conditions. Ekiner and
forms, and can be classed as zeolites (aluminosilicate com- Simmons [117] describe the controlled annealing of hollow
positions), or non-zeolites, such as aluminophosphates, fiber polyimide membranes. The annealing conditions
silico-aluminophosphates and silica [108]. The molecular patented are for the polyimide based membrane to exist
sieve framework forms a well-defined repeating structure of under a vacuum less than 15 inches of mercury at between
regular channels and cages. Gas separation is dependent on 100-250oC for 6-30 hours. This controlled annealing
the size of these channels and cages relative to the kinetic improves chemical resistance and ensures that the resulting
diameter of the gas. The difference in kinetic diameter of gas hollow fibers have the necessary mechanical strength for
Carbon Dioxide Separation through Polymeric Membrane Recent Patents on Chemical Engineering, 2008, Vol. 1, No. 1 57
high pressure and temperature applications. However, results in a doubling of selectivity, with a loss in
annealing conditions for polymeric membranes are relatively permeability. This arises because the compatibilizer prevents
well known and therefore the novelty of some of the patent’s phase separation within the membrane and hence reduces the
claims is questionable. Weinberg [83] deals with aromatic- free volume. Too much PSMA in the membrane leads to
polyimide based membranes that have improved perfor- itself phase separating, which affects both selectivity and
mance at low temperature. This allows the membrane to be permeability to the detriment of performance Table 3.
utilized in cold temperature applications without the need for
heating of the feed gas. The improved performance relies on 3.1. Carbon Membranes
the increased solubility of carbon dioxide at these Carbon membranes are a variant of polymeric memb-
temperatures being greater than the loss in diffusivity. The ranes that operate as molecular sieves [119]. These
patented example of asymmetric hollow fibers of this membranes generally have higher permeability and selec-
aromatic polyimide can be seen in Table 2. However, none tivity for carbon dioxide than polymerics, Fig. (4). However,
of these recent patents are able to achieve a selectivity and the carbon structures are not easily formed into thin layers
permeability combination that exists above Robeson’s upper and so while the permeability may be high, the actual flux
bound. through the thick membranes may not. The membranes are
Table 2. The Temperature Dependent Permeability (Barrer) fabricated by pyrolyzing organic materials, typically
and Selectivity of an Aromatic-Polyimide Based Mem- polymers, in a non-oxidizing atmosphere upon a structural
brane, for a CO2/N2 Gas Mixture of 72:28 Mole Ratio support that can withstand the high temperatures. The
at 448 kPa [81]. resulting membrane is comprised almost entirely of carbon
and manifests as an active surface with controlled pore
structure. These pore structures allow for effective separation
Temperature performance of novel aromatic-polyimide membranes
of composite gas mixtures through both a molecular sieve
-22oC 10oC 50oC mechanism, as well as by surface diffusion. The choice of
the organic precursor material is important, because this will
CO2 Permeability (barrer) 0.232 0.147 0.091 influence pore size and structure, and hence determine the
N2 Permeability (barrer) 0.0035 0.0045 0.0053 performance of the membrane. Suitable precursors include
resins, surfactants, graphite and polymers [120]. Their
CO2/N2 66.3 32.7 17.1 advantage over polymeric membranes is that they can with-
stand high temperatures and are more durable. Therefore,
carbon membranes are often employed in chemical reactors
Two recent patents have been awarded for polymeric and catalytic systems. Different production processes for
blends. The patent awarded to Ekiner and Simmons [100] carbon membranes have been covered [121-124]. These
covers polyamide, polyimide and polyamide-imide blends, patents generally involve heating of the organic material
which have increased mechanical strength and chemical above its decomposition temperature in an argon or nitrogen
resistance over the pure polymeric membranes, with only rich environment.
slight changes in permeability and selectivity. Seo [118]
describes semi-crystalline amorphous polymeric blends with Carbon membranes can be relatively brittle and this can
a compatibilizer agent within the membrane matrix to ensure lead to cracking, greatly diminishing their performance
miscibility of the two polymers. The patent examples of [119], as well as making fabrication of carbon based
poly(phenylene oxide) with Nylon 6 are provided in Table 3. membrane modules difficult. Furthermore, differences in the
Poly (phenylene oxide) has been patented previously as a gas thermal expansion coefficient with the support can
separation membrane material, with reasonable selectivity exasperate cracking at high temperature or if the membrane
and permeability. The addition of the semi-crystalline Nylon experiences thermal cycling. This increases the associated
6, results in a decrease in permeability for only a slight cost of the membrane modules compared with polymeric
increase in selectivity. However, addition of the membranes. The recent patent of Foley, Rajagopalan and
compatibilizer poly(styrene-co-maleic anhydride) (PSMA) Merritt [125] strengthens carbon membranes by incor-
Table 3. Permeability (Barrer) and Selectivity of Poly (Phenylene Oxide) (PPO) Membranes with Nylon 6, with the Addition of a
Compatibilizer, Poly(Styrene-co-Maleic Anhydride) (PSMA), for Single Gases at 35oC and 1 atm [118].
Table 4. Carbon Dioxide Permeability (Barrer) and Selectivity in Mixed Matrix Membranes Based on Polyvinylacetate Within the
Inclusion of Various Zeolites, Measured for Single Gases at 35oC and 410 kPa [132].
Silicalite, is a common non-zeolite hydrophobic crystal- Table 6. The Carbon Dioxide Permeability (Barrer) and Selec-
line silica. Grose and Flanigen [136] show that treating such tivity of Liquid-Phased Based Mixed Matrix Memb-
a non-zeolite with organosilicon compounds also improves ranes Made of Silicone Rubber on a Porous Poly-
the selectivity of a polyvinyl acetate based mixed matrix sulfone Support, with the Inclusion of Poly Ethylene
membrane through the reduction of micro-cavities, in this Glycol (PEG), Activated Carbon or Carbonate to
case by 33% (Table 5). Improve Separation Performance, Measured for
Single Gases at Ambient Temperature
Table 5. Gas Selectivity of Mixed Matrix Membranes Based on
Polyvinylacetate with Various Molecular Sieves
Included, Measured for Single Gases at 35oC and 410 Phase Particle CO2 Selectivity
kPa [135]. Permeability (CO2/N2)
Silicone 14.3 11
Continuous Molecular Sieve Selectivity Rubber
Phase (CO2/N2)
Silicone Polyethylene Glycol 4.89 42
Poly vinyl acetate Na-SSZ-13 34.7 Rubber
Poly vinyl acetate APDMS treated Na-SSZ-13 51.2 Silicone Activated Carbon 29.4 15
Rubber
Poly vinyl acetate Silicalite 32.3
Silicone Polyethylene Glycol + 24.2 47
Poly vinyl acetate APDIPS-treated Silicalite 36.9
Rubber Activated Carbon
Poly vinyl acetate APDMS-treated silicalite 43.1
Silicone Activated Carbon + 16.2 20.1
Rubber carbonate
Additional treatments of molecular sieves can be under- Silicone PEG + Activated 14.3 40.5
taken to improve performance, with washed zeolites covered Rubber Carbon + carbonate
in the patent awarded to Kulkarni et al. [137]. Washing
zeolites in aqueous ionic solutions alters their operating pH
and surface functionality, in this case making a more basic increase in permeability of 70% and selectivity by a factor of
structure that will therefore increase the solubility of carbon 4 is achieved, compared to previous silicone rubber memb-
dioxide within the mixed matrix. ranes on porous and non-porous supports [140].
Mixed matrix membranes based on polymers with Marand and Kim [141] cover the inclusion of meso-
intrinsic porosity (PIMs) as well as rubbery continuous porous silica into mixed matrix membranes. The patent
phases have also been patented [138, 139]. Kulprathipanja example is based on polysulfone for the polymeric phase,
and Charoenphol [138] add activated carbon to increase the with obtained permeabilities and selectivities provided in
selectivity of silicone rubber by surface diffusion. The Table 7. The inclusion of mesoporous silica MCM41 and
activated carbon has a particle size between 0.1 and 5 MCM48 into polysulfone increases the permeability of
microns. Improvements in both the selectivity and permea- carbon dioxide with slight changes to the selectivity.
bility are shown in Table 6. The inclusion of polyethylene Increasing the weight of the silica substantially increases the
glycol acts as a plasticizer on the silicone rubber and permeability of carbon dioxide because of the increase in
therefore assists the emulsion with activated carbon. An micro-cavities within the membrane, resulting in a small loss
in selectivity. Functionalizing the silica with amine groups
increases the association with the polysulfone phase and
60 Recent Patents on Chemical Engineering, 2008, Vol. 1, No. 1 Kentish et al.
Table 7. Permeabilities (Barrer) and Selectivity of Polysulfone Based Mixed Matrix Membranes with Mesoporous Silica [141]
readily carried across the membrane, whereas diffusion of carbon dioxide, of which arsenite salts are suggested to be
non-reactive gases is inhibited, see Fig. (9). The active the most practical. With the inclusion of carbonate in these
carrier is generally basic in nature, given that carbon dioxide membrane systems, as well as the catalysts, the permeability
is acidic. The driving force for gas transportation remains the and selectivity are dramatically increased. The difference in
partial pressure difference across the membrane; however the carbon dioxide permeability and selectivity can be compared
facilitator carrier increases both the permeability and in Table 8.
selectivity of the membrane through the increased loading.
The immobilized liquid nature of the facilitator
The facilitator carrier can be either fixed-sited within the
membrane poses practical problems, such as leakage and
polymeric matrix or mobile. An illustrated schematic of a
evaporation of water, as well as loss of the facilitator through
fixed-sited carrier, polyvinylamine, in operation is provided
degradation. Hence, their performance over long periods of
in Fig. (9). time presents problems for large scale applications. Much of
the recently patented facilitated transport membranes have
focused on reducing these aging effects. In this regard,
Sirkar et al. [151] disclose the use of dendrimers as carriers.
The use of an amine-rich dentritic structure such as the
Starburst polyamidoamine (PAMAM) [152] leads to high
CO2 solubiltiy. These structures can be immobilised in a
polymeric matrix or alternatively, dissolved in a CO2-philic
liquid solvent which is placed within a mesoporous subs-
trate.
Recent patents have been awarded for the incorporation
of fixed carriers into existing porous polymeric supports,
generating a composite structure [153, 148]. This is then
swollen by the addition of water vapour, facilitating the
transfer of carbon dioxide along the polymer chain through
the membrane. Methods differ for the casting and cross-
linking of the fixed carrier layer, as well as attachment to the
porous polymeric support, with the desired result improving
mechanical and thermal properties of the composite layer to
increase stability of the membrane [153, 148]. Use of a
Fig. (9). Schematic of fixed carrier facilitator transport membrane polyvinylamine selective layer on a porous poly sulfone
for transport of carbon dioxide (reprinted from [148]). support, when polymer cross linking occurs by glutaral-
dehyde, results in a carbon dioxide permeability of 4100
The first facilitated transport membranes patent was barrer and a CO2/CH4 selectivity of 70, at room temperature
awarded to General Electric in 1967 [149, 150]. This related for a CO2/CH4 gas mixture. In contrast, fluorine based cross-
to cellulose acetate films swollen by the inclusion of an linkers, such as NH4F, provide fixed facilitator layers with
aqueous carbonate solution. Carbon dioxide readily dissolves greater permeability (3095 Barrer) and CO2/CH4 selectivity
and reacts with water to form the bicarbonate anion. (1143) [148]. A possible reason for this is the fluorine anion,
being considerably basic, allows increased carbon dioxide
H2O + CO2 (aq) H2 CO3 (aq) H + (aq) + HCO-3 (aq) loading within the membrane. The molecular weight of the
Carbonate acts as a carrier by increasing the amount of fixed facilitator polymer influences the selectivity but not the
carbon dioxide absorbed: permeability of carbon dioxide in the membrane, as shown in
Fig. (10).
CO32- (aq) + CO2 (aq) + H2O 2HCO-3 (aq) (+ Heat)
More recent patents have focused on hydrogel films from
Hence, this reaction occurs on the feed side of the cross-linked hydrophilic polymers, such as polyvinyl alc-
membrane and the bicarbonate anion transports through to ohol, polyvinylacetate, polyvinyl pyrrolidone, polyethylene
the permeate side, where the reverse reaction occurs and oxide, polyacrylamide, bends and copolymers, cast on
carbon dioxide is released. This patent also allows for the permeable supports [154, 155]. These hydrogels have a high
inclusion of catalysts into the facilitator membrane to water absorbing power and therefore can accommodate
increase the rate of reaction between the carbonate and
Table 8. Wet Cellulose Acetate Facilitated Membranes for Carbon Dioxide Separation, at Ambient Temperature and 4 kPa [149]
Table 9. Carbon Dioxide Permeability (Barrer) and Selectivity in a Range of Mobile Carrier Facilitated Transport Membranes.
Test Gases are Mixtures of 90% N2 10% CO2 at 98 kPa or 75% H2 25% CO2 at 300 kPa, at Ambient Temperature
Vinyl alcohol / acrylate copolymer [158] 2 M K2 CO3 and 0.05 M 18-crown-6 740 670
Vinyl alcohol / acrylate copolymer [158] 2 M K2 CO3 and 0.05 M EDTA 2400 1417
Carbon Dioxide Separation through Polymeric Membrane Recent Patents on Chemical Engineering, 2008, Vol. 1, No. 1 63
Table 10. Carbon Dioxide Permeability (Barrer) and Selectivity in a Range of Mobile, Fixed and Combined Carrier Facilitated
Transport Membranes, for Gas Mixtures of 40/20/40 or 75/25/0 of H2, CO2 with N2, at 200-300 kPa and Ambient
Temperature
Polyvinyl alcohol [155] Glycine (50 %wt) - polyethylenimine (25 %wt) 194 28
Polyvinyl alcohol (cross linked Glycine (50 %wt) - polyethylenimine (25 %wt) 186 31
formaldehyde) [155]
Polyvinylalcohol (cross linked) [155] Dimethylglycine (23.6 %wt) - polyethylenimie (23.6 %wt) 602
Polyvinylalcohol (cross linked (23.6 % wt) Dimethylglycine - polyethylenimine (23.6 %wt) - KOH (6.4 %wt) 338 1782
formaldehyde) [155]
Polyvinylalcohol (cross link) [155] Aminoisobutyric acid (27.2 %wt) - polyallylamine (10.1 %wt) - KOH (16.8 %) 6196 262
Polyvinylalcohol (cross link) [155] Aminoisobutyric acid (19.6 %wt) - polyallylamine (9.8 %wt) - KOH (18.1 8278 170
%wt)
the efforts to prevent membrane degradation, the study of [27] Plate N, Yampol'skii YP. Relationship between structure and
minor component effects will be an area of interest in the transport properties for high free volume polymeric materials, in:
Polymeric Gas Separation Membranes. Baton Rouge: CRC Press
near future. 1994; 115-208.
To conclude, with the rapidly increasing interest in [28] Kanehashi S, Nagai K. Analysis of dual-mode model parameters
for gas sorption in glassy polymers. J Membrane Sci 2005; 253:
carbon dioxide capture to mitigate global warming, gas 117-138.
separation polymeric membranes will remain an active [29] Favre E. Carbon dioxide recovery from post-combustion processes:
research area and the patented literature will continue to Can gas permeation membranes compete with absorption? J
grow as new discoveries are made in the art. Membrane Sci 2007; 294: 50-59.
[30] Hendriks C. Carbon dioxide removal from coal-fired power plants.
REFERENCES Dortecht: Kluwer Academic Publishers; 1994.
[31] Roberts C., Gibbins J.R., Panesar R., Kelsall G. Improvement in
[1] Carapellucci R, Milazzo A. Membrane systems for CO2 capture power generation with post-combustion capture of CO2.
and their integration with gas turbine plants. Proc Inst Mech Eng Cheltenham: IEA Greenhouse Gas R & D Programme; 2004.
Part A. J Power Energy 2003; 217: 505-517. [32] Robeson L. Correlatoin of separation factor versus permeability for
[2] Thambimuthu K, Davidson J, Gupta M. CO2 capture and resuse. In: polymeric membranes. J Membr Sci 1991; 62: 165-185.
Proc. Canda; IPCC Workshop on carbon capture and storage; [33] Saufi S, Ismail A. Fabrication of carbon membranes for gas
2002. separation - a review. Carbon 2004; 42: 241-259.
[3] Aaron D, Tsouris C. Separation of CO2 from flue gas: a review. [34] Watson, E.R., Rowley, G.V., Wunderlich, C.R.: US3432585
Separ Sci. Technol 2005; 40: 321-348. (1969).
[4] Rao A, Rubin E. A technical, economic and environmental [35] Lee, M.-S., Choi, S.-H., Shin, Y.-C.: US20030134550 (2003).
assessment of amine-based CO2 capture technology for power plant [36] Hoehn, H.H., Richter, W.J.K.: US3899309 (1975).
greenhouse gas control. Environ Sci Technol 2002; 36: 4467-4475. [37] Hoehn, H.H.: US3822202 (1974).
[5] Feron P. CO2 capture: The characterisation of gas separation/ [38] Bentz, F., Elfert, K., Kunzel, H.E., Wolf, G.D.: US4217227 (1980).
removal membrane systems applied to the treatment of flue gases [39] Richter, W.J.K., Hoehn, H.H.: DE1941022 (1970).
arising from power generation using fossil fuel. Cheltenham: IEA [40] Richter, W.J.K., Hoehn, H.H.: DE1941932 (1970).
Greenhouse Gas R & D Programme; 1992. [41] Steadly, H., Laccetti, A.J.: US4770777 (1988).
[6] Abertz V, Brinkmann T, Dijkstra M, et al. Developments in [42] Hayes, R.A.: US5076817 (1991).
membrane research: from material via process design to industrial [43] Harris, J.E., Berger, A., Chopdekar, V.M., Matzner, M., Spanswick
application. Adv Eng Mater 2006; 8: 328-358. J.: US4713438 (1987).
[7] Basu A, Akhtar J, Rahman M, Islam M. A Review of separation of [44] Manos, P.: EP0219878 (1987).
gases using membrane systems. Petrol Sci Technol 2004; 22: 1343- [45] Richter, W.J.K., Hoehn, H.H.: US3567632 (1971).
1368. [46] Sanders, E.S.J., Wan, H.S., Beck, H.N.: US4975228 (1990).
[8] Stern S. Polymers for gas separation: the next decade. J Membrane [47] Sanders, E.S.J., Overman, D.C.: EP0500974 (1992).
Sci 1994; 94: 1. [48] Beck, H.N., Sanders, E.S.J., Lipscomb, G.G.: US4962131 (1990).
[9] Powell C, Qiao G. Polymeric CO 2/N2 gas separation membranes [49] Anada, J.N., Feay, D.C., Bales, S.E., Jeanes, T.O.: EP0242147
for the capture of carbon dioxide from power plant flue gases. J (1987).
Membrane Sci 2006; 279: 1-49. [50] Jeanes, T.O.: EP0316960 (1989).
[10] Maiser G. Gas separation with polymer membranes. Angew Chem [51] Chen, N., Tien, C.-F., Patton, S.M.: US5232471 (1993).
Int Ed. 1998; 37: 2960. [52] Tien, C.-F., Surnamer, A.D.: EP0455216 (1991).
[11] Koros W. Gas separation membranes: needs for combined [53] Pedretti, U., Gandini, A., Roggero, A., Sisto, R., Valentini, C.,
materials science and processing approaches. Macromol Symp Assogna, A., Stopponi, A.: US5169416 (1992).
2002; 188:13. [54] Laverty, B.W., Vujosevic, R., Dang S., Yao B., Matsuura T.,
[12] Baker R. Future directions of membrane gas separation technology. Chowdhury G.: GB2334526 (1999).
Ind Eng. Chem Res 2002; 41: 1393. [55] Percec, E.S., Li, G.S.: US4596860 (1986).
[13] Graham TP. Mag 1866; 32: 402. [56] Li, G.S.: US4586939 (1986).
[14] Loeb, S., Sourirajan, S.: US3133132 (1964). [57] Farias, O., Gandini, A., Monga, R., Roggero, A., Sisto, R.,
[15] Jawad M. Future for desalination by reverse osmosis. Desalination Valentini, C.: EP0360318 (1990).
1989; 72: 23-28. [58] Hachisuga, H.: JP11342322 (1999).
[16] Podall H. Recent advances in reverse osmosis membranes for [59] Hachisuga, H., Matsumoto, K., Obara T.: JP6238138 (1994).
desalination. Chem Eng Prog 1971; 67: 260-266. [60] Illing, G.: DE19936044 (2001).
[17] Koros W. Gas Separation, in: Membrane Separation Systems - [61] Koros, W.J., Walker, D.R.B.: US5262056 (1993).
Recent Developments and Future Directions Baker RW. William [62] Chiao, C.C.: US4717395 (1988).
Andrew Publishing; 1991. [63] Bikson, B., Coplan, M.J., Goetz, G.: US4508852 (1985).
[18] Paul D, Yampol'skii Y. Polymeric gas separation membranes. [64] Coplan, M.J., Park, C.H., Williams, S.C.: US4414368 (1983).
baton rouge: CRC Press 1994. [65] Rose, J.B.: US4268650 (1981).
[19] Spillman R. Economics of gas separation by membranes. Chem [66] Rose, J.B.: US4273903 (1981).
Eng Prog 1989; 85: 41. [67] Quentin, J.: US4054707 (1977).
[20] Mazur W, Chan M. Membranes for natural gas sweetening and [68] Quentin, J.: US3709841 (1973).
CO2 enrichment. Chem Eng Prog 1982; 78: 38-43. [69] Chiao, C.C.: US4828585 (1989).
[21] Coady A, Davis J. CO2 recovery by gas permeation. Chem Eng [70] Bourganel, J.: US4026977 (1977).
Prog 1982; 78: 43-49. [71] Graefe, A.F., Saltonstall, C.W.J., Schell, W.J.: US3875096 (1975).
[22] Fritzsche A, Kurz J. The separation of gases by membranes, in: [72] Kawakami, J.H., Bikson B., Gotz, G., Ozcayir, Y.: EP0426118
Handbook of industrial membrane technology porter MC, editor. (1991).
William Andrew Publishing 1990; 559-593. [73] Hayes, R.A.: US4880442 (1989).
[23] Hill T. Surface diffusion and thermal transpiration in fine tubes and [74] Hayes, R.A.: US4717393 (1988).
pores. J Chem. Phys. 1956; 25; 730-745. [75] Hayes, R.A.: US4705540 (1987).
[24] Hwang S-T, Kammermeyer K. Membrane Separations. New York: [76] Kohn, R.S., Coleman, M.R., Chung, T.-S.: US5055116 (1991).
Wiley-Interscience 1975. [77] Macheras, J.T.: US5635067 (1997).
[25] Rhim H, Hwang S-T. Transport of capillary condensate. J Colloid [78] Black, L.E., Boucher, H.A.: US4571444 (1986).
Interf. Sci. 1975; 52: 174-181. [79] Wan, W.-K.: US4836927 (1989).
[26] Lee K-H, Hwang S-T. The transport of condensible vapors through [80] White, L.S.: US20016180008 (2001).
a microporous Vycor glass membrane. J Colloid Interf. Sci. 1986; [81] Carlsen, D.B., Andrus, R.G., Hall, R.T.: US5605627 (1997).
110: 544-555. [82] Ekiner, O.M., Simmons, J.W.: WO9405404 (1994).
[83] Weinberg, M.G.: EP0554862 (1993).
66 Recent Patents on Chemical Engineering, 2008, Vol. 1, No. 1 Kentish et al.
[84] Iwama, A., Iwahori, H., Kazuse, Y.: US4358378 (1982). [130] Rojey, A., Deschamps, A., Grehier, A., Robert, E.: US4925459
[85] Makino, H., Nakatani, M.: US4690873 (1987). (1990).
[86] Alegranti, C.W.: US4113628 (1978). [131] Rhone, P.: FR2079460 (1971).
[87] Pfeifer, J., Ciba, G.A.: EP0141781 (1985). [132] Hasse, D.J., Kulkarni, S.S., Corbin, D.R.: US2003089227 (2003).
[88] Makino, H., Yoshihiro, H.T., Shimazaki, H.: US4370290 (1983). [133] Sterzel, H.-J., Sanner, A.: EP0154248 (1985).
[89] Makino, H., Kusuki, Y., Harada, T., Shimazaki, H., Isida, T.: [134] Kulprathipanja, S., Neuzil, R.W., Li, N.N.: US5127925 (1992).
US4528004 (1985). [135] Kulkarni, S., Hasse, D.J., Corbin, D.R., Patel, A.N.:
[90] Makino, H., Kusuki, Y., Harada, T., Shimazaki, H., Isida, T.: US20036508860 (2003).
US4474858 (1984). [136] Grose, R.W., Flanigen, E.M.: US4061724 (1977).
[91] Shimatani, S., Yamamoto, M., Shimazu, A., Iwama, A.: [137] Kulkarni, S., Ekiner, O.M., Hasse, D.J.: US2005230305 (2005).
US4964887 (1990). [138] Kulprathipanja, S., Charoenphol, J.: US2003089228 (2003).
[92] Blinka, T.A., Itatani, H., Wang, I.-F.: US5042992 (1991). [139] Te, H.H.J.C., Mulder, M.H.V., Smolders, C.A., Bargeman, D.,
[93] Jeanes, T.O., Summers, J.D., Sanders, E.S.J.: US4988371 (1991). Schroder, G.A., Setec, B.V.: EP0254759 (1988).
[94] Chung, T.-S., Chng, M.L., Shao, L.: US20040177753 (2004). [140] Henis, J.M.S., Tripodi, M.K.: US4230463 (1980).
[95] Lee, Y.-M., Park, H.B., Lee, C.-H.: US20040236038 (2004). [141] Marand, E., Kim, S.: US2007022877 (2007).
[96] Maeda, M.: US5969087 (1999). [142] Freeman, B.D., Matteucci, S., Lin, H.: US2007137477 (2007).
[97] Simmons, J.W.: WO0249747 (2002). [143] Kulkarni, S., Hasse, D.J.: US2007199445 (2007).
[98] Langsam, M.: US5939520 (1999). [144] Ekiner, O.M., Fleming, G.K.: US5468430 (1995).
[99] Sakellaropoulos, G.P., Kaldis, S.P., Kapantaidakis, G.C., Dabou, [145] Vu D, Koros W, Miller S. Mixed matrix membranes using carbon
X.S.: EP0778077 (1997). molecular sieves. J Membrane Sci 2003; 211: 335.
[100] Ekiner, O.M., Simmons, J.W.: US20060156920 (2006). [146] Miller, S.J., Yuen, L.-T.: US2005043167 (2005).
[101] Hsieh H. Inorganic membranes. Membr Mater Proc 1990; 84: 91. [147] Miller, S.J., Kuperman, A., Vu, D.Q.: US2006107830 (2006).
[102] Iwahara, H., Yamaji, T., Azuma, S.: JP56041804 (1981). [148] Hagg, M.-B., Kim, T.-J., Li, B.: WO05089907 (2005).
[103] Oshima, H., Seki, Y.: JP8071385 (1996). [149] Gen, E.: GB1076438 (1967).
[104] Shreiber, E.H., Eardley, E.P., Srinvasan, V., van Hassel, B.A., [150] Gen, E.: GB1167797 (1967).
Shah, M.M.: US20026623714 (2002). [151] Sirkar, K.K., Kovvali, S., Chen, H.: WO03008070 (2003).
[105] Ku, A.Y.-C., Ruud, J.A., Molaison, J.L., Schick, L.A., [152] Kovvali A, Chen H, Sirkar KK. Dendrimer Membranes: A CO2-
Ramaswamy, V.: WO07037933 (2007). Selective Molecular Gate. J Am Chem Soc 2000; 122: 7594-7595.
[106] Gobina, E.: US2006112822 (2006). [153] Wang, Z., Wang, S., Lu, Q.: CN1363414 (2002).
[107] Ku, A.Y.-C., Ruud, J.A., Molaison, J.L., Schick, L.A., [154] Ho, W.S.W.: US20006099621 (2000).
Ramaswamy, V.: WO07037933 (2007). [155] Ho, W.S.W.: WO06050531 (2006).
[108] Dyer A. An Introduction to Zeolite Molecular Sieves. New York: J [156] Kulprathipanja, S., Charoenphol, J.: WO03039728 (2003).
Wiley & Sons 1988. [157] Ho, W.S.W.: US5611843 (1997).
[109] Guiver, M.D., Robertson, G.P., Thi, H.N.L.: CA2421875 (2004). [158] Nakabayashi, M., Okabe, K., Mishima, T., Mano, H., Haraya, K.:
[110] Suzuki, H.: EP0180200 (1986). EP0638353 (1995).
[111] Berger, C.: US3567666 (1971). [159] Lackner, K., West, A.C., Wade, J.L.: WO06113674 (2006).
[112] McKeown, N.B., Budd, P.M., Msayib, K., Ghanem, B.: [160] Qi Z, Cussler EL. Microporous hollow fibres for gas absorption II:
WO05012397 (2005). Mass transfer across the membrane. J Membrane Sci 1985; 23:
[113] Young, J.S., Long, G.S., Espinoza, B.F.: WO06028594 (2006). 333-345.
[114] Davis,H.J., Thomas, N.W.: US4020142 (1977). [161] Feron P, Jansen A, Klaassen R. Membrane technology in Carbon
[115] Dye, R.C., Jorgensen, B., Pesiri, D.R.: US20046681648 (2004). Dioxide removal. Energy Conv Man 1992; 33: 421-428.
[116] Wang, H., Yeager, G.W.: US2007056901 (2007). [162] Yeon S-H, Lee K-S, Sea B, ParkY-I, Lee K-H. Application of
[117] Ekiner, O.M., Simmons, J.W.: US2006196355 (2006). pilot-scale membrane contractor hybrid system for removal of
[118] Seo, Y.: US2007185264 (2007). carbon dioxide from flue gas. J Membrane Sci 2005; 257: 156-160.
[119] Ismail A., David L. A review on the latest development of carbon [163] Thakore, Y.B., Stoy, V.: US4954145 (1990).
membranes for gas separation. J Membrane Sci 2001; 193: 1-18. [164] Ward, W.J.: US4147754 (1979).
[120] Soffer, A., Koresh, J.E., Saggy, S.: US4685940 (1987). [165] Lee, G.S., Lee, G.H., Park, Y.I., Seo, B.G., Yoen, S.H.:
[121] Rao, M.B., Sircar, S., Golden, T.C.: US5104425 (1992). KR0042656 (2004).
[122] Rao, M.B., Sircar, S., Abrado, J.M., Baade, W.F.: US5354547 [166] Baba, T., Fukazama, T., Nishino, Y.: JP3218912 (1991).
(1994). [167] Yuan H.: US2007163432 (2007).
[123] Rao, M.B., Sircar, S., Golden, T.C.: US5431864 (1995). [168] Birbara, P.J., Nalette, T.A.: US5281254 (1994).
[124] Lee, Y.M., Park, H.B., Seo, I.Y.: KR008782 (2002). [169] Jansen, A.E., Feron, P.H.M.: US5749941 (1998).
[125] Foley, H.C., Rajagopalan, R., Merritt, A.R.: US2007017861 [170] Feron, P.H.M., Jansen, A.E.: NL9400483 (1995).
(2007). [171] Hesse, H.J.F.A., Smit, M.J., du Toit, F.J.: US20016312655 (2001).
[126] Lee S. Handbook of alternative fuel technologies. New York: [172] Al-Juaied M., Koros W.J. Performance of natural gas membranes
Taylor & Francis 2007. in the presence of heavy hydrocarbons. J Membrane Sci 2006; 274:
[127] Hagg, M.-B., Lie, J.A.: WO07017650 (2007). 227-243.
[128] Zimmerman C, Singh A, Koros W. Tailoring mixed matrix [173] Vu DQ, Koros WJ, Miller SJ. Effect of condensable impurities in
composite membranes for gas separation. J Membrane Sci 1997; CO2/CH 4 gas feeds on carbon molecular sieve hollow-fiber
137: 145. membranes. Ind Eng Chem Res 2003; 42: 1064-1075.
[129] Mahajan R, Zimmerman C, Koros W. Fundamental, practical
aspects of mixed matrix gas separation membranes. ACS Symp
Series 1999; 733: 277.