Upload
others
View
3
Download
0
Embed Size (px)
Citation preview
S E P A R A T I ON S : MA T E R I A L S , D E V I C E S A ND P RO C E S S E S
Simultaneously enhancing interfacial adhesion andpervaporation separation performance of PDMS/ceramiccomposite membrane via a facile substrate surface graftingapproach
Guining Chen | Haipeng Zhu | Yingting Hang | Quan Liu | Gongping Liu |
Wanqin Jin
State Key Laboratory of Materials-Oriented
Chemical Engineering, College of Chemical
Engineering, Nanjing Tech University, Nanjing,
China
Correspondence
Dr Gongping Liu, State Key Laboratory of
Materials-Oriented Chemical Engineering,
College of Chemical Engineering, Nanjing Tech
University, 5 Xinmofan Road, Nanjing 210009,
China.
Email: [email protected]
Funding information
Topnotch Academic Programs Project of
Jiangsu Higher Education Institutions (TAPP);
Ministry of Education of China, Grant/Award
Number: IRT17R54; National Natural Science
Foundation of China, Grant/Award Numbers:
21490585, 21776125, 21922805; National
Key Basic Research Program, Grant/Award
Number: 2017YFB0602500
Abstract
A facile substrate surface silane-grafting approach was demonstrated to enhance both
interfacial adhesion and pervaporation separation performance of PDMS composite
membrane. With C16 grafted ceramic substrate, the PDMS/ceramic composite mem-
brane exhibited up to 1.7 times stronger interfacial adhesion force between separation
layer and substrate layer, meanwhile 1.5 times larger butanol/water separation factor
that is higher than state-of-the-art membranes. This novel approach paves a new ave-
nue to developing composite membranes with high and stable separation performance.
K E YWORD S
butanol recovery, ceramic hollow fiber, interfacial adhesion, PDMS membrane, surface
grafting
1 | INTRODUCTION
Separation is an essential process in chemical industry, among which
membrane technology can lower global energy use and reduce carbon
dioxide footprint.1 However, it remains challenge to develop high-
performance membranes enabling replacement of conventional sepa-
ration processes.2 Although a great number of membrane materials
with outstanding transport properties (permeability) have been devel-
oped, most of them for gas or vapor separation are based on symmet-
ric membrane with a thick separation layer, and thus providing a low
permeance (or flux) during realistic separation process.3 To realize a
high-efficiency separation process, a thin-film composite (TFC) mem-
brane is often required, consisting of a thin selective layer supported
on a porous substrate.
Two methods are often used to fabricate TFC membranes: Interfa-
cial polymerization and surface coating.4 Rubbery polymers, such as
polydimethylsiloxane (PDMS) and polyether block amide (PEBA), have
been widely used for pervaporation separation of volatile organic
compounds (VOCs)5 and gas separations (e.g., O2/N2, H2/CO2).3 They
are fabricated into TFC membranes mainly based on surface coating
approach, whose structural stability is of great concern due to the dif-
ferent swelling properties6,7 and/or interfacial incompatibility8
between selective layer and substrate. Thus, this kind of TFC mem-
branes is prone to be delaminated as applied in practical separation
process.6 A transition layer is usually introduced to enhance the inter-
facial adhesion of composite membranes by creation of ionic9 or
chemical bonding7,10 between selective layer and substrate. However,
preparation of the transition layer would complicate the membrane
fabrication process, and meanwhile, introduce additional transport
resistance causing loss of flux. Another general challenge forGuining Chen and Haipeng Zhu contributed equally to this study.
Received: 31 December 2018 Revised: 14 August 2019 Accepted: 24 August 2019
DOI: 10.1002/aic.16773
AIChE Journal. 2019;65:e16773. wileyonlinelibrary.com/journal/aic © 2019 American Institute of Chemical Engineers 1 of 6
https://doi.org/10.1002/aic.16773
developing high-performance TFC membranes is formation of a thin
and defect-free selective layer on a macroporous substrate.4 Dilute
polymer solution could reduce the membrane thickness to increase
the permeance. However, it may also inevitably suffer the polymer
penetrating into the substrate pores,11 which would result in defects
to lower the selectivity and higher transport resistance to sacrifice the
permeance.12 Recently, a sacrificial nanostrand layer was delicately
deposited on top of an ultrafiltration substrate to realize fabrication of
an ultrathin polyamide separation layer providing ultrafast molecular
transport.13 Nevertheless, removal process of the sacrificial
nanostrand layer might damage the separation layer and thus remains
challenging for most TFC membranes.
In this work, alternatively, we propose a facile substrate surface
grafting approach to simultaneously enhance interfacial adhesion and
separation performance of PDMS/ceramic composite membrane.
Specifically, it is realized by grafting long alkane chains (C16) onto the
surface of ceramic substrate to enhance the molecular interaction
between the surface groups of the substrate and PDMS chains of the
separation layer, and meanwhile create an organophilic surface
to improve the wetting and spreading of PDMS solution on the
substrate.
2 | SUBSTRATE SURFACE GRAFTING ANDCOMPOSITE MEMBRANE FORMATION
As shown in Figure 1a, a macro-porous Al2O3 hollow fiber (average
pore size � 1,100 nm)14 was modified with 5 wt% hexadecy-
ltrimethoxysilane (HDTMS)/ethanol solution for 4 hr and then annealed
at 120�C for 12 hr. The surface hydroxyl groups of Al2O3 substrate was
reacted with the methyoxyl groups of HDTMS to form Al O Si cova-
lent bond. HDTMS has been used to modify porous inorganic mem-
brane (TiO2, Al2O3) to create a hydrophobic surface for separation of
nonpolar organic solvents15 or membrane distillation.16 Alternatively,
the long C16 chains attached on the substrate surface aim to interact
with PDMS chains to provide considerable interfacial interactions for
the final PDMS/ceramic composite membrane. From the IR analysis
(Figure S1), it is found that after modification the ceramic substrate
shows new peaks at 2,944 and 2,876 cm−1 corresponding to the C H
stretching vibrations from CH3 and CH2 , and 910 cm−1
corresponding to the characteristic peak of Si O C (Figure S1b). This
result combined with the spectrum of HDTMS (Figure S1c) indicate
successful grafting of the alkane chains on the ceramic substrate. The
formation of Al O Si bond was further confirmed by XPS characteri-
zation. In the Al 2p scan, there is a new peak at 76.48 eV corresponding
to the Al O Si bonding17 in HDTMS modified ceramic substrate
(Figure S2). Furthermore, in the O 1s scan, new peaks appear at 531.13,
531.95, and 533.68 eV, which are related to Si O C, Si OH, and
Si O Si bonds, respectively18,19 (Figure S3). It suggests that there are
some unreacted methyoxyl groups, hydrolytic methyoxyl groups, and
reaction between two methyoxyl groups to form Si O Si bond.
The long alkane chains on the surface could regulate surface prop-
erty of the ceramic substrate, which is evidenced by the contact angle
test. Water was dropped on the substrate surface to measure the
hydrophobicity. As shown in Figure 1b, the water contact angle on
the unmodified substrate becomes 0� within 1 s, suggesting a very
hydrophilic surface due to the surface hydroxyl groups (Al–OH). After
HDTMS grafting, the ceramic substrate surface is transformed to be
very hydrophobic, showing a stable water contact angle of 145�,
which is resulted from super-hydrophobicity of the surface attached
F IGURE 1 Design and fabrication of PDMS membrane supported on surface-grafted ceramic substrate: (a) ceramic hollow fiber substrate issurface grafted with C16 chains using hexadecyltrimethoxysilane (HDTMS) and then dip-coated with PDMS solution to form PDMS/ceramichollow fiber composite membrane; (b) water contact angle on the surface of unmodified and modified ceramic substrate; (c) typical SEM imagesof cross-section of PDMS selective layer supported on the modified ceramic hollow fiber substrate [Color figure can be viewed atwileyonlinelibrary.com]
2 of 6 CHEN ET AL.
C16 chains rather than the changes of surface nanostructure
(Figure S4). These C16 chains meanwhile make the substrate surface
very organophilic that exhibit high affinity towards PDMS solution
using n-heptane as the solvent, as confirmed by the low contact angle
of n-heptane on the modified ceramic substrate (19.8� shown in
Figure S5). Thus, the wetting and spreading of PDMS solution on the
surface of ceramic substrate could be significantly improved during
the coating process of composite membrane preparation. Therefore, a
homogenous PDMS separation layer was easily deposited on the sur-
face of ceramic hollow fiber substrate via a facile dip-coating method.
As displayed in Figure 1c, a uniform hollow fiber structure is observed
for the PDMS/ceramic composite membrane. The ceramic hollow
fiber substrate has an asymmetric porous structure consisting of
sponge-like pores on the top and finger-like pores underneath
(Figure S6), which offer smooth coating surface and low transport
resistance, respectively.9 Typically shown in Figure 1c, an even PDMS
separation layer with controlled thickness is coated on the outer
surface of the porous ceramic substrate.
3 | INTERFACIAL ADHESION OFCOMPOSITE MEMBRANES
To probe interfacial adhesion of the as-prepared PDMS/ceramic
composite membrane, we first employed molecular dynamics
(MD) simulation to study the interfacial molecular interaction of
PDMS chains with ceramic (Al2O3) surface before and after surface
grafting of C16 chains.20 The constructed PDMS–unmodified ceramic
interface and PDMS–C16 modified ceramic interface models are given
in Figure 2a,b, respectively. According to the thermodynamics theory,
the interaction energy ΔE can be calculated as: ΔE = EPDMS-substrate
– (EPDMS + Esubstrate), where EPDMS-substrate is the energy of PDMS-
substrate interface; EPDMS and Esubstrate are the energies of the
equilibrated PDMS and substrate, respectively. The calculation results
in Table 1 indicate that the interaction energy between the PDMS
and substrate is enhanced by 14 times after grafting C16 on the sub-
strate surface, from −318.8 to −5,652.5 kcal/mol. Both the van der
Waals and electrostatic interactions are improved in the PDMS-
modified substrate interface, where the electrostatic interaction based
on locally charged atoms (Scheme S2a)21 dominates the enhancement
of interfacial interaction.
With the above atomic-level understanding, we then experimentally
probed the interfacial adhesion behavior of the composite membranes
using an in situ nanoindentation/scratch technique22 (Figure 2c). The
measurement monitors and records the scratch distance relationships
with the dynamic load, friction force, and corresponding friction coeffi-
cient. As shown in Figure S7, critical load at the failure is considered as
the interfacial adhesion force of the PDMS layer onto the ceramic sub-
strate. More details of the nanoindentation/scratch measurements are
provided in the Supporting Information. Figures 2d,e presents typical
scratch morphologies of the PDMS/ceramic composite membranes by
ramping the critical load to maximum. It can be directly seen that the
cracking of the PDMS-substrate interface is significantly reduced in the
surface modified substrate supported PDMS composite membrane. To
quantify the interfacial strength, we further measured the critical loads
of PDMS/ceramic composite membranes with membrane thickness
F IGURE 2 Interfacial adhesion between PDMS layer and ceramic substrate: (a) unmodified and (b) surface modified ceramic-PDMS interfacemodels constructed by molecular dynamics simulation (“in-cell” display style) to calculate the interfacial interaction energy; (c) schematic ofnanoindentation/scratch test on the PDMS/ceramic composite membrane to measure the interfacial adhesion force; SEM images of surfacescratch morphology of PDMS membrane layer supported on (d) unmodified and (e) surface modified ceramic hollow fiber substrate; (f) measuredinterfacial adhesion force of PDMS membranes with various thicknesses supported on unmodified and surface modified ceramic hollow fibersubstrate. The values for unmodified samples are adopted from our previous study22 [Color figure can be viewed at wileyonlinelibrary.com]
CHEN ET AL. 3 of 6
from 5 ± 0.2 to 12 ± 0.3 μm prepared by varying coating viscosity from
3.0 to 15 cP (Figure 2f). Generally, the composite membrane with
thicker PDMS layer exhibits higher interfacial adhesion, which is consis-
tent with our previous study.22 Film thickness is a key parameter
influencing the critical load (interfacial adhesion) in the nanoscratch test.
In principle, film thickness can have two opposing effects: Thicker films
that are harder than the underlying substrate provide more load support
and so delay the onset of the substrate deformation that is often the
precursor of film failure (higher critical load); and thicker films can be
more highly stressed and more easily through thickness crack and
delaminate when deformed (lower critical load) since the driving force
for spallation to reduce stored elastic energy is greater.
Notably, with the same thickness (e.g., 5 ± 0.2 μm), PDMS layer
coated on the surface-modified ceramic hollow fiber achieves stron-
ger interfacial adhesion than that on the unmodified substrate
(e.g., 30.67 mN vs. 17.9 mN). The enhancement is more remarkable
for the composite membrane with thinner PDMS layer, which is par-
ticularly favorable for developing composite membrane with thinner
membrane thickness and thus higher permeate flux. Noting that the
membrane thickness is thicker than recently reported PDMS thin-
composite membranes applied for flue gas and air separations,23
propane/propene separation24 and water vapor removal from air,25
which might be due to the diverse applications have different require-
ments in membrane thickness, as well as using different substrates to
fabricate the PDMS membrane.
Two possible reasons can be attributed to the enhanced interfacial
adhesion: (a) substrate surface grafted C16 chains interact with PDMS
chains20; (b) PDMS chains penetrating the substrate pores provide
mechanical interlocking.26 The first contribution has been verified by
the highly increased interfacial interaction energy of the composite
membrane using C16 grafted substrate according to the MD simula-
tion calculation (Figure 2a,b, Table 1). The second factor was studied
by comparing the penetration of PDMS into the porous substrate
before and after surface grafting C16. As shown in Figures S8 and S9,
there is little difference in the EDX line scans of Si element (only from
PDMS layer) for the cross-section of composite membrane supported
on unmodified and modified ceramic hollow fiber substrate,
suggesting a similar penetration of PDMS for both composite
membranes. Therefore, the significant improvement of interfacial
adhesion force probed in the PDMS membrane coated on the modi-
fied substrate is mainly owing to the highly enhanced molecular inter-
action between PDMS chains and ceramic substrate surface grafted
with C16 chains. It is noted that the measured interfacial adhesion
force between PDMS separation layer and ceramic hollow fiber sub-
strate is an actual parameter for determining the structural stability of
the resulting composite membrane, whereas the calculated interaction
energy between PDMS and (unmodified or modified) ceramic is used
to understand the interfacial interaction mechanism.
4 | SEPARATION PERFORMANCE OFCOMPOSITE MEMBRANES
The separation performance of PDMS/ceramic composite membranes
was evaluated by pervaporation recovery of butanol from aqueous
solution—A key process for in situ concentrating butanol from bio-
mass fermentation process of biobutanol production.27 Typical sepa-
ration conditions (i.e., operating temperature and feed composition)
were chosen to simulate the biobutanol recovery process from its fer-
mentation broth. As shown in Figure 3a, increasing the membrane
thickness generally reduces the total flux while increases the separa-
tion factor [YA/YB/(XA/XB), Yi and Xi are the weight fractions of
components in permeate and feed side, respectively; A: n-butanol; B:
water]. The thickness-dependent flux is reasonable according to the
Fick's law that membrane flux is in inverse proportion to its thickness.
While the higher separation factor with thicker membrane indicates
that some minor defects were eliminated as increasing the separation
layer thickness. These defects might be produced by the nonideal
coating of PDMS solution on the surface of substrate. As discussed
above, the wetting and spreading of PDMS solution can be highly
improved by regulating the surface wettability with the aid of grafting
organophilic C16 chains on the substrate. As expected, the separation
factor of the PDMS composite membranes coated on modified sub-
strate is much higher than using the unmodified substrate. For
instance, the separation factor for �12 ± 0.3 μm-thick PDMS compos-
ite membrane is improved from 36 to 53 by using the surface C16
grafted substrate. The slightly lower total flux in the modified hollow
fiber supported PDMS composite membrane is actually due to the
desirable suppression of water flux compared with the unmodified
hollow fiber supported membrane, as shown in Figure 3b.
Compared with reported membranes for butanol recovery, our
ceramic hollow fiber supported PDMS composite membranes exhibit
good separation performance (blue dash line in Figure 3c), especially
high flux, owing to the thin PDMS layer and low transport resistance
of the ceramic hollow fiber. Notably, the substrate surface grafting
approach preserves the high flux while further enhances the separation
factor of PDMS/ceramic hollow fiber composite membrane (red solid
line in Figure 3c). To show the great potential in practical application,
we further applied the surface modified ceramic hollow fiber supported
PDMS composite membrane with enhanced interfacial adhesion and
separation performance for recovering acetone–butanol–ethanol (ABE)
TABLE 1 Interaction energies between PDMS and substrate
ModelTotal energy(kcal/mol)
van der Waals(kcal/mol)
Electrostatic(kcal/mol)
PDMS −2,655.9 −206.1 −3,096.5
Unmodified substrate −43,746.3 −35,620.2 −8,178.3
C16 modified substrate −41,737.0 −33,778.8 −8,186.2
PDMS-unmodified
substrate
−46,783.9 −39,871.2 −11,290.5
PDMS-modified
substrate
−50,045.4 −39,465.6 −11,571.6
EPDMS-unmodified substrate −381.8 −4,044.9 −15.8
EPDMS-modified substrate −5,652.5 −5,480.7 −288.9
4 of 6 CHEN ET AL.
solvents that are full products in biobutanol fermentation process.
As expected, the membrane performance is excellent and stable
during more than 100 hr continuous operation, with a total flux
�1,081 g/m2 hr and separation factor [YA/YB/(XA/XB), Yi and Xi are
the weight fractions of components in permeate and feed side,
respectively; A: acetone, n-butanol or ethanol; B: water] for acetone
�28.1, for butanol �28.9, and for ethanol �6.2 (Figure 3d). Neverthe-
less, longer operation time would be required to obtain a more compre-
hensive structural stability during separation process.
5 | CONCLUSIONS
In summary, we have demonstrated a facile substrate surface grafting
approach simultaneously enhancing interfacial adhesion and separation
performance of PDMS/ceramic composite membrane. The long orga-
nophilic alkane chains (C16) grafted on the substrate surface highly
enhanced the molecular interaction and thus interfacial adhesion (up to
1.7-fold) between substrate with PDMS separation layer; meanwhile
significantly improved the wetting and spreading of PDMS solution on
the substrate to afford much larger butanol/water separation factor
(up to 1.5-fold) without loss of flux in the PDMS/ceramic hollow fiber
composite membrane that is higher than state-of-the-art polymeric
membranes. This novel approach might open a new door to developing
highly permeable, selective, and stable composite membranes.
ACKNOWLEDGMENTS
This work was financially supported by National Key Basic Research
Program (2017YFB0602500), National Natural Science Foundation of
China (Nos. 21922805, 21776125, 21490585), Innovative Research
Team Program by the Ministry of Education of China (No. IRT17R54)
and Topnotch Academic Programs Project of Jiangsu Higher
Education Institutions (TAPP).
ORCID
Gongping Liu https://orcid.org/0000-0002-3859-1278
Wanqin Jin https://orcid.org/0000-0001-8103-4883
F IGURE 3 Separation performance of PDMS/ceramic hollow fiber composite membrane: Effect of substrate surface grafting and membranethickness on (a) the total flux and separation factor and (b) individual flux for pervaporation separation of 1 wt% butanol/water mixtures at 40�C;(c) performance comparison with state-of-the-art polymeric membranes in literature for butanol recovery from aqueous solution, more details arelisted in Table S1; (d) a typical result of PDMS membrane supported on surface-modified substrate for continuous pervaporation separation ofacetone/butanol/ethanol/water (0.6/1.2/0.3/98 wt%) mixtures at 40�C. The values for unmodified samples are adopted from our previousstudy22 [Color figure can be viewed at wileyonlinelibrary.com]
CHEN ET AL. 5 of 6
REFERENCES
1. Koros WJ, Zhang C. Materials for next-generation molecularly selec-
tive synthetic membranes. Nat Mater. 2017;16:289-297.
2. Koros WJ, Lively RP. Water and beyond: expanding the spectrum of
large-scale energy efficient separation processes. AIChE J. 2012;58(9):
2624-2633.
3. Baker RW, Low BT. Gas separation membrane materials: a perspec-
tive. Macromolecules. 2014;47(20):6999-7013.
4. Lau WJ, Ismail AF, Misdan N, Kassim MA. A recent progress in
thin film composite membrane: a review. Desalination. 2012;287:
190-199.
5. Ong YK, Shi GM, Le NL, et al. Recent membrane development for per-
vaporation processes. Prog Polym Sci. 2016;57:1-31.
6. Wu H, Zhang X, Xu D, Li B, Jiang Z. Enhancing the interfacial stability
and solvent-resistant property of PDMS/PES composite membrane
by introducing a bifunctional aminosilane. J Membr Sci. 2009;337(1):
61-69.
7. Zhou H, Su Y, Chen X, Luo J, Tan S, Wan Y. Plasma modification of
substrate with poly(methylhydrosiloxane) for enhancing the interfacial
stability of PDMS/PAN composite membrane. J Membr Sci. 2016;520:
779-789.
8. Chen J, Chen X, Yin X, Ma J, Jiang Z. Bioinspired fabrication of com-
posite pervaporation membranes with high permeation flux and struc-
tural stability. J Membr Sci. 2009;344(1):136-143.
9. Zhao C, Wu H, Li X, et al. High performance composite membranes
with a polycarbophil calcium transition layer for pervaporation dehy-
dration of ethanol. J Membr Sci. 2013;429:409-417.
10. Liu Y-L, Yu C-H, Ma L-C, Lin G-C, Tsai H-A, Lai J-Y. The effects of
surface modifications on preparation and pervaporation dehydration
performance of chitosan/polysulfone composite hollow-fiber mem-
branes. J Membr Sci. 2008;311(1):243-250.
11. Vankelecom IFJ, Moermans B, Verschueren G, Jacobs PA. Intrusion
of PDMS top layers in porous supports. J Membr Sci. 1999;158(1):
289-297.
12. Shin C, Jiang X, Ko W, Balsara NP. Effect of pore penetration on
transport through supported membranes studied by electron micros-
copy and pervaporation. J Membr Sci. 2017;542:18-23.
13. Karan S, Jiang Z, Livingston AG. Sub–10 nm polyamide nanofilms
with ultrafast solvent transport for molecular separation. Science.
2015;348(6241):1347-1351.
14. Dong Z, Liu G, Liu S, Liu Z, Jin W. High performance ceramic hollow
fiber supported PDMS composite pervaporation membrane for bio-
butanol recovery. J Membr Sci. 2014;450:38-47.
15. Gao N, Li M, Jing W, Fan Y, Xu N. Improving the filtration perfor-
mance of ZrO2 membrane in non-polar organic solvents by surface
hydrophobic modification. J Membr Sci. 2011;375(1):276-283.
16. Chen X, Gao X, Fu K, et al. Tubular hydrophobic ceramic membrane
with asymmetric structure for water desalination via vacuum mem-
brane distillation process. Desalination. 2018;443:212-220.
17. Armelao L, Gross S, Obetti G, Tondello E. Er3+-doped SiO2–Al2O3 thin
films prepared by the sol–gel route. Surf Coat Technol. 2005;190(2):
218-222.
18. Barr TL. An ESCA study of the termination of the passivation of ele-
mental metals. J Phys Chem. 1978;82(16):1801-1810.
19. Armyanov S, Stankova NE, Atanasov PA, et al. XPS and μ-Raman
study of nanosecond-laser processing of poly(dimethylsiloxane)
(PDMS). Nucl Instrum Methods Phys Res Sect B. 2015;360:30-35.
20. Liu G, Xiangli F, Wei W, Liu S, Jin W. Improved performance of
PDMS/ceramic composite pervaporation membranes by ZSM-5
homogeneously dispersed in PDMS via a surface graft/coating
approach. Chem Eng J. 2011;174(2):495-503.
21. Patra M, Karttunen M, Hyvönen MT, Falck E, Lindqvist P,
Vattulainen I. Molecular dynamics simulations of lipid bilayers: major
Artifacts due to truncating electrostatic interactions. Biophys J. 2003;
84(6):3636-3645.
22. Hang Y, Liu G, Huang K, Jin W. Mechanical properties and interfacial
adhesion of composite membranes probed by in-situ nano-
indentation/scratch technique. J Membr Sci. 2015;494:205-215.
23. Liang CZ, Yong WF, Chung T-S. High-performance composite hollow
fiber membrane for flue gas and air separations. J Membr Sci. 2017;
541:367-377.
24. Liang CZ, Chung T-S. Ultrahigh flux composite hollow Fiber membrane
via highly Crosslinked PDMS for recovery of hydrocarbons: propane
and propene.Macromol Rapid Commun. 2018;39(5):1700535.
25. Liang CZ, Chung T-S. Robust thin film composite PDMS/PAN hollow
fiber membranes for water vapor removal from humid air and gases.
Sep Purif Technol. 2018;202:345-356.
26. Wei W, Xia S, Liu G, Gu X, Jin W, Xu N. Interfacial adhesion between
polymer separation layer and ceramic support for composite
membrane. AIChE J. 2010;56(6):1584-1592.
27. Liu G, Wei W, Jin W. Pervaporation membranes for Biobutanol pro-
duction. ACS Sustain Chem Eng. 2014;2(4):546-560.
SUPPORTING INFORMATION
Additional supporting information may be found online in the
Supporting Information section at the end of this article.
How to cite this article: Chen G, Zhu H, Hang Y, Liu Q, Liu G,
Jin W. Simultaneously enhancing interfacial adhesion and
pervaporation separation performance of PDMS/ceramic
composite membrane via a facile substrate surface grafting
approach. AIChE J. 2019;65:e16773. https://doi.org/10.1002/
aic.16773
6 of 6 CHEN ET AL.