Article
pubs.acs.org/est
Degradation of Polyamide Nanofiltration and Reverse Osmosis
Membranes by Hypochlorite
Van Thanh Do,† Chuyang Y. Tang,†,‡,* Martin Reinhard,§ and James O. Leckie§
†
School of Civil & Environmental Engineering and ‡Singapore Membrane Technology Centre Nanyang Technological University,
Singapore, 639798
§
Department of Civil and Environmental Engineering, Stanford University, Stanford, California 94305, United States
S Supporting Information
*
ABSTRACT: The degradation of polyamide (PA) nanofiltration
and reverse osmosis membranes by chlorine needs to be
understood in order to develop chlorine-resistant membranes.
Coated and uncoated fully aromatic (FA) and piperazine (PIP)
semi-aromatic PA membranes were treated with hypochlorite
solution and analyzed by X-ray photoelectron spectroscopy (XPS)
and Fourier transform infrared (FTIR). XPS results showed that in
chlorine treated FA PA membranes the ratio of bound chlorine to
surface nitrogen was 1:1 whereas it was only 1:6 in the case of PIP
PA membranes. Surface oxygen of uncoated FA and PIP
membranes increased with increasing hypochlorite concentration
whereas it decreased for coated FA membranes. High resolution
XPS data support that chlorination increased the number of
carboxylic groups on the PA surface, which appear to form by hydrolysis of the amide bonds (C(O)−N). FTIR data indicated
the disappearance of the amide II band (1541 cm−1) and aromatic amide peak (1609 cm−1) in both coated and uncoated
chlorinated FA membranes, consistent with the N-chlorination suggested by the XPS results. Furthermore, the surface charge of
chlorinated membranes at low pH (<6) became negative, consistent with amide-nitrogen chlorination. Chlorination appeared to
both increase and decrease membrane hydrophobicity depending on chlorination exposure conditions, which implied that Nchlorination and hydrolysis may be competing processes. The effects of property changes on the membrane performance were
also observed for NF90, BW30, and NF270 membranes.
al. in 1994.4 The mechanisms that have been identified to
explain the properties and performance changes of chlorinated
polyamide membranes are summarized in Supporting Information S1. Chlorination of the amide nitrogen occurs when
active chlorine species (i.e., hypochlorous acid) attack the lone
electron pair of either the N or O atom of the amide group and
rearrange to the N-chloroamide.4−7 A direct ring chlorination
mechanism has also been proposed: the aromatic ring of mphenylene diamine is attacked by active (electrophilic) chlorine
species and substitution occurs preferentially at the para
position. 8,9 Indirect ring chlorination (termed Orton rearrangement) can be initiated by rapid N-chlorination followed by an
intramolecular rearrangement in which chlorine migrates to the
ring.10−12 Most of the previous studies have focused on the
incorporation of chlorine into the membrane matrix, but
systematic studies on oxygen composition changes and the role
of chlorine in promoting amide hydrolysis as a significant
competing degradation reaction are not reported.4
1. INTRODUCTION
Polyamide-based thin film composite (TFC) membranes are
the most widely used reverse osmosis and nanofiltration
membranes today, mainly because of their high selectivity and
water permeability.1 The basic types of membrane structures
and chemistries are illustrated in Figure 1. The fully aromatic
(FA) polyamide (PA) membrane is formed by interfacial
polymerization of m-phenylene diamine and trimesoyl chloride
(TMC) to obtain a three-dimensionally cross-linked rejection
layer, where the degree of cross-linking, n ranges from 0 (fully
linear) to 1 (fully cross-linked).2 The semi-aromatic PA
membrane is similarly synthesized by piperazine (PIP) and
TMC. Additional surface coating with polyvinyl alcohol (PVA)
is used for some commercial membranes to improve membrane
fouling resistance.2,3
A drawback of PA membranes is that they are degraded by
chlorine, which is commonly added in form of sodium
hypochlorite as a disinfectant to control biofouling or as a
membrane cleaning agent.4 Addressing the need for chlorineresistant membranes requires a mechanistic understanding of
the interactions between chlorine and the PA rejection layer of
membrane and how these effects impact membrane performance. A critical review of prior studies was reported by Glater et
© 2012 American Chemical Society
Received:
Revised:
Accepted:
Published:
852
September 3, 2011
December 1, 2011
December 14, 2011
January 5, 2012
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Figure 1. Schematic diagram of basic membrane structures and chemistries. Diagram is not to scale.
chemistry. In addition, the FA PA membranes SW30HR and
BW30 are coated with a polyvinyl alcohol (PVA) surface
coating. The physiochemical properties of these membranes are
provided in the Supporting Information S2. Membranes were
provided by Dow/FilmTec (Minneapolis, MN, U.S.), except
HL, which was from GE Osmonics (Minnetonka, MN, U.S.).
Sodium hypochlorite (∼10% NaOCl, reagent grade) was
obtained from Sigma Aldrich (St. Louis, MO, U.S.). Exact
concentrations for the soaking solutions were determined by a
standard titration method using sodium thiosulfate.27 All other
reagents and chemicals were of analytical grade with purity over
99%. Milli-Q water (Millipore, Billerica, MA, U.S.) was used in
all preparations and experiments.
2.2. Membrane Chlorination Procedures. Membrane
coupons, which were preserved as received at 4 °C, were
cleaned and soaked in Milli-Q water for 24 h before
chlorination experiments. Membranes were presoaked in
NaOCl solutions at the same testing conditions for 1 min to
remove excess water on the surface before being soaked in
NaOCl solutions with concentrations of 10, 100, 1000, and
2000 ppm for either 1 or 24 h to accelerate laboratory
degradation process.17,19,20 Since acidification is typically
performed in NF/RO plants for scaling control,28 soaking
solutions were adjusted to pH 5 by the addition of HCl or
NaOH so that HOCl is the main species.20 Samples were
contained in concealed 0.5 L Wheaton glass bottles with PTFElined caps, covered with aluminum foil (to protect the chlorine
from sunlight degradation), and constantly mixed on a shaker at
room temperature (∼21 °C). After exposure tests, the average
chlorine depletion of the soaking solutions was less than 10%,
and is within the magnitude reported in the literature.20
After soaking, the samples were thoroughly rinsed with MilliQ water. For XPS, FTIR, and contact angle measurements, the
membranes were vacuum-dried while zeta potential measurements were performed on wet samples immediately after
chlorination.
2.3. X-ray Photoelectron Spectroscopy (XPS). To
obtain information about composition and bonding chemistry
for the surface layer (top 1 to 5 nm sample thickness), XPS
analysis was carried out on a Kratos AXIS Ultra spectrometer
(Shimadzu, Columbia, MD, U.S.) with a monochromatic
aluminum Kα X-ray source at 1486.7 eV. To compensate for
membrane surface charging, the electron flood gun was
Effects of chlorination on membrane performance have been
reported in the literature but findings appear to be inconsistent.
The decline in water flux after membrane chlorination13−20 has
been attributed to an increase in membrane hydrophobicity
caused by chlorine attachment,13 “membrane tightening”,14,15
or a more rigid polymer conformation.17,18,21,22 In contrast, a
brief exposure to chlorine at high pH is used to treat PA RO
membranes after fabrication to improve performance.23,24 The
observed increase in flux is usually accompanied by a decrease
in salt rejection13−20,25 and proposed to be the result of the
polyamide chain cleavage,13−15 or physical separation of PA
rejection layer from its polysulfone support.18 Meanwhile,
better salt rejection of chlorine-treated membranes has been
attributed to the result of membrane tightening,14,15 or
enhanced PA chain cross-linking due to the formation of azocompounds or quinone-like species.18,26 Opposite trends are
observed in membrane surface charges and wettability as well.
Membrane zeta potential is observed to generally become more
negative after chlorination.19,22 Such change in surface charge
does not seem to be adequately explained by ring chlorination
or the Orton rearrangement mechanism. Hydrophobicity of
chlorinated membranes is reported to both increase and
decrease depending on chlorine concentration, soaking pH and
duration.19,22 To explain these observations by a single
mechanism is difficult. Therefore, more investigations and
possibly additional mechanisms are required to obtain insight
into the membrane degradation process by chlorination.
This paper presents evidence that chlorine treatment leads to
the uptake of chlorine and oxygen by PA membranes. Changes
in membrane surface and bulk chemistry as well as surface
charge and wettability are interpreted that subsequent reactions
with hypochlorite appear to hydrolyze the amide C−N bond of
the PA layer. The results show that chlorine treatment can
significantly modify the membrane properties.
2. MATERIALS AND METHODS
2.1. Chemicals and Materials. The commercial thin film
composite cross-linked PA membranes investigated in the
current study include three RO membranes (SW30HR, BW30,
and XLE) and three nanofiltration membranes (NF90, NF270,
and HL). According to our previous characterization work,2,3
NF270 and HL membranes have the semi-aromatic PIP PA
chemistry, the other four membranes are of the FA PA
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operated at 3.6 eV. Survey spectra were recorded 3 times per
sample, over the range of 0−1000 at 1 eV resolution. High
resolution scans had a resolution of 0.1 eV. Calibration for the
elemental binding energy were done based on the reference for
carbon 1s at 285 eV.29 Data were processed by standard
software with Shirley background and relative sensitivity factor
(RSF) of 0.78, 0.477, 0.278, and 0.891 for O 1s, N 1s, C 1s, and
Cl 2p peaks, respectively. Replicate analyses were done at each
chlorination condition for NF90, BW30, and NF270
membranes.
2.4. Attenuated Total Reflection-Fourier Transform
Infrared (ATR-FTIR). Bonding chemistry of the chlorinated
membranes was obtained using an FTIR (IRPrestige-21,
Shimadzu, Columbia, MD, USA) with 45° multi-reflection
HATR ZnSe flat plate crystal (PIKE Technologies, Madison,
WI, U.S.) as ATR element. Each spectrum was averaged from
50 scans over the range of 650−4000 cm−1 at a resolution of 2
cm−1. Baselines were corrected for atmospheric CO2 and water
vapor. One replicate was done for each sample.
2.5. Zeta Potential and Contact Angle Measurement.
Membrane surface charge was measured by a SurPASS
electrokinetic analyzer (Anton Paar GmbH, Graz, Austria)
with an adjustable gap cell and using 10 mM NaCl as
electrolyte solution. The cell channel height was adjusted to
∼110 ± 5 μm. The solution pH was automatically titrated from
3 to 9 using 0.1 M HCl and NaOH. The zeta potential was
calculated from the streaming potential using the Fairbrother−
Mastin formula.30
Contact angle measurements were performed with an OCA
Goniometer (Dataphysics Instruments, Filderstadt, Germany)
by the sessile drop method. A syringe with a needle diameter of
0.525 mm was used to place a water droplet of 10 μL on the
membrane. Tangent lines to both sides of the droplet static
image were generated and averaged by the software SCA20.
The reported contact angle of each membrane sample was the
average of 40 measurements (2 independent membrane
coupons and 20 different locations for each sample) with
errors indicated by the standard deviations.
2.6. Membrane Performance Tests. The laboratory-scale
NF/RO filtration system consisting of four identical cross-flow
test cells (CF042, Sterlitech, Kent, WA, U.S.) is illustrated and
fully described in Supporting Information S3. Each cell houses
42 cm2 (4.6 cm ×9.2 cm) of active membrane area. Spacers of
1.2 mm thickness from GE Osmonics (Minnetonka, MN, USA)
were used for all filtration tests.
Membrane performance tests were conducted for NF90,
BW30, and NF270. Prior to each filtration test, virgin
membranes (soaked in MiliQ water for 24 h) and freshly
degraded membranes were cleaned thoroughly with MiliQ
water. A 10 mM of NaCl feed solution at 21 °C and natural pH
(pH ≈ 6) was recirculated through the system for 24 h at 1 L/
min cross-flow velocity, corresponding to a superficial velocity
of 22.6 cm/s. The operating pressures for NF90, BW30, and
NF270 were set at 100, 260, and 70 psi, respectively, to obtain
similar virgin membrane fluxes (around 1.2 to 1.5 m/day).
Permeate flux was determined by a gravimetrical method. Salt
rejection was calculated from permeate and tank conductivity
measured by an Ultrameter II conductivity meter (Myron L
Company, Carlsbad, CA, U.S.). The equations to determine the
water permeability coefficient, A (m/s.Pa) and the solute
permeability coefficient, B (m/s) are provided in Supporting
Information S3 .
3. RESULTS AND DISCUSSION
3.1. Chlorine and Oxygen on Membrane Surfaces
Elemental Changes after Chlorination. Six membranes
Figure 2. Atomic percent of chlorine and nitrogen of chlorinated
uncoated fully aromatic (NF90 and XLE), PVA coated fully aromatic
(SW30HR and BW30), and uncoated poly(piperazinamide) (HL and
NF270) membranes at pH 5; 2000 ppm ×24 h, 1000 ppm ×24 h and
1000 ppm ×1 h.
Figure 3. Ratio of (a) oxygen to carbon and (b) oxygen to nitrogen as
a function of the atomic percent of bound chlorine for (●) NF270 and
(▲) NF90 at different chlorination conditions: pH 5; 2000 ppm × 24
h, 1000 ppm × 24 h, 1000 ppm × 1 h, 100 ppm × 24 h, 100 ppm × 10
h and 10 ppm × 100 h. The dotted and dashed lines represent the (a)
O/C and (b) O/N ratio for virgin NF270 and NF90, respectively.
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Figure 4. High resolution XPS spectra and deconvoluted peak assignments of (a) O 1s, C 1s, N 1s for virgin and (b) O 1s, C 1s, N 1s, Cl 2p for
chlorinated NF90 (2000 ppm × 24 h, pH 5). The Cl 2p peak of different bonding state is deconvoluted into Cl 2p3/2 and Cl 2p1/2. The peak
intensity ratio of Cl 2p3/2 over Cl 2p1/2 is constant (=2) and the binding energy of Cl 2p3/2 peak was used to identify chemical bonding.
In spite of the small chlorine uptake, the performance of
chlorinated PIP membranes is reported to be impaired by
chlorine exposure.19 This phenomenon requires a different
explanation for the attack of chlorine on the PIP PA structure.
The XPS results revealed that chlorination increased the O/
C ratio on the uncoated membrane surfaces (Figure 3a). This
ratio increased from 0.2 (virgin) to 0.3 (2000 ppm ×24 h) for
NF270 and from 0.15 (virgin) to 0.21 (2000 ppm × 24 h) for
NF90. The O/N ratio, which indicates the degree of PA crosslinking, was plotted against the chlorine content (Figure 3b).
Theoretically, the ratio of O/N is 1:1 for a fully cross-linked PA
layer (n = 1, Figure 1) and is 2:1 for a linear PA layer (n = 0).2
The O/N ratio of NF90 increased from 1.15 for virgin
membrane to 1.44 for the membrane treated with 2000 ppm
for 24 h. NF270 experienced the same increase in O/N ratio
from 1.24 to 1.69, which means that the chlorine treated
membranes were less cross-linked and that more C−N bonds
were broken. The increase of oxygen content and decrease in
the number of C−N bonds are hypothesized to result from C−
N bond hydrolysis, which leads to additional carboxylic acid
groups. Mechanistically, facilitated hydrolysis of the chlorinated
C−N bond may be explained by the polarization of the amide
carbon due to chlorine substitution at the nitrogen, which
makes the carbon more susceptible to nucleophilic attack by
hydroxide. Additional evidence for chlorination promoted
hydrolysis is presented in Sections 3.2 and 3.3.
3.2. Changes in Membrane Chemistry Due to
Chlorination. The high resolution XPS spectra for O, C, N,
and Cl of virgin and chlorinated (at 2000 ppm × 24 h) NF90
are illustrated in FIGURE 4. Changes in chemical bonding at
with 3 different chemistries were exposed to 1000 ppm NaOCl
solutions for 1 h at pH 5. In addition, NF90, BW30, and NF270
membranes were treated at 2000 and 1000 ppm for 24 h. The
results from the XPS survey scan show that the amount of
chlorine attached onto the PA surface decreased in the order:
uncoated FA > coated FA > PIP membranes. The correlations
between the chlorine (%) uptake of the surface layer and the
nitrogen atomic percentage are presented in Figure 2. The
chlorine to nitrogen atomic ratios (Cl/N ratio) of uncoated FA
membranes (NF90 and XLE) cluster around the 1:1 ratio line,
which suggests that chlorine attaches to the nitrogen of the
secondary amide via the N-chlorination mechanism. The
chlorine and nitrogen atomic percentages of the coated FA
membranes were 1:1 at 1000 ppm NaOCl × 1 h; however, both
percentages increased significantly at 1000 and 2000 ppm
NaOCl × 24 h. The average surface nitrogen content was ∼6%
at 1000 and 2000 ppm ×24 h, which is higher than nitrogen
content of virgin BW30.2 This is further accompanied with a
significant reduction in the oxygen content (Supporting
Information S4 and S5). These observations suggest that the
PVA coating was likely partially detached under severe
chlorination conditions employed. In addition, elevation of
the Cl/N ratio from 1 to 1.56 and 2.3 could suggest that
chlorine also binds to the coating PVA layer. The observation
that the PIP membranes NF270 and HL had Cl/N ratios much
less than 1 is consistent with the fact that tertiary nitrogen is
not chlorinated, as reported in the literature.6,12,26 The absence
of amide protons accounts for the low chlorine incorporation
into PIP membranes.4,12 Chlorination might still occur at the
noncross-linked nitrogen atoms, which exist at low abundance.
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Figure 6. Zeta potential for virgin and chlorinated (a) NF90 and (b)
NF270 as a function of pH. Background electrolyte was 10 mM NaCl.
The uncertain in zeta potential measurements is estimated to be ∼ ± 5
mV (Supporting Information S8 and Tang et.al41).
Figure 5. ATR−FTIR spectra for (a) NF90, (b) BW30, and (c)
NF270: virgin and chlorinated at pH 5; 2000 ppm × 24 h, 1000 ppm
× 24 h and 1000 ppm × 1 h.
Figure 7. Contact angle (deg) for virgin and chlorinated membranes.
Error bar indicates the standard deviations of 40 measurements (2
independent membrane coupons and 20 different locations for each
sample).
the surface of the PA layer can be understood through analysis
of the shifts in the binding energy (BE) of the deconvoluted
peak spectra. The assignments for deconvoluted peaks are
summarized in the table inserted in Figure 4.31−33 Only the
chlorine peak representing covalent bonding (∼200.7 eV) is
discussed. After chlorination, the second deconvoluted peak of
O 1s (∼532.6 eV) corresponding to H···OC−N, OC−O
bonds was shifted upward by about 0.6 eV; the second
deconvoluted C 1s (∼ 286.2 eV) peak, which is assigned to C−
O, C−N, C−Cl bonds, was shifted upward by about 0.13 eV.
For NF270, an increase in peak intensity was observed for the
second O 1s peak (∼532.6 eV, Supporting Information S6).
Although these shifts are not sufficiently distinctive to
deconvolute and assign new peaks, they may indicate an
increase in the number of carboxylic groups due to the
chlorine-promoted C−N bond hydrolysis.
Bulk chemistry changes due to chlorination in both
polysulfone and PA layers were obtained from the FTIR
spectra for virgin and chlorinated NF90, BW30 and NF270
(Figure 5). Peak assignments for the FTIR spectra of these PA
membranes were reported in detail elsewhere.3 The FA amide
signature peaks at wave numbers of 1541, 1609, and 1663 cm−1
experienced prominent changes in case of the NF90 and BW30
membranes, consistent with literature data.7,17,20,34,35 The
disappearance of the amide II band (1541 cm−1) for N−H
in-plane bending and N−C stretching vibration and aromatic
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ment and the ATR-FTIR measurement can reveal important
information on the degree of membrane chlorination across the
PA rejection layer.2 Although the XPS results showed less
surface chlorine on BW30 than on NF90 at short exposure
(1000 ppm × 1 h), FTIR spectra of chlorinated BW30 show a
complete disappearance of the amide II band (1541 cm−1) and
the aromatic amide peak (1609 cm−1). The latter suggests that
the PVA coating did not protect the FA PA matrix from
chlorine attack under the severe chlorination conditions applied
in this study. Therefore, the lower XPS chlorine signal for the
PVA coated membranes (Figure 2) was merely a reflection that
less PA was exposed at the membrane surface due to the
presence of the coating. Chlorine might have penetrated
through the coating and caused the damage to the PA
underneath. No changes in the polysulfone layer can be
observed at a wave band 1145−1350 cm−1, which is consistent
with the finding of Ettori et. al that polysulfone was not
chemically modified by chlorination.20 FTIR spectra from 2700
to 3800 cm−1 for the three membranes are provided in the
Supporting Information S7. For NF90 and BW30 FA
membranes, the magnitude of broad peaks centered ∼3300
cm−1, which are assigned to N−H and/or O−H stretching3
depleted as chlorination conditions became more severe. On
the other hand, for the NF270 PIP membrane, only a slight
reduction in the C−H stretching peak at 2970 cm−1 was
observed.3
3.3. Changes in Membrane Surface Charge and
Hydrophilicity. The surface charge of NF90 and NF270
membranes before and after chlorination is presented in Figure
6 and that of BW30 is provided in Supporting Information S8.
Both NF90 and NF270 membranes became more negative as
the chlorine concentration increased, which agrees with
previous observations.19,37 It is useful to note that the
magnitude of this negative charge shift within a membrane is
not constant; at low pH, the shift magnitude is relatively large.
The iso-electrical point of virgin NF90 is at pH ≈ 5.5 and the
positive charge at low pH is contributed by the protonated
amide group.38 All chlorinated membranes were negatively
charged at the lowest measured pH leading to the speculation
that due to N−Cl bond formation, amide nitrogen can no
longer form −NH2+ groups.19 Meanwhile, the negative charge
at high pH is associated with deprotonation of carboxylic acid.38
The more negative zeta potential at high pH reconfirms that
the number of carboxylic groups on the surface increased,
consistent with the chlorine-promoted hydrolysis mechanism.
The hydrophobicity of the membranes evaluated by contact
angle is illustrated in Figure 7 and more data of other
membranes is in Supporting Information S9. A higher value of
the contact angle denotes greater difficulty in wetting the
membrane. Despite the measurement uncertainty, some general
trends can be observed. The membrane surfaces become more
hydrophobic under severe chlorination conditions. However,
NF270 and BW30 treated at 1000 ppm for 1 h became more
hydrophilic. Both trends in wettability might be explained by
the competing effects of N-chlorination and hydrolysis
processes. The incorporation of chlorine on the membrane
surface can cause an increase in hydrophobicity and inhibition
of membrane wetting. However, an increase in carboxylic/
hydroxyl functional groups can increase membrane wetting.
3.4. Changes in Membrane Performance. To evaluate
the changes in intrinsic membrane properties, water permeability coefficient, A (m/s.Pa) and solute permeability
coefficient, B (m/s) for virgin and chlorinated membranes
Figure 8. Virgin and chlorinated membrane performance: (a) water
permeability coefficient, A (m/s·Pa) and (b) solute permeability
coefficient, B (m/s). The operating pressures for NF90, BW30, and
NF270 were set at 100, 260, and 70 psi, respectively.
amide peak (1609 cm−1) for N−H deformation vibration and
CC ring stretching vibration3 strongly suggests that chlorine
replaced hydrogen of the amide nitrogen via electrophilic
substitution in N-chlorination. This FTIR information is
consistent with the Cl/N ratio from XPS results in Figure 2.
It was observed that the amide I band (1663 cm−1), which
represents CO stretching (major contributor) and C−N
stretching and C−C−N deformation vibration, was shifted to a
higher wavenumber. Since the CO stretching of benzoic acid
is at 1680 cm−1,20,36 it can be hypothesized that the breakage of
hydrogen bonds between CO and N−H groups17,20 and
additional carboxyl groups by hydrolysis have contributed to
this shift.
In contrast to the obvious spectra changes for NF90 and
BW30, there was no noticeable change in the FTIR peaks
detected for the PIP membrane NF270 (Figure 5c). This result
is consistent with the XPS survey spectra (Figure 2) results in
which the nitrogen in the tertiary PA of NF270 was less prone
to chlorine attack. Nevertheless, a small amount of chlorine was
still incorporated into the PIP PA layer, assumed to be at
nitrogen atoms of noncross-linked amine groups.
It is also interesting to compare the XPS and FTIR results for
the PVA coated membrane BW30. Since XPS measures only
the top 1−5 nm thickness of a sample, its signal responds
mainly to coating material and exposed surface PA. Meanwhile,
ATR-FTIR has much deeper sample penetration depth and
allows measurement of the PA properties across the active
layer. Thus, a comparison between the surface XPS measure857
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(21) Avlonitis, S.; Hanbury, W.; Hodgkiess, T. Chlorine degradation
of aromatic polyamides. Desalination 1992, 85, 321−334.
(22) Kwon, Y.-N.; Leckie, J. O. Hypochlorite degradation of
crosslinked polyamide membranes: I. Changes in chemical/morphological properties. J. Membr. Sci. 2006, 283 (1−2), 21−26.
(23) Cadotte, J. E. Interfacially synthesized reverse osmosis membrane
1981.
were presented in Figure 8. Higher A and B values indicate that
the membrane is more permeable to water or solute.39 In the
current study, chlorination decreased both A and B values. The
decrease of A with increasing exposure to chlorine can be
explained by the decrease of membrane wettability due to
chlorine incorporation into the membranes13 in addition to any
possible changes in the PA polymer conformation.17,18,21,22 The
more negative membrane surface charge due to increased
carboxylic functional groups can enhance electrostatic repulsion
between the membrane and anionic solutes; therefore, salt
passage through the chlorinated membranes was reduced19,40
despite of the reduced cross-linking degree (Figure 3b).
In conclusion, the data presented in this study suggest that
the chlorination of FA PA membranes promotes the hydrolysis
of the amide C−N bond. The simultaneous occurrence of the
N-chlorination and C−N hydrolysis leads to opposite effects.
While the incorporation of chlorine into the PA backbone
makes the membrane more hydrophobic and less permeable,
the hydrolysis of the C−N bond has the potential to make the
membrane more hydrophilic. This proposed mechanism could
possibly explain the disparate and often contradictory
observations reported in the literature.
■
ASSOCIATED CONTENT
S Supporting Information
*
S1. Chlorination mechanisms of fully aromatic polyamide
membranes. S2. Membrane physiochemical properties. S3. NF/
RO filtration system and performance evaluation. S4. Elemental
compositions of virgin and chlorinated membranes by XPS. S5.
Surface oxygen content for chlorinated BW30 membrane. S6.
High resolution XPS spectra for virgin and chlorinated BW30
and NF270 membranes. S7. ATR−FTIR spectra at wavenumber from 2700 to 3800 cm−1. S8. Surface charge of virgin
and chlorinated BW30 and replicates for virgin membranes. S9.
Hydrophilicity of virgin and chlorinated membranes. This
material is available free of charge via the Internet at http://
pubs.acs.org.
■
AUTHOR INFORMATION
Corresponding Author
*Tel: (65) 67905267; fax: (65) 67910676; e-mail: cytang@ntu.
edu.sg.
ACKNOWLEDGMENTS
This research was financially funded by the Tier 1 Research
Grant No. RG6/07, Ministry of Education, Singapore. V.T.D. is
supported by the Singapore Stanford Partnership Program. We
thank Professor William B. Krantz for valuable discussions and
help. The authors also thank the Singapore Membrane
Technology Centre for technical support and GE Osmonics
and Dow/FilmTec for providing the membrane samples.
■
■
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