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Imprinting of metal receptors into multilayer polyelectrolyte films: fabrication and applications in marine antifouling

Sreenivasa Reddy Puniredd a, Dominik Jańczewski *a, Dewi Pitrasari Go a, Xiaoying Zhu a, Shifeng Guo a, Serena Lay Ming Teo b, Serina Siew Chen Lee b and G. Julius Vancso *cd
aInstitute of Materials Research and Engineering, A*STAR (Agency for Science, Technology and Research), 3 Research Link, 117602, Singapore. E-mail:; Fax: +65 6872 0785; Tel: +65 6874 5443
bTropical Marine Science Institute, National University of Singapore, 18 Kent Ridge Road, 119227, Singapore
cInstitute of Chemical and Engineering Sciences, A*STAR, 1, Pesek Road, Jurong Island, 627833, Singapore. E-mail:; Fax: +31 53 4893823; Tel: +31 53 489 2974
dMESA+ Institute for Nanotechnology, Materials Science and Technology of Polymers, University of Twente, P.O. Box 217, 7500 AE Enschede, The Netherlands

Received 5th August 2014 , Accepted 26th September 2014

First published on 26th September 2014


Polymeric films constructed using the layer-by-layer (LbL) fabrication process were employed as a platform for metal ion immobilization and applied as a marine antifouling coating. The novel Cu2+ ion imprinting process described is based on the use of metal ion templates and LbL multilayer covalent cross-linking. Custom synthesized, peptide mimicking polycations composed of histidine grafted poly(allylamine) (PAH) to bind metal ions, and methyl ester containing polyanions for convenient cross-linking were used in the fabrication process. Two methods of LbL film formation have been investigated using alternate polyelectrolyte deposition namely non-imprinted LbLA, and imprinted LbLB. Both LbL films were cross linked at mild temperature to yield covalent bridging of the layers for improved stability in a sea water environment. A comparative study of the non-imprinted LbLA films and imprinted LbLB films for Cu2+ ion binding capacity, leaching rate and stability of the films was performed. The results reveal that the imprinted films possess enhanced affinity to retain metal ions due to the preorganization of imidazole bearing histidine receptors. As a result the binding capacity of the films for Cu2+ could be improved by seven fold. Antifouling properties of the resulting materials in a marine environment have been demonstrated against the settlement of barnacle larvae, indicating that controlled release of Cu ions was achieved.


The ongoing quest for complex, advanced materials systems necessitates the development of various thin polymeric films for applications in a variety of fields including membrane technology,1–3 microelectronics,4 optical sensing,5 and biomedical applications.6,7 Particular attention is directed toward the management of the molecular payloads within the film e.g. selective loading, and controlled delivery or multiplexed release.8,9 The layer-by-layer (LbL) electrostatic fabrication process utilizing alternate deposition of positively and negatively charged polyions on a substrate10 is a simple yet versatile method for the preparation of thin polyelectrolyte multilayer coatings.11–14 Polymeric films with enhanced affinity toward metal ions are needed for applications in ion capture and separation,1–3,15 catalysis,16,17 protein binding, metal affinity chromatography18 and antimicrobial materials.19 The selective adsorption and separation of metal ions from aqueous waste has also received increasing consideration in environmental protection in recent years.20 For example, numerous adsorbents have been developed for the removal of copper ions from industrial wastewater and in other applications.21,22 However, these adsorbents still suffer from drawbacks such as limited selectivity and low reusability. Molecular-imprinting techniques (MIPs) have become acclaimed in many fields, such as chemosensor fabrication, molecular separation, and catalysis and drug delivery.23–27 Ion imprinted polymers can be considered as a sub category within MIPs22,27 and refer to materials with improved affinity toward metals by the pre-organization of metal receptors within polymeric matrix in the presence of metal ion templates. This process is typically achieved by the reduction of receptor mobility through various ways such as bulk polymerization, precipitation polymerization, and suspension polymerization. Since the receptor sites are embedded deeply into the polymeric matrix, these imprinting techniques often produce materials exhibiting high selectivity but low rebinding capacity and poor site accessibility to target ions.28 In order to conquer these drawbacks, thin film surface-ion-imprinted polymers were proposed as a promising solution. Films obtained by surface ion-imprinted techniques exhibit good characteristics, such as complete removal of templates and fast adsorption kinetics.29–33 Small molecules and ions have been loaded into non-cross-linked LbL fabricated thin electrostatic film systems using both the traditional solution, the LbL method,16,34 as well as spray deposition approaches.35 The films obtained show not only a high affinity to metals but also possess reversible loading–unloading capability.36 Enhanced selectivity of such films toward the ions loaded is attributed to the reduced mobility of polyions upon deposition in the electrostatic multilayer.37 This affinity however can potentially be further increased by the reduction of receptor mobility, for example through covalent cross-linking of the LbL layers. The ion imprinting through covalent cross-linking of multilayer systems in the presence of metal templates has not been presented until now. Studies, which employed cross-linking of LbL systems in the presence of ions have focused only on moderately coordinating the polyethylenimine/polyacrylic acid (PEI/PAA) couple. Enhanced affinity of the films toward specific metals upon cross-linking has not been demonstrated, nor discussed, in the corresponding reports.38,39 Finally, the direct imprinting of metals into a polyelectrolyte film by the immobilization of metal templated receptors was demonstrated only for a single PEI layer (non LbL) using an epichlorohydrin crosslinker.40,41 However a single polymer layer is inferior compared to LbL coatings in terms of substrate coverage and the number of receptors available. Reported systems used also rather poorly coordinating PEI receptors.

Protein complexes with metal ions play an important role in various biological processes.42 A common structural feature of such protein-metal assemblies43 are peptide motifs typically arranged in a special sequence of residues to ensure the strong interactions between the metal ions and donor atoms from the peptide backbones or functional side groups.29,44 These motifs are frequently bearing residues such as histidine (His), since nitrogen of the imidazole moiety is known for its high affinity to metals.45,46 It is used as a metal coordinating component of polymeric systems and it can be grafted on various polymeric backbones mimicking peptide architecture.47–49 Hence in this work we shall describe a system in which this specific coordinating capacity of histidine is utilized.

Marine fouling has been a serious problem for maritime technologies, from ship hull protection to off-shore stationary structures and high value-added underwater sensing and communications.50,51 Marine fouling has been controlled traditionally through the use of antifouling paints with toxic constituents or biocides.52 Before its ban tributyltin (TBT) was the active agent in antifouling paints and used extensively in the maritime sector for over thirty years.53 As an alternative, copper based coatings are ten–twelve folds less harmful than those containing TBT,54,55 however still remain problematic and are criticized for excessive metal pollution. Copper is used as an antifouling agent with a leaching rate in the order of 10-15 μg cm−2 per day. Hence a surface of one square meter can be kept clean of biological growth by annual leaching of approximately 30 grams of copper.56 Those levels are suspected to be toxic to aquatic organisms, through the accumulation in filter feeders, such as mussels, and damage larval stages of aquatic invertebrates and fish species.57 Designing and fabricating new, effective and environmentally friendly coating systems as alternatives to TBT-based antifouling paints poses an important challenge for the scientific community. The ideal antifouling coating with embedded metal ions would prevent marine growth as well as maintain a long performance life whilst fulfilling the expectations of the increasingly strict environmental regulations.

In this work we investigate the concept of improving of thin LbL polymeric film affinity to Cu2+ ions by reducing the mobility of metal receptors in the presence of guest molecules. This concept is typically referred to as metal ion imprinting.22 Utilizing the properties of the polymer grafted imidazole bearing histidine receptor, we synthesized a peptide mimicking material with high affinity to copper. Two alternative approaches for the fabrication of metal attracting films were compared. In the first imprinting approach, thin LbL films composed of custom synthesized histidine grafted polyallyamine were cross-linked in the presence of Cu2+ ions to immobilize receptors in a conformation suitable for the metal ion coordination. In the second non-imprinting approach, the films were cross-linked without the presence of ions to provide a reference material. The structure and properties of both films are extensively characterized. Finally, anti-fouling applications of the copper ion selective LbL films are demonstrated.



Poly(isobutylene-alt-maleic anhydride) (PIAMA, Mw: 6 kDa), poly(allylamine hydrochloride) (PAH, Mw: 58 kDa), L-histidine methyl ester dihydrochloride, 3-aminopropyltrimethoxysilane (APTMS), N,N-diisopropylethylamine (DIPEA), copper(II) nitrate trihydrate (Cu(NO3)2 × 3H2O), sodium chloride, sea salt and sodium hydroxide (all from Sigma Aldrich), N,N-dimethylformamide (DMF), dimethylsulfoxide (DMSO), toluene, methanol, acetone and isopropanol (all from Tedia) were used directly as received without further purification. Dialysis membrane tubing (MWCO: 3.5 kD) was received from Fisher Scientific. Silicon wafers (Latech Scientific Supply Pte. Ltd) were 0.6 mm thick, with one side polished and with a natural silicon dioxide layer. QSX 303 Silicon dioxide 50 nm quartz crystal microbalance (QCM) chips were obtained from Analytical Technologies Pte Ltd. Deionized (DI) water with 18 MΩ cm−1 resistivity was obtained from a Millipore Nanopure system.


Synthesis of PIAMA-Ester (PIAMA-Me). PIAMA-Me synthesis was achieved following a modification of the method described previously (Scheme 1).58 To the solution of poly(isobutylene-alt-maleic anhydride) (1.0 g, 6.5 mmol) in 300 mL of methanol, DIPEA (1.2 mL, 6.9 mmol) was added and the mixture was stirred for 16 h at 50°C. After the evaporation of methanol and DIPEA, the material was suspended in water using a small excess of NaOH with respect to the carboxylic groups in the polymer backbone. The polymer solution was dialyzed against 0.01 M NaOH and subsequently against pure water for a few days. The purified polymer aqueous solution was concentrated by rotary evaporator and finally freeze dried to yield the solid polymer. To properly identify the composition of the polymers obtained, NMR spectra were compared with the NMR results of poly (isobutylene-alt-maleic anhydride) opened by a treatment with a stoichiometric amount of NaOH to carboxyl groups. NMR calculated Mn: 8 kDa. 1H NMR integrated for a single repeating unit: (D2O) δH: 0.5-1.36 ppm (6H, m), 3.67 ppm (2H, s). IR: 1860 cm−1, 1780 cm−1, 1730 cm−1, 1580 cm−1.
image file: c4sc02367f-s1.tif
Scheme 1 The synthesis of PIAMA-Me.
Synthesis of PAH-Histidine (PAH-His). To a solution of L-histidine methyl ester (2.63 g, 11 mmol) in 20 mL of DI water, 1 g of PAH (7.4 mmol of the repeating units) was added in small portions (Scheme 2). The solution was stirred for 1 h at room temperature and small portions of 5M NaOH were added until the solution pH reached 10. The solution was freeze dried for 72 h. 2 mL of DMSO was added to the freeze dried polymer-histidine mixture and kept under vacuum at 65°C for 72 h. After evaporation of DMSO, the remaining polymer was dissolved in water and dialyzed against diluted HCl for 12 h and against pure water for several days. The polymer solution was concentrated by rotary evaporator and freeze dried to yield a white solid powder (1.7 g, yield 81.7%). NMR calculated Mn: 80 kDa. 1H NMR integrated for a single repeating unit: (D2O) δH: 0.5-1.76 ppm (3H, m), 4.05 ppm (0.2H, s), 7.10 ppm (0.22H, s) and 7.85 ppm (0.21H, s). IR: 620 cm−1, 1260 cm−1, 1750 cm−1.
image file: c4sc02367f-s2.tif
Scheme 2 The synthesis of PAH-His.

Binding constant evaluation from the solution

Optical absorption spectra were recorded using a UV-VIS spectrometer to investigate the complexation of copper ions with PAH-His and to establish equilibrium metal-binding constants for PAH-His in solution. In all experiments, water was used as a reference. A copper ion titration was performed by adding aliquots of a Cu(NO3)2 stock solution (15 mM) to 6 mM of PAH-His solution in water. All calculations and model fittings were carried out using MS Excel software.

Surface modification

Silicon substrates were cut into 2 × 2 cm2 slides by a DISCO dicing machine (DAD 321), cleaned with acetone and isopropanol in ultrasonic bath for 10 min, rinsed with DI water and finally dried with a stream of nitrogen. Subsequently, silicon slides were treated by oxygen plasma (200 W) for 2 min in a triple P plasma processor (Duratek, Taiwan). This cleaning procedure created a surface rich in hydroxyl groups at the oxide surface to facilitate the subsequent silanization process. The hydroxyl-covered substrates were rinsed with methanol–toluene mixture and toluene, and then immersed in a 3 mM APTMS solution in toluene for 3 h. Subsequently, they were rinsed copiously with toluene, sonicated for 10 min, rinsed again successively with toluene, methanol and water and blown dry with nitrogen and dried under vacuum at 100°C for 5 h.

Polymeric film fabrication

PIAMA-Me, PAH-His and 1 mM of Cu(NO3)2 × 3H2O complexed with PAH-His (referred to in this work as PAH-His(Cu)) stock solutions (1 mg mL−1) were prepared by dissolving the corresponding solids in 0.5 M NaCl. The synthesized PAH-His and PAH-His(Cu) solutions had the pH values of pH = 6.5 and pH = 5.5, respectively. The cleaned silicon wafers were treated with APTMS to impart positive charges onto the surface. Subsequently, the substrates were immersed into the PIAMA-Me solution for 10 min, rinsed with DI water for 2 min and dried with a flow of nitrogen gas. In the second step, the substrates were immersed into the PAH-His solution for 10 min, followed by 2 min of rinsing with DI water and blown dry with nitrogen. This cycle was repeated until the desired number of 14 bi-layers was reached. PAH-His was always deposited as the outermost layer. Such fabricated films were cross-linked by heating the silicon substrate at 80°C for 12 h under vacuum.58,59 The described process of LbL assembly of PIAMA-Me and PAH-His polymers is referred to as non-imprinted LbLA in this work (Fig. 2 and 3).

Cross-linked LbL films with Cu2+ ions preloaded at the fabrication stage were obtained by alternating immersions of the silicon slides prepared as described above, but using polymer solutions PIAMA-Me and PAH-His(Cu). 18 bi-layers (PIAMA-Me and PAH-His(Cu)) were assembled in this way using PAH-His(Cu) as the outermost layer. The process of LbL assembly of PIAMA-Me and PAH-His(Cu) polymers is referred to as imprinted LbLB in this work (Fig. 1).

image file: c4sc02367f-f1.tif
Fig. 1 (A) UV-VIS absorption spectra of PAH-His coordinated with Cu. (B) Example of absorption spectra fitted with three different signals for 2.3 mL of PAH-His (6 mM) added to the 2 mL of Cu(NO3)2 (15 mM). (C) Integration of the signal intensity at 620 nm, 770 nm and 820 nm, fitting data to the binding model.

LbL films-loading and releasing of copper ions

The preparation process of the Cu2+ imprinted LbLB and non-imprinted LbLA films on silicon substrates are illustrated in Fig. 2 and 3. The loading and releasing of the copper ions was achieved by the following procedure. Imprinted LbLB films were first washed using 1 M HCl for 5 min to remove the Cu2+ ions as the Cu2+ were present during the LbL process, and copious amounts of DI water, followed by drying with a stream of nitrogen. Non-imprinted LbLA and imprinted LbLB films were immersed in 15 mM solution of Cu(NO3)2 to absorb the Cu2+ ions for 1h to ensure that equilibrium was reached and the films were washed with copious amounts of water and dried with nitrogen. In the next step, Cu2+ ion-loaded non-imprinted LbLA and imprinted LbLB films were rinsed with 1 M HCl for 5 min to extract the Cu2+ ions followed by washing with DI water and drying with nitrogen. The above procedure is repeated several times to load and release the copper from the films. The non-imprinted LbLA and imprinted LbLB films with Cu2+ ions were investigated using XPS to ensure that there were no copper ions left on the surface after washing with HCl.
image file: c4sc02367f-f2.tif
Fig. 2 Schematic illustration of PIAMA-Me, PAH-His and PAH-His(Cu).

image file: c4sc02367f-f3.tif
Fig. 3 LbL film formation by different processing methods, (non-imprinted LbLA refers to assembly of PIAMA-Me and PAH-His, and imprinted LbLB refers to assembly of PIAMA-Me and PAH-His(Cu)). Cross linking of the films as employed followed by loading and releasing of copper within the LbL films. Schematic representation of the polymer PIAMA-Me, PAH-His and PAH-His(Cu) are shown in Fig. 2.

LbL assembly and metal loading monitored by QCM

In situ quartz crystal microbalance (QCM) measurements were conducted using a Qsense E4 multichannel instrument equipped with silicon dioxide-coated crystals. The surface of silicon dioxide chips were modified with APTMS similar to the silicon wafers as described above. For in situ QCM measurements, the as-prepared silane modified QCM chips were fixed in the chamber of the QCM instrument and the crystals were sealed with a silicon rubber O-ring. Then the APTMS films were stabilized in a flow of water followed by 0.5 M NaCl until the frequency reached equilibrium at the flow rate of 250[thin space (1/6-em)]μL min−1. PIAMA-Me polymer solutions of (1 mg mL−1 in 0.5 M NaCl) were passed through the chamber at a rate of 250[thin space (1/6-em)]μL min−1 until the frequency reached equilibrium followed by the injection of 0.5 M NaCl through the chamber at the same rate until the frequency became stable enough to remove any loosely bound molecules. Afterwards PAH-His polymer solutions (1 mg mL−1 in 0.5 M NaCl) were pumped at the same flow rate followed by a NaCl washing step (non-imprinted LbLA). Similarly, in imprinted LbLB films, alternate injections of PIAMA-Me and PAH-His(Cu) polymer solutions in 0.5 M NaCl were delivered at a flow rate of 250[thin space (1/6-em)]μL min−1 until the frequency became stable, followed by 0.5 M NaCl salt injection after every polymer layer was deposited. The procedure was repeated until the required number of bi-layers was reached. Finally, the layers were rinsed with DI water at a flow rate of 250[thin space (1/6-em)]μL min−1 to remove any possible excess of salt. Each layer deposition was carried out for 30 min to 1 h to achieve saturated adsorption. The frequency change of the quartz crystals was monitored throughout the adsorption process. The crystals were removed from the QCM instrument and dried with nitrogen. Cross linking of the LbLA and LbLB films grown on QCM chips were performed at 80°C for 12 h under vacuum.

Cross-linked non-imprinted LbLA films built on QCM chips were immersed in 15 mM of Cu(NO3)2 solutions for 1 h and washed with 1M HCl, similar to the silicon wafers. Cross-linked films prepared by the imprinted LbLB method on QCM were washed with 1 M of HCl for 5 min and dried. For copper loading experiments, non-imprinted LbLA and imprinted LbLB films on QCM chips, after washing with HCl as described above, were loaded into the chamber of the QCM instrument. Subsequently, the LbL films were stabilized in a flow of water at a rate of 250[thin space (1/6-em)]μL min−1 until the frequency reached equilibrium. Then the sequence of different concentrations of Cu(NO3)2 stock solutions (0.1, 0.2, 0.4, 1, 2, 4, 8, 15, 25, 35 and 45 mM) were injected. For each concentration 250[thin space (1/6-em)]μL of the Cu(NO3)2 solutions were injected and the frequency was allowed to reach equilibrium followed by injection of 1 mL of DI water through the chamber at the rate of 250[thin space (1/6-em)]μL min−1. The injection of water was intended to remove any loosely bound Cu2+. This procedure was repeated for all concentrations. The frequency change of the quartz crystal was monitored throughout the loading of copper ions. Finally, the crystals were removed from the QCM instrument and dried with nitrogen. Cu2+ ions loaded from non-imprinted LbLA and imprinted LbLB films on QCM chips were washed with 1 M of HCl for 5 min and copious amounts of DI water to remove copper ions, followed by dry blowing with nitrogen. The above procedure was repeated several times to load and unload the Cu2+ ions using the QCM process on non-imprinted LbLA and imprinted LbLB films. The mass deposited on the crystal (Δm) was calculated using the Sauerbrey equation.60

image file: c4sc02367f-t1.tif(1)

For a 5, 15, 25, 35, 45 MHz quartz crystal, n = 1, 3, 5, 7; where C = 17.7 ng s−1 cm−2, n = overtone number and Δf = frequency change.


Stability and the leaching rate of copper from the cross linked non-imprinted LbLA and imprinted LbLB films were evaluated by immersing them in artificial sea water solutions. The silicon wafers with 7 bi-layers films from non-imprinted LbLA and 10 bi-layers from imprinted LbLB were immersed in artificial seawater (prepared by dissolving 38.5 g L−1 sea salt in DI water), for up to 90 days. Samples were removed and rinsed by DI water after 1, 7, 15, 45 and 90 days of immersion. The surfaces were characterized by XPS after drying with nitrogen.

Larval culture

Amphibalanus amphitrite barnacle larvae were spawned from adults collected from the Kranji mangrove, Singapore. The nauplii larvae were fed with an algal mixture 1[thin space (1/6-em)]:[thin space (1/6-em)]1 v/v of Tetraselmis suecica (CSIRO Strain number CS-187) and Chaetoceros muelleri (CSIRO Strain number CS-176) at a density of ∼5 × 105 mL−1, and reared at 27 °C in 2.7% salinity, 0.2 μm filtered seawater (FSW). Under these conditions, the nauplii metamorphosed into cyprids in 5 days. The cyprids were aged for 2 days at 4–6 °C prior to use in settlement assays.

Barnacle settlement and toxicity assay

The assay method as described by Wang et al.61 was adapted in this work. Positive controls consisted of plasma-cleaned silicon wafers. A 200 μL drop of filtered seawater (FSW) containing 15–25 barnacle cyprids were added to each wafer kept in individual Petri dishes. In addition, 100 μL of FSW containing 15–25 stage 2 barnacle nauplii was introduced to each droplet giving a final volume of 300 μL. The control, as well as the non-imprinted LbLA and imprinted LbLB films with copper loaded samples were incubated in the dark at 26–28 °C and the results were scored after 24 hours. For the assessment of barnacle settlement, juvenile barnacles and metamorphosing cyprids that had attached firmly to the substrate were counted as ‘settled’. The number of dead nauplii and cyprids were also enumerated for an assessment of toxicity.

Results and discussion

To investigate the concept of molecular imprinting of metal receptors in the LbL electrostatic thin film matrix and to employ this material in the fabrication of antifouling polymeric coatings, two custom synthesized polyelectrolytes were developed. The polymer PIAMA-Me was constructed by the opening of polyanhydride units with two nucleophilic agents, namely methanol and hydroxide. The resulting polyanion is bearing negatively charged carboxylic groups and ester functions for covalent cross-linking with amine (Fig. 2 and 3).58 The results of FTIR analysis confirm the partial conversion of the anhydride polymer (PIAMA) to ester (PIAMA-Me) through the methanolysis reaction as shown in Scheme 1. The double peak (1860 cm−1 and 1780 cm−1) belonging to the C[double bond, length as m-dash]O of the anhydride polymer (PIAMA) disappears and a new peak at 1730 cm−1, attributed to the C[double bond, length as m-dash]O of the ester bond, becomes visible. In addition, a peak at 1580 cm−1 can be associated to a newly formed COO (Fig. S1A in the ESI).62 The methanolysis reaction of PIAMA was further verified by the comparison of the 1H NMR spectra of PIAMA-Me and purified polyanhydride as shown in Fig. S2 (ESI). The presence of a peak at 3.66 ppm in the polymer PIAMA-Me spectrum, belonging to the protons of methyl ester, confirms successful conversion. The methyl ester peak (3.66 ppm) integrated area, and the dimethyl group protons of the main chain (peaks between 0.5–1.36 ppm) allow us to estimate the degree of substitution with the methyl esters groups to obtain the value of 70% (Scheme 1).

The polycation (PAH-His) was synthesized by the grafting of L-histidine side groups on the polyallylamine backbone. Following this approach, peptide mimicking polymer bearing histidine moieties for metal ion complexation and primary amine groups used in the LbL assembly was synthesized (Scheme 2). The successful polymer synthesis was confirmed by the appearance of peaks at 620 cm−1 and 1260 cm−1, which are assigned to OCN bending and amide C–N stretching and N–H bending frequencies respectively. The ester peak visible at 1750 cm−1 in pure histidine, and it’s absence in the PAH-His spectrum (see ESI Fig. S1B) as well as the presence of the peaks at 1260 cm−1 (amide C–N stretching) and at 1570 cm−1 (amide carbonyl) in the PAH-His polymer spectrum, confirm successful chemical transformation.63 The PAH-His structure and histidine substitution degree were examined and quantitatively evaluated by 1H-NMR as shown in Fig. S3 (ESI). The reaction completion is confirmed by the disappearance of the methyl ester peak at 3.67 ppm and the presence of new peaks at 4.05, 7.10 and 7.85 ppm, which can be associated to the methine and imidazole protons in the His moiety, respectively. The backbone substitution degree is determined to 20% owing to the clearly visible signal of imidazole protons (7 and 8 ppm) and the aliphatic backbone proton peaks between 1 and 2 ppm. This allowed us to estimate the indices of the repeating units, describing the composition of polymer PAH-His, to 130 and 500 for PAH-substituted and non-substituted groups respectively (Scheme 2).

Complexation of copper ions in aqueous solutions

UV-visible absorption spectroscopy experiments were employed to establish the mechanism of interactions between the synthesized polymer (PAH-His) and Cu2+ ions in solution. The titration of PAH-His with Cu(NO3)2 in water followed by the observation of absorption changes allowed us to propose a binding model for these molecules. On the basis of previous reports,44,47 we employed the working hypothesis that two histidine ligands bind to a single copper ion. To simplify the model, repeating histidine units of the polymer were treated as individual; independently binding molecules and polyallylamine interactions with ions were omitted. This is justified since primary amine interactions with Cu2+ are reported to be much weaker compared to imidazole complexation.18,36,64 As shown in Fig. 1A, the addition of copper nitrite to the PAH-His solutions results in the appearance of a new peak at 620 nm. The peak intensity increases continuously with the addition of copper and reaches the absorption maxima approximately for a 1[thin space (1/6-em)]:[thin space (1/6-em)]2 metal to ligand ratio. After the saturation, the intensity of the signal at 620 nm decreases with a clear shoulder increase at longer wavelengths. Upon further metal addition a new signal near 820 nm appears which can be assigned to free Cu2+ ions.44,65 All of the UV absorption spectra were fitted by three peaks representing the concentration of three different species present in the solution using the asymmetric modification of the Gaussian function.66,67 The peak at 620 nm is attributed to the formation of a 1[thin space (1/6-em)]:[thin space (1/6-em)]2 copper complex with PAH-His, the peak around 770 nm corresponds to the formation of a 1[thin space (1/6-em)]:[thin space (1/6-em)]1 copper complex with PAH-His and a peak at 820 nm is linked to free copper ions (Fig. 1B and S4).44 Examples of the fitting procedure are provided in the ESI.

The integrated absorption values for the three signals are provided in Fig. 1C. The changes observed in the signal intensity variations were subsequently used to establish the binding constants of this system. Titration curves were fitted by assuming that 1[thin space (1/6-em)]:[thin space (1/6-em)]1 and 1[thin space (1/6-em)]:[thin space (1/6-em)]2 equilibriums are present68 as described by the equations 2–5.

M + PAH-His ⇔ M(PAH-His)(2)
image file: c4sc02367f-t2.tif(3)
M(PAH-His) + PAH-His ⇔ M(PAH-His)2(4)
image file: c4sc02367f-t3.tif(5)

The absorbance signals presented in Fig. 1C clearly support the co-existence of the 1[thin space (1/6-em)]:[thin space (1/6-em)]1 and 1[thin space (1/6-em)]:[thin space (1/6-em)]2 stoichiometry of the Cu2+ and PAH-His complex. The fitting of the data provides binding constant values of K1 = 8.43 × 103 M−1 (log K1 = 3.93) and K2 = 2.63 × 104 M−1 (log K2 = 4.42). Based on the above observations it appears that the 1[thin space (1/6-em)]:[thin space (1/6-em)]2 metal–PAH-His coordination dominates the 1[thin space (1/6-em)]:[thin space (1/6-em)]1 interactions. The results are consistent with a large stability constant observed for other histidine grafted polymers.44,47

LbL film fabrication

Synthesized polymers were used for the fabrication of thin film structures using alternating deposition of polyelectrolytes in a typical electrostatic LbL protocol,10–13 followed by the interlayer film cross-linking performed through amide bond formation.58,59 Two different designs were compared to investigate the effect of metal imprinting on the affinity of the polymeric matrix to bind Cu2+ ions. The imprinting of ion receptors was achieved by the immobilization of histidine moieties around preorganized metal atoms in the covalent, interlayer cross-linking process (Fig. 3).

The two methods used essentially differ in the cross-linking step. Non-imprinted LbLA films are cross-linked without the metal template present and as such, the mobility of the receptors is reduced, maintaining random arrangement not influenced by the presence of copper. In contrast, for the imprinted LBLB system, the film is loaded with Cu2+ ions at the stage of fabrication, so the subsequent cross-linking process is intended to “freeze” histidine receptors in the given conformation around the guest molecules (Fig. 3). By using these approaches, two types of structures with similar chemical composition but different arrangement of metal receptors can be obtained. Film cross-linking evidence was acquired using FTIR and XPS methods. The disappearance of the ester peak (1730 cm−1) in the non-imprinted LbLA film and the evolution of a new peak at 1590 cm−1 (amide C–N stretch) indicate amide bond formation (Fig. 4) and successful covalent attachment between the layers.62

image file: c4sc02367f-f4.tif
Fig. 4 FTIR spectra of non-imprinted LbLA film before and after cross linking.

The XPS spectra (Fig. S5 in the ESI) further confirmed the cross-linking of the LbL films in addition to the FTIR analysis. Fig. S5A and B are the N1s core-level spectra for non-cross linked and cross-linked LbLA films, respectively, which are fitted into primary amine, amide, imide and protonated amine components with binding energy (B.E.) values of 398.9 eV, 399.9 eV, 400.8 and 401.8 eV.69 In the spectra of cross-linked non-imprinted LbLA films, the peak component for the free and protonated amines are small. The increase of the amide peak intensity demonstrates that the free amine is reacting with the ester. A similar trend is also observed for the imprinted LbLB films (Fig. S5C and D). The thickness of the cross linked LbL films were measured by ellipsometry and by the AFM scratch method as shown in Fig. 5. For the non-imprinted LbLA, the thickness growth of the films is linear up to 8 bi-layers and exponential afterwards, following the trends reported in the literature (Fig. 5A).70 Similarly, for the imprinted LbLB we observed linear growth up to 14 bi-layers and exponential increase afterwards. The thickness of the non-imprinted LbLA and imprinted LbLB films were also measured independently using the AFM scratch method. The obtained thickness values correlate well with the ellipsometry measurements as shown in Fig. 5A and B. To achieve a good comparison among the structures studied, films of similar thicknesses and comparable masses of the polymers deposited were used. This corresponds to 7 bi-layers and 10 bi-layers for non-imprinted LbLA and imprinted LBLB, respectively.

image file: c4sc02367f-f5.tif
Fig. 5 Thickness data of non-imprinted LbLA (A) and imprinted LbLB (B) films from ellipsometry and the AFM scratch test.

The morphology of the LbL films was studied using AFM (Fig. S6 in the ESI). The AFM images in Fig. S6 show clear variations of the film surface depending on the fabrication method applied. Fig. S6A shows cluster/coil-like features on the non-cross linked LbLA film, and no significant changes in the morphology upon application of the cross-linking procedure (Fig. S6B). Rather different morphology is observed for LbLB films. The LbLB film is fairly smooth (Fig. S6D) when compared to LbLA (Fig. S6B). The surface roughness Rq (the quadratic mean value of roughness, obtained over a 5 × 5 μm2 surface area) for an LbLA film without cross-linking exhibited a value of Rq = 16 ± 0.5 nm (Fig. S6A) compared to Rq = 13 ± 0.5 nm (Fig. S6B) for the cross-linked film. Similarly, for the imprinted LbLB films, the roughness values of the non-cross linked film (Rq = 10 ± 1 nm from Fig. S6C) decreased to 8 ± 1 nm (Fig. S6D) after cross-linking. The results are consistent with previous reports showing that the surface roughness values are reduced with an increased cross-linking density.58,70

LbL growth and metal affinity assessed by QCM

To compare LbLA and LbLB film affinity to ions by establishing binding constants for each film and finally to answer the question if the proposed molecular imprinting method allows us to enhance the metal binding capacity of LbL structures, QCM experiments were performed. The buildup of the macromolecules during fabrication of LbL structures on the APTES modified chips, was monitored following frequency changes of QCM signals (Fig. 6). The alternating addition of polycation and polyanion leads to a stepwise rise in the mass for the deposited layers in both non-imprinted and imprinted films (Fig. 6), demonstrating successful layer by layer assembly. The observed increase in the mass of LbLA (Fig. 6A) is higher than LbLB (Fig. 6B). This is most likely related to the pH of the polymer solution. This parameter is lowered by the presence of Cu salt in the PAH-His(Cu), and is responsible for thinner layers of LbLB.71
image file: c4sc02367f-f6.tif
Fig. 6 Frequency changes monitored by QCM-D for (A) non-imprinted LbLA (7 bi-layers) and (B) imprinted LbLB (10 bi-layers) films.

Successful LbL deposition is known to be facilitated by the overcompensation of charges, which in turn promotes the binding of the subsequent polyelectrolytes.10 Earlier studies suggest that for electrostatically driven LbL deposition both the substrate and the polyelectrolyte species must be sufficiently charged. If the charge is insufficient, the adsorbed layers may be partially removed upon adsorption on the next polyelectrolyte layer.72 Similar behavior is observed here when the LbL films were assembled by LBLA with PIAMA-Me and PAH-His polymers. It is also suggested that the reason for such behavior is the formation of free polyelectrolyte complexes in the solution, which are entropically favored in this case compared to a multilayer on the surface.73,74 Similar complexes may occur when PAH-His is interacting with PIAMA-Me.

Thickness values found from the QCM data for the cross-linked 7 bi-layer non-imprinted LbLA and the 10 bi-layer imprinted LbLB films are 35 ± 5 nm. The total mass of the PAH-His layers in the non-imprinted LbLA and imprinted LbLB films are 15.9, and 9.3, μg cm−2, respectively.

Film–metal affinity experiments were carried out by passing Cu2+ solutions of different concentrations over the thin film until an equilibrium state was reached (Fig. S7 in the ESI). The adsorption isotherms obtained in this way display a typical profile of saturation with increased concentration of guest molecules (Fig. 7A). The amount of absorbed mass was calculated from the Sauerbrey equation as stated in the experimental section. The equilibrium adsorbed amount of metal for imprinted LbLB films is 11.25 μg cm−2, whereas for non-imprinted LbLA only 4.95 μg cm−2 could be immobilized. These observations clearly demonstrate the higher adsorption capacity of the LbLB compared to the non-imprinted LbLA and support the hypothesis of enhanced affinity of the polymeric film to the metal upon imprinting of the receptor structure during the fabrication process.

image file: c4sc02367f-f7.tif
Fig. 7 (A) Saturation isotherms monitored by QCM-D for Cu2+ loading in non-imprinted LbLA and imprinted LbLB films. The surface proved fully saturable and followed normal Langmuir-like adsorption behavior. ΔF represents the frequency change (Hz). (B) Adsorption isotherms of non-imprinted LbLA and imprinted LbLB films for Cu2+ ions fitted by the Langmuir model. [M] denotes the molar concentration of Cu2+.

QCM equilibrium adsorption experiments were conducted to investigate the binding behavior and binding constants for both LbLA and LbLB (Table 1). The saturation isotherms of these films are displayed in Fig. 7A. With the concentration of the copper solution increased, the adsorption capacity of both films first increases sharply then the increase slows down until saturation is reached.

Table 1 Equilibrium constants for PAH-His and imprinted and non-imprinted LbL films from different methods
Process Method Binding constant logK
PAH-His (solution) UV-Visible K 1 = 8.43 x 103, K2 = 2.63 x 104 K 1 = 3.93, K2 = 4.42
Non-imprinted - LbLA QCM (from Langmuir isotherm) K 1 = 1.04 x 103 K 1 = 3.02
Imprinted - LbLB QCM (from Langmuir isotherm) K 1 = 7.24 x 103 K 1 = 3.86

A typical method for assessing guest affinity for thin films is based on the application of the simple Langmuir adsorption isotherm model (Fig. 7B). Using this approach we assume a homogeneous distribution of binding sites with equal energy across the film and that the guest diffusion through the thin film is fast and is not the limiting step.36,41,75 Learning from initial experiments in solution we also know that both films are interacting with metal ions utilizing predominantly receptors composed of two histidine groups per binding site. In the case of the film affinity this simplifies binding to a 1[thin space (1/6-em)]:[thin space (1/6-em)]1 type of interaction but with stoichiometry of two histidine moieties per Cu2+. The data obtained in this way (Table 1) displays substantially higher binding affinity of Cu2+ for the imprinted LbLB film (logK = 3.9) compared to the non-imprinted LbLA (logK = 3.0).

The Cu2+ template-defined organization of PAH-His receptors was protected in the cross-linking process of the LbLB film fabrication. After the template extraction, imprinted LbLB structures remained in place to furnish a spatial configuration of the histidine ligands for the Cu2+ coordination. In contrast, enhanced metal binding cavities derived from spatial arrangements of functional groups, and corresponding to Cu2+, were absent in the LbLA film due to the lack of metal template in the preparation process. As such LbLA displays randomly immobilized histidine receptors with lower affinity to copper ions compared to LbLB.

Rebinding capacities of the LbLA and LbLB films were calculated using QCM collected data after washing the films with 1M HCl. Both films showed Cu rebinding levels of 90% and 95% respectively (see the saturation isotherms in the ESI Fig. S8). A comparison of LbLA and LbLB for affinity toward the Cu2+ ion was also investigated using XPS (Fig. 8). The intensities of the Cu2p3/2 peak at 933 eV and the Cu2p1/2 peak at 953 eV were used for monitoring the trapped copper inside the LbL films.15 Copper can be detected for both types of imprinted LbLA and non-imprinted LbLB films, and it can be removed by washing with 1M of HCl for 5 min. The cycle can be repeated several times and these results indicate that both films possess stable affinity toward copper ions.

image file: c4sc02367f-f8.tif
Fig. 8 Cu 2p XPS spectra of the LbL film before and after loading of copper in the (A) non-imprinted LbLA films and (B) imprinted LbLB films.

The study of the leaching behavior for the metal-bearing films is an important way to obtain valuable information about the chemical properties of the metals in stabilized products and their potential environmental risks in antifouling applications. A better understanding of the leaching rate of the metals trapped inside the LbL films exposed to different environmental conditions is helpful for practical applications. To compare the copper stabilization effect the non-imprinted LbLA and imprinted LbLB films were subjected to a prolonged 90 day leaching experiments (Fig. 9) in an artificial sea water environment.

image file: c4sc02367f-f9.tif
Fig. 9 Cu 2p XPS spectra of the non-imprinted LbLA (A) and imprinted LbLB films (B) against sea salts.

XPS results provide another confirmation of the enhanced affinity of the imprinted LbLB film toward Cu2+ ions. Substantially lower amounts of copper ions leach out of the LbLB film after six weeks of exposure to artificial sea water as compared with the LbLA film. The leaching rate of copper from non-imprinted LbLA is thus obviously faster and all the copper is leached out from the film within a week as shown in the XPS spectra (Fig. 9A). In addition, we have also monitored the N1s XPS spectra of both types of films. The corresponding results (Fig. S9A and B) showed similar spectra indicating that the films are stable in the sea water environment for a prolonged period of time. Thickness values for both films showed the same values even after 45 days in sea salt solution with minor 5–10% loss after 90 days (measured by ellipsometry). From the above results we can state that the cross-linking between the ester groups from the polyanion and amine groups from the polycation, plays a vital role in improving chemical stability of the films under seawater conditions. Moreover, the presented method can be also used to design surfaces with a customized leaching rate of metal ions in addition to an enhancement of copper binding within the imprinted film.

Antifouling properties

Barnacles are common, cosmopolitan macrofouling organisms and can rapidly colonize unprotected surfaces submerged in the marine environment. Barnacle larvae (cyprids) are widely used in the lab scale antifouling tests, since cyprids of the barnacles settle readily in static water assays.76 In this study a barnacle cyprid bioassay was conducted to evaluate the settlement and toxicity effects of imprinted LbLA and non-imprinted LbLB films with copper.

Slightly elevated mortality was observed for naupli incubated for 24 hours on surfaces coated with copper loaded LbL films fabricated with both of the discussed methods compared to the control sample. The lethal concentration (LC50) reported for barnacles nauplii is 0.71 μg mL−1.77 The leached Cu concentration in the model experiment, when the LbLA sample was immersed in 300 μL of water, was established at 60 μg mL−1. Thus the amount of copper released from our materials in a typical biological experiment is well below the toxicity threshold. There was no settlement of the cyprids on non-imprinted LbLA and imprinted LbLB films with copper (Fig. 10). These results indicate that Cu2+ released from the surface is reaching required fouling preventive concentrations. As the assay is conducted in a static droplet, the concentration of copper present in the seawater droplet is the cumulative value achieved over the 24 hour leaching period.

image file: c4sc02367f-f10.tif
Fig. 10 Cyprid settlement and toxicity of imprinted and non-imprinted LbL films with copper loading. Each value is the mean of 8 replicate measurements. The error bars here are standard deviations.

The statistical comparisons were performed using GraphPad Prism 5 (GraphPad Software Inc.). Cyprid mortality and settlement test data were analyzed using a Kruskal–Wallis test and Dunn's post test to evaluate the performance of the LbL films with copper loading. There is no significant difference between the cyprid mortality on imprinted LbLA and non-imprinted LbLB films and control samples (Kruskal–Wallis test, p = 0.1133 and Dunn's post test, p > 0.05).78 Therefore we can conclude that there is no toxicity difference among those surfaces. However, there was no cyprid settlement for non-imprinted LbLA and imprinted LbLB films. The results suggest that the amount of copper slowly released into solution from the surface was low but sufficient to deter settlement.


A peptide mimicking polymer, bearing histidine side groups, was used to construct thin LbL architectures with a high affinity to bind Cu2+ ions. Enhanced binding ability was achieved through a metal imprinting process involving covalent immobilization of receptors within the film structure in the presence of metal ions. A polycation bearing imidiazole-type histidine ligands for metal binding, and a polyanion with high density of methyl esters for covalent cross-linking were custom synthesized for this task. A comparison of metal imprinted LbLB and non-imprinted LbLA films allowed us to conclude that by following the established approach it is possible to enhance the affinity of thin films to bind copper up to seven-fold. This number is likely to be increased when further process optimization at the fabrication stage is considered. Physical and chemical characterization techniques showed that the prepared imprinted LbLB films display excellent stability under harsh seawater conditions and very slow leaching rate of metals compared to non-imprinted LbLA films.

Finally, the films are promising antifouling materials showing noticeable performance against barnacles. We believe that the presented approach may lead to a generic platform for marine antifouling materials with very low net release rate of biocides. Particularly it may help to reduce the amount of copper currently used in commercial antifouling products. By further improvement of metal ion binding one can imagine that this technology can be directly used to obtain paints with very high metal affinity. For example, absorbing copper in places with a high concentration like harbors or polluted river mouths and then slowly releasing it in an open sea could be envisaged. The fabrication approach presented can also benefit metal extraction processes used for example by the water purification or natural resources recovery industries. The phenomenon described here for copper ions could be extended for other metals like Fe, Zn, Co and Ni and their possible applications could be further explored in heavy metal separations, antifungal layers, protein binding, catalysis and fluorescence sensing.


The authors are grateful to the Agency for Science, Technology and Research (A*STAR) for providing financial support under the Innovative Marine Antifouling Solutions (IMAS) program. The authors also thank to Dr. Su Xiao Di and Khin Moh Moh Aung (both from IMRE) for helpful discussion and technical support for QCM experiments.

Notes and references

  1. T. Farhat and P. T. Hammond, Adv. Funct. Mater., 2005, 15, 945 CrossRef CAS.
  2. T. Farhat and P. T. Hammond, Adv. Funct. Mater., 2006, 16, 433 CrossRef CAS.
  3. J. E. Gu, S. Lee, C. M. Stafford, J. S. Lee, W. Choi, B. Y. Kim, K. Y. Baek, E. P. Chan, J. Y. Chung, J. Bang and J. H. Lee, Adv Mater., 2013, 25, 4778 CrossRef CAS PubMed.
  4. M. C. Petty, Stud. Interface Sci., 2002, 16, 317 CAS.
  5. I. Welterlich and B. Tieke, Macromolecules, 2011, 44, 4194 CrossRef CAS.
  6. S. A. Makohliso, L. Giovangrandi, D. Leonard, H. J. Mathieu, M. Ilegems and P. Aebischer, Biosens. Bioelectron., 1998, 13, 1227 CrossRef CAS.
  7. A. Shukla, J. C. Fang, S. Puranam and P. T. Hammond, J. Controlled Release, 2012, 157, 64 CrossRef CAS PubMed.
  8. J. Song, D. Jańczewski, Y. Guo, J. Xu and G. J. Vancso, Nanoscale, 2013, 5, 11692 RSC.
  9. J. Song, D. Jańczewski, Y. Ma, M. Hempenius, J. Xu and G. J. Vancso, J. Colloid Interface Sci., 2013, 405, 256 CrossRef CAS PubMed.
  10. G. Decher, Science, 1997, 277, 1232 CrossRef CAS.
  11. Y. Yan, M. Björnmalm and F. Caruso, Chem. Mater., 2014, 26, 452 CrossRef CAS.
  12. A. L. Becker, A. P. Johnston and F. Caruso, Small, 2010, 6, 1836 CAS.
  13. G. Decher and J. B. Schlenoff, Multilayer Thin Films: Sequential Assembly of Nanocomposite Materials, ed. G. Decher and J. B. Schlenoff, Wiley-VCH, 2003 Search PubMed.
  14. D. Jańczewski, J. Song and G. J. Vancso, Eur. Polym. J., 2014, 54, 87 CrossRef PubMed.
  15. S. R. Puniredd and M. P. Srinivasan, Ind. Eng. Chem. Res., 2005, 46, 464 CrossRef.
  16. A. Mentbayeva, A. Ospanova, Z. Tashmuhambetova, V. Sokolova and S. Sukhishvili, Langmuir, 2012, 28, 11957 CrossRef PubMed.
  17. M. A. Rahim, M. S. Islam, T. S. Bae, W. S. Choi, Y.-Y. Noh and H.-J. Lee, Langmuir, 2012, 28, 8486 CrossRef CAS PubMed.
  18. S. Bhattacharjee, J. Dong, Y. Ma, S. Hovde, J. H. Geiger and G. L. Baker, Langmuir, 2012, 28, 6885 CrossRef CAS PubMed.
  19. R. G. de Paiva, M. A. de Moraes, F. C. de Godoi and M. M. Beppu, J. Appl. Polym. Sci., 2012, 126, E17 CrossRef CAS.
  20. D. Jańczewski, D. N. Reinhoudt, W. Verboom, C. Hill, C. Allignol and M. Duchesne, New J. Chem., 2008, 32, 490 RSC.
  21. A. H. Chen, S. C. Liu, C. Y. Chen and C. Y. Chen, J. Hazard. Mater., 2008, 154, 184 CrossRef CAS PubMed.
  22. G. P. Rao, C. Lu and F. Su, Sep. Purif. Technol., 2007, 58, 224 CrossRef CAS PubMed.
  23. K. Haupt and K. Mosbach, Chem. Rev., 2000, 100, 2495 CrossRef CAS PubMed.
  24. W. Li and S. J. Li, Oligomers Polymer Composties Molecular Imprinting, Springer, 2006 Search PubMed.
  25. R. Y. Liu, G. J. Guan, S. H. Wang and Z. P. Zhang, Analyst, 2011, 136, 184 RSC.
  26. P. Turkewitsch, B. Wandelt, G. D. Darling and W. S. Powell, Anal. Chem., 1998, 70, 2025 CrossRef CAS.
  27. G. Wulff, Chem. Rev., 2002, 102, 1 CrossRef CAS PubMed.
  28. Y. Zhan, X. Luo, S. Nie, Y. Huang, X. Tu and S. Luo, Ind. Eng. Chem. Res., 2011, 50, 6355 CrossRef CAS.
  29. X. Y. Bi, R. J. Lau and K. L. Yang, Langmuir, 2007, 23, 8079 CrossRef CAS PubMed.
  30. B. J. Gao, F. Q. An and Y. Zhu, Polymer, 2007, 48, 2288 CrossRef CAS PubMed.
  31. Buhani, Narsito, Nuryono and E. S. Kunarti, Desalination, 2010, 251, 83 CrossRef CAS PubMed.
  32. Buhani, Suharso and Sumadi, Desalination, 2010, 259, 140 CrossRef CAS PubMed.
  33. G. Z. Fang, J. Tan and X. P. Yan, Anal. Chem., 2005, 77, 1734 CrossRef CAS PubMed.
  34. X. Huang, A. B. Schubert, J. D. Chrisman and N. S. Zacharia, Langmuir, 2013, 29, 12959 CrossRef CAS PubMed.
  35. K. C. Krogman, K. F. Lyon and P. T. Hammond, J. Phys. Chem. B, 2008, 112, 14453 CrossRef CAS PubMed.
  36. S. Wijeratne, M. L. Bruening and G. L. Baker, Langmuir, 2013, 29, 12720 CrossRef CAS PubMed.
  37. H. Chen, G. Zeng, Z. Wang and X. Zhang, Macromolecules, 2007, 40, 653 CrossRef.
  38. P. Schuetz and F. Caruso, Adv. Funct. Mater., 2003, 13, 929 CrossRef CAS.
  39. A. M. Balachandra, J. Dai and M. L. Bruening, Macromolecules, 2002, 35, 3171 CrossRef CAS.
  40. T. Li, S. Chen, H. Li, Q. Li and L. Wu, Langmuir, 2011, 27, 6753 CrossRef CAS PubMed.
  41. H. Deng, L. Gao, S. Zhang and J. Yuan, Ind. Eng. Chem. Res., 2012, 51, 14018 CrossRef CAS.
  42. D. Sanna, G. Micera, C. Kállay, V. Rigóc and I. Sóvágóc, Dalton Trans., 2004, 2702 RSC.
  43. I. Sóvágó and K. Ősz, Dalton Trans., 2006, 3841 Search PubMed.
  44. X. Bi and K.-L. Yang, Langmuir, 2007, 23, 11067 CrossRef CAS PubMed.
  45. P. Deschamps, P. P. Kulkarni, M. Gautam-Basak and B. Sarkar, Coord. Chem. Rev., 2005, 249, 895 CrossRef CAS PubMed.
  46. H. Sigel and R. B. Martin, Chem. Rev., 1982, 82, 385 CrossRef CAS.
  47. D. E. Fullenkamp, L. He, D. G. Barrett, W. R. Burghardt and P. B. Messersmith, Macromolecules, 2013, 46, 1167 CrossRef CAS PubMed.
  48. Y. Kobayashi, Y. Takashima, A. Hashidzume, H. Yamaguchi and A. Harada, Sci. Rep., 2012, 3, 1243 Search PubMed.
  49. Y.-C. Chung, W.-Y. Hsieh and T.-H. Young, Biomaterials, 2010, 31, 4194 CrossRef CAS PubMed.
  50. S. Dobretsov, R. M. Abed and M. Teplitski, Biofouling, 2013, 29, 423 CrossRef CAS PubMed.
  51. M. Tasso, S. L. Conlon, A. S. Clare and C. Werner, Adv. Funct. Mater., 2012, 22, 39 CrossRef CAS.
  52. D. M. Yebra, S. Kill and K. Dam-Johansen, Prog. Org. Coat., 2004, 50, 75 CrossRef CAS PubMed.
  53. E. Almeidaa, T. C. Diamantinoa and O. de Sousab, Prog. Org. Coat., 2007, 59, 2 CrossRef PubMed.
  54. A. P. Negri and A. J. Heyward, Mar. Environ. Res., 2001, 51, 17 CrossRef CAS.
  55. A. Sousa, L. Genio, S. Mendo and C. Barrosoi, Appl. Organomet. Chem., 2005, 19, 324 CrossRef CAS.
  56. I. Omae, Chem. Rev., 2003, 103, 3431 CrossRef CAS PubMed.
  57. G. Damiens, C. Mouneyrac, F. Quiniou, E. His, M. Gnassia-Barelli and M. Romeo, Environ. Pollut., 2006, 140, 492 CrossRef CAS PubMed.
  58. X. Zhu, D. Jańczewski, S. S. C. Lee, S. L.-M. Teo and G. J. Vancso, ACS Appl. Mater. Interfaces, 2013, 5, 5961 CAS.
  59. X. Zhu, S. Guo, D. Jańczewski, F. J. P. Velandia, S. L.-M. Teo and G. J. Vancso, Langmuir, 2014, 30, 288 CrossRef CAS PubMed.
  60. K. A. Marx, Biomacromolecules, 2003, 4, 1099 CrossRef CAS PubMed.
  61. Y. Wang, D. E. Betts, J. A. Finlay, L. Brewer, M. E. Callow, J. A. Callow, D. E. Wendt and J. M. DeSimone, Macromolecules, 2011, 44, 878 CrossRef CAS.
  62. E. Pretsch, P. Bnhlmann, and C. Affolter, Structure Determination of Organic Compounds, Springer, 2009 Search PubMed.
  63. J. G. Mesu, T. Visser, F. Soulimani and B. M. Weckhuysen, Vib. Spectrosc., 2005, 39, 114 CrossRef CAS PubMed.
  64. R. J. Sundberg and R. B. Martin, Vib. Spectrosc., 1974, 74, 471 CAS.
  65. H. Yang, M. Pritzker, S. Y. Fung, Y. Sheng, W. Wang and P. Chen, Langmuir, 2006, 22, 8553 CrossRef CAS PubMed.
  66. J. Song, D. Jańczewski, Y. Ma, L. V. Ingen, C. E. Sim, Q. Goh, J. Xu and G. J. Vancso, Eur. Polym. J., 2013, 49, 2477 CrossRef CAS PubMed.
  67. A. L. Stancik and E. B. Brauns, Vib. Spectrosc., 2008, 47, 66 CrossRef CAS PubMed.
  68. A. E. Hargrove, Z. Zhong, J. L. Sessler and E. V. Anslyn, New J. Chem., 2010, 34, 348 RSC.
  69. S. R. Puniredd and M. P. Srinivasan, Langmuir, 2005, 21, 7812 CrossRef CAS PubMed.
  70. I. Choi, R. Suntivich, F. A. Plamper, C. V. Synatschke, A. H. E. Muller and V. V. Tsukruk, J. Am. Chem. Soc., 2011, 133, 9592 CrossRef CAS PubMed.
  71. K. Glinel, C. Déjugnat, M. Prevot, B. Schöler, M. Schönhoff and R. V. Klitzing, Colloids Surf., A, 2007, 303, 3 CrossRef CAS PubMed.
  72. B. Schoeler, G. Kumaraswamy and F. Caruso, Macromolecules, 2002, 35, 889 CrossRef CAS.
  73. S. T. Dubas and J. B. Schlenoff, Macromolecules, 2001, 34, 3736 CrossRef CAS.
  74. D. P. Go, A. Hung, S. L. Gras and A. J. O'Connr, J. Phys. Chem. B, 2012, 116, 1120 CrossRef CAS PubMed.
  75. Z. Pei, H. Anderson, T. Aastrup and O. Ramstrom, Biosens. Bioelectron., 2005, 21, 60 CrossRef CAS PubMed.
  76. E. R. Holm, Integr. Comp. Biol., 2012, 52, 348 CrossRef PubMed.
  77. C. Bressy, C. Hellio, J. P. Maréchal, B. Tanguy and A. Margaillan, Biofouling, 2010, 26, 769 CrossRef CAS PubMed.
  78. D. Rittschof, B. Orihuela, T. Harder, S. Stafslien, B. Chisholm and G. H. Dickinson, PLoS One, 2011, 6, e16487 CAS.


Electronic supplementary information (ESI) available: FTIR, NMR spectra of synthesized polymers, XPS spectra and AFM images of non-cross linked and cross linked LBLA and LBLB films, UV-Visible absorption spectra of copper complexation with PAH-His, QCM data of LBLA and LBLB films and stability of the films are provided in the electronic supplementary information. See DOI: 10.1039/c4sc02367f

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