Introduction

Underwater installations in marine environment are suffering biofouling problems. This also accounts for vessels and warships resulting in increased drag resistance and oil consumption, which in turn results in high CO2 emission and economic loss [1,2,3]. Besides, a wide range of marine sensors have been set up to monitor seawater properties (e.g. temperature, turbidity, CO2, conductivity…), marine ecosystems and environmental contaminants [4,5,6]. Fouling on these sensors could however disrupt reading and greatly shorten the sensors’ life-time [7]. In aquaculture, fouling on cage nets has a negative effect on solidity of the nets as well as on fish growth, health and welfare [8, 9]. The direct economic costs of biofouling control are estimated to 5–10% of production costs in aquaculture industry (2012 estimate) [8]. In addition, many indirect effects of biofouling remain broadly unassessed, meaning that the overall impact of biofouling in aquaculture is unquestionably underestimated [8]. Meanwhile, it is known that water quality monitoring with sensors is critical in aquaculture since water quality, e.g. pH, dissolved oxygen and carbon dioxide value, is crucial for fish health. The presence of fouling on the surface of sensors causes significant drift, poor signal-to-noise ratio and high background signal, leading to incorrect reading from the sensors [10, 11]. In consequence, it is urgent to protect the sensors’ surface from serious fouling issues.

Antifouling (AF) paints have been widely used to control and prevent biofilm settlement on submerged surfaces. Tributyltin (TBT) based AF paints had been widely used before they were banned by International Maritime Organization (IMO) due to the detrimental impact of TBT on marine environment [12]. Meanwhile, the growing concern for environmental problems has increasingly restricted the use of biocide-based paints. Thus, lots of attention has been attracted to the development of practical and environment friendly silicone-based Fouling Release Coating (FRC) techniques. Polydimethylsiloxane (PDMS) paints possesses nonleachant properties, ultrasmooth topology, environmental friendliness, stability in water, low free energy, optimum molecular mobility, water and fouling repellency, stability against heat and oxidation, and good adhesion on different substrate materials [13]. It can weaken the attachment of fouling organisms due to low surface energy and low elastic modulus, thus promoting the release of accumulated fouling by dynamic forces caused by movement through the water [14]. However, it also suffers from the disadvantage of being less effective on slow moving and stationary installations, such as slow moving or moored vessels, installed sensors, and aquaculture nets and cages [15].

One effective strategy to overcome this weakness is to develop PDMS/nanofillers nanocomposite materials. The nanofillers like metal oxides, noble metals, and graphene-based materials can increase the resistance against microorgram attacks [16]. Nanomaterials like ZnO nanoparticles (NPs), β-MnO2 Cu2O nanocubes, titania nanospheres, Ag@SiO2, carbon nanofillers (GO, carbon nanotubes (CNT)) have been used as effective nanofillers in antifouling field [17,18,19]. Sherif A. EI-Safty has made a series of PDMS/nanofiller antifouling coatings, with GO–ZnO nanorod, SiO2-doped ZnO and β-MnO2 nanorod working as nanofillers [20,21,22]. The changed surface topography (nanostructure, surface roughness) and surface wettability leads to the improved fouling release (FR) property and lower adhesion strength between biofilm and surface. Beigbeder et al. have demonstrated that low amounts of CNT can result in a significant enhancement of FR property of PDMS-based coatings [23, 24]. Irani and coworkers showed that the loading of pristine and fluorinated MWCNT into PDMS can reduce the pseudobarnacle adhesion strength by 47% and 67% respectively [25]. Among various nanofillers, GO nanosheets with plentiful carboxylic and hydroxyl functional groups have been proved to have excellent antifouling properties [26, 27]. Moreover, the functional groups can provide opportunities to attach metal and metal oxide NPs in order to improve application performance in the antifouling field [28,29,30,31]. Kim et. al. have developed GO nanopaints that exhibit not only antibacterial properties in lab tests, but also antifouling properties in field tests [32]. Especially, Qin et al. have developed GO-based antifouling coating on sensor surfaces via layer-by-layer technique without compromising the sensor’s performance [33]. The valuable antifouling property and adaptability on sensor surfaces makes GO a promising nanofiller in PDMS. In addition, metal oxide NPs like copper oxide (CuO), zinc oxide (ZnO) and titanium dioxide (TiO2) have been used as nanofillers in order to enhance the antifouling property of the PDMS matrix [20, 22, 34,35,36,37]. Among these NPs, ZnO exhibits various advantages, such as low cost, environmental friendliness and optimal antifouling property owing to its highest hydrophobicity and surface roughness. The selective toxicity to bacteria and low toxicity to human cells of ZnO makes it a promising candidate in the antifouling field [36, 38, 39].

In light of these facts, ZnO–GO nanocomposite has been prepared through the nucleation of ZnO NPs in the abundant functional groups of GO’s surfaces [40]. With the incorporation of ZnO–GO into PDMS, we have thus obtained a serious of PZGO nanocomposites with different mass ratio (from 0.05 to 2% wt%) of ZnO–GO to PDMS. In this work, PZGO nanocomposite has been developed with the aims of addressing short-term biofouling effect of sensors. Owing to the high surface roughness (4.02 nm) and hydrophobicity (117°) of the developed PZGO nanocomposite and antimicrobial property of ZnO NPs, PZGO nanocomposite delivered competitive antifouling performance with 97.6% fouling inhibition. The study provides an alternative for developing antifouling coatings to address sensor’s durability problem caused by fouling.

Experimental

Materials

Graphene oxide (GO) was purchased from Abalonyx Norway. Zinc acetate dehydrate (Zn (CH3COO)2·2H2O, ≥ 99.0%), Lithium hydroxide monohydrate ( LiOH·H2O, ≥ 98.0%), Tetrahydrofuran (C4H8O, ≥ 99.9%), absolute alcohol (CH3CH2OH, 100%), n-hexane (CH3(CH2)4CH3, ≥ 96.0%), glutaraldehyde solution (grade 1, 25% in H2O) and Sylgard(R) 184 were obtained from Sigma-Aldrich.

Preparation of ZnO–GO Nanocomposite

As shown in Scheme 1 (1), a facile one-pot reaction was used to synthesized ZnO–GO composites [40]. In brief, 0.55 g Zn (CH3COO)2·2H2O was added into 50.0 ml absolute ethanol and dissolved by stirring under 80 °C for 15 min, the obtained mixture was then cooled to 40 °C. Subsequently, 0.2 g dissolved LiOH·H2O in 30 ml alcohol and varying amounts of 2 mg/ml GO aqueous solution were mixed with the above solution by stirring for 45 min under 40 °C. After cooling and the addition of 100 ml n-hexane, the final mixture was left overnight at 4 °C The resulting precipitates were then separated by washing with DI water and absolute ethanol for three times in turn under centrifugation. Finally, the ZnO–GO nanocomposites were obtained by vacuum drying at 60 °C for 12 h.

Scheme 1
scheme 1

(1) Preparation of ZnO–GO nanocomposites through a one-pot method. (2) Preparation of PZGO nanocomposite and spin coating the coating surface

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Preparation of PDMS/ZnO–GO Surface

Scheme 1 (2) represents the preparation of PZGO nanocomposites coating surface. ZnO–GO was first dispersed in tetrahydrofuran (THF) by probe sonication for 20 min. The suspension was then added into PDMS (part A), followed by water bath sonication for 30 min and then mechanical stirring (1000 rpm) for 30 min. Subsequently, part B (the ratio of part A to part B is 10:1) was mixed with above mixture through mechanical stirring until all THF solvent had completely evaporated. The obtained PZGO mixture was then placed in a vacuum desiccator and degassed to remove the air bubbles. Finally, the PZGO mixture was spin-coated (1000 rpm, 30 s) on round cover slips which had been rinsed with water and ethanol to get a thin film on one side of each cover slip. Curing was carried out in an oven at 65 °C for 4 h. Pristine PDMS surface worked as control sample. The control was made by mixing part A and part B in a ratio of 10:1, following the same procedures as the preparation of PZGO film. In this work, PZGO nanocomposites were named based on the mass ratio of ZnO–GO to PDMS, as summarized in Table 1. For example, PZGO0.05 represents 0.05 wt% mass ratio of ZnO–GO to PDMS.

Table 1 Different mass ratios of ZnO–GO to PDMS in the formation of PZGO
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Characterization

Fourier transform infrared (FTIR) spectra were recorded with a Bruker ALPHA FTIR spectrometer. X-ray diffraction (XRD) was obtained with DaVinci1 from 10° to 80°. UV–visible absorption spectra were recorded by Cary 60 UV–vis at the range of 200 to 500 nm. Raman spectra were determined by InVia Reflex Spectrometer System with 532 nm laser excitation. Scanning electron microscopy (SEM) images were obtained by using FEI APREO, which is a Field Emission SEM. Transmission electron microscopy (TEM) images were obtained with in-lens cold field emission microscopy (Hitachi S-5500 S(T)EM) with an accelerating voltage at 30 kV. X-ray spectrometer (EDX) were investigated for element analysis of samples. Raman spectra were recorded by InVia Reflex Spectrometer System with 532 nm laser excitation. The surface property of the synthesized materials was analyzed with Atomic force Microscopy (AFM, Veeco Metrology). AFM was used to measure surface morphology and roughness under PeakForce Quantitative NanoMechanics mode. Contact angle and surface free energy (SFE) were measure with drop shape analyzer DSA25 (KRÜSS) by sessile drop technique. Static water contact angle measurements were performed with deionized water five times for each sample. Dynamic WCA including advancing contact angle (θadv) and receding contact angle (θrec) was measured with 25 µl of deionized water being expanding and shrinking on the sample at a rate of 0.75 µl/s. The difference between θadv and θrec is referred as hysteresis. SFE was determined through measuring surface contact angles of pure water (polar liquid) and diiodomethane (disperse liquid). In this work, we Owens, Wendt, Rabel and Kaelble (OWRK model) [41, 42] was applied to calculate the SFE of PDMS and PZGO nanocomposite. This model was also used by our previous work to calculate SFE [43].

Preparation of Bacterial Strains and Bacteria Adhesion Testing

Synechococcus sp. Strain PCC 7002, a marine cyanobacterium, was inoculated and cultured in 40 mL batches of AA+-medium in 75cm3 Nunc Easyflask culture flasks with filter caps. The cultures were grown overnight on a shaker at 30 °C and 30 µmol photons m−2 s−1 to OD730 of roughly 0.4. AA+-medium is a derivative of A+ [44], with the P1 trace metal solution replaced by a very similar 1000X BG-11 trace mineral solution [45].

The antibacterial activity of PDMS and PZGO was studied by testing against Synechococcus sp. Strain PCC 7002. In brief, the sterilized coverslips with PDMS and PZGO were placed into each well of 12-well plates. 5 ml of Synechococcus sp. Strain PCC 7002 culture with OD730 of 0.4 was added into each well. The soaked coverslips in each well were incubated at 30 °C. After incubation for 7 days, the unattached cells were removed from the coverslips by washing coverslips with AA+ medium three times. Subsequently, the attached biofilm on coverslips was fixed with 2.5% glutaraldehyde for 2 h at 4 °C before measuring with confocal laser scanning microscopy (CLSM). In this work, coverage (%) was defined as the ratio of the adhesion area of the cells to the total area of surface. Five points were selected randomly for each sample, resulting in the statistical data. The standard Student t-test was used to compare the difference between control glass slides and modified glass slides.

Preparation of Algal Cultures and Algal Adhesion Testing

An axenic culture of the marine diatom P. tricornutum (Bacillariophyceae) clone Pt 1.8.6 (CCMP2561) obtained from the culture collection of the Provasoli-Guillard National Center for Culture of Marine Phytoplankton (Bigelow Laboratory for Ocean Sciences, USA) was used for the adhesion testing. P. tricornutum cultures were grown in f/2 medium made with 0.2 µm filtered and autoclaved local seawater supplemented with f/2 vitamins and inorganic nutrients, filter sterilized and added after autoclaving (Guillard, 1975). Cultures were grown under a 16 h photoperiod at 22 °C, 35 µmol photons m−2 s−1.

Coverslips with coatings of PDMS and PZGO were firstly sterilized with EtOH (10 s) and then placed into each well of 12-well plates. 5 ml of P. tricornutum with a cell concentration of 1 × 105 cells/ml was added into individual wells and maintained at 22 °C. After one week of incubation, coverslips were taken out from each well and washed with f/2 medium three times to remove loosely attached algae. Subsequently, the coverslips with attached algae was fixed with 2.5% glutaraldehyde for 2 h at 4 °C, and then imaged with CLSM. Five random fields were imaged for each sample. The coverage (%) of attached algae were quantified with ImageJ software through calculating CLSM images.

Results and discussion

Structure and Morphology Analysis of ZnO–GO

ZnO–GO nanocomposite was synthesized through a facile one-pot reaction. Figure 1A shows FTIR spectra of GO and ZnO–GO nanocomposite. It can be seen from the spectrum of GO that the peaks at around 3170, 1712, 1602, 1187 and 1035 cm−1 are assigned to O–H stretching vibration, C=O stretching vibration of COOH groups, skeletal vibration of unoxidized domains, C–OH stretching vibrations and C–O stretching vibrations, respectively [46]. In the spectrum of ZnO–GO, the weaker peaks of hydroxyl, carboxyl and epoxide groups indicate the reduction of GO. Furthermore, a new peak at around 447 cm−1 is attributed to ZnO which is in accordance with the UV spectrum that is discussed below [47]. As shown in the UV spectrum in Fig. 1B, GO exhibited a peak at around 249 nm and a shoulder at around 300 nm attributing to π–π* transition of C=C bond and n–π* in C=O bond, respectively [48]. Besides, the peak at around 352 nm revealed the forming of ZnO NPs [49]. Moreover, the absorption peak at around 300 nm of ZnO–GO nanocomposites became unobvious, which further proved that GO has been reduced. All these indicators from the UV spectra are in accordance with FTIR spectra. Meanwhile, it is clear to see the weak peak at around 2θ = 11.3°, from Fig. 1C, assigning to reduced GO, and the new appeared peaks at around 2θ = 31.8°, 34.5°, 36.3°, 47.6°, 56.7°, 62.9°,68.0° attributing to the decorating of ZnO NPs (JCPDS No. 36-1451) on GO surface. Overall, the FTIR, UV and XRD spectra of GO and ZnO–GO nanocomposites are consistent.

Fig. 1
figure 1

(A) FTIR spectra of GO and ZnO–GO nanocomposite; (B) UV spectra of GO and ZnO–GO nanocomposites; (C) XRD spectra of GO and ZnO–GO nanocomposites

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The morphology of ZnO–GO nanocomposites was examined through SEM and TEM. As shown in Fig. 2A, some wrinkles were observed on GO, which provided a large surface for ZnO NPs to attach and were important for preventing aggregation of ZnO NPs. To estimate the chemical compositions of ZnO–GO nanocomposite, EDX measurement was performed. Figure 2D shows presence of Zn, O and C in sample. Si comes from the sample substrate where the sample was prepared. The SEM and TEM images and EDX sprectrum of ZnO–GO demonstrated ZnO NPs were deposited on the surface of GO, and this is consistent with FTIR, UV and XRD results.

Fig. 2
figure 2

SEM pictures of A GO, B ZnO–GO, C TEM picture of ZnO–GO nanocomposite, D EDX spectrum of ZnO–GO

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Structure and Surface Properties of PDMS and PZGO Nanocomposites

Raman spectra of PDMS and PZGO nanocomposites are presented in Fig. 3. It was noticed that the peak at around 487, 619 and 707 cm−1 are attributed to symmetric Si–O–Si cm−1, rocking of Si–CH3 and symmetric stretching of Si–C, respectively. The Si–CH3 symmetric and asymmetric stretching bands where at 2904 and 2964 cm−1. Regarding the PZGO nanocomposites, no markedly difference was noticed in the spectra of PZGO 0.05 and PZGO0 due to the low content of ZnO–GO. With the increased amount of ZnO–GO, two new peaks at around 1348 and 1597 cm−1, as shown in the insertion Fig. 3, were observed. These two peaks correspond to the dominant peaks of GO, which indicated the presence of ZnO–GO nanocomposites.

Fig. 3
figure 3

Raman spectra of PDMS and PZGO nanocomposites with different mass ratios of ZnO–GO to PDMS

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Figure 4 shows SEM images of pure PDMS and PZGO nanocomposites. PDMS displays smooth and featureless surface property, as shown in Fig. 4A. ZnO–GO nanofillers can be clearly observed from Fig. 4B–E. The SEM images of PZGO nanocomposites were studied to determine the effect of the distribution of ZnO–GO on the surface properties of PZGO nanocomposites. PZGO0.05, PZGO0.1 and PZGO0.2 exhibited well-dispersion and no aggregation characteristics. The good dispersion of ZnO–GO nanofillers in PDMS matrix resulted in a homogenous surface which could reduce fouling settlement. Conversely, the increased loading of nanofillers after PZG0.2 caused clustering and accumulation of ZnO–GO in PDMS matrix. Nanofillers’ aggregation decreased surface homogeneity, thus facilitating fouling settlements.

Fig. 4
figure 4

SEM images of A PDMS, B PZGO0.05, C PZGO0.1, D PZGO0.2, E PZGO2

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PDMS and PZGO nanocomposites’ topographies were investigated via AFM as shown in Fig. 5. Plain PDMS showed a surface roughness (Ra) of 2.53 nm. PZGO nanocomposites exhibited a progressive increase of Ra with raised incorporation of ZnO–GO nanofillers. It showed the rough surface peaked at PZGO0.2 with the value of 4.02 nm, resulting from the good distribution of ZnO–GO nanofillers. However, the continuous boost of ZnO–GO nanofillers led to inhomogeneous surface due to aggregation, which in turn diminished Ra of PZGO2 to 3.28 nm.

Fig. 5
figure 5

3D AFM images of A PDMS, B PZGO0.05, C PZGO0.1, D PZGO0.2, E PZGO2

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Wetting properties and SFE of PZGO nanocomposites filled with different amount of ZnO–GO nanofillers compared to plain PDMS are shown in Fig. 6. The pure PDMS showed a contact angle of 107° and so exhibited hydrophobic behavior. There was a gradually increase of WCA with raised loading of ZnO–GO nanofillers into PDMS. WCA raised up to 117° by the introduction of 0.2 wt% nanofiller indicating better hydrophobicity. But higher amount of nanofillers after PZGO0.2 does not lead to a continuous raising of hydrophobicity and Ra due to inhomogeneous surface caused by aggregation of ZnO–GO. In addition, with good dispersibility of ZnO–GO, the increased content of ZnO–GO nanofillers reduced the SFE from 20.02 mN/m (PDMS) to 9.06 mN/m (PZGO0.2), whereas the cluster of ZnO–GO nanofillers increased SFE. The results of Ra (Fig. 5F), WCA and SFE reflect that, with good distribution, raised content of ZnO–GO induces high Ra, high WCA and low SFE, which benefit for antifouling property. On the other hand, the cluster of ZnO–GO has negative impact on antifouling property due to low Ra, low WCA and high SFE. Furthermore, as shown in Fig. 6B, the incorporation of ZnO–GO nanofiller does not have an obvious impact on neither θadv nor θrec. However, △θ increased from 31° to 55° with the amount of ZnO–GO increasing from 0.2 wt.% to 2 wt.%, resulting from aggregation of ZnO–GO.

Fig. 6
figure 6

A Comparison of WCA and SFE of PDMS and PZGO nanocomposites; B Dynamic water contact angle of PDMS and PZGO nanocomposites

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Antifouling tests

Bacteria

Visual confirmation of antifouling effect against Synechoccocus sp 7002 of pure PDMS and PZGO nanocomposites was investigated by CLSM. As shown in Fig. 7A, the biofilm fully covered the surface of pure PDMS after 7 days incubation. As observed from Fig. 7B to Fig. 7E, the incorporation of ZnO–GO nanofillers can decrease the attachment of Synechoccocus sp 7002 significantly. Significantly lower green fluorescence was observed on the surface of PZGO0.2 and PZGO2 compared to pure PDMS. Statistical analysis of Synechoccocus sp 7002 fouling was obtained through Image J. As shown in Fig. 7F, the increased amount of ZnO–GO nanofillers resulted in gradually reduced biofilm attachment until PZGO0.2, which indicates improved antifouling property. On the other hand, the continuous increased loading of ZnO–GO after PZGO0.2 caused a slight increase of biofilm coverage due to serious aggregation of ZnO–GO. Aggregations results in nonhomogeneous topology and in turn leads to more fouling attachment on the clustered surface. A good dispersion of nanofillers produces rougher surface, higher hydrophobicity and lower biofilm attachment. Notably, PZGO0.2 presents the best antifouling property with only 8.5% biofilm coverage, while pure PDMS shows 55.2% biofilm coverage. Also, PZGO0.2 displays the highest Ra of 4.02 nm and the best hydrophobicity of 117° based on surface analysis. Above all, these results imply that distribution of nanofillers is crucial to surface topology and fouling inhibition. It is reported that the increased nanoscale surface roughness and hydrophobicity can lead to good antifouling property. The reason for this is that the nanoscale surface roughness can trap air between surface interstices, so that the rough surface is equivalent to a composite surface of vapor and solid. Such enhanced rough surface (Scheme 2) caused by the incorporation of ZnO–GO nanofillers can prevent water from penetrating into interstices’ groves, which consequently leads to increased hydrophobic property [50, 51]. Also, this phenomenon can afford increased antifouling property caused by declined surface-fouling bond [51, 52]. In addition, antimicrobial property of ZnO–GO nanofillers also contributes to the decreased fouling attachment.

Fig. 7
figure 7

CLSM images showing adhesion of Synechoccocus sp 7002 A PDMS, B PZGO0.05, C PZGO0.1, D PZGO0.2, E PZGO2; F, Statistic biofilm coverage (adhesion ratio) of Synechoccocus sp 7002, error bars are shown as ± SD (n = 5). *P < 0.05

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Scheme 2
scheme 2

Hydrophobic behavior of PZGO nanocomposite that prevent fouling adhesion

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Algae

To investigate antifouling property against microalgae, round glass slides with pure PDMS and PZGO coating surfaces were immersed in P. tricornutum suspensions for 7 days. P. tricornutum is a typical biofouling organism because it participates in early stage of biofouling [53]. The CLSM images clearly indicates that good dispersion of ZnO–GO (Fig. 8B–D) provided less biofilm attachment, while aggregation of ZnO–GO (Fig. 8E) offered more serious fouling surface. This is because good dispersion of ZnO–GO brings about higher Ra and hydrophobicity, which are beneficial to antifouling property. Unlike the antifouling test with Synechoccocus sp 7002 where PZGO0.2 displayed the best antifouling property, PZGO0.1 resulted in the lowest biofilm coverage when performing antifouling tests with P. tricornutum. The biofilm coverage dropped from 43.7% when cells were grown on pure PDMS to 2.4% when the surface was coated with PZGO0.1 (Fig. 8F). It has been reported that the toxicity of ZnO NPs on algae is ascribed to the interaction between algae and ZnO NPs [54]. As for P. tricornutum, Cai et al. demonstrated that ZnO NPs can’t attach on its surface and proved its resistance to the toxicity of ZnO NPs. Because the slender shape and surface charge of P. tricornutum can decrease the interaction with ZnO NPs and lead to low toxicity of ZnO NPs on P. tricornutum [55]. Therefore, it is hypothesized that the antifouling property of PZGO against P. tricornutum mostly comes from homogeneous topology, while antimicrobial effect of ZnO–GO only contributes a little. Thus, the increased loading of ZnO–GO from PZGO0.1 to PZGO0.2 does not cause a raised biofilm inhibition, because PZGO 0.1 and PZGO0.2 shows similar topology. But we’re still unsure why the antifouling property of PZGO0.2 against P. tricornutum gets worse compared to PGZO0.1.

Fig. 8
figure 8

CLSM images showing adhesion of P. tricornutum A PDMS, B PZGO0.05, C PZGO0.1, D PZGO0.2, E PZGO2; F, Statistic biofilm coverage (adhesion ratio) of P. tricornutum, error bars are shown as ± SD (n = 5). *P < 0.05

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Conclusion

It is still a major challenge to improve the durability relating to biofouling resistance for sensors. In order to address the issue, a series of PZGO nanocomposites with different amount of ZnO–GO nanofillers were spin coated on round glass slides for antifouling tests with two microorganisms. The higher hydrophobic property and Ra of the synthesized PZGO nanocomposites were beneficial from the good dispersion of ZnO–GO nanofillers in PDMS, thus resulting in good antifouling property. The antifouling test proved that the PZGO nanocomposites showed superior antifouling property, but the optimal mass ratio of ZnO–GO to PDMS differed between Synechoccocus sp 7002 and P. tricornutum. PZGO0.2 showed the lowest biofilm coverage of 8.5% in the antifouling test against Synechoccocus sp 7002, while PZGO0.1 displayed the best antifouling property against P. tricornutum with 2.4% biofilm attachment. We believe that PZGO nanocomposite can provide a potential possibility for developing antifouling coating for sensor.