Interfactant action of an amphiphilic polymer upon directing graphene oxide layer formation on sapphire substrates
© The Author(s) 2017
Received: 5 January 2017
Accepted: 4 May 2017
Published: 15 May 2017
Quality assured surface pre-treatment may greatly enhance adhesive interactions and, thus, the performance and durability of material joints. This holds true as well for substrates used in coating processes as for adherents introduced into bonding processes. Wettable polymeric wetting agents—shortly called polymeric interfactants—contribute to modifying surfaces and governing the properties of interphases. This is demonstrated for amphiphilic polymers directing the adsorption of graphene oxide (GO) nano-sheets from aqueous dispersion on alumina surfaces. In this contribution, contact angle measurements as well as X-ray photoelectron spectroscopy and scanning force microscopy investigations are applied for the characterization of thin films. GO is adsorbed either from a buffered dispersion on pristine aluminum oxide surfaces or on alumina modified with a few nanometers thin layer of a polymeric interfactant. Laterally extended nanoparticles and GO nano-sheets are preferentially found on interfactant layers whereas on pristine aluminum oxide smaller adsorbates dominate. The driving forces directing the GO attachment are discussed using a phenomenological model based on polymer/substrate interactions governing the sticking probabilities of GO nano-sheets with different sizes.
Adhesive bonding technology and especially bonded light metal joints play an important role in vehicle and aircraft construction . Among numerous approaches for the surface pretreatment of light metal adherents or substrates, layers formed by amphiphilic polymers may contribute in increasing the durability of adhesive joints or coatings [2, 3]. The adsorption behavior of amphiphilic polymers on oxide, hydroxide or carbonate-based reaction layers on the surfaces of light metal alloys recently was investigated by dissipative particle dynamics (DPD) simulations [4, 5]. The resulting some nanometers thin adsorbates were characterized by electron emission, e.g. using X-ray photoelectron spectroscopy (XPS) or optically stimulated electron emission (OSEE), by wetting techniques, and with respect to their chemical interaction with liquid water [5, 6]. Concerning the film nucleation and growth of further moieties on top of the resulting polymer-coated surfaces, the feasible interface active agent (interfactant) effect with respect to directing the attachment of molecular films and the interaction with these films was discussed . Based on this conception, polymeric interfactant films are two-dimensional layers with molecular dimensions, and they are made up of molecular entities in a way that each molecule spans between the solid substrate below it and the neighboring phase which extends over the half-space above it. Generally, this neighboring phase may be air, a liquid (like water ) or a solid, e.g. a cured adhesive or nano-particles. The interfactant layer may feature a homogeneous thickness all over the substrate, or it may exhibit some local variations in height leading to a difference between the roughness of the interfactant layer and the substrate roughness. A laterally homogeneous layer thickness is to be expected for layers of conventional adhesion promoters or coupling agents which exhibit an essentially linear head–tail structure, like surface-active material [4, 7–9]. The head group and often also the tail group are functional, and they may be different from each other. Depending on the length of the spacer (or backbone) unit between these terminal groups and on the temperature with respect to a critical temperature, the two-dimensional layers may be liquid, amorphous or highly ordered, e.g. forming a 2D crystalline layer in a self-assembly process resulting in a self-assembled monolayer (SAM) [8, 9]. Most pronounced during film growth, the molecular entities may be laterally mobile with respect to each other—which may hold true not only for the spacer chain and the tail group but also for the head group attached to the substrate. Such mobility of head groups is restricted in case of an intra-layer linking which is known for silane layers on oxide surfaces or also for alkyl thiol SAMs on gold surfaces showing disulphide links close to the substrate surface [9, 10]. On the other hand, a laterally variable layer thickness may be expected for layers formed from polymers with a more complex shape than a linear one. As it was shown for amphiphilic polymers, such non-linear shape may result from intramolecular interactions, a phenomenon which is quite common also for polypeptides, e.g. globular proteins [4–6]. Especially for such polymeric monolayers the term polymeric interfactant layer was suggested recently .
The formation of graphene oxide (GO) layers on substrates is governed by the interactions between GO sheets (or flakes) and the substrate surface. GO may be considered a molecule with a hydrophobic polyaromatic backbone separated by cycloaliphatic structures containing C=C double bonds and hydrophilic hydroxyl and epoxy groups; and the edges of this nearly flat carbon grid expose carboxylic acid groups [11, 12]. The properties of reduced graphene oxide as a conducting material adsorbed on surfaces depend on the morphology of the constituting nano-sheets and the overall assembly arrangement . Following the intended application of GO, reduced GO or graphene films, the morphology of the constituting adsorbed nano-sheets may be aspired to result smooth and flat or, alternatively, corrugated, e.g. wrinkled or crumpled [14–17]. The interaction between the substrate and graphene or between adsorbed nanoparticles and GO may govern the formation of wrinkles [14, 15] in the flexible nano-sheets. Wrinkles may occur on graphene planes and have high aspect ratios, with a height below 15 nm and lengths above 100 nm . The layer assembly may be tuned by covalent interactions of the carboxylic and hydroxyl functional groups and by electrostatic interactions with polyelectrolytes [18, 19]. Thin graphene oxide layers may be obtained by dipping hydrophilic substrates like pretreated quartz in a 70 °C hot aqueous dispersion of exfoliated GO, resulting in continuous and homogeneous films . Chemical adsorption was investigated by Ou et al. who contacted an aqueous GO formulation for 12 h at 80 °C with a (3-aminopropyl)triethoxysilane (APTES-SAM) covered Si wafer . In a similar way, covalent anchoring was shown by Su and Chiou who attached GO to aminothiol modified gold surfaces . Using such conventional adhesion promoter layers as substrates for the formation of GO films requires first the attachment of the organic layers to the respectively used substrate and, second, an adequate, e.g. chemical, interaction with the subsequently applied GO sheets. Therefore, polymeric interfactants may provide promising prospects since they strongly attach to a wide range of distinct substrate surfaces and, thus, may also be eligible for attaching GO nano-sheets.
In this section, the experimental procedures applied for the manufacture of the layer systems on surfaces of aluminum oxide single crystals as well as the analysis methods used for characterizing the layers will be described.
Sapphire (α-aluminum oxide, corundum single crystal) samples, single-side chemo-mechanically polished were purchased from TBL-Kelpin Dr. Gerd Lamprecht (Neuhausen, Germany).
A water-based formulation “G50 wb” containing the amphiphilic polymer Additive G50 (Straetmans High TAC GmbH, Hamburg, Germany) was used. The effective polymer will be denoted as “G50” throughout this contribution. Properties of the polymer formulation were described elsewhere [5, 6]. Based on a parent formulation containing 4 wt% of organic constituents comprising polymer and triethanolamine (TEA) for adjusting the pH value, diluted formulations with a concentration of 2 wt% were prepared by adding demineralized water to the parent formulation.
A commercially available 4 mg/mL aqueous graphene oxide (GO) dispersion from Graphenea (San Sebastián, Spain) was used to prepare a formulation containing 0.5 mg/mL GO in 0.15 M acetate buffer. Acetic acid and sodium acetate were used in reagent grade (Sigma-Aldrich).
The sapphire substrates were coated by immersion in the formulation based on Additive G50. Two distinct sequences of immersion and water rinsing were applied: 17 h of immersion and 45 min rinsing leading to samples labelled G50-17h, and 27 h immersion and 4 h of rinsing providing samples labelled G50-27h. The GO dispersion was homogenized by applying an ultrasonic treatment for 5 min before use. After 1 h in contact with the GO dispersion, the coated substrates were rinsed gently for some seconds with water and then submerged in deionized water for 2 min; followed by blowing with air. Finally, the samples were allowed to dry and were stored under environmental conditions at room temperature.
Investigations of the surface composition were performed with X-ray photoelectron spectroscopy (XPS). XPS spectra with an information depth of around 0.01 µm were taken using a Kratos Ultra system applying excitation of photoelectrons by monochromatic Al Kα radiation within an area of approximately 0.2 mm2. The system was operated at a base pressure of 4 × 10−8 Pa, the sample neutralization was performed with low energy electrons (<5 eV). An electrostatic lens was used, the take-off angle of electrons was 0°, and the pass energy was fixed to 20 eV (or, respectively, 40 eV in case of some less concentrated constituents) in high resolution spectra and 160 eV in survey spectra. Elemental ratios were calculated based on the area of the peaks and considering relative sensitivity factors. Atomic concentrations for the detected elements are given in atomic percent, abbreviated by at%. The given at% values may be translated to weight percent values by considering the respective atomic masses. For each sample two positions were investigated. When calculating the thickness of adsorbates, a compact and homogeneous layer is assumed. The equation of d = − ln(y) × X was employed, in which d is the thickness of the layers, y is the Al2p signal intensity ratio between covered and pristine Al2O3 samples, and X is the inelastic mean free path of Al2p electrons, assumed to be 3.3 nm in an organic adsorbate layer .
The sample surface topography was analyzed using scanning force microscopy (SFM). Two distinct instrumental setups were applied. An SFM from Asylum Research was operated in the tapping mode in air. Silicon probes (model Tap150Al-G, back side of the cantilever covered with Al) with a resonance frequency of 150 kHz and a force constant of 5 N/m were used. A scanning probe microscope operated in the SFM ‘tapping mode’ in air (Digital Instruments Nanoscope III multimode with phase extender box) was employed profiting from a maximum scan range of the scanner around 100 µm. Si cantilevers (Nanosensors) with a resonance frequency around 250 kHz corresponding to force constants around 20 N/m were used. The nominal tip diameter was in the range of 10 nm. For characterizing the structures of the adsorbates, height differences, among other criteria, were evaluated. The values reported are an average of at least ten height differences measured.
The apparent contact angles were measured using a goniometer (ramé-hart instrument co., USA) by sessile drop technique, and MiliQ grade water was used as probe liquid; the volume of the drops was constant (10 μL) for each measurement at a temperature of 22 °C. The contact angle values reported are an average value of at least three separate drops on different substrate areas. The recorded images were analyzed by Drop Image ramé-hart instruments software.
Results and discussion
In this section, we will highlight and discuss characteristics of adsorbing graphene oxide from a buffered aqueous dispersion on pristine aluminum oxide surfaces and on Al2O3 surfaces covered with thin films of an amphiphilic polymer denoted as G50.
Results of XPS investigations, with surface concentrations given in atomic % (at%), for distinct pristine sapphire samples (average values are given) and for these substrates after contact with 2 wt% G50 formulation either for 17 h and then rinsed 45 min (samples G50-17h) or for 27 h and then rinsed 4 h (samples G50-27h)
1.0 ± 0.1
43.7 ± 0.5
20.3 ± 0.7
34.0 ± 0.5
G50-17h, sample 1
0.4 ± 0.1
28.6 ± 2.2
52.1 ± 5.1
0.5 ± 0.1
16.1 ± 3
G50-17h, sample 2
0.3 ± 0.1
27.0 ± 0.7
55.9 ± 2.3
0.5 ± 0.1
16 ± 1.6
G50-27h, sample 1
0.4 ± 0.1
32.8 ± 1.7
47.6 ± 3.0
0.4 ± 0.1
22.7 ± 1.4
G50-27h, sample 2
0.3 ± 0.1
29.3 ± 0.7
51.0 ± 1.6
0.4 ± 0.1
18.9 ± 0.9
Results of contact angle investigations with the contact angles given in °, as performed for pristine sapphire, a G50/sapphire film (sample G50-17h), a GO/sapphire adsorbate, a GO/G50/sapphire film, and a dried deposit of GO dispersion (intensively rinsed with water)
76.9 ± 1.1
72.2 ± 3
65.5 ± 4
53.1 ± 2.1
Dried GO dispersion
36 ± 2
Results of XPS investigations, with surface concentrations given in atomic % (at%), performed for a dried deposit of GO dispersion (intensively rinsed with water), pristine sapphire, a G50/sapphire film (sample G50-17h), and a GO/G50/sapphire film
Dried GO dispersion
0.2 ± 0.3
22.5 ± 0.4
0.1 ± 0.1
76.5 ± 0.5
0.5 ± 0.1
1.0 ± 0.1
44.2 ± 0.1
20.5 ± 0.4
0.2 ± 0.1
33.9 ± 0.1
0.3 ± 0.1
27.0 ± 0.7
55.9 ± 2.3
0.5 ± 0.1
16.0 ± 1.6
0.3 ± 0.1
30.0 ± 0.4
0.6 ± 0.1
61.6 ± 0.9
0.6 ± 0.1
7.3 ± 1.7
The deposition of graphene oxide on sapphire surfaces modified with G50 was performed from buffered GO dispersions during an immersion period of 1 h. The respective survey scans obtained from XPS investigations are shown in Fig. 2 in the spectra labelled B and C. As highlighted in Table 3, the Al2p signal intensity decreased as compared to the sample G50-17h due to material deposition from the GO dispersion. In detail, besides C- and O-containing species also Mn and S species and probably N-containing species were deposited. In addition, XPS signals with a high spectral resolution in the C1s region (not shown) reveal similar spectroscopic features for the interfactant G50 and the graphene oxide. Two dominant C1s peaks centered around 285 and 287 eV are attributed to hydrocarbonaceous species with C*–H or C*–C bonds and, respectively, to species with C*–O single bonds. On a molecular level, these ones are assigned to polyoxyalkylene moieties in G50-based polymers and to functional groups in graphene oxide, like carbon-bonded hydroxyls, phenols, ethers, or epoxy moieties [5, 28]. As a consequence, the adsorption of moieties from the GO dispersion will be inferred from evaluating the attenuation of the sapphire-related Al2p XPS signal intensity, from contact angle measurements, and from SFM investigations. Subsequently, the thus obtained findings will be described.
Finally, pristine sapphire substrates were immersed in buffered aqueous GO dispersion, and a change of surface properties was observed. The water contact angle decreased from 76.9 ± 1.1° to 65.5 ± 4°, and the surface roughness Ra inferred from SFM images increased from 0.9 to 1.8 ± 0.7 nm. For a more detailed discussion, SFM height images are shown in Fig. 4c and on a smaller scale in Fig. 5c. The surface of the GO/sapphire sample was clearly more corrugated than the surface of pristine sapphire. When comparing the surface structure of GO/sapphire adsorbates with the one of GO/G50/sapphire films, it became clear that in contrast to the latter one the GO/sapphire sample did not manifest particulate adsorbates with a particle width above 5 µm, and especially extended GO nano-sheets were not imaged when investigating more than ten surface regions.
Concerning the GO/G50/sapphire films, the SFM height images in Fig. 7c and d show regions with adjacent single GO sheets extended horizontally over the surface. This finding indicated some robustness of the nano-sheet adsorbates against rinsing with water. Concerning GO/sapphire adsorbates, in Fig. 7a a region with an Ra roughness value of 3.1 ± 0.5 nm is presented which is higher than the value of 1.8 ± 0.7 nm obtained before rinsing. The SFM phase image in Fig. 7b was acquired in the same region; and the phase contrast indicates three types of domains with distinct deformability. The domains with the lowest phase angle coincided with topographically low areas and, therefore, were attributed to the sapphire substrate. In contrast, the domains with the highest phase angle corresponded with topographically high areas which were around 6 nm higher than the substrate and dominantly were laterally extended by several 100 nm. These domains were interpreted as elevated graphene oxide adsorbates. However, they appeared rougher and more pitted than the GO sheets shown in Fig. 7c and d. Also, the material constituting the third domain appeared significantly rough and scattered; and straight edges of adsorbates or the voids in between them were hardly discerned.
Summarizing, the adsorbates found on GO/sapphire samples appeared to expose a much longer contour length of their lateral boundaries as compared to the much wider particulate adsorbates which were characteristic for GO/G50/sapphire films. Somehow, the interfactant layers seemed to hinder the random deposition of GO-based material and to favor the attachment of several micrometer wide graphene oxide sheets. A driving force for the latter aspect was discussed above based on dominating contributions from van der Waals interactions. A possible driving force for the deposition of smaller particles in case of the GO/sapphire system is highlighted subsequently, based on polar and electrostatic contributions. The pH value of the buffer solution was 4.75, GO suspensions are characterized by a negative ζ-potential at pH values around 5, and alumina and probably also sapphire surfaces are characterized by positive ζ-potentials at these pH values [30–32]. Therefore, favorable polar and electrostatic interactions may be expected between GO and sapphire surfaces. Predominantly the edges of GO sheets are regions which are rich in acidic groups [14, 33]. Therefore, the adsorption of GO sheets with a high ratio of functionalized edges may be preferred on sapphire as compared to the adsorption of GO sheets with epoxy-functionalized faces. Demonstratively, this promoting ratio will be the higher the smaller GO sheets are, and the competing effect will be lower for smaller GO sheets. In this way, the finding of smaller particulate adsorbates in case of the GO/sapphire system than in case of the GO/G50/sapphire system may be expectable. Still, possible influences of water-soluble, S- and N-containing molecular species in the GO dispersion will need to be assessed to embrace all the interactions competing with the interfactant action of the amphiphilic polymer layer.
An amphiphilic polymer was used as interface active agent (interfactant) governing interphase properties during the adsorption of graphene oxide (GO) particles. The interfactant directed the adsorption of graphene oxide (GO) nano-sheets from aqueous dispersion on sapphire surfaces in a face-to-substrate geometry, favoring the adsorption of several micrometers wide sheets to the adsorption of smaller and more hydrophilic entities. The study provides a model system illustrating how assembly of nano-particles or the attachment of polymers could be controlled due to interfactant nano-layers formed on various oxide surfaces.
YC and KR developed and worked out the protocol for graphene oxide immobilization. MS developed, performed and—with MN—adapted the formulation of the amphiphilic polymer used as an interfactant. WLC and MN adapted the methodology of interfactant layer formation for sapphire substrates. YC and MN performed and evaluated Scanning Probe Microscopy and XPS investigations. KV and YC performed and evaluated contact angle measurements. YC, WLC, KR and MN took part in setting up the experiments and in analysing and merging the obtained data. WLC, KR, MN, KB and SD contributed in the conceptual approach and in discussing the obtained data. YC and MN drafted the manuscript. All authors read and approved the final manuscript.
The authors are grateful to Dr. Hauke Brüning for fruitful discussions.
The authors declare that they have no competing interests.
Availability of data and materials
All relevant data of the article are presented in the manuscript (in tables or figures).
Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.
Open AccessThis article is distributed under the terms of the Creative Commons Attribution 4.0 International License (http://creativecommons.org/licenses/by/4.0/), which permits unrestricted use, distribution, and reproduction in any medium, provided you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made.
- Brockmann W, Hennemann OD, Kollek H, Matz C. Adhesion in bonded aluminium joints for aircraft construction. Int J Adhes Adhes. 1986;6:115–43. doi:10.1016/0143-7496(86)90016-3.View ArticleGoogle Scholar
- Cavalcanti WL, Brinkmann A, Noeske M, Buchbach S, Straetmans F, Soltau M. Anticorrosive systems-dual-purpose defenders. Eur Coat J. 2012;10:30–3.Google Scholar
- Scharf S, Noeske M, Cavalcanti WL, Schiffels P. Multi-functional, self-healing coatings for corrosion protection: materials, design and processing. In: Makhlouf AH, editor. Handbook of smart coatings for materials protection. Cambridge: Woodhead Publishing; 2014. doi:10.1533/9780857096883.1.75.Google Scholar
- Cavalcanti WL, Noeske PLM. Investigating dynamic interactions by multi-scale modelling: from theory to applications. Chem Model. 2014;11:175–200. doi:10.1039/9781782620112-00175.View ArticleGoogle Scholar
- Gonçalves LMG, Sanchez LC, Stamboroski S, Urena YRC, Cavalcanti WL, Ihde J, Noeske M, Soltau M, Brune K. Instantly investigating the adsorption of polymeric corrosion inhibitors on magnesium alloys by surface analysis under ambient conditions. J Surf Eng Mater Adv Technol. 2014;4:282–94. doi:10.4236/jsemat.2014.45032.Google Scholar
- Stamboroski S, Stachera PN, Ureña YRC, Hrycyna GH, Ribas Neto WIT, de Azambuja WK, Salz D, Ihde J, Noeske PLM, Cavalcanti WL. Implementation of diverse non-centrosymmetric layer concepts for tuning the interface activity of a magnesium alloy. Appl Adhes Sci. 2016;4:6. doi:10.1186/s40563-016-0063-7.View ArticleGoogle Scholar
- Schreiber F. Structure and growth of self-assembling monolayers. Prog Surf Sci. 2000;65:151–256. doi:10.1016/S0079-6816(00)00024-1.View ArticleGoogle Scholar
- Onclin S, Ravoo BJ, Reinhoudt DN. Engineering silicon oxide surfaces using self-assembled monolayers. Angew Chem Int Ed. 2005;44:6282–304. doi:10.1002/anie.200500633.View ArticleGoogle Scholar
- Ulman A. Formation and Structure of self-assembled monolayers. Chem Rev. 1996;96:1533–54. doi:10.1021/cr9502357.View ArticleGoogle Scholar
- Fenter P, Eberhardt A, Eisenberger P. Self-assembly of n-alkyl thiols as disulfides on Au(111). Science. 1994;266:1216–8. doi:10.1126/science.266.5188.1216.View ArticleGoogle Scholar
- He H, Klinowski J, Forster M, Lerf A. A new structural model for graphite oxide. Chem Phys Lett. 1998;287:53–6. doi:10.1016/S0009-2614(98)00144-4.View ArticleGoogle Scholar
- Zhang Y, Wu C, Guo S, Zhang J. Interactions of graphene and graphene oxide with proteins and peptides. Nanotechnol Rev. 2013;2:27–45. doi:10.1515/ntrev-2012-0078.Google Scholar
- Palma CA, Samorì P. Blueprinting macromolecular electronics. Nat Chem. 2011;3:431–6. doi:10.1038/nchem.1043.View ArticleGoogle Scholar
- Wang F, Liu J. Evaporation induced wrinkling of graphene oxide at the nanoparticle interface. Nanoscale. 2015;7:919–23. doi:10.1039/c4nr05832a.View ArticleGoogle Scholar
- Deng S, Berry V. Wrinkled, rippled and crumpled graphene: an overview of formation mechanism, electronic properties, and applications. Mater Today. 2016;19:197–212. doi:10.1016/j.mattod.2015.10.002.View ArticleGoogle Scholar
- Chen PY, Sodhi J, Qiu Y, Valentin TM, Steinberg RS, Wang Z, Hurt RH, Wong IY. Multiscale graphene topographies programmed by sequential mechanical deformation. Adv Mater. 2016;28:3564–71. doi:10.1002/adma.201506194.View ArticleGoogle Scholar
- Zou F, Zhou H, Jeong DY, Kwon J, Eom SU, Park TJ, Hong SW, Lee J. Wrinkled surface-mediated antibacterial activity of graphene oxide nanosheets. ACS Appl Mater Interfaces. 2017;9:1343–51. doi:10.1021/acsami.6b15085.View ArticleGoogle Scholar
- Su PG, Chiou CF. Electrical and humidity-sensing properties of reduced graphene oxide thin film fabricated by layer-by-layer with covalent anchoring on flexible substrate. Sensors Actuators B. 2014;200:9–18. doi:10.1016/j.snb.2014.04.035.View ArticleGoogle Scholar
- Zhang D, Tong J, Xia B, Xue Q. Ultrahigh performance humidity sensor based on layer-by-layer self-assembly of graphene oxide/polyelectrolyte nanocomposite film. Sensors Actuators B. 2014;203:263–70. doi:10.1016/j.snb.2014.06.116.View ArticleGoogle Scholar
- Wang X, Zhi L, Müllen K. Transparent, conductive graphene electrodes for dye-sensitized solar cells. Nano Lett. 2008;8:323–7. doi:10.1021/nl072838r.View ArticleGoogle Scholar
- Ou J, Wang J, Liu S, Mu B, Ren J, Wang H, Yang S. Tribology study of reduced graphene oxide sheets on silicon substrate synthesized via covalent assembly. Langmuir. 2010;26:15830–6. doi:10.1021/la102862d.View ArticleGoogle Scholar
- Esplandiu MJ, Noeske PLM. XPS investigations on the interactions of 1,6-hexanedithiol/Au(111) layers with metallic and ionic silver species. Appl Surf Sci. 2002;199:166–82. doi:10.1016/S0169-4332(02)00608-6.View ArticleGoogle Scholar
- Zhang D, Wang Y, Gan Y. Characterization of critically cleaned sapphire single-crystal substrates by atomic force microscopy, XPS and contact angle measurements. Appl Surf Sci. 2013;274:405–17. doi:10.1016/j.apsusc.2012.12.143.View ArticleGoogle Scholar
- González-Martín ML, Labajos-Broncano L, Jańczuk B, Bruque JM. Wettability and surface free energy of zirconia ceramics and their constituents. J Mater Sci. 1999;34:5923–6. doi:10.1023/A:1004767914895.View ArticleGoogle Scholar
- Witek G, Noeske M, Mestl G, Shaikhutdinov SK, Behm RJ. Interaction of platinum colloids with single crystalline oxide and graphite substrates: a combined AFM, STM and XPS study. Catal Lett. 1996;37:35–9. doi:10.1007/BF00813516.View ArticleGoogle Scholar
- Dai J, Wang G, Ma L. Study on the surface energies and dispersibility of graphene oxide and its derivatives. J Mater Sci. 2015;50:3895–907. doi:10.1007/s10853-015-8934-z.View ArticleGoogle Scholar
- Wang S, Zhang Y, Abidi N, Cabrales L. Wettability and surface free energy of graphene films. Langmuir. 2009;25:11078–81. doi:10.1021/la901402f.View ArticleGoogle Scholar
- Larciprete R, Fabris S, Sun T, Lacovig P, Baraldi A, Lizzit S. Dual path mechanism in the thermal reduction of graphene oxide. J Am Chem Soc. 2011;133:17315–21. doi:10.1021/ja205168x.View ArticleGoogle Scholar
- Spyrou K, Rudolf P. An introduction to graphene. In: Georgakilas V, editor. Functionalization of graphene. New York: Wiley; 2014. doi:10.1002/9783527672790.ch1.Google Scholar
- Corrales Ureña YR, Wittig L, Vieira Nascimento M, Faccioni JL, Noronha Lisboa Filho P, Rischka K. Influences of the pH on the adsorption properties of an antimicrobial peptide on titanium surfaces. Appl Adhes Sci. 2015;3:7. doi:10.1186/s40563-015-0032-6.View ArticleGoogle Scholar
- Lei Z, Christov N, Zhao XS. Intercalation of mesoporous carbon spheres between reduced graphene oxide sheets for preparing high-rate supercapacitor electrodes. Energy Environ Sci. 2011;4:1866–73. doi:10.1039/c1ee01094h.View ArticleGoogle Scholar
- Franks GV, Meagher L. The isoelectric points of sapphire crystals and alpha-alumina powder. Colloids Surf A: Physicochem Eng Asp. 2003;214:99–110. doi:10.1016/S0927-7757(02)00366-7.View ArticleGoogle Scholar
- Shen X, Lin X, Yousefi N, Jia J, Kim JK. Wrinkling in graphene sheets and graphene oxide papers. Carbon. 2014;66:84–92. doi:10.1016/j.carbon.2013.08.046.View ArticleGoogle Scholar