Applied Surface Science 315 (2014) 516–522 Contents lists available at ScienceDirect Applied Surface Science journal homepage: www.elsevier.com/locate/apsusc Influence of different solvents on the morphology of APTMS-modified silicon surfaces G. Jakša a , B. Štefane b , J. Kovač a,∗ a b Jožef Stefan Institute, Jamova 39, SI-1000 Ljubljana, Slovenia Faculty of Chemistry and Chemical Technology, Aškerčeva 5, SI-1000 Ljubljana, Slovenia a r t i c l e i n f o Article history: Received 23 December 2013 Received in revised form 28 April 2014 Accepted 23 May 2014 Available online 2 June 2014 Keywords: APTMS Aminosilane, Silicon Solvents XPS AFM a b s t r a c t In this study 3-aminopropyltrimethoxysilane (APTMS) was used for the modification of single-crystal silicon wafers (1 1 1). We deposited the self-assembled layers from a solution of APTMS in five solvents with different polarities under various reaction conditions. The influence of the different solvents on the morphology of the modified surfaces was studied, since the possible heterogeneity may significantly influence the application of such surfaces. The surface composition and the chemical bonding were characterized by X-ray photoelectron spectroscopy and the morphology of the modified surfaces was investigated using atomic force microscopy and scanning electron microscopy. Our results show that the amount of coatings and the morphology of the modified surface strongly depend on the type of solvent. Silanization carried out in acetonitrile and toluene leads to the formation of a rough surface with a large density of APTMS polymerized molecules in the form of islands. The surfaces modified in N,N-dimethylformamide were smoother, with a lower density of APTMS islands. When using acetone and ethanol as a solvent we prepared a smooth, thin, modified surface, with a very low density of the APTMS islands. We discuss the influence of the polarity/nature of the solvents on the morphology of the modified surfaces. © 2014 Elsevier B.V. All rights reserved. 1. Introduction Aminosilanes are used for surface modification and adhesion promotion. They have the ability to form a durable bond between organic and inorganic materials. A surface modified with aminosilanes has many applications: it can be used in chromatography [1], as a biosensor (immobilization of DNA, proteins, etc.) [2–5], in medicine [6], for attaching metal nanoparticles [7], for the detection of specific gases [8] and explosives [9,10], etc. The general formula for organosilanes is R Si X3 , where X is a hydrolysable group and R is a non-hydrolyzable organic substituent with the desired functionality. A reactive silanol group (formed by the hydrolysis of the hydrolysable group) can condense with another silanol group (a silanol group of the surface or a silanol group from another organosilane molecule) and form siloxane linkages [1,11,12]. There are many studies on optimizing silanization conditions: silanization with different aminosilanes [13–15], different aminosilane concentrations [16], the temperature of deposition [17,18], the time of silanization [16,17], the drying/curing ∗ Corresponding author. Tel.: +386 1 477 3403. E-mail address: janez.kovac@ijs.si (J. Kovač). http://dx.doi.org/10.1016/j.apsusc.2014.05.157 0169-4332/© 2014 Elsevier B.V. All rights reserved. conditions [12,16,19], the wetting behaviour [20] the presence of water [16], the type of solvent [21], etc. The 3-aminopropyltrimethoxysilane (APTMS) used in our study is one of the most commonly used aminosilanes. The APTMS molecule has three methoxy groups and is capable of polymerization in the presence of water [13]. Water can be added in solution, it may be present on the substrate surface, or it may come from the atmosphere. The presence of water can give rise to a number of possible surface structures: the covalent attachment of molecules, horizontal polymerization and the formation of oligomers/polymers of silanes in solution, which can also attach to the surface [14,15]. In general, it was believed that the aminosilanemodified silicon surface is homogeneous, but this is not always the case. A possible heterogeneity in the surface morphology and the chemistry may be present, and it may significantly influence the application of modified surfaces. Therefore, the aim of our study was to investigate the influence of different solvents on the APTMS modification of Si wafers. In our previous study we showed that the number of polymerized molecules and the layer thickness depend on the number of aminosilane bonding sites [14]. Among the published studies in this field we found only one study on SiO2 silanization with APTES molecules carried out using different solvents, performed by Vandenberg et al. [21]. They studied the water stability of prepared aminosilane layers, but did not include a study G. Jakša et al. / Applied Surface Science 315 (2014) 516–522 Fig. 1. Chemical structure of (3-aminopropyl)-trimethoxysilane. of the influence on the morphology of the modified surfaces. In the majority of published studies the authors modified the surface in a different solvent and then they focused on a particular application property. Since the morphology of the modified surface greatly depends on the solvent, it is important to find the right conditions for the intended use. The most widely used solvent for silanization is toluene [17,22,23]. However, silanization can also be performed with bicyclohexyl [24], acetone [25], water [12] or a mixture of a few solvents [26–28]. Because of the polar nature of the APTMS molecule, we expected better solubility in polar solvents. In the presence of non-polar solvents the APTMS molecules tend to form polymer structures. In this study we used five solvents with different polarities. We carried out the silanization in a non-polar solvent (toluene), polar aprotic solvents (acetone, N,N-dimethylformamide and acetonitrile) and a polar protic solvent (ethanol) for various deposition times and temperatures. Our results show that with the use of the appropriate solvent we can significantly influence the morphology of the modified surface and consequently its adhesion/adsorption properties. In our previous study we showed that with APTMS molecules the modified surface of MEMS (micro-electromechanical systems) can be used for the detection of explosive gases [29]. For the best response of the sensor (selectivity, rapid response, reversibility, etc.) it is essential to understand the modification parameters. 2. Materials and methods 2.1. Materials Silicon wafers (1 1 1 orientation, resistivity 10 cm), polished on one side, were used as a substrate for the chemical modifications. The 3-aminopropyltrimethoxysilane (Fig. 1) was obtained from Sigma–Aldrich and was used as received. The solvents were purchased from Sigma–Aldrich and were of pro-analysis grade. The solvents were dried prior to use in accordance with standard procedures [30]. The toluene was dried using sodium and distilled afterwards. Ethanol absolute (≥99.8%) was dried using CaH2 and distilled afterwards. Acetone puriss was dried over CaSO4 and distilled before use. Acetonitrile (HPLC grade) was dried using CaH2 (24 h) and filtered before use over a 0.2-m filter. The N,N-dimethylformamide (anhydrous) was stored, before use, over molecular sieves (H2 O ≤ 0.005%). 2.2. Preparation/modification of the silicon wafers The silicon wafers were cut into suitable sizes (approximately 1 cm × 1 cm) and ultrasonically cleaned for 10 min in acetone to remove any organic contamination. After cleaning the native oxide 517 layer was reduced from the silicon with dilute HF (HF:deionized water = 1:10) for 2 min, followed by a deionized water rinse, streamed with nitrogen and dried in an oven at 100 ◦ C for 30 min. The reduced silicon wafers were then immediately oxidized in a controlled manner using an oxygen plasma (1 min, p = 50 Pa, P = 200 W). The modification of the freshly cleaned wafers was carried out in a 3-mM solution of 3-aminopropyltrimethoxysilane (APTMS) in an anhydrous solvent. The silanization reaction took place in a closed Schlenk flask for a specific time (1, 2 and 6 h) at 25 ◦ C and at higher temperature: (a) 70 ◦ C (toluene, ethanol, acetonitrile and N,N-dimethylformamide) or (b) 50 ◦ C (acetone). The Schlenk flask was purged with nitrogen prior to and during the silanization. After completion of the silanization step, the wafers were rinsed with toluene (2×), a mixture of toluene and methanol = 1:1 (2×), methanol (2×) and dried at 80 ◦ C for 15 min in a clean oven, to remove the physisorbed APTMS molecules and any traces of solvent from the surface. The characterization was carried out immediately upon cooling and the data were averaged from three independent measurements. 2.3. Surface characterization The surface topography and surface roughness were investigated with an atomic force microscope (AFM), model Solver Pro, produced by the NT-MDT company. An oscillating semi-contact mode with Si tips was used for the surface imaging over the range 1 m × 1 m–10 m × 10 m. The mean surface roughness Ra was calculated after the subtraction of the proper background from the image. The chemical composition of the surfaces was determined by Xray photoelectron spectroscopy (XPS). This analysis was performed with a TFA XPS spectrometer, produced by Physical Electronics Inc., equipped with a monochromated Al-K␣ X-ray source (1486.6 eV, energy resolution ∼0.6 eV), under ultra-high vacuum (10−7 Pa). The analysis area was 0.4 mm in diameter and the signal during the XPS analysis came from a 6-nm-thick surface layer. During the analysis, both survey and high-resolution spectra were recorded. In the survey spectrum, the elements that were present were identified and their concentrations were calculated by dividing the peak intensities by the relative sensitivity factors provided by the XPS spectrometer manufacturer using a model of the homogenous distribution of the elements in a matrix [31]. Each sample was analyzed at two different points and the average composition was calculated. In addition to the wide-energy-range spectra, the high-energy-resolution spectra of the characteristic peaks of the elements Si 2p, C 1s, O 1s and N 1s were recorded over a narrow energy range. From the shape and the shift of the energy of the XPS spectra, the chemical bonding of the surface elements was inferred. The XPS spectra were processed with the software MultiPak. All the components were referenced according to the C C/C H component in the C 1s core level at a binding energy of 284.8 eV. The morphology of the modified surfaces was analyzed with a scanning electron microscope (SEM). The SEM analysis was carried out with a FE-SEM Zeiss ULTRA plus scanning electron microscope. The microscopy was performed with a 5-kV accelerating voltage using a standard Everhart–Thornley SE detector. 3. Results The modified surfaces with APTMS molecules were characterized using the AFM, SEM and XPS techniques to determine the morphology, roughness, surface composition and chemical bonding of the APTMS film. Fig. 2 shows the topography of the APTMS coatings obtained after 3 h of silanization at 25 ◦ C from five different solvents. From 518 G. Jakša et al. / Applied Surface Science 315 (2014) 516–522 Fig. 2. AFM images (2 m × 2 m) of Si wafer (a) and APTMS molecules on Si wafer after 3 h of deposition at 25 ◦ C from: ethanol (b), acetone (c), N,N-dimethylformamide (d), toluene (e) and acetonitrile (f). the AFM images of the modified surfaces we can observe differences in the topography. The surfaces modified with various solvents contain different numbers of bright spots, which are polymerized aminosilane molecules in the form of islands. In our previous study we showed that the polymerization process took place already in solution and not directly on the surface [14]. The smaller islands are from 1 to 2 nm in height and around 20 nm in width. The bigger islands, as a result of increased polymerization, are from 4 to 10 nm Table 1 Mean surface roughness (Ra ), density of APTMS islands, from XPS calculated total thickness (nm) of Si-oxide + silane layer and thickness of silane layer on modified Si surfaces after 3 h of deposition at 25 ◦ C in different solvents: ethanol, acetone, N,N-dimethylformamide (DMF), toluene and acetonitrile. Ra [nm] Number of islands [m2 ] Thickness [nm] (SiO2 + silane) Thickness [nm] (silane layer) Si wafer Ethanol Acetone DMF Toluene Acetonitrile 0.09 – 1.4 ± 0.2 – 0.16 27 ± 3 1.8 ± 0.2 0.4 ± 0.2 0.15 23 ± 3 2.3 ± 0.2 0.9 ± 0.2 0.14 24 ± 3 2.2 ± 0.2 0.8 ± 0.2 0.29 63 ± 6 2.6 ± 0.2 1.2 ± 0.2 0.43 110 ± 10 3.2 ± 0.2 1.8 ± 0.2 G. Jakša et al. / Applied Surface Science 315 (2014) 516–522 519 Table 3 Nitrogen concentration (atomic %) on APTMS surfaces modified from different solvents at different times and temperatures. Higher temperatures are related to 50 ◦ C in the case of acetone and 70 ◦ C in the case of ethanol, N,N-dimethylformamide (DMF), toluene and acetonitrile. Fig. 3. Scanning electron microscopy images of Si-oxide surfaces modified with APTMS molecules. (a) 3 h of deposition from acetone at 25 ◦ C and (b) 3 h of deposition from toluene at 25 ◦ C. in height and around 50 nm in width. The mean surface roughness and the density of the islands are given in Table 1, for all five solvents. We performed SEM analyses to understand the surface morphology of a larger area of the samples (50 m and more). The SEM images of the modified surfaces after 3 h of deposition from acetone and toluene at 25 ◦ C are shown in Fig. 3. We investigated the surface composition and the chemical bonding at the modified surfaces using the XPS technique. Due to the small size of the polymerized islands present on the surface we did not expect that the XPS technique would directly reveal this type of heterogeneity, since only a laterally averaged composition can be obtained from the XPS. The acquired XPS spectra of the uncoated oxidized silicon wafer showed peaks of carbon, oxygen and silicon. The carbon signal on the oxidized wafer is Ethanol Acetone DMF Toluene Acetonitrile 25 ◦ C N (at.%) at 1 h N (at.%) at 3 h N (at.%) at 6 h 1.6 1.8 2.2 2.1 2.3 2.3 1.3 2.1 3.3 3.0 3.6 4.8 2.1 7.3 11.5 Higher T N (at.%) at 1 h N (at.%) at 3 h N (at.%) at 6 h 1.8 1.7 1.7 1.8 2.2 2.4 2.6 4.3 4.0 4.5 9.3 9.7 10.4 10.9 11.1 related to the carbon from the contamination layer. The XPS spectra of the modified Si wafers contain, in addition to carbon, oxygen and silicon related peaks, also nitrogen peak, which is related to the amino group from the APTMS molecules. From the intensities of these peaks we calculated the C, O, Si and N concentrations (Table 2) in the model of homogeneous elemental distribution. As it is expected that the layered structure is formed on modified surfaces, the results for the concentration have limited accuracy and can only be used for a relative comparison among the different samples. Since the nitrogen signal is the most relevant information of the APTMS molecules present on the surface, we represent in Table 3 the concentration of N on the modified surfaces for various solvents after different silanization times and for two different temperatures. We also studied high-energy-resolution XPS spectra of the modified surfaces. The C 1s signal is composed of three different components. These components are related to different types of carbon-atom bonds on the APTMS molecule. The component at a binding energy of 284.8 eV corresponds to C C and/or C H bonds; the component at binding energies of 286.3 eV corresponds to C O bonds; and the component at 287.9 eV is related to O C O and C O bonds. Due to the APTMS polymerization and the different types of interaction between the APTMS molecules and the oxidized silicon wafer [14], the high-energy-resolution N 1s spectra are composed of two different components: the component at a binding energy of 399.2 eV corresponds to NH2 bonds and the component at a binding energy of 401.0 eV corresponds to NH3 + type of bonds. The representative C 1s and N 1s spectra are also given in Ref. [14]. Typical high-energy-resolution Si 2p XPS spectra obtained after the silanization are shown in Fig. 4 a, where different components can be recognized. At binding energies of 99.3 eV (Si 2p3/2 ) and 99.9 eV (Si 2p1/2 ) is the signal from the bulk silicon wafer beneath the oxide layer. The silicon signal from the Si oxide layer and the aminosilanes is located at higher binding energies. The signal at 102.2 eV corresponds to the aminosilane on the silicon oxide and the signal at 103.0 eV corresponds to the silicon oxide. Fig. 4b shows the Si 2p spectra, one above the other (reference sample and Table 2 Surface composition (atomic %) on the Si wafer after silanization from different solvents. 3 h of deposition at 25 ◦ C and 3 h of deposition at 50 ◦ C (acetone) and 70 ◦ C (ethanol, N,N-dimethylformamide (DMF), toluene and acetonitrile) (higher T). Temp Element Si wafer Ethanol Acetone DMF Toluene Acetonitrile 25 ◦ C C O Si N 10.8 49.6 39.6 – 25.9 38.9 33.4 1.8 17.0 46.6 34.1 2.3 17.4 45.8 34.7 2.1 35.8 34.8 25.8 3.6 43.8 27.2 21.7 7.3 Higher T C O Si N 10.8 49.6 39.6 – 23.1 39.1 36.1 1.7 21.2 46.5 30.1 2.2 34.7 32.7 28.3 4.3 53.5 21.3 15.9 9.3 57.8 18.6 12.7 10.9 520 G. Jakša et al. / Applied Surface Science 315 (2014) 516–522 a 1000 900 b SiO2 silane Si 2p Si-bulk Si 2p APTMS, acetonitrile Si-bulk (2p3/2, 2p1/2) Intensity (a.u.) 700 600 500 SiO2 400 300 silane on SiO2 Normalized Intensity 800 APTMS, toluene APTMS, DMF APTMS, acetone APTMS, ethanol 200 Oxidized Si 100 0110 108 106 104 102 100 98 96 94 Binding Energy (eV) 110 108 106 104 102 100 98 96 94 Binding Energy (eV) Fig. 4. Typical high-energy-resolution Si 2p spectra (a), and stack plot of Si 2p spectra obtained after 3 h of silanization from different solvents at higher temperatures (b) (50 ◦ C in the case of acetone and 70 ◦ C in the case of ethanol, N,N-dimethylformamide (DMF), toluene and acetonitrile). modified surfaces in different solvents, 3 h deposition time at elevated temperatures). From the XPS data we also estimated the thickness of the silane layer. In the Si 2p spectra we estimated the relative thickness of the silicon oxide layer and the silane layer, comparing the intensities of the bulk Si components and the total Si O components at 102–103 eV, which represents the Si atoms involved at the SiO2 interface and the Si atoms from the silane overlayer. For the thickness calculation we used equation d = L cos()ln(1 + R/Ro ), where L is the attenuation length of the electrons in the Si-oxide overlayer (3.485 nm), is the angle of emission of the electrons (15◦ , 45◦ , 75◦ ), R is the measured ratio of the oxide- and substrate-measured intensities and Ro is the parameter 0.9329, as was proposed in Ref. [32]. The thickness of 1.4 ± 0.2 nm obtained on the uncoated wafer is related to the Si-oxide layer formed after the oxygen plasma treatment of the Si wafers. For silane-coated samples with different solvents we first calculated the total thickness of the silane and oxide layers and in the second step we subtracted from the total thickness the thickness of the initial silicon oxide layer. In this way we estimated the thickness of the pure silane layers, which is given in Table 1. 4. Discussion The AFM, XPS and SEM results show significant differences in the morphology and the composition of the APTMS-modified Si surface with respect to the solvent used for the modification. Therefore, we divided all five studied solvents with different polarities into two groups. Ethanol, acetone and N,N-dimethylformamide solvents lead to the formation of a relatively smooth, homogenous APTMS film with a low density of islands. In contrast, toluene and acetonitrile form a rough layer, with a large number of polymerized islands. 4.1. Solvents forming smooth APTMS films AFM images of the modified surfaces obtained from acetone, N,N-dimethylformamide and ethanol are shown in Fig. 2b–d. We observed a slightly increased mean surface roughness compared to the reference Si wafer (Table 1). The surfaces are relatively uniform with a low density of islands (23–27 islands/m2 ). In ethanol and acetone applying longer deposition times and elevated temperatures (70 ◦ C for ethanol and 50 ◦ C for acetone, 6 h of deposition), similar modified surfaces were formed. The surfaces were slightly rougher (Ra ∼ 0.3 nm) but the islands remain approximately the same size, so there is no further polymerization observed. The AFM images of the surface modified in N,N-dimethylformamide, for longer deposition times and at elevated temperatures, show a slightly rougher surface (Ra ∼ 0.5 nm) compared to the ethanol and acetone and a denser distribution of islands. SEM images of the modified surfaces (3 h at 25 ◦ C) with ethanol and N,N-dimethylformamide were very similar to those with the acetone (Fig. 3a). The surfaces were relatively flat and no large, polymerized APTMS islands were found. The XPS results (Table 2) of the surface composition show an increased concentration of C and N, which confirms the successful APTMS bonding to the silicon surface after the silanization process for all three solvents. At this point it should be noted that for longer deposition times the concentration of nitrogen on the surface does not increase significantly. Aminosilane layers are not so thick and the polymerization of the APTMS molecules is lower, compared to acetonitrile and toluene (higher N concentrations, rougher surface, increased polymerization). Similar behaviour was observed at higher temperatures. During higher temperature deposition, the nitrogen concentration slightly increased with time in the case of acetone and N,N-dimethylformamide, but it remained constant in the case of ethanol (Table 3). This observation can be explained in terms of the solvents nature/polarity. Ethanol is a polar protic solvent with OH groups. This solvent can solvolyze the Si O Si bonds (like hydrolysis in the case of water). In the case of higher concentrations of ethanol, the solvolysis of the Si O Si linkages is much faster than the competitive condensation reaction (from 2 × ( Si OH) to Si O Si bonds), which leads to the lower polymerization. It is known that in water (also a polar protic solvent) aminosilane layers spontaneously hydrolysed to a mono-layer [13,21]. This observation suggests that a similar process is taking place in ethanol as a solvent and that the estimated thickness of the formed APTMS film is about one mono-layer. The other four solvents are different in terms of structure/nature and could not solvolyse the molecules in this way. From high-energy-resolution Si 2p XPS spectra (Fig. 4b) we estimated that the APTMS coatings prepared from acetone, ethanol and N,N-dimethylformamide are relatively thin since a signal from the Si bulk at 99.9 eV is still present in the XPS spectra. We assume this from the fact that the XPS sampling depth is around 6 nm. G. Jakša et al. / Applied Surface Science 315 (2014) 516–522 4.2. Solvents forming rough APTMS films Using toluene and acetonitrile as the media for the silanization leads to the formation of a rough layer with a large number of polymerized islands (Fig. 2). The obtained surfaces were rougher (Table 1) with higher density of islands compared to the Si wafer and the modified surface from acetone, ethanol and N,Ndimethylformamide (Fig. 2a–d). By using toluene and acetonitrile for longer deposition times (6 h, AFM results not shown here) we observed an increased density of islands and rougher surfaces (Ra ∼ 0.6 nm) compared to the 3 h deposition time. Modification using both mentioned solvents at elevated temperature (70 ◦ C, 6 h) produces an even denser distribution of islands (Ra ∼ 1.5 nm). Some of the formed islands also measure around 500 nm in diameter. SEM analyses confirmed that modification with toluene (Fig. 3b) and acetonitrile under the same preparation conditions (3 h at 25 ◦ C) leads to the formation of strongly polymerized surfaces. At longer deposition times (6 h) and at higher deposition temperatures (70 ◦ C) we observed further polymerization of the molecules on the surface. The distribution of polymerized APTMS molecules is dense and some islands are around 1 m wide. The XPS results are in agreement with the morphology analyses showing higher atomic concentrations of carbon and nitrogen on the investigated surfaces. A modified silicon surface using toluene and acetonitrile solvents with APTMS contains more carbon and nitrogen than a surface modified with the acetone, ethanol and N,N-dimethylformamide solvents (Table 2). For longer silanization times the amount of nitrogen on the surface strongly increased (Table 3). This is related to the increased coverage of the APTMS coating and more aminosilanes on the surface. Together with the results of the AFM and SEM imaging we concluded that most of the aminosilanes are in the form of polymerized islands. The deposition carried out at higher temperatures (70 ◦ C) leads to even stronger polymerization and thicker coatings compared to that at 25 ◦ C. In the case of toluene and acetonitrile the nitrogen concentration is higher (two times higher at 25 ◦ C and five times higher at 70 ◦ C) compared to the ethanol. The thickness of the APTMS coating is reflected in the shape of the Si 2p XPS spectra (Fig. 4b). In the case of the toluene the signal from the Si bulk at 99 eV is greatly reduced and has almost disappeared. The signal from the Si bulk completely disappeared when using acetonitrile as a solvent. This confirms the thick aminosilane coatings on the oxidized Si wafer for the silanization carried out in acetonitrile and toluene. 5. Conclusions In this study we prepared self-assembled APTMS films on silicon oxide surfaces from five different solvents under various reaction conditions. Using the analytical techniques XPS, AFM and SEM we investigated the surface composition, the chemical bonding, the morphology and the roughness of the SiO2 surface before and after silanization. Our results show that the composition and the morphology of the surfaces modified in various solvents were not the same in the morphology. Our results show that ethanol and acetone as solvents form thin APTMS coatings with a low density of islands containing the polymerized molecules, even for longer deposition times and higher deposition temperatures. The thickness of the aminosilane layer on that modified surface is about one monolayer, probably due to a spontaneous solvolysis. The APTMS coatings prepared using the N,N-dimethylformamide solvent are slightly thicker, particularly for prolonged deposition times and higher deposition temperatures. The deposition of APTMS from acetonitrile and toluene leads to the formation of thick coatings with a high density of islands containing polymerized APTMS molecules. Acetonitrile as a solvent produces a slightly thicker coating than 521 toluene. We concluded that the modification of the silicon surface by APTMS aminosilane molecules strongly depends on the type of solvent. In the case of deposition in ethanol (polar protic solvent), spontaneous solvolysis of the polymerized molecules is present and a primarily smooth and thin modified surface is obtained. The choice of solvent should be optimized for the particular application of the modified silicon surfaces, since in some cases a monolayer is desired, but in the other cases a polymerized morphology on the surface can be beneficial. Acknowledgements The authors would like to thank Tatjana Filipič and Prof. Dr. Marjan Marinšek for help during the XPS, AFM and SEM measurements. The work was supported by the Slovenian Research Agency (programme P2-0082, projects J2-4287 and J7-5497). References [1] E.F. Vansant, P. Van Der Voort, K.C. Vrancken, Characterization and chemical modification of the silica surface, Elsevier, Amsterdam, 1995. [2] R.A. Shircliff, P. Stradins, H. Moutinho, J. Fennell, M.L. Ghirardi, S.W. Cowley, H.M. Branz, I.T. Martin, Angle-resolved XPS analysis and characterization of monolayer and multilayer silane films for DNA coupling to silica, Langmuir 29 (2013) 4057–4067. [3] L.A. Chrisely, G.U. Lee, C.E. O’Ferrall, Covalent attachment of synthetic DNA to self-assembled monolayer films, Nucleic Acids Res. 24 (1996) 3031–3039. [4] C. Kneuer, M. Sameti, E.G. Haltner, T. Schiestel, H. Schirra, H. Schmidt, C.-M. Lehr, Silica nanoparticles modified with aminosilanes as carriers for plasmid DNA, Int. J. Pharm. 196 (2000) 257–261. [5] N. Keegan, G. Suarez, J.A. Spoors, P. Ortiz, H.J.C.J. McNeil, A microfabrication compatible approach to 3Dimensonal patterning of bio-molecules at bio-MEMS and biosensor surfaces, IEEE BioCAS (2009) 17–20. [6] S.P. Low, N.H. Voelcker, L.T. Canham, K.A. Williams, The biocompatibility of porous silicon in tissues of the eye, Biomaterials 30 (2009) 2873–2880. [7] C.-F. Chen, S.-D. Tzeng, M.-H. Lin, S. Gwo, Electrostatic assembly of gold colloidal nanoparticles on organosilane monolayers patterned by microcontact electrochemical conversion, Langmuir 22 (2006) 7819–7824. [8] T.H. Tran, J.-W. Lee, K. Lee, Y.D. Lee, B.-K. Ju, The gas sensing properties of single-walled carbon nanotubes deposited on an aminosilane monolayer, Sens. Actuators B: Chem. 129 (2008) 67–71. [9] L. Senesac, T.G. Thundat, Nanosensors for trace explosive detection, Mater. Today 11 (2008) 28–36. [10] Y. Engel, R. Elnathan, A. Pevzner, G. Davidi, E. Flaxer, F. Patolsky, Supersensitive detection of explosives by silicon nanowire arrays, Angew. Chem. 49 (2010) 6830–6835. [11] K. Moriguchi, S. Utagawa, Silane: chemistry applications and performance, Nova, New York, 2012. [12] E. Metwalli, D. Haines, O. Becker, S. Conzone, C.G. Pantano, Surface characterizations of mono-, di-, and tri-aminosilane treated glass substrates, J. Colloid Interface Sci. 298 (2006) 825–831. [13] M. Zhu, M.Z. Lerum, W. Chen, How to prepare reproducible, homogeneous, and hydrolytically stable aminosilane-derived layers on silica, Langmuir 28 (2011) 416–423. [14] G. Jakša, B. Štefane, J. Kovač, XPS and AFM characterization of aminosilanes with different numbers of bonding sites on a silicon wafer, Surf. Interface Anal. 45 (2013) 1709–1713. [15] E. Asenath-Smith, W. Chen, How to prevent the loss of surface functionality derived from aminosilanes, Langmuir 24 (2008) 12405–12409. [16] F. Zhang, M.P. Srinivasan, Self-assembled molecular films of aminosilanes and their immobilization capacities, Langmuir 20 (2004) 2309–2314. [17] J.A. Howarter, J.P. Youngblood, Optimization of silica silanization by 3aminopropyltriethoxysilane, Langmuir 22 (2006) 11142–11147. [18] R.M. Pasternack, S. Rivillon Amy, Y.J. Chabal, Attachment of 3(aminopropyl)triethoxysilane on silicon oxide surfaces: dependence on solution temperature, Langmuir 24 (2008) 12963–12971. [19] J. Kim, G.J. Holinga, G.A. Somorjai, Curing induced structural reorganization and enhanced reactivity of amino-terminated organic thin films on solid substrates: observations of two types of chemically and structurally unique amino groups on the surface, Langmuir 27 (2011) 5171–5175. [20] B.M. Law, A. Mukhopadhyay, J.R. Henderson, J.Y. Wang, Wetting of silicon wafers by n-alkanes, Langmuir 19 (2003) 8380–8388. [21] E.T. Vandenberg, L. Bertilsson, B. Liedberg, K. Uvdal, R. Erlandsson, H. Elwing, I. Lundstrom, Structure of 3-aminopropyl triethoxy silane on silicon oxide, J. Colloid Interface Sci. 147 (1991) 103–118. [22] L. Pasquardini, L. Lunelli, C. Potrich, L. Marocchi, S. Fiorilli, D. Vozzi, L. Vanzetti, P. Gasparini, M. Anderle, C. Pederzolli, Organo-silane coated substrates for DNA purification, Appl. Surf. Sci. 257 (2011) 10821–10827. 522 G. Jakša et al. / Applied Surface Science 315 (2014) 516–522 [23] S. Guha Thakurta, A. Subramanian, Fabrication of dense, uniform aminosilane monolayers: a platform for protein or ligand immobilization, Coll. Surf. A: Physicochem. Eng. Aspect 414 (2012) 384–392. [24] G.C. Allen, F. Sorbello, C. Altavilla, A. Castorina, E. Ciliberto, Macro-, microand nano-investigations on 3-aminopropyltrimethoxysilane self-assemblymonolayers, Thin Solid Films 483 (2005) 306–311. [25] J. Böhmler, L. Ploux, V. Ball, K. Anselme, A. Ponche, Necessity of a thorough characterization of functionalized silicon wafers before biointerface studies, J. Phys. Chem. C 115 (2011) 11102–11111. [26] P.A. Heiney, K. Grüneberg, J. Fang, C. Dulcey, R. Shashidhar, Structure and growth of chromophore-functionalized (3-aminopropyl)triethoxysilane selfassembled on silicon, Langmuir 16 (2000) 2651–2657. [27] Z.H. Wang, G. Jin, Silicon surface modification with a mixed silanes layer to immobilize proteins for biosensor with imaging ellipsometry, Colloids Surf. B: Biointerfaces 34 (2004) 173–177. [28] N. Rathor, S. Panda, Aminosilane densities on nanotextured silicon, Mater. Sci. Eng.: C 29 (2009) 2340–2345. [29] D. Strle, B. Stefane, U. Nahtigal, E. Zupanic, F. Pozgan, I. Kvasic, M. Macek, J. Trontelj, I. Musevic, Surface-functionalized COMB capacitive sensors and CMOS electronics for vapor trace detection of explosives, IEEE Sens. J. 12 (2012) 1048–1057. [30] W.L.F. Armarego, C.L.L. Chai, Purification of Laboratory Chemicals, 5th ed., Elsevier, 2003. [31] J.F. Moulder, W.F. Stickle, P.E. Sobol, K.D. Bomben, Handbook of X-ray Photoelectron Spectroscopy, Physical Electronics Inc., Eden Praire, MN, 1995. [32] M.P. Seah, S.J. Spencer, Ultrathin SiO2 on Si. VII. Angular accuracy in XPS and an accurate attenuation length, Surf. Interface Anal. 37 (2005) 731–736.