Existence, release, and antibacterial actions of silver nanoparticles on Ag–PIII TiO2 films with different nanotopographies
Jinhua Li, Yuqin Qiao, Hongqin Zhu, Fanhao Meng, Xuanyong Liu
State Key Laboratory of High Performance Ceramics and Superfine Microstructure, Shanghai Institute of Ceramics, Chinese Academy of Sciences, Shanghai, People’s Republic of China
Abstract: Nanotopographical TiO2 films (including nanorod, nanotip, and nanowire topographies) were successfully fabricated on the metallic Ti surface via hydrothermal treatment and then underwent Ag plasma immersion ion implantation to incorporate Ag with TiO2. The surface morphology, phase component, and chemical composition before and after Ag–PIII were characterized. In view of the potential clinical applications, both Gram-negative Escherichia coli and Gram-positive Staphylococcus aureus were used to estimate their antimicrobial effect. The nanostructured TiO2 films on a Ti surface exhibit a better bacteriostatic effect on both microbes compared to the pristine Ti. The nanotopographies of the TiO2 films affect the nucleation, growth, and distribution of Ag nanoparticles in the films during Ag–PIII process. The Ag nanoparticles are completely embedded into the nanorod film while partially exposed out of the nanotip and nanowire films, which account for the significant differences in the release behaviors of Ag ions in vitro. However, no significant difference exists in their antimicrobial activity against both microbes. The antimicrobial actions of the Ag@TiO2 system described here consist of two methods – the contact-killing action and the release-killing action. Nevertheless, based on the observed results, the contact-killing action should be regarded as the main method to destroy microbes for all the Ag plasma-modified TiO2 nanofilms. This study provides insight to optimize the surface design of Ti-based implants to acquire more effective antimicrobial surfaces to meet clinical applications.
Keywords: silver, nanoparticles, titania, nanostructure, antibacterial, plasma
Nanotechnology has the powerful capability to integrate nanobionics into materials science and engineering. Hence, a great deal of interest has been paid to the investigations on nanostructured/nanofunctionalized biomaterials. The biological effects of a nanofeatured surface can be enhanced, and the clinical applications of biomedical materials can be promoted.1 It is widely accepted that, once being implanted into the human body, a range of interactions emerges at the interface of the biomaterials surface and the physiological environment. Hence, the surface of biomaterials plays a crucial role in the response of artificial implants to the physiological environment. The performance of biomedical implant devices depends predominantly on the surface features, such as surface topography, microstructure, component, and resulting properties.1
Titanium-based implants are important to reinforce the human lifespan and its quality.2 Nevertheless, bacteria tend to adhere on their surfaces and produce biofilms.3 Actually, implant-associated failures are mainly caused by bacterial infections.4,5 Once attaching upon the implants, the microbes proliferate and assemble to generate biofilms and, subsequently, trigger tissue infection.6 It is a general strategy to load antibiotics onto implant surfaces to reduce infections.4 Nowadays, however, a great deal of attention has been paid to the antibiotic-resistant bacteria, some of which has produced intractable resistance by using existing antibiotics.7 In view of such circumstances, it is a development trend to endow implant materials/devices with self-antibacterial performance to inhibit bacterial attachment and resultant infections.8,9
TiO2 can inhibit microbe adhesion due to its excellent photocatalytic activity.10–12 Nevertheless, this function will inevitably attenuate in darkness, for example, in the human body.13,14 Furthermore, to cure persistent infections, it is a promising antibacterial method to damage the membrane functions of bacteria.15,16 Ag (including nanoparticle, ion, and metal) has the powerful ability to fight against a wide spectrum of bacteria and fungi, owing to its nonspecific antibacterial skill.8,17,18 In addition, the possibility that Ag-resistant microbes will come out in the future seems remote indeed over a period of time.19 It is considered that Ag nanoparticles are rather more reactive than bulk Ag metal, owing to a large reactive specific surface area. Thus, kinds of Ag nanoparticle-modified surfaces have been designed and prepared.20–22
Plasma immersion ion implantation (PIII) technology has now been extensively utilized to modify the surfaces of a variety of biomedical materials/devices and found especially suitable for the ones with complex geometry shapes, due to the non-line-of-light feature.23 The Ag–PIII method has been successfully developed for the purpose of enhancing the antibacterial ability of biomaterials and related devices to minimize infections.24 Nowadays, the Ag–PIII technique has been broadly attempted to modify polymer-based biomaterials25–27 and titanium-based biomaterials.28,29 The growth habit of the Ag nanoparticles within the TiO2 matrix obeys the classical nucleation theory when Ag plasma interacts with TiO2 film.30 The topographies of TiO2 films also influence the distribution of electric field and plasma sheath around TiO2 films.31
In the present work, nanostructured TiO2 films (including nanorod, nanotip, and nanowire topographies) were prepared on a titanium surface via hydrothermal method to obtain nanotopographies and subsequently treated by PIII procedure to incorporate with Ag nanoparticles. The effect of TiO2 nanotopographies on the growth habit of Ag nanoparticles in TiO2 films was discussed. The influence of Ag plasma-modified TiO2 nanofilms on microbes (Escherichia coli and Staphylococcus aureus) was evaluated.
Materials and methods
Preparation and modification of samples
Commercially pure titanium (Cp Ti) plates with sizes of 10×10×1 mm were ultrasonically cleaned in ethanol, deionized water, and ultrapure water three times for each. After that, they then underwent pickling in 5% weight oxalic acid solution at 100°C for 2 hours to eliminate the oxide layers and to obtain homogeneous surfaces. After that, the specimens were ultrasonically cleaned and dried in ambient atmosphere for further use. The TiO2 nanostructures on titanium surface were hydrothermally fabricated. Briefly, the pretreated Ti plates were soaked in the mixed solution of hydrogen peroxide (30% weight H2O2) and sodium hydroxide (5 M NaOH) solution in Teflon-lined reaction vessels at a designated temperature and period (Table 1). After the reaction vessels cooling down, the Ti plates were gently cleaned with fresh water, dried, followed by protonation in dilute hydrochloric acid (0.1 M HCl) for 2 hours. After that, the samples were cleaned, dried, and finally heat-treated to obtain the nanostructured surfaces on titanium. And the as-obtained samples were designated as “nanorod,” “nanotip,” and “nanowire,” respectively (Table 1).
Table 1 Experimental details for the fabrication and modification of samples
The PIII technique was used to implant Ag into the nanotopographical titanium surfaces. The implantation parameters are listed in Table 2. The cathode rod was made of pure Ag metal with a purity of 99.99% weight and diameter of 10 mm. The ultimate samples were obtained and denoted as “Ag@nanorod”, “Ag@nanotip”, and “Ag@nanowire”, respectively. The whole fabrication procedures are illustrated in Figure 1.
Table 2 Important instrumental parameters used in Ag–PIII33
The surface morphology was observed by field emission scanning electron microscopy (SEM; S-4800, Hitachi Ltd., Tokyo, Japan). The crystallinity of the films was characterized using an X-ray diffractometer (XRD; D/Max, Rigaku, Tokyo, Japan) fitted with a Cu Kα (λ=1.541 Å) source at 40 kV and 100 mA in the range of 2θ=15°–80° with a step size of 0.02°. Phase identification was performed with the help of the standard Joint Committee on Powder Diffraction Standards database. During the X-ray diffraction test, the glancing angle of the incident beam against the sample surfaces was fixed at 1°. The chemical compositions and chemical states of the sample surfaces were investigated by X-ray photoelectron spectroscopy (XPS; PHI 5802, Physical Electronics Inc, Eden Prairie, MN, USA). At the same time, the transmission electron microscope (TEM) characterization was conducted on a field-emission TEM (JEM-2100F, JEOL, Tokyo, Japan) with an accelerating voltage of 200 kV. Specimens for the characterization were scratched off the surfaces and then dispersed in ethanol using ultrasound. A droplet of the suspension was located on a holey copper grid covered with porous carbon film (Quantifoil Micro Tools GmbH, Jena, Germany).
Ag ions release
The as-prepared Ag–PIII specimens were immersed in 10 mL fresh water at 37°C for 1 day, 3 days, and 7 days, successively. At the end of each immersion period, the leaching solution was gathered, and the release amount of Ag ions was determined by using inductively coupled plasma mass spectrometry (Nu Instruments Ltd, Wrexham, UK).
Antimicrobial efficiency determination
The antimicrobial activity on the Cp Ti, nano-TiO2, and Ag–PIII samples was estimated by the microbial counting method using E. coli (E. coli, ATCC 25922; American Type Culture Collection [ATCC], Manassas, VA, USA) and S. aureus (S. aureus, ATCC 25923; American Type Culture Collection). The samples were sterilized in an autoclave at 121°C for 40 minutes. A solution containing the bacteria at a concentration of 107 colony-forming unit (CFU)/mL was introduced onto the sample to a density of 60 μL/cm2. The samples with the microbial solution were incubated at 37°C for 24 hours. The dissociated microbial solution was collected and inoculated into a standard agar culture medium. After incubation at 37°C for 24 hours, the active bacteria were counted in accordance with the National Standards of the People’s Republic of China GB/T 4789.2 protocol, and the antimicrobial ratio was calculated using the following formula,
where A is the average number of the bacteria on the control sample (CFU/sample); B is the average number of bacteria on the testing samples (CFU/sample).
In the SEM examination, a solution containing the bacteria at a concentration of 107 CFU/mL was put on the sample to a density of 60 μL/cm2, incubated at 37°C for 24 hours, fixed, and dehydrated in a series of ethanol solutions (30%, volume–volume [v/v]; 50% v/v; 75% v/v; 90% v/v, 95% v/v; and 100% v/v) for 10 minutes each sequentially, with the final dehydration conducted in absolute ethanol (twice) followed by drying in the hexamethyldisilazane ethanol solution series.
Results and discussion
Characterization of samples
Figure 2 shows the surface morphology of Ti metal plates after undergoing the corresponding treatments. Compared to the rough Cp Ti surface (Figure 2A), three different architectures were obtained by altering the experimental parameters, as given in Figure 2C, E, and G. From the visual fields of SEM at high magnification, three types of nanowire, nanotip, and nanorod topographies (Figure 2D, F, and H, respectively) were generated when metallic Ti plates reacted in the corresponding hydrothermal conditions, while the Cp Ti presented a comparatively flat morphology at high magnification (Figure 2B).
Figure 2 SEM morphology of the synthesized Cp Ti (A, B), nanowire (C, D), nanotip (E, F), and nanorod (G, H) at low- and high-magnification, respectively.
From the XPS full spectra acquired in Figure 3A, it can be seen that only Ti and O elements existed on the surfaces of the nanorod, nanotip, and nanowire samples. From Figure 3B, the XPS high-resolution spectra of Ti 2p contain two peaks centered at around 464.56 eV and 458.83 eV, which correspond to the typical binding energy for the Ti 2p1/2 and Ti 2p3/2 in TiO2, respectively.32,33 The peaks located at around 530.47 eV in Figure 3C are allotted to the O 1s in TiO2.34 In addition to the chemical components, it is also essential to identify the crystal structures of TiO2 (including amorphous, anatase, rutile, brookite, or their mixed phases). The XRD data of the nanorod, nanotip and nanowire are revealed in Figure 3D. As can be clearly found from this figure, the crystal structure is the mixed phases of anatase and rutile.35
After the Ag–PIII process, the surface topographies seemed without significant change at low magnification (Figure 4A, C, and E). From the visual field of SEM at high magnification, the nanowire topography was damaged to some extent (Figure 4B); whereas, the nanotip topography was destroyed severely (Figure 4D). Furthermore, homogeneously distributed nanoparticles can be seen on the entire surfaces of both Ag@nanowire and Ag@nanotip (white arrows in Figure 4B and D). On the contrary, the nanorod topography was not altered too much, and no nanoparticles were found on Ag@nanorod surface (Figure 4F). The XPS full spectra of all the Ag–PIII samples further indicated the presence of Ag element (Figure 5A). Figure 5B shows the XPS high-resolution Ag 3d spectra acquired from the Ag–PIII samples. The Ag 3d doublets at around 368.10 eV (Ag 3d5/2) and 374.10 eV (Ag 3d3/2) with a spin energy separation of 6.0 eV are assigned to metallic Ag,36,37 demonstrating that the observed nanoparticles are metallic Ag.
Figure 4 SEM morphology of the as-synthesized Ag@nanowire (A, B), Ag@nanotip (C, D), and Ag@nanorod (E, F) at low- and high-magnification, respectively.
Figure 5 XPS full spectra (A) and the corresponding Ag 3d XPS spectra (B) of the Ag@nanowire, Ag@nanotip, and Ag@nanorod.
To further testify the existing forms of metallic Ag on the three nanotopographical surfaces, the Ag–PIII specimens were characterized by the TEM method. The results are shown in Figure 6. Figure 6A gives the typical bright-field (BF) TEM view of Ag-implanted TiO2 nanowires scratched off from the Ag@nanowire surface. From this figure, one can see abundant nanoparticles along the nanowires, which were demonstrated as Ag nanoparticles by the energy-dispersive X-ray spectroscopy (EDS) spectrum (Figure 6C, corresponding to the rectangular area in Figure 6A). The corresponding high-resolution transmission electron microscope image in Figure 6B clearly displays the existing forms of Ag nanoparticles on the nanowires. In detail, these nanoparticles are divided into two types. Some Ag nanoparticles are completely immersed in the TiO2 nanowires, while other Ag nanoparticles are partially embedded in the nanowires with partially being exposed. Meanwhile, the high-resolution TEM image lattice patterns in Figure 6B further verify the nanoparticles are metallic Ag nanoparticles, and they possess excellent crystallinity. A similar situation exists in the Ag-implanted TiO2 nanotips. Nevertheless, it is observed that the number of Ag nanoparticles on the nanotips (Figure 6D) is smaller than that of the former in Figure 6A. On the contrary, there are no Ag nanoparticles around the Ag-implanted TiO2 nanorods, as shown in Figure 6G. Figure 6I depicts the corresponding EDS analysis result, obtained from the rectangular area in Figure 6G, which further certifies the existence of Ag element and agrees well with the XPS analysis result in Figure 5. From Figure 6H, one can find lots of tiny nanoparticles completely immersed in the TiO2 nanorods. Obviously, these tiny nanoparticles are the Ag nanoparticles, which did not migrate to the nanorod surface during the Ag–PIII process. These observed results imply that the nanotopographies of TiO2 films on titanium surface can affect the growth habit of Ag nanoparticles in TiO2 films during the Ag–PIII process.
In fact, during the Ag–PIII process, the nanotopographies of TiO2 films may affect the distribution of electric field around TiO2 films and the structure of Ag plasma sheath around the films.31 As a result, the difference in the nanotopographies of TiO2 films may influence the nucleation, growth, and distribution of Ag nanoparticles in the TiO2 nanofilms (Figure S1). This hypothesis may account for the observed results for the Ag-implanted TiO2 nanowires, nanotips, and nanorods. The exact mechanism remains unclear, and more work should be done to explain the mechanism in detail. On the basis of the XPS analysis, the contents of Ag element on the Ag@nanowire, Ag@nanotip, and Ag@nanorod are about 3.0%, 2.7%, and 1.9%, respectively. Up to now, the whole process aforementioned can be proposed and illustrated in Figure S1. Finally, as shown in Figure 4, three types of Ag-implanted TiO2 nanotopographies were formed on the metallic titanium surface. And, the existing forms of Ag nanoparticles in the TiO2 nanofilms will influence the Ag ions release and the related antimicrobial actions.
Ag ions release
The release behaviors of Ag ions from the Ag–PIII samples in fresh water are shown in Figure 7A. For the Ag@nanowire and Ag@nanotip, the Ag ions were obviously released from the Ag nanoparticles, especially for the Ag@nanowire. However, during the immersing period, no Ag ions were detected by the inductively coupled plasma mass spectrometry, indicating that Ag ions were not released from the Ag@nanorod. The XPS analysis was also conducted on the immersed samples after 7 days. As shown in Figure 7B, Ag element can still be detected on these samples in the form of metallic Ag (Figure 7C). Based on the analysis, the residual contents of Ag on the Ag@nanowire, Ag@nanotip, and Ag@nanorod are approximately 1.0%, 1.2%, and 1.8%, respectively. These observed results are quite consistent with the corresponding existing forms of Ag nanoparticles in TiO2 nanofilms. Understandably, whether the Ag ions can be released will affect the antimicrobial actions of the Ag-implanted TiO2 nanofilms.
It has been reported that the antibacterial behavior of Ag nanoparticles relies upon the availability of Ag ions,38,39 and the released amount of Ag ions in surrounding aqueous environment plays a key role in the antibacterial activity of Ag-loaded nano-TiO2.18 Furthermore, direct physical contact with the Ag nanoparticles can also induce bacteria death.8,40,41 To evaluate the antibacterial ability of the as-prepared Ag–PIII specimens and to determine the antibacterial mechanism behind (including release killing and contact killing), the adhering microbes were dissociated off the surfaces and recultivated on an agar base on the bacterial counting method. Figure 8A shows the typical photographs of the bacterial colonies on the specimens, combined with the bacteria counting results. All the nanostructured TiO2 surfaces can inhibit the proliferation of E. coli and S. aureus to some extent, especially for the nanorod TiO2.
Figure 8 Typical photographs of recultivated Escherichia coli and Staphylococcus aureus colonies on agar (A) and the corresponding percentage reduction of bacteria colonies (B, C).
This could be attributed to the topography difference of the nano-TiO2 surfaces. After Ag implantation, all the surfaces of Ag–PIII samples have the strong capability to suppress the growth of the two kinds of bacteria. The amounts of E. coli and S. aureus on the Ag-implanted TiO2 nanofilms are notably decreased after 24 hours, as shown in Figure 8B and C.
To determine the reason, SEM method was used to observe the membrane morphology and integrity of both E. coli and S. aureus bacteria, as shown in Figure 9. Cell division dominates on the Cp Ti, while not the same on the surfaces of Ag–PIII specimens, revealing that the surfaces of Ag-implanted TiO2 can kill the bacteria. Most of the E. coli cells cultured on the Cp Ti were at the stage of binary fission with rod shape (white arrow in Figure 9A1), which look smooth and without obvious damage. However, serious disruption of the cytoplasmic membrane can be seen on all the surfaces of Ag–PIII specimens, causing the lysis of the cell and the leakage of cytoplasma (white arrows in Figure 9B1, C1, and D1). This is also true for S. aureus cells, which present smooth and intact cytoplasmic membranes and produce abundant and continuous biofilms, implying that S. aureus can grow well on Cp Ti (white arrow in Figure 9A2).
Nevertheless, the phenomena of cell lysis and cytoplasma leakage are prevailing on all surfaces of the Ag–PIII samples (white arrows in Figure 9B2, C2, and D2), indicating that S. aureus bacteria cannot survive well on the surfaces of Ag–PIII specimens. The observed results indicate that the death of both E. coli and S. aureus cells on the surfaces of Ag–PIII specimens can be ascribed to the damage of the microbial membrane integrity. Therefore, the Ag plasma-modified TiO2 nanofilms have a significant antimicrobial function on both the bacteria, ie, Gram-negative E. coli and Gram-positive S. aureus.
Research focusing on the material characteristics of TiO2 nanomaterials like topography, component, crystallinity, phase composition, etc, may shed light on the mechanism behind antibacterial actions (such as membrane penetration) and the release of Ag ions may affect the surface properties of TiO2 and subsequent radical generation and lipid peroxidation on the surface.11,42–44 In this work, the dissolution of Ag nanoparticles release the antimicrobial Ag ions in the aqueous environment as Reaction 1, and partially contributes to the antimicrobial ability of the Ag–PIII surfaces through a release-killing way.45
The Ag ions released from the Ag nanoparticles can trigger inactivation of respiratory enzymes and interruption of electron transport46,47 and interfere with permeability of microbial membrane and replication of DNA.48 However, although the release amount of Ag+ ions had a significant difference (Figure 7A), the Ag-implanted TiO2 nanofilms showed no significant difference here in the antimicrobial activity against both microbes (Figure 8B and C). For the Ag-implanted TiO2 nanorods, understandably, it kills microbes via a direct physical contact that is, a sole contact-killing action. For the Ag-implanted TiO2 nanowires and nanotips, they kill microbes via a two-level antimicrobial action comprising the release-killing ability and the contact-killing ability.
On the basis of the observed results, the contact-killing action is the main way to destroy microbes for all the Ag-implanted TiO2 nanofilms. In fact, electrons can be captured and bounded by Ag nanoparticles owing to the building of the Schottky barrier at the interface of Ag/TiO2, as Reaction 2, suppressing electron/hole recombination and thus inducing oxidation and reduction quantum yields.49 The produced h+ holes will react with the on-surface OH- ions or H2O molecules and generate •OH radicals based on Reaction 3 or Reaction 4, or subsequently transform into H2O2 molecules, according to Reaction 5 since the •OH radicals have quite short lifespan.50,51
Consequently, •OH or H2O2 species accumulate near the cell membrane of bacteria and conduct the reaction of lipid peroxidation, that is, a contact-killing antibacterial way, destroying the membrane integrity of bacteria and eventually causing the inactivation of bacteria.40 The hypothesized antimicrobial mechanism for Ag plasma-modified TiO2 nanofilms can be illustrated in Figure 10. The aforementioned explanation for the antibacterial behaviors of various Ag– PIII nano-TiO2 surfaces is mainly a hypothesis, based on the observed experimental results. The true mechanism remains not clear. It is essential to do more studies to elucidate the mechanism behind in detail. It is considered that, by optimizing the PIII parameters, Ag nanoparticles with different existing forms, including the exposed ones on the surface and the embedded ones beneath the surface, are incorporated with TiO2 nanorod film, followed by the antibacterial experiment to further investigate the antibacterial ability.
Figure 10 Illustration for antibacterial mechanism with both release-killing and contact-killing actions of Ag nanoparticles-loaded TiO2 nanofilms in darkness.
The Ag plasma-modified nanostructured TiO2 films (including nanorod, nanotip, and nanowire topographies) were successfully prepared on the titanium surface via a combination of hydrothermal method and Ag–PIII technique. Compared to the acid-etched titanium, the nanostructured TiO2 films possess some bacteriostatic effect toward both Gram-negative E. coli and Gram-positive S. aureus. The existing forms of the Ag nanoparticles show differently in the TiO2 films with different nanotopographies, which results in the significantly different release behaviors of Ag ions. However, the antimicrobial evaluation tests show no significant difference against both microbes. The antimicrobial actions of the Ag@TiO2 system here consist of two paths, that is, the contact killing and the release killing. Nevertheless, on the basis of the obtained results, the contact-killing action should be considered as the main way to destroy microbes for all the Ag plasma-modified TiO2 nanofilms. This study provides insight to the antimicrobial design of Ti-based implants surfaces.
The authors received joint financial support from: the National Basic Research Program of China (973 Program, 2012CB933600); the National Natural Science Foundation of China (31100675, 51071168, and 81271704); the Shanghai Science and Technology R&D Fund under grant 11JC1413700.
The authors report no conflicts of interest in this work.
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Qualitatively, the nucleation and growth behavior of Ag nanoparticles in TiO2 nanofilms can be comprehended by the classical nucleation theory.1 The excess free energy (ΔG) can be described by Equation S1,2
in which: r, the cluster radius; γ, the surface tension of the cluster; RT, the product of ideal gas constant (R) and the absolute temperature (T); S, the ratio of the solute concentrations at saturation and equilibrium conditions; and Vm, the molar volume of the bulk crystal.
When S >1 (supersaturated condition), the increase of r value will result in the decrease of ΔG value, making the clusters more stable. The critical radius of a nucleus (r*) at supersaturated condition can be determined by setting dΔG/dr = 0 as Equation S2, at which ΔG* is maximum,
Based on Equation S2, r* is in inverse ratio to lnS, revealing that an increase in lnS procures a decrease in minimum nucleus radius (r*). Thus, when the concentration of Ag atoms exceeds the solubility limit of metal atoms in TiO2 nanofilm matrix, the system will relax by the nucleation and growth of the Ag nanoparticles.
During the Ag–PIII process, energetic Ag plasma could be blocked by the substrate, and part of the kinetic energy will be transformed into heat energy in the ultrashort period in restricted regions, which is called the atomic scale heating.3
In the present situation, cathodic-arc Ag ions undergo three acceleration zones. The first zone is beside the cathode spot, generating the initial ion kinetic energy (Ek). The second zone is in the space charge sheath between the Ag plasma and TiO2 nanofilm surface. Additional kinetic energy QeVb is acquired for the ion of charge state Q with a negative bias voltage (Vb) applied to the TiO2 nanofilm, where e is the elementary charge. The third zone is in the nanoscale vicinity of TiO2 nanofilm matrix where image charge acceleration emerges and procures kinetic energy (Ei). Besides, Ag ions also possess substantial potential energy which contains ionization energy EQ, cohesive energy Ec, and excitation energy of bound electrons Ee. The ionization energy (EQ) is defined as the essential energy to remove a bound electron from an ion with charge state Q, generating an ion with charge state Q + 1. Thus, the ionization energy EQ of a triply charged Ag ion should be the summation of all the three ionization steps as follows in Equation S3,3
The general formula to express the total energy of an Ag ion is given by Equation S4,3
The previously reported and the presently calculated compositions of the total energy for the Ag ion reaching TiO2 nanofilm matrix are listed in Table S1.
Figure S1 Proposed schematic illustration of basic physical processes (from left to right) involved in the formation of Ag nanoparticles in TiO2 nanofilms during the Ag–PIII process.
Here, the mean charge state (Q) equals to approximately 2.4 The donation of electronic excitation energies (Ee) is comparatively slight and negligible in Table S1.5 The kinetic energy Ei induced by image charge acceleration is calculated on the basis of Equation S5,6
Considering the work function (W) of the TiO2 nanofilm matrix, the value of W is about 4.13 eV,7 and the kinetic energy Ei can be estimated, approximately 2.11 eV.
On the basis of the data in Table S1, the total energy gain of an individual Ag ion is much higher than the minimum displacement energy ranging from 10–40 eV,3 which thus can potentially remove and dislodge stationary Ag atoms in the TiO2 nanofilm matrix, which may explain the observed results for the Ag-implanted TiO2 nanowires and nanotips. However, this explanation cannot completely meet the situation for the Ag-implanted TiO2 nanorods. The nanorod topography of TiO2 film may influence the electric field distribution and Ag plasma sheath structure around the TiO2 film during the Ag–PIII process, thus affecting the nucleation, growth, and distribution of Ag nanoparticles in the TiO2 nanorods.
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