Investigation of Kelvin Probe Force Microscopy and Optical Properties of F8BT Polymer Incorporated with ZnONR/AgNP Nanocomposite

Investigation of Kelvin Probe Force Microscopy and Optical Properties of F8BT Polymer Incorporated with ZnONR/AgNP Nanocomposite | Research Square window.SnipcartSettings = { analytics: { enabled: false } }; (function() { var accessVector = localStorage.getItem('access_vector') || ''; window.dataLayer = window.dataLayer || []; if (accessVector) { window.dataLayer.push({ user: { profile: { profileInfo: { snid: accessVector } } } }); } })(); (function(w,d,s,l,i){w[l]=w[l]||[];w[l].push({'gtm.start':new Date().getTime(),event:'gtm.js'});var f=d.getElementsByTagName(s)[0],j=d.createElement(s),dl=l!='dataLayer'?'&l='+l:'';j.async=true;j.src='https://www.googletagmanager.com/gtm.js?id='+i+dl;f.parentNode.insertBefore(j,f);})(window,document,'script','dataLayer','GTM-K279D39R'); Browse Preprints In Review Journals COVID-19 Preprints AJE Video Bytes Research Tools Research Promotion AJE Professional Editing AJE Rubriq About Preprint Platform In Review Editorial Policies Our Team Advisory Board Help Center Sign In Submit a Preprint Cite Share Download PDF Research Article Investigation of Kelvin Probe Force Microscopy and Optical Properties of F8BT Polymer Incorporated with ZnONR/AgNP Nanocomposite Ishaq Musa This is a preprint; it has not been peer reviewed by a journal. https://doi.org/ 10.21203/rs.3.rs-4989599/v1 This work is licensed under a CC BY 4.0 License Status: Posted Version 1 posted You are reading this latest preprint version Abstract The optical properties and work function of poly(9,9-dioctylfluorene-co-benzothiadiazole) (F8BT) and its nanocomposites with ZnO nanorods (ZnONRs) and silver nanoparticles (AgNPs) were extensively studied using techniques such as Scanning Probe Microscopy (SPM) and optical spectroscopy. Kelvin Probe Force Microscopy (KPFM) measurements revealed significant differences in contact potential and a work function of around 4.484 eV for pure F8BT. Furthermore, optical absorption measurements showed increased absorbance and noticeable changes in bandgap when AgNPs and ZnONRs were added, indicating improved light-absorbing properties of the nanocomposites. The band gap of F8BT is typically around 2.50 eV, but the introduction of ZnO nanorods increases it to 2.63 eV. This could be due to the interaction between F8BT and ZnONRs. Additionally, the incorporation of silver nanoparticles (AgNPs) further raises the band gap to 2.66 eV. Analysis of the Photoluminescence (PL) spectra reveals a significant increase in emission intensity for the F8BT/AgNP/ZnONR combination, attributed to exciton recombination and the impact of localized surface Plasmon resonance in the nanocomposites. F8BT ZnONRs AgNPs KPFM Optical spectroscopy Figures Figure 1 Figure 2 Figure 3 Figure 4 Figure 5 Figure 6 1. Introduction There is a significant amount of research being conducted on nanocomposite materials, which involve combining organic polymers with inorganic nanoparticles. These materials are of great interest due to their ability to display improved properties that are superior to those of their components. One material in particular, F8BT (poly(9,9-dioctylfluorene-alt-benzothiadiazole)), shows great potential for optoelectronic applications such as LEDs, photovoltaic devices, and field-effect transistors. This is due to its adjustable optical band gap, high photoluminescence efficiency, and strong charge transport properties. However, it is important to note that F8BT has its limitations, including suboptimal light absorption and limited charge separation efficiency, which require further improvements[ 1 – 4 ]. The addition of metal and semiconductor nanoparticles into polymer matrices has displayed promising potential in addressing these constraints. Silver nanoparticles (AgNPs) are well-known for their impressive and potent localized surface plasmon resonance (LSPR) effects. These effects can significantly boost light absorption and scattering in the visible range, resulting in a substantial enhancement in the photoluminescence of the polymer. As a result, incorporating AgNPs into polymer matrices offers significant advantages for various applications, including the creation of high-quality LEDs and plasmon-enhanced solar cells[ 5 – 7 ]. Zinc oxide nanostructures have become a major focus in nanomaterial research due to their distinctive features such as high electron mobility and wide bandgap. These qualities make them highly desirable for use in a range of optoelectronic devices. ZnONRs are known for their ability to serve as effective electron transport layers, which help improve the separation and movement of electric charges. This attribute is especially important in efforts to enhance the efficiency of solar cells[ 8 – 10 ]. The combination of AgNPs and ZnONRs in polymer matrices offers an innovative approach to overcoming limitations that have slowed the advancement of many technologies. Researchers can tap into the synergistic effects of metallic and semiconductor nanoparticles, opening up new possibilities in materials science and engineering. Additionally, integrating these nanoparticles into polymer matrices not only improves performance but also creates opportunities for sustainable and affordable solutions[ 11 – 13 ]. This research aims to explore how the combination of AgNPs and ZnONRs affects the structural, optical, and electronic properties of F8BT-based nanocomposites. The research will involve incorporating these nanomaterials into the polymer matrix and using advanced characterization techniques such as Atomic Force Microscopy (AFM), Kelvin Probe Force Microscopy (KPFM), optical absorption, and Photoluminescence (PL) spectroscopy to understand the improvements. Atomic Force Microscopy (AFM) is a technique used to analyze the surface characteristics and texture of nanocomposites, providing valuable insights into how adding AgNPs and ZnONRs affects the topography of the polymer matrix. Changes in surface roughness can directly impact the optoelectronic properties by altering the available area for light absorption and charge transport. Additionally, Kelvin Probe Force Microscopy (KPFM) is employed to map the distribution of surface potential, allowing for the measurement of contact potential differences (CPD) and the computation of work function values. This offers important information about the electronic properties of the nanocomposites and how the addition of nanomaterials alters charge transport and energy levels within the system[ 14 – 16 ]. The main aim of optical absorption studies is to evaluate the nanocomposites' light absorption capability. Enhanced absorption, especially in the visible spectrum, is crucial for boosting the performance of optoelectronic devices such as solar cells. The interaction among the F8BT polymer, AgNPs, and ZnONRs is expected to lead to alterations in the bandgap, potentially improving the material's response to incoming light. Photoluminescence (PL) spectroscopy is utilized to examine how exciton dynamics and recombination processes function in nanocomposites. The addition of AgNPs is anticipated to bring about localized surface plasmon resonance (LSPR) effects, which can enhance emission intensity through exciton-plasmon interactions[ 17 – 19 ]. The combination of F8BT polymer with ZnO nanorods/Ag nanoparticles composite is expected to enhance the optical absorption and photoluminescence properties of the materials when compared to their individual use. This expectation is based on the remarkable qualities of both materials and the possible synergistic effects resulting from their interaction. The objective of this study is to comprehend the mechanisms behind these enhanced properties and to explore the potential technological applications of this composite material. 2. Experimental methods Zinc acetate dehydrate (98+%, sigma Aldrich), lithium hydroxide monohydrate (sigma Aldrich), ethanol, Silver nitrate (AgNO3), chloroform, Poly (9,9-dioctylfluorene-alt-benzothiadiazole) F8BT (Mn ≥ 376.200 g/mol), powder (Mw = 240.000 g/mol) were purchased from Sigma Aldrich and used as obtained 2.1. Preparation of ZnONR and AgNP ZnO nanorods were previously synthesized by heating a solution containing 5.5g of zinc acetate dehydrate in 250ml of ethanol until it became clear[ 20 ]. The solution was then refluxed for 1 hour, with 150ml of the solvent removed by distillation and replaced with fresh ethanol. Next, 1.39g of lithium hydroxide monohydrate was added to the solution and mixed in an ultrasonic bath at 0°C for 1 hour, resulting in a clear solution of ZnO sol-gel nanoparticles. To produce the ZnO nanorods, the solution containing ZnO nanoparticles was heated and combined with 10% distilled water (DW) at 60°C for 48 hours, resulting in the formation of a white powder precipitate. In a separate recent synthesis[ 21 ], silver nanoparticles were created by mixing 1.18 mM AgNO3 aqueous solutions with deionized water. Following this, 50 mL of Pistacia Palaestina (P. Palaestina) leaf extract was gradually added to each 50-mL AgNO3 solution. The mixture was then heated in a heating mantle, with the temperature maintained at a range of 80 to 84°C for 2 hours while continuously stirring. The successful formation of silver nanoparticles was confirmed by the emergence of a brownish-yellow to black color. To purify the resulting nanoparticles, the solution was centrifuged at 10,000 rpm for 10 minutes, a process that was repeated five times to ensure the recovery of pure silver nanoparticles. 2.2 Preparation of the Nanocomposite F8BT/ZnONR /AgNP To produce a thin film of pure F8BT and nanocomposites, we made two solutions: one for the pure F8BT, and the other for the nanocomposites. Each solution involved dissolving 20 mg of F8BT in 2 ml of chloroform solution. We then combined the mixture with 1mg of ZnO nanorods and 1mg of AgNPs, and used sonication to evenly disperse the blend for 30 minutes. After cleaning glass and silicon wafer substrates to remove impurities, we applied the F8BT/ZnO/Ag nanocomposite solution onto each 1cm square using a spin coater, which entailed depositing a specific amount of solution onto the center of the substrate and spinning it at 1500 rpm for 30 second to create a uniform thin film. The resulting thin film was dried in a vacuum heating oven at 60 degrees Celsius to remove any remaining solvent and ensure the film's structure and consistency. 2.3 characterization methods The morphology, surface potential, and work function of the F8BT polymer and the F8BT/ZnONR/AgNP nanocomposite were evaluated using Scanning Probe Microscopy (SPM-9700HT, Shimadzu, Tokyo, Japan). Atomic Force Microscopy (AFM) and Kelvin Probe Force Microscopy (KPFM) were employed to achieve precise assessments of morphology and surface potential. The samples were mounted on a piezoelectric stage, with a conductive PtSi probe attached to the cantilever, enabling consistent oscillatory motion as the probe scanned the surface. This setup generated detailed topographic maps. KPFM further enhanced the analysis by producing surface potential images alongside the topographic maps at each scan point, providing valuable insights into the surface potential. Proper sample preparation, including secure mounting for stability, was essential to ensure accurate mapping. Scanning was performed at a speed of 0.5 Hz with a resolution of 256 × 256 pixels, resulting in high-definition images with a spatial resolution of 0.2 nm. Different tip models were utilized for topography and KPFM. For topography and phase mode, the SPP-NCHR model by Nanoworld was used, force constant of 42 N/m and a resonance frequency of 330 kHz. For KPFM, a conductive Pt/Ir-coated tip with a resonance frequency of 75 kHz and a force constant of 2.8 N/m was employed. Additionally, UV–vis absorption spectra were recorded using a UV-2600i spectrophotometer (Shimadzu, Tokyo, Japan), and photoluminescence spectra were obtained with an RF-6000 spectrofluorometer (Shimadzu, Tokyo, Japan). 3. Results and discussion 3.1 AFM and Phase mode of F8BT/ZnONR/AgNP The in-depth investigation in Fig. 1 utilized Atomic Force Microscopy (AFM) to analyze the F8BT polymer and its nanocomposites with silver nanoparticles (Ag) and zinc oxide nanorods (ZnONR). This analysis offers valuable insight into the morphological and compositional changes resulting from the inclusion of these nanomaterials. The AFM topography image of the pristine F8BT polymer in Fig. 1 (a) displays a surface with uniformly distributed features of varying heights between 4nm to 11 nm and a surface roughness Ra = 4.8 nm. The accompanying phase image in Fig. 1 (b) reveals uniform phase contrast, indicating homogeneity in the polymer's properties. Line profiles extracted from these images in Fig. 1 (c) show minor variations in surface topography and consistent phase shift, suggesting uniform compositional properties. The phase shift along the A-B line ranges from 141.5° to 148° for pristine F8BT polymer. When Ag nanoparticles are introduced, the AFM topography image in Fig. 1 (d) shows significant changes in surface morphology, with distinct features and increased surface roughness Ra = 7.12 nm. The phase image in Fig. 1 (e) displays varying phase contrast, reflecting differences in composition between the Ag nanoparticles and the surrounding polymer matrix. Line profiles in Fig. 1 (f) provide a detailed analysis of the Ag nanoparticle's influence, showing significant peaks and sharp changes in phase shift. The presence of an Ag nanoparticle and F8BT polymer is highlighted by the phase peak. The phase shift along the A-B profile ranges from 141° to 145°, passing through a region with a dark spot corresponding to smaller Ag nanoparticles, as indicated by the reduced phase shift. In the case of the F8BT/ZnONR nanocomposite, the AFM topography image in Fig. 1 (h) shows even more pronounced surface features and higher surface roughness Ra = 10.52 nm compared to the F8BT/Ag composite, with the ZnO nanorods appearing as prominent structures and creating distinct topographical features. The phase image in Fig. 1 (i) also exhibits varied phase contrast around the ZnONR, indicating a substantial difference in composition between the ZnO nanorods and the polymer. Line profiles in Fig. 1 (j) further highlight the influence of ZnONRs on the polymer surface, showing substantial elevations and corresponding shifts in the phase profile from 114 to 122°, indicating the significant impact of ZnONRs on the polymer's local composition. The AFM analysis demonstrates how the incorporation of Ag nanoparticles and ZnO nanorods into the F8BT polymer matrix alters the surface shape and composition. The detailed images and line profiles provide a thorough understanding of the structural changes caused by these nanocomposites. 3.2 Kelvin Probe Force Microscopy (KPFM) Figure 2 illustrates the use of Atomic Force Microscopy (AFM) and Kelvin Probe Force Microscopy (KPFM) to examine pristine F8BT on a silicon substrate. In Fig. 2 (a), a 2D AFM topography image shows the surface features of the F8BT at a scan size of 2 µm × 2 µm. Figure 2 (b) presents a 3D projection of the topography, displaying granular features with varying heights. The line profile in Fig. 2 (c) reveals a substantial height of 8 nm. Figure 2 (d) presents the surface potential, indicating regions of higher potential in red and lower potential in blue. The graph demonstrates fluctuations in voltage between point A and point B. Figure 2 (e) offers a 3D projection of the surface potential, showing changes throughout the space. Lastly, Fig. 2 (f) shows the line profile of the contact potential difference (CPD) of the pristine F8BT, which is measured at 44 mV. Figure 3 illustrates the characteristics of the KPFM of the F8BT/ZnONR nanocomposites on a silicon substrate. The topography image from an AFM in Fig. 3 (a) shows the surface appearance of the nanocomposite, with ZnO nanorods embedded in the F8BT matrix, with the polymer material indicated by the darker areas. Figure 3 (b) showcases a three-dimensional view of the surface topography, highlighting variations in height. ZnO nanorods are evident in the 3D surface plot, reaching a maximum height of about 42.73 nm, while the polymer areas have a lower profile. Figure 3 (c) presents a line profile extracted from image 3(a), displaying differences in height across the nanocomposite surface. ZnO nanorods have a height of approximately 13 nm and a lateral length of around 155 nm, while the surrounding polymer matrix shows a lower height of about 3 nm. These findings suggest that the ZnO nanorods are effectively embedded within the polymer matrix, impacting the nanocomposite's optical characteristics. In Fig. 3 (d), a potential map of the F8BT/ZnONR nanocomposite is shown, acquired through Kelvin probe force microscopy (KPFM), revealing variations in surface potential. ZnO nanorods have different contact potential differences (CPD) compared to the F8BT polymer. The color scale on the map indicates the uneven distribution of surface potential, ranging from red (higher potential) to blue (lower potential). Figure 3 (e) provides a three-dimensional view of the surface potential map, offering a clearer visualization of potential differences. The regions with ZnO nanorods exhibit slightly different potential compared to the surrounding F8BT regions. Lastly, in Fig. 3 (f), the line profile of CPD along the A-B line from image 3(d) provides quantitative information about surface potential variations, with a CPD difference between ZnO nanorods and F8BT of approximately 14 mV and 38 mV, indicating a distinction of the two materials. The KPFM for the Highly Ordered Pyrolytic Graphite (HOPG) reference sample, grade ZYA, is shown in Fig. 4 . The sample measures 10 mm by 10 mm with a thickness of 1 mm and has a mosaic spread of 0.4 ± 0.1°. According to the Fig. 4 (b), the average Contact Potential Difference (CPD) for this sample is around 28 mV. This sample was supplied by MikroMasch. Kelvin Probe Force Microscopy (KPFM) is a technique used to precisely measure the work function of materials. The surface potential is a key factor in KPFM and is responsible for the difference in work function values between the sample surface and the AFM probe tip. This difference is calculated using Eq. (1) that includes the electron charge and the Contact Potential Difference[ 22 , 23 ]. $$\:{{\upvarphi\:}}_{\text{s}\text{a}\text{m}\text{p}\text{l}\text{e}}={{\upvarphi\:}}_{\text{t}\text{i}\text{p}}-\text{e}{\text{V}}_{\text{C}\text{P}\text{D}}\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:1\:$$ To ensure accurate measurements of the work function of pristine F8PT and F8BT/ZnONR nanocomposites, it is important to determine the work function of the cantilever in the equipment. Calibration is necessary to obtain reliable measurements and commonly involves using a reference material with a known work function for standardization. In this study, Highly Oriented Pyrolytic Graphite (HOPG) with a work function range of 4.5 to 5 eV is used as the reference material for calibration and measurement accuracy[ 24 , 25 ]. Using Eq. (1), we can derive similar equations for the F8BT and HOPG substrates. The work function of the F8BT substrate is represented as \(\:{\:\varphi\:}_{F8BT}\) , and its specific Contact Potential Difference is denoted as V (CPD, F8PT) . Similarly, the work function of the HOPG substrate is \(\:{\varphi\:}_{HOPG}\:\) and its distinct Contact Potential Difference is V (CPD,HOPG) . The difference between the work functions of these two substrates can be determined using the following equations. $$\:{{\upvarphi\:}}_{\text{F}8\text{B}\text{T}}={{\upvarphi\:}}_{\text{H}\text{O}\text{P}\text{G}}+\text{e}\left({\text{V}}_{\left(\text{C}\text{P}\text{D},\:\text{H}\text{O}\text{P}\text{G}\right)}-{\text{V}}_{\left(\text{C}\text{P}\text{D},\:\text{F}8\text{B}\text{T}\right)\:}\:\right)\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:\:2$$ Upon analyzing the CPD values displayed in Fig. 2 (f) and Fig. 4 (b), which indicate a measurement of 44mV and 28mV for V (CPD,F8BT) and V (CPD,HOPG) respectively, and considering the work function of HOPG at 4.5 eV, it was determined using Eq. 2 that the work function of the F8BT polymer is 4.484 eV. The work function represents the energy difference between the Fermi level and the vacuum level. By utilizing the HOMO and LUMO levels of F8BT at -5.9 eV and − 3.3 eV[ 26 ], relative to the vacuum level, the work function can be computed as the absolute value of the Fermi level, giving an equivalent of 4.6 eV. This calculated value closely matches the experimental value that was obtained. The work function of ZnO nanorods in F8BT/ZnONR nanocomposites was calculated using the contact potential difference (CPD) of ZnONR, which was found to be 38mV for lengths of approximately 13 nm and 155 nm, resulting in a work function of 4.49 eV. The CPD of F8BT was determined to be 14 mV with a work function of 4.514 eV. It is worth noting that the CPD of F8BT decreases in hybrid systems due to various factors such as charge transfer, work function alignment, and morphological effects. In ZnO NRs/F8BT nanocomposites, charge transfer at the material interface reduces the number of free charges at the surface, leading to a lower CPD. Additionally; differences in work function between the materials can cause charges to redistribute, resulting in a reduced CPD. The introduction of F8BT can also impact the CPD by altering the surface roughness and nanostructure of ZnO NRs in the hybrid structure[ 27 , 28 ]. 3.3 Optical properties of F8BT and F8BT/ZnONR/AgNP nanocomposites An analysis of the absorbance and energy gap of F8BT, as well as its combinations with ZnO nanorods and silver nanoparticles, indicates how these nanomaterials affect the optical properties of the polymer. In the absorbance spectra Fig. 5 (a), F8BT shows two absorption peaks at 320 nm and 464 nm, representing π-π* transitions and electronic transitions within the polymer backbone[ 2 , 3 ]. When ZnO nanorods are introduced, absorbance at both wavelengths increases, potentially improving light absorption through enhanced scattering and light-harvesting efficiency[ 29 ]. Furthermore, the semiconducting nature of ZnO nanorods can promote charge transfer interactions with the polymer, further impacting light absorption. The inclusion of silver nanoparticles also increases absorbance, in the 320 nm and 446 nm regions, due to the plasmonic properties of AgNP. The combined effects of ZnO nanorods and AgNP result in the highest overall absorbance, indicating synergistic interactions. Additionally, the charge transfer interactions facilitated by the semiconducting nature of ZnO nanorods can enhance charge separation and transport within the polymer, further improving the absorption performance. Moreover, the plasmonic properties of silver nanoparticles allow for effective trapping and localization of light, leading to increased photon absorption and potential enhancement of the charge generation process[ 30 , 31 ]. Overall, the synergistic effects of ZnO nanorods and AgNP on absorbance suggest their potential as crucial components in the development of high-performance photovoltaic devices. The analysis of energy gaps Fig. 5 (b) reveals the direct optical bandgap of the materials through the Tauc plot. Pure F8BT typically has a bandgap of 2.50 eV, a common characteristic for conjugated polymers used in optoelectronic applications. When ZnO nanorods are introduced to the polymer matrix, the bandgap increases to 2.63 eV. This shift is likely due to the interaction between F8BT and the ZnO nanorods, causing a slight adjustment in the electronic structure of the polymer, resulting in an increased energy required for electronic transitions. ZnO, as a wide-bandgap semiconductor, may also induce changes in the energy levels of the composite material through hybridization effects[ 32 ]. The addition of AgNPs to the F8BT matrix results in a further increase in the bandgap to 2.66 eV. The presence of AgNPs may be affecting the electronic environment of the polymer due to strong plasmonic interactions at the nanoparticle surface, potentially altering the density of states in the composite material. The higher bandgap seen when adding silver nanoparticles suggests the modification of electronic properties within the polymer, possibly due to the creation of new electronic states or the influence of nanoparticle-induced polarization effects[ 33 , 34 ]. Surprisingly, when both AgNPs and ZnO nanorods are combined with F8BT, the bandgap remains at 2.63 eV, similar to the F8BT + ZnONR composite. This indicates that the simultaneous presence of both nanomaterials leads to a balancing effect on the bandgap, with the electronic effects of ZnO nanorods and AgNPs neutralizing each other to stabilize the bandgap at this value. This suggests that the composite reaches a state of electronic equilibrium, wherein the influences of the two nanomaterials on the polymer’s electronic structure are complementary. The addition of ZnO nanorods and silver nanoparticles to the F8BT polymer not only improves the absorption of light, but also changes the electronic structure of the material, resulting in adjustable optical properties[ 8 , 35 , 36 ]. These nanocomposites, with their increased absorbance and shifts in bandgap due to the plasmonic effects of AgNPs, show potential for use in advanced optoelectronic applications like solar cells or light-emitting devices, where controlling optical absorption and electronic transitions is crucial. The photoluminescence spectra depicted in Fig. 6 demonstrate the emission characteristics of the F8BT polymer in its pristine state and when incorporated with ZnO nanorods (ZnONR), silver nanoparticles (AgNP), and a combination of both ZnONR and AgNP. The peak emission for the pure F8BT polymer is observed at 558 nm; however, its intensity is lower compared to the other samples, suggesting a reduced emission efficiency in its pure form. Incorporating ZnO nanorods into F8BT (F8BT/ZnONR) substantially enhances PL intensity, with the emission peak shifting to 547 nm, indicating a blue shift. This significant increase in PL intensity suggests that ZnO nanorods promote improved exciton recombination, possibly due to the coupling of excitons in F8BT with surface states on the ZnO nanorods. The interaction between F8BT and ZnO nanorods likely leads to enhanced charge separation and reduced non-radiative losses, thereby increasing the radiative recombination rate. The blue shift might be attributed to changes in the local environment of F8BT molecules, as ZnO nanorods can modify the polymer’s electronic structure by inducing strain or altering molecular packing[ 37 – 40 ]. Adding silver nanoparticles (AgNP) to F8BT (F8BT/AgNP) results in a higher PL intensity, with the emission peak remaining at 547 nm, similar to F8BT/ZnONR. This enhancement is likely due to localized surface plasmon resonance (LSPR) effects from the AgNPs, which amplify the local electromagnetic field around the F8BT molecules, leading to increased radiative decay rates. However, the PL intensity is lower than F8BT/ZnONR, suggesting that while LSPR can boost emission, it may not be as effective as the exciton-surface state interaction seen with ZnO nanorods. Additionally, the nanoparticles may introduce non-radiative decay pathways or cause partial quenching of the excitons[ 41 – 43 ].The nanocomposite F8BT/ZnONR/AgNP, which includes ZnO nanorods and Ag nanoparticles, shows a moderate PL intensity. The peak moves slightly to 550 nm, indicating a small shift toward red compared to the separate ZnONR or AgNP composites. The increase in emissions in systems containing F8BT, ZnO nanoparticles, and silver nanoparticles can be attributed to several factors related to their interactions and properties. One significant factor is energy transfer mechanisms like Förster Resonance Energy Transfer (FRET), where non-radiative energy transfer occurs between a donor (F8BT) and an acceptor (ZnO or Ag NPs) when they are nearby and their energy levels align. This results in enhanced emission from the acceptor due to efficient energy transfer[ 44 , 45 ]. Additionally, improved charge separation and reduced recombination in hybrid systems play a role, where excited electrons in F8BT can be efficiently transferred to the conduction band minimum of ZnO or the Fermi level of Ag NPs. This efficient charge transfer minimizes non-radiative recombination and increases the radiative recombination rate, resulting in higher emission intensity. Furthermore, the presence of ZnO and Ag NPs can help passivate surface states and defects in F8BT, reducing non-radiative decay paths and enhancing photon emission[ 46 , 47 ]. 4. Conclusions The research investigated the optical properties and work function of poly(9,9-dioctylfluorene-co-benzothiadiazole) (F8BT) and its nanocomposites with ZnO nanorods (ZnONRs) and silver nanoparticles (AgNPs) using Scanning Probe Microscopy (SPM) and optical spectroscopy techniques. Kelvin Probe Force Microscopy (KPFM) revealed a work function of approximately 4.484 eV for pure F8BT. The addition of ZnONRs and AgNPs resulted in significant changes in contact potential, suggesting their substantial influence on the electronic properties of the nanocomposites. Optical absorption measurements demonstrated that the presence of ZnONRs and AgNPs enhanced the light-absorbing properties of F8BT, resulting in an increase in band gap from 2.50 eV for pure F8BT to 2.63 eV with ZnONRs and further to 2.66 eV with AgNPs. This observation indicates a strong interaction between the polymer and the nanostructures. Furthermore, photoluminescence (PL) spectroscopy unveiled a remarkable enhancement in emission intensity for the F8BT/AgNP/ZnONR nanocomposite. This enhancement was attributed to exciton recombination and the effects of localized surface plasmon resonance (LSPR) induced by the AgNPs. In summary, the addition of ZnONRs and AgNPs significantly enhanced the optical and electronic properties of F8BT, making the resulting nanocomposites highly promising for various applications in optoelectronic devices, such as photovoltaics and light-emitting systems. Declarations Authors contribution Ishaq Musa:Writing – review & editing, Writing – original draft, Visualization, Methodology, Investigation, Conceptualization,Formal analysis. Data availability All data in this study are available from the corresponding author upon request. Declaration The author has no conflicts of interest to declare that are relevant to the content of this article. Acknowledgments The author thanks Palestine Technical University—Kadoorie (PTUK) and the Palestinian Ministry of Higher Education for facilities and support. FUNDING DECLARATION There was no Funding References M. Mamada, R. Komatsu, C. Adachi, ACS Appl. Mater. Interfaces. 12 , 28383 (2020) B. Ghasemi, J. Ševčík, V. Nádaždy, K. Végsö, P. Šiffalovič, P. Urbánek, I. Kuřitka, Polymers. 14 , 641 (2022) M. Mbarek, L. Sagaama, K. Alimi, Opt. Mater. 91 , 447 (2019) G.E. Khalil, A.M. Adawi, D.G. Lidzey, Phys. E: Low-Dimensional Syst. Nanostruct. 118 , 113829 (2020) R. Kato, M. Uesugi, Y. Komatsu, F. Okamoto, T. 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Commun. 12 , 1772 (2021) Additional Declarations No competing interests reported. Cite Share Download PDF Status: Posted Version 1 posted You are reading this latest preprint version Research Square lets you share your work early, gain feedback from the community, and start making changes to your manuscript prior to peer review in a journal. As a division of Research Square Company, we’re committed to making research communication faster, fairer, and more useful. We do this by developing innovative software and high quality services for the global research community. Our growing team is made up of researchers and industry professionals working together to solve the most critical problems facing scientific publishing. Also discoverable on Platform About Our Team In Review Editorial Policies Advisory Board Help Center Resources Author Services Accessibility API Access RSS feed Manage Cookie Preferences © Research Square 2026 | ISSN 2693-5015 (online) Privacy Policy Terms of Service Do Not Sell My Personal Information {"props":{"pageProps":{"initialData":{"identity":"rs-4989599","acceptedTermsAndConditions":true,"allowDirectSubmit":true,"archivedVersions":[],"articleType":"Research Article","associatedPublications":[],"authors":[{"id":361294715,"identity":"a1abb7ee-d823-4c01-9785-19c7aacdbd9b","order_by":0,"name":"Ishaq Musa","email":"data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAZAAAAAyAQMAAABI0h/eAAAABlBMVEX///8AAABVwtN+AAAACXBIWXMAAA7EAAAOxAGVKw4bAAAAxklEQVRIiWNgGAWjYBACNghlA2WyEa8ljYGHaC1QcJgELXwM3GmSP2rO59lLpCUwfCg7zGDOf4CQw3i3SfMcu13MI5F2gHHGucMMljMSiNDCwHY7sUcivYGZt+0wg8ENAg4DaZH88e8cRMtfkJbzRDhMgrftAFBL2gFmRpCWA4Qcxsy72Zq3L7mY58yzhIM959J5CPpFvr13480f3+zy2NvTDB/8KLOWIxhiDMwQCmwySC2PAQENcIBwDNFaRsEoGAWjYMQAAIVuO/5rIOUNAAAAAElFTkSuQmCC","orcid":"","institution":"Palestine Technical University - Kadoorie","correspondingAuthor":true,"prefix":"","firstName":"Ishaq","middleName":"","lastName":"Musa","suffix":""}],"badges":[],"createdAt":"2024-08-28 08:51:18","currentVersionCode":1,"declarations":"","doi":"10.21203/rs.3.rs-4989599/v1","doiUrl":"https://doi.org/10.21203/rs.3.rs-4989599/v1","draftVersion":[],"editorialEvents":[],"editorialNote":"","failedWorkflow":false,"files":[{"id":65802052,"identity":"699f9f16-4c22-43d3-91e5-b20a67192abf","added_by":"auto","created_at":"2024-10-03 00:32:44","extension":"png","order_by":1,"title":"Figure 1","display":"","copyAsset":false,"role":"figure","size":889467,"visible":true,"origin":"","legend":"\u003cp\u003e(a) Topography of F8BT polymer (b) Phase image of F8BT polymer (c) line profiles of phase shift and height of F8BT polymer extract from images (a) and (b), (d)Topography of F8BT /Ag nanocomposite (e) Phase image of F8BT /Ag nanocomposite (f) line profiles of phase shift and height of F8BT /Ag nanocomposite extract from images (d) and (e), (h)Topography of F8BT /ZnONR nanocomposite (j) Phase image of F8BT /ZnONR nanocomposite (f) line profiles of phase shift and height of F8BT /ZnONR nanocomposite extract from images (h) and (j).\u003c/p\u003e","description":"","filename":"1.png","url":"https://assets-eu.researchsquare.com/files/rs-4989599/v1/42cf2ae539d8caad8f464470.png"},{"id":65802403,"identity":"f9062d3b-b9b3-43d3-bdca-3ef961da24ed","added_by":"auto","created_at":"2024-10-03 00:40:44","extension":"png","order_by":2,"title":"Figure 2","display":"","copyAsset":false,"role":"figure","size":582669,"visible":true,"origin":"","legend":"\u003cp\u003e(a) AFM topography images of pristine F8BT on a Si substrate, Scan sizes: (2 μm\u003c/p\u003e\n\u003cp\u003e× 2 μm); (b)Three-dimensional projection of Topography of pristine F8BT, (c) line profiles \u0026nbsp;of size pristine F8BT identified in the image (a), (d) surface potential images of pristine F8BT deposit on the Silicon substrate, (e) Three-dimensional projection surface potential of pristine F8BT ,(f) CPD line profiles for sizes pristine F8BT identified in image (d), the bias voltage is 6 volts.\u003c/p\u003e","description":"","filename":"2.png","url":"https://assets-eu.researchsquare.com/files/rs-4989599/v1/2aafc16153221efda6a67ad2.png"},{"id":65802053,"identity":"74a2e4e0-81ae-407f-b180-13b69ade16bc","added_by":"auto","created_at":"2024-10-03 00:32:44","extension":"png","order_by":3,"title":"Figure 3","display":"","copyAsset":false,"role":"figure","size":526307,"visible":true,"origin":"","legend":"\u003cp\u003e(a) AFM topography images of F8BT/ZnONR nanocomposite on a Si substrate with scan sizes of (2 μm × 2 μm); (b) Three-dimensional projection of the topography of the F8BT/ZnONR nanocomposite; (c) Line profiles of the F8BT/ZnONR nanocomposite identified in image (a); (d) Surface potential images of the F8BT/ZnONR nanocomposite deposited on the silicon substrate; (e) Three-dimensional projection of the surface potential of the F8BT/ZnONR nanocomposite; (f) CPD line profiles of F8BT/ZnONR nanocomposite identified in image (d), the bias voltage is 6 volts.\u003c/p\u003e","description":"","filename":"3.png","url":"https://assets-eu.researchsquare.com/files/rs-4989599/v1/5472a02dcca46144b3ae139c.png"},{"id":65802057,"identity":"21f95afd-8cbb-4c63-9da9-04e1a0b19960","added_by":"auto","created_at":"2024-10-03 00:32:44","extension":"png","order_by":4,"title":"Figure 4","display":"","copyAsset":false,"role":"figure","size":309248,"visible":true,"origin":"","legend":"\u003cp\u003e(a) Surface potential of the standard sample Highly Ordered Pyrolytic Graphite (HOPG), (b) Height profile (CPD) of HOPG that was obtained from image (a).\u003c/p\u003e","description":"","filename":"4.png","url":"https://assets-eu.researchsquare.com/files/rs-4989599/v1/d112913c26d902661605bbb1.png"},{"id":65802404,"identity":"eed9f506-1694-451b-b062-552006f49501","added_by":"auto","created_at":"2024-10-03 00:40:44","extension":"png","order_by":5,"title":"Figure 5","display":"","copyAsset":false,"role":"figure","size":180769,"visible":true,"origin":"","legend":"\u003cp\u003e(a)The absorption spectrum of F8BT, F8BT/ZnONR , F8BT/AgNP\u0026nbsp; and F8BT/ZnONR/AgNP nanocompsites , (b) (αℎυ)\u003csup\u003e1/2\u003c/sup\u003e vs. Photon energy of \u0026nbsp;F8BT, F8BT/ZnONR , F8BT/AgNP and F8BT/ZnONR/AgNP nanocompsites.\u003c/p\u003e","description":"","filename":"5.png","url":"https://assets-eu.researchsquare.com/files/rs-4989599/v1/59002cbf55bf1512cee432a6.png"},{"id":65802055,"identity":"a6f461cb-97d0-42a7-ba32-29bfe2b3f7e3","added_by":"auto","created_at":"2024-10-03 00:32:44","extension":"png","order_by":6,"title":"Figure 6","display":"","copyAsset":false,"role":"figure","size":196667,"visible":true,"origin":"","legend":"\u003cp\u003eThe Photoluminescence spectrum of F8BT, F8BT/ZnONR , F8BT/AgNP and F8BT/ZnONR/AgNP Nanocompsites.\u003c/p\u003e","description":"","filename":"6.png","url":"https://assets-eu.researchsquare.com/files/rs-4989599/v1/db3bb2aaf461632c81738b84.png"},{"id":66335355,"identity":"18338eee-689b-46ed-ad07-6fe4de68d9d0","added_by":"auto","created_at":"2024-10-10 14:32:09","extension":"pdf","order_by":0,"title":"","display":"","copyAsset":false,"role":"manuscript-pdf","size":2951303,"visible":true,"origin":"","legend":"","description":"","filename":"manuscript.pdf","url":"https://assets-eu.researchsquare.com/files/rs-4989599/v1/5e662dac-c58f-41ef-be6f-cf0257074100.pdf"}],"financialInterests":"No competing interests reported.","formattedTitle":"Investigation of Kelvin Probe Force Microscopy and Optical Properties of F8BT Polymer Incorporated with ZnONR/AgNP Nanocomposite","fulltext":[{"header":"1. Introduction","content":"\u003cp\u003eThere is a significant amount of research being conducted on nanocomposite materials, which involve combining organic polymers with inorganic nanoparticles. These materials are of great interest due to their ability to display improved properties that are superior to those of their components. One material in particular, F8BT (poly(9,9-dioctylfluorene-alt-benzothiadiazole)), shows great potential for optoelectronic applications such as LEDs, photovoltaic devices, and field-effect transistors. This is due to its adjustable optical band gap, high photoluminescence efficiency, and strong charge transport properties. However, it is important to note that F8BT has its limitations, including suboptimal light absorption and limited charge separation efficiency, which require further improvements[\u003cspan additionalcitationids=\"CR2 CR3\" citationid=\"CR1\" class=\"CitationRef\"\u003e1\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR4\" class=\"CitationRef\"\u003e4\u003c/span\u003e]. The addition of metal and semiconductor nanoparticles into polymer matrices has displayed promising potential in addressing these constraints. Silver nanoparticles (AgNPs) are well-known for their impressive and potent localized surface plasmon resonance (LSPR) effects. These effects can significantly boost light absorption and scattering in the visible range, resulting in a substantial enhancement in the photoluminescence of the polymer. As a result, incorporating AgNPs into polymer matrices offers significant advantages for various applications, including the creation of high-quality LEDs and plasmon-enhanced solar cells[\u003cspan additionalcitationids=\"CR6\" citationid=\"CR5\" class=\"CitationRef\"\u003e5\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR7\" class=\"CitationRef\"\u003e7\u003c/span\u003e].\u003c/p\u003e \u003cp\u003eZinc oxide nanostructures have become a major focus in nanomaterial research due to their distinctive features such as high electron mobility and wide bandgap. These qualities make them highly desirable for use in a range of optoelectronic devices. ZnONRs are known for their ability to serve as effective electron transport layers, which help improve the separation and movement of electric charges. This attribute is especially important in efforts to enhance the efficiency of solar cells[\u003cspan additionalcitationids=\"CR9\" citationid=\"CR8\" class=\"CitationRef\"\u003e8\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR10\" class=\"CitationRef\"\u003e10\u003c/span\u003e].\u003c/p\u003e \u003cp\u003eThe combination of AgNPs and ZnONRs in polymer matrices offers an innovative approach to overcoming limitations that have slowed the advancement of many technologies. Researchers can tap into the synergistic effects of metallic and semiconductor nanoparticles, opening up new possibilities in materials science and engineering. Additionally, integrating these nanoparticles into polymer matrices not only improves performance but also creates opportunities for sustainable and affordable solutions[\u003cspan additionalcitationids=\"CR12\" citationid=\"CR11\" class=\"CitationRef\"\u003e11\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR13\" class=\"CitationRef\"\u003e13\u003c/span\u003e].\u003c/p\u003e \u003cp\u003eThis research aims to explore how the combination of AgNPs and ZnONRs affects the structural, optical, and electronic properties of F8BT-based nanocomposites. The research will involve incorporating these nanomaterials into the polymer matrix and using advanced characterization techniques such as Atomic Force Microscopy (AFM), Kelvin Probe Force Microscopy (KPFM), optical absorption, and Photoluminescence (PL) spectroscopy to understand the improvements.\u003c/p\u003e \u003cp\u003eAtomic Force Microscopy (AFM) is a technique used to analyze the surface characteristics and texture of nanocomposites, providing valuable insights into how adding AgNPs and ZnONRs affects the topography of the polymer matrix. Changes in surface roughness can directly impact the optoelectronic properties by altering the available area for light absorption and charge transport. Additionally, Kelvin Probe Force Microscopy (KPFM) is employed to map the distribution of surface potential, allowing for the measurement of contact potential differences (CPD) and the computation of work function values. This offers important information about the electronic properties of the nanocomposites and how the addition of nanomaterials alters charge transport and energy levels within the system[\u003cspan additionalcitationids=\"CR15\" citationid=\"CR14\" class=\"CitationRef\"\u003e14\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR16\" class=\"CitationRef\"\u003e16\u003c/span\u003e].\u003c/p\u003e \u003cp\u003eThe main aim of optical absorption studies is to evaluate the nanocomposites' light absorption capability. Enhanced absorption, especially in the visible spectrum, is crucial for boosting the performance of optoelectronic devices such as solar cells. The interaction among the F8BT polymer, AgNPs, and ZnONRs is expected to lead to alterations in the bandgap, potentially improving the material's response to incoming light. Photoluminescence (PL) spectroscopy is utilized to examine how exciton dynamics and recombination processes function in nanocomposites. The addition of AgNPs is anticipated to bring about localized surface plasmon resonance (LSPR) effects, which can enhance emission intensity through exciton-plasmon interactions[\u003cspan additionalcitationids=\"CR18\" citationid=\"CR17\" class=\"CitationRef\"\u003e17\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR19\" class=\"CitationRef\"\u003e19\u003c/span\u003e].\u003c/p\u003e \u003cp\u003eThe combination of F8BT polymer with ZnO nanorods/Ag nanoparticles composite is expected to enhance the optical absorption and photoluminescence properties of the materials when compared to their individual use. This expectation is based on the remarkable qualities of both materials and the possible synergistic effects resulting from their interaction. The objective of this study is to comprehend the mechanisms behind these enhanced properties and to explore the potential technological applications of this composite material.\u003c/p\u003e"},{"header":"2. Experimental methods","content":"\u003cp\u003eZinc acetate dehydrate (98+%, sigma Aldrich), lithium hydroxide monohydrate (sigma Aldrich), ethanol, Silver nitrate (AgNO3), chloroform, Poly (9,9-dioctylfluorene-alt-benzothiadiazole) F8BT (Mn\u0026thinsp;\u0026ge;\u0026thinsp;376.200 g/mol), powder (Mw\u0026thinsp;=\u0026thinsp;240.000 g/mol) were purchased from Sigma Aldrich and used as obtained\u003c/p\u003e \u003cdiv id=\"Sec3\" class=\"Section2\"\u003e \u003ch2\u003e2.1. Preparation of ZnONR and AgNP\u003c/h2\u003e \u003cp\u003eZnO nanorods were previously synthesized by heating a solution containing 5.5g of zinc acetate dehydrate in 250ml of ethanol until it became clear[\u003cspan citationid=\"CR20\" class=\"CitationRef\"\u003e20\u003c/span\u003e]. The solution was then refluxed for 1 hour, with 150ml of the solvent removed by distillation and replaced with fresh ethanol. Next, 1.39g of lithium hydroxide monohydrate was added to the solution and mixed in an ultrasonic bath at 0\u0026deg;C for 1 hour, resulting in a clear solution of ZnO sol-gel nanoparticles. To produce the ZnO nanorods, the solution containing ZnO nanoparticles was heated and combined with 10% distilled water (DW) at 60\u0026deg;C for 48 hours, resulting in the formation of a white powder precipitate. In a separate recent synthesis[\u003cspan citationid=\"CR21\" class=\"CitationRef\"\u003e21\u003c/span\u003e], silver nanoparticles were created by mixing 1.18 mM AgNO3 aqueous solutions with deionized water. Following this, 50 mL of Pistacia Palaestina (P. Palaestina) leaf extract was gradually added to each 50-mL AgNO3 solution. The mixture was then heated in a heating mantle, with the temperature maintained at a range of 80 to 84\u0026deg;C for 2 hours while continuously stirring. The successful formation of silver nanoparticles was confirmed by the emergence of a brownish-yellow to black color. To purify the resulting nanoparticles, the solution was centrifuged at 10,000 rpm for 10 minutes, a process that was repeated five times to ensure the recovery of pure silver nanoparticles.\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec4\" class=\"Section2\"\u003e \u003ch2\u003e2.2 Preparation of the Nanocomposite F8BT/ZnONR /AgNP\u003c/h2\u003e \u003cp\u003eTo produce a thin film of pure F8BT and nanocomposites, we made two solutions: one for the pure F8BT, and the other for the nanocomposites. Each solution involved dissolving 20 mg of F8BT in 2 ml of chloroform solution. We then combined the mixture with 1mg of ZnO nanorods and 1mg of AgNPs, and used sonication to evenly disperse the blend for 30 minutes. After cleaning glass and silicon wafer substrates to remove impurities, we applied the F8BT/ZnO/Ag nanocomposite solution onto each 1cm square using a spin coater, which entailed depositing a specific amount of solution onto the center of the substrate and spinning it at 1500 rpm for 30 second to create a uniform thin film. The resulting thin film was dried in a vacuum heating oven at 60 degrees Celsius to remove any remaining solvent and ensure the film's structure and consistency.\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec5\" class=\"Section2\"\u003e \u003ch2\u003e2.3 characterization methods\u003c/h2\u003e \u003cp\u003eThe morphology, surface potential, and work function of the F8BT polymer and the F8BT/ZnONR/AgNP nanocomposite were evaluated using Scanning Probe Microscopy (SPM-9700HT, Shimadzu, Tokyo, Japan). Atomic Force Microscopy (AFM) and Kelvin Probe Force Microscopy (KPFM) were employed to achieve precise assessments of morphology and surface potential. The samples were mounted on a piezoelectric stage, with a conductive PtSi probe attached to the cantilever, enabling consistent oscillatory motion as the probe scanned the surface. This setup generated detailed topographic maps. KPFM further enhanced the analysis by producing surface potential images alongside the topographic maps at each scan point, providing valuable insights into the surface potential. Proper sample preparation, including secure mounting for stability, was essential to ensure accurate mapping. Scanning was performed at a speed of 0.5 Hz with a resolution of 256 \u0026times; 256 pixels, resulting in high-definition images with a spatial resolution of 0.2 nm. Different tip models were utilized for topography and KPFM. For topography and phase mode, the SPP-NCHR model by Nanoworld was used, force constant of 42 N/m and a resonance frequency of 330 kHz. For KPFM, a conductive Pt/Ir-coated tip with a resonance frequency of 75 kHz and a force constant of 2.8 N/m was employed. Additionally, UV\u0026ndash;vis absorption spectra were recorded using a UV-2600i spectrophotometer (Shimadzu, Tokyo, Japan), and photoluminescence spectra were obtained with an RF-6000 spectrofluorometer (Shimadzu, Tokyo, Japan).\u003c/p\u003e \u003c/div\u003e"},{"header":"3. Results and discussion","content":"\u003cdiv id=\"Sec7\" class=\"Section2\"\u003e \u003ch2\u003e3.1 AFM and Phase mode of F8BT/ZnONR/AgNP\u003c/h2\u003e \u003cp\u003eThe in-depth investigation in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e utilized Atomic Force Microscopy (AFM) to analyze the F8BT polymer and its nanocomposites with silver nanoparticles (Ag) and zinc oxide nanorods (ZnONR). This analysis offers valuable insight into the morphological and compositional changes resulting from the inclusion of these nanomaterials. The AFM topography image of the pristine F8BT polymer in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e (a) displays a surface with uniformly distributed features of varying heights between 4nm to 11 nm and a surface roughness Ra\u0026thinsp;=\u0026thinsp;4.8 nm. The accompanying phase image in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e (b) reveals uniform phase contrast, indicating homogeneity in the polymer's properties. Line profiles extracted from these images in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e (c) show minor variations in surface topography and consistent phase shift, suggesting uniform compositional properties. The phase shift along the A-B line ranges from 141.5\u0026deg; to 148\u0026deg; for pristine F8BT polymer. When Ag nanoparticles are introduced, the AFM topography image in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e (d) shows significant changes in surface morphology, with distinct features and increased surface roughness Ra\u0026thinsp;=\u0026thinsp;7.12 nm. The phase image in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e (e) displays varying phase contrast, reflecting differences in composition between the Ag nanoparticles and the surrounding polymer matrix. Line profiles in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e (f) provide a detailed analysis of the Ag nanoparticle's influence, showing significant peaks and sharp changes in phase shift. The presence of an Ag nanoparticle and F8BT polymer is highlighted by the phase peak. The phase shift along the A-B profile ranges from 141\u0026deg; to 145\u0026deg;, passing through a region with a dark spot corresponding to smaller Ag nanoparticles, as indicated by the reduced phase shift. In the case of the F8BT/ZnONR nanocomposite, the AFM topography image in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e (h) shows even more pronounced surface features and higher surface roughness Ra\u0026thinsp;=\u0026thinsp;10.52 nm compared to the F8BT/Ag composite, with the ZnO nanorods appearing as prominent structures and creating distinct topographical features. The phase image in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e (i) also exhibits varied phase contrast around the ZnONR, indicating a substantial difference in composition between the ZnO nanorods and the polymer. Line profiles in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003e (j) further highlight the influence of ZnONRs on the polymer surface, showing substantial elevations and corresponding shifts in the phase profile from 114 to 122\u0026deg;, indicating the significant impact of ZnONRs on the polymer's local composition. The AFM analysis demonstrates how the incorporation of Ag nanoparticles and ZnO nanorods into the F8BT polymer matrix alters the surface shape and composition. The detailed images and line profiles provide a thorough understanding of the structural changes caused by these nanocomposites.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec8\" class=\"Section2\"\u003e \u003ch2\u003e3.2 Kelvin Probe Force Microscopy (KPFM)\u003c/h2\u003e \u003cp\u003eFigure \u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e illustrates the use of Atomic Force Microscopy (AFM) and Kelvin Probe Force Microscopy (KPFM) to examine pristine F8BT on a silicon substrate. In Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e(a), a 2D AFM topography image shows the surface features of the F8BT at a scan size of 2 \u0026micro;m \u0026times; 2 \u0026micro;m. Figure\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e(b) presents a 3D projection of the topography, displaying granular features with varying heights. The line profile in Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e(c) reveals a substantial height of 8 nm. Figure\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e(d) presents the surface potential, indicating regions of higher potential in red and lower potential in blue. The graph demonstrates fluctuations in voltage between point A and point B. Figure\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e(e) offers a 3D projection of the surface potential, showing changes throughout the space. Lastly, Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e(f) shows the line profile of the contact potential difference (CPD) of the pristine F8BT, which is measured at 44 mV.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eFigure \u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e illustrates the characteristics of the KPFM of the F8BT/ZnONR nanocomposites on a silicon substrate. The topography image from an AFM in Fig.\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e(a) shows the surface appearance of the nanocomposite, with ZnO nanorods embedded in the F8BT matrix, with the polymer material indicated by the darker areas. Figure\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e(b) showcases a three-dimensional view of the surface topography, highlighting variations in height. ZnO nanorods are evident in the 3D surface plot, reaching a maximum height of about 42.73 nm, while the polymer areas have a lower profile. Figure\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e(c) presents a line profile extracted from image 3(a), displaying differences in height across the nanocomposite surface. ZnO nanorods have a height of approximately 13 nm and a lateral length of around 155 nm, while the surrounding polymer matrix shows a lower height of about 3 nm. These findings suggest that the ZnO nanorods are effectively embedded within the polymer matrix, impacting the nanocomposite's optical characteristics. In Fig.\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e(d), a potential map of the F8BT/ZnONR nanocomposite is shown, acquired through Kelvin probe force microscopy (KPFM), revealing variations in surface potential. ZnO nanorods have different contact potential differences (CPD) compared to the F8BT polymer. The color scale on the map indicates the uneven distribution of surface potential, ranging from red (higher potential) to blue (lower potential). Figure\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e(e) provides a three-dimensional view of the surface potential map, offering a clearer visualization of potential differences. The regions with ZnO nanorods exhibit slightly different potential compared to the surrounding F8BT regions. Lastly, in Fig.\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003e(f), the line profile of CPD along the A-B line from image 3(d) provides quantitative information about surface potential variations, with a CPD difference between ZnO nanorods and F8BT of approximately 14 mV and 38 mV, indicating a distinction of the two materials.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eThe KPFM for the Highly Ordered Pyrolytic Graphite (HOPG) reference sample, grade ZYA, is shown in Fig.\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003e. The sample measures 10 mm by 10 mm with a thickness of 1 mm and has a mosaic spread of 0.4\u0026thinsp;\u0026plusmn;\u0026thinsp;0.1\u0026deg;. According to the Fig.\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003e(b), the average Contact Potential Difference (CPD) for this sample is around 28 mV. This sample was supplied by MikroMasch.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eKelvin Probe Force Microscopy (KPFM) is a technique used to precisely measure the work function of materials. The surface potential is a key factor in KPFM and is responsible for the difference in work function values between the sample surface and the AFM probe tip. This difference is calculated using Eq.\u0026nbsp;(1) that includes the electron charge and the Contact Potential Difference[\u003cspan citationid=\"CR22\" class=\"CitationRef\"\u003e22\u003c/span\u003e, \u003cspan citationid=\"CR23\" class=\"CitationRef\"\u003e23\u003c/span\u003e].\u003cdiv id=\"Equa\" class=\"Equation\"\u003e\u003cdiv format=\"TEX\" class=\"mathdisplay\" id=\"FileID_Equa\" name=\"EquationSource\"\u003e\n$$\\:{{\\upvarphi\\:}}_{\\text{s}\\text{a}\\text{m}\\text{p}\\text{l}\\text{e}}={{\\upvarphi\\:}}_{\\text{t}\\text{i}\\text{p}}-\\text{e}{\\text{V}}_{\\text{C}\\text{P}\\text{D}}\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:1\\:$$\u003c/div\u003e\u003c/div\u003e\u003c/p\u003e \u003cp\u003eTo ensure accurate measurements of the work function of pristine F8PT and F8BT/ZnONR nanocomposites, it is important to determine the work function of the cantilever in the equipment. Calibration is necessary to obtain reliable measurements and commonly involves using a reference material with a known work function for standardization. In this study, Highly Oriented Pyrolytic Graphite (HOPG) with a work function range of 4.5 to 5 eV is used as the reference material for calibration and measurement accuracy[\u003cspan citationid=\"CR24\" class=\"CitationRef\"\u003e24\u003c/span\u003e, \u003cspan citationid=\"CR25\" class=\"CitationRef\"\u003e25\u003c/span\u003e].\u003c/p\u003e \u003cp\u003eUsing Eq.\u0026nbsp;(1), we can derive similar equations for the F8BT and HOPG substrates. The work function of the F8BT substrate is represented as\u003cspan class=\"InlineEquation\"\u003e\u003cspan class=\"mathinline\"\u003e\\(\\:{\\:\\varphi\\:}_{F8BT}\\)\u003c/span\u003e\u003c/span\u003e, and its specific Contact Potential Difference is denoted as V\u003csub\u003e(CPD, F8PT)\u003c/sub\u003e. Similarly, the work function of the HOPG substrate is \u003cspan class=\"InlineEquation\"\u003e\u003cspan class=\"mathinline\"\u003e\\(\\:{\\varphi\\:}_{HOPG}\\:\\)\u003c/span\u003e\u003c/span\u003eand its distinct Contact Potential Difference is V\u003csub\u003e(CPD,HOPG)\u003c/sub\u003e. The difference between the work functions of these two substrates can be determined using the following equations.\u003cdiv id=\"Equb\" class=\"Equation\"\u003e\u003cdiv format=\"TEX\" class=\"mathdisplay\" id=\"FileID_Equb\" name=\"EquationSource\"\u003e\n$$\\:{{\\upvarphi\\:}}_{\\text{F}8\\text{B}\\text{T}}={{\\upvarphi\\:}}_{\\text{H}\\text{O}\\text{P}\\text{G}}+\\text{e}\\left({\\text{V}}_{\\left(\\text{C}\\text{P}\\text{D},\\:\\text{H}\\text{O}\\text{P}\\text{G}\\right)}-{\\text{V}}_{\\left(\\text{C}\\text{P}\\text{D},\\:\\text{F}8\\text{B}\\text{T}\\right)\\:}\\:\\right)\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:\\:2$$\u003c/div\u003e\u003c/div\u003e\u003c/p\u003e \u003cp\u003eUpon analyzing the CPD values displayed in Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e(f) and Fig.\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003e(b), which indicate a measurement of 44mV and 28mV for V\u003csub\u003e(CPD,F8BT)\u003c/sub\u003e and V\u003csub\u003e(CPD,HOPG)\u003c/sub\u003e respectively, and considering the work function of HOPG at 4.5 eV, it was determined using Eq.\u0026nbsp;2 that the work function of the F8BT polymer is 4.484 eV. The work function represents the energy difference between the Fermi level and the vacuum level. By utilizing the HOMO and LUMO levels of F8BT at -5.9 eV and \u0026minus;\u0026thinsp;3.3 eV[\u003cspan citationid=\"CR26\" class=\"CitationRef\"\u003e26\u003c/span\u003e], relative to the vacuum level, the work function can be computed as the absolute value of the Fermi level, giving an equivalent of 4.6 eV. This calculated value closely matches the experimental value that was obtained.\u003c/p\u003e \u003cp\u003eThe work function of ZnO nanorods in F8BT/ZnONR nanocomposites was calculated using the contact potential difference (CPD) of ZnONR, which was found to be 38mV for lengths of approximately 13 nm and 155 nm, resulting in a work function of 4.49 eV. The CPD of F8BT was determined to be 14 mV with a work function of 4.514 eV. It is worth noting that the CPD of F8BT decreases in hybrid systems due to various factors such as charge transfer, work function alignment, and morphological effects. In ZnO NRs/F8BT nanocomposites, charge transfer at the material interface reduces the number of free charges at the surface, leading to a lower CPD. Additionally; differences in work function between the materials can cause charges to redistribute, resulting in a reduced CPD. The introduction of F8BT can also impact the CPD by altering the surface roughness and nanostructure of ZnO NRs in the hybrid structure[\u003cspan citationid=\"CR27\" class=\"CitationRef\"\u003e27\u003c/span\u003e, \u003cspan citationid=\"CR28\" class=\"CitationRef\"\u003e28\u003c/span\u003e].\u003c/p\u003e \u003c/div\u003e \u003cdiv id=\"Sec9\" class=\"Section2\"\u003e \u003ch2\u003e3.3 Optical properties of F8BT and F8BT/ZnONR/AgNP nanocomposites\u003c/h2\u003e \u003cp\u003eAn analysis of the absorbance and energy gap of F8BT, as well as its combinations with ZnO nanorods and silver nanoparticles, indicates how these nanomaterials affect the optical properties of the polymer. In the absorbance spectra Fig.\u0026nbsp;\u003cspan refid=\"Fig5\" class=\"InternalRef\"\u003e5\u003c/span\u003e (a), F8BT shows two absorption peaks at 320 nm and 464 nm, representing π-π* transitions and electronic transitions within the polymer backbone[\u003cspan citationid=\"CR2\" class=\"CitationRef\"\u003e2\u003c/span\u003e, \u003cspan citationid=\"CR3\" class=\"CitationRef\"\u003e3\u003c/span\u003e]. When ZnO nanorods are introduced, absorbance at both wavelengths increases, potentially improving light absorption through enhanced scattering and light-harvesting efficiency[\u003cspan citationid=\"CR29\" class=\"CitationRef\"\u003e29\u003c/span\u003e]. Furthermore, the semiconducting nature of ZnO nanorods can promote charge transfer interactions with the polymer, further impacting light absorption. The inclusion of silver nanoparticles also increases absorbance, in the 320 nm and 446 nm regions, due to the plasmonic properties of AgNP. The combined effects of ZnO nanorods and AgNP result in the highest overall absorbance, indicating synergistic interactions. Additionally, the charge transfer interactions facilitated by the semiconducting nature of ZnO nanorods can enhance charge separation and transport within the polymer, further improving the absorption performance. Moreover, the plasmonic properties of silver nanoparticles allow for effective trapping and localization of light, leading to increased photon absorption and potential enhancement of the charge generation process[\u003cspan citationid=\"CR30\" class=\"CitationRef\"\u003e30\u003c/span\u003e, \u003cspan citationid=\"CR31\" class=\"CitationRef\"\u003e31\u003c/span\u003e]. Overall, the synergistic effects of ZnO nanorods and AgNP on absorbance suggest their potential as crucial components in the development of high-performance photovoltaic devices.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eThe analysis of energy gaps Fig.\u0026nbsp;\u003cspan refid=\"Fig5\" class=\"InternalRef\"\u003e5\u003c/span\u003e(b) reveals the direct optical bandgap of the materials through the Tauc plot. Pure F8BT typically has a bandgap of 2.50 eV, a common characteristic for conjugated polymers used in optoelectronic applications. When ZnO nanorods are introduced to the polymer matrix, the bandgap increases to 2.63 eV. This shift is likely due to the interaction between F8BT and the ZnO nanorods, causing a slight adjustment in the electronic structure of the polymer, resulting in an increased energy required for electronic transitions. ZnO, as a wide-bandgap semiconductor, may also induce changes in the energy levels of the composite material through hybridization effects[\u003cspan citationid=\"CR32\" class=\"CitationRef\"\u003e32\u003c/span\u003e]. The addition of AgNPs to the F8BT matrix results in a further increase in the bandgap to 2.66 eV. The presence of AgNPs may be affecting the electronic environment of the polymer due to strong plasmonic interactions at the nanoparticle surface, potentially altering the density of states in the composite material. The higher bandgap seen when adding silver nanoparticles suggests the modification of electronic properties within the polymer, possibly due to the creation of new electronic states or the influence of nanoparticle-induced polarization effects[\u003cspan citationid=\"CR33\" class=\"CitationRef\"\u003e33\u003c/span\u003e, \u003cspan citationid=\"CR34\" class=\"CitationRef\"\u003e34\u003c/span\u003e]. Surprisingly, when both AgNPs and ZnO nanorods are combined with F8BT, the bandgap remains at 2.63 eV, similar to the F8BT\u0026thinsp;+\u0026thinsp;ZnONR composite. This indicates that the simultaneous presence of both nanomaterials leads to a balancing effect on the bandgap, with the electronic effects of ZnO nanorods and AgNPs neutralizing each other to stabilize the bandgap at this value. This suggests that the composite reaches a state of electronic equilibrium, wherein the influences of the two nanomaterials on the polymer\u0026rsquo;s electronic structure are complementary. The addition of ZnO nanorods and silver nanoparticles to the F8BT polymer not only improves the absorption of light, but also changes the electronic structure of the material, resulting in adjustable optical properties[\u003cspan citationid=\"CR8\" class=\"CitationRef\"\u003e8\u003c/span\u003e, \u003cspan citationid=\"CR35\" class=\"CitationRef\"\u003e35\u003c/span\u003e, \u003cspan citationid=\"CR36\" class=\"CitationRef\"\u003e36\u003c/span\u003e]. These nanocomposites, with their increased absorbance and shifts in bandgap due to the plasmonic effects of AgNPs, show potential for use in advanced optoelectronic applications like solar cells or light-emitting devices, where controlling optical absorption and electronic transitions is crucial. The photoluminescence spectra depicted in Fig.\u0026nbsp;\u003cspan refid=\"Fig6\" class=\"InternalRef\"\u003e6\u003c/span\u003e demonstrate the emission characteristics of the F8BT polymer in its pristine state and when incorporated with ZnO nanorods (ZnONR), silver nanoparticles (AgNP), and a combination of both ZnONR and AgNP. The peak emission for the pure F8BT polymer is observed at 558 nm; however, its intensity is lower compared to the other samples, suggesting a reduced emission efficiency in its pure form. Incorporating ZnO nanorods into F8BT (F8BT/ZnONR) substantially enhances PL intensity, with the emission peak shifting to 547 nm, indicating a blue shift. This significant increase in PL intensity suggests that ZnO nanorods promote improved exciton recombination, possibly due to the coupling of excitons in F8BT with surface states on the ZnO nanorods. The interaction between F8BT and ZnO nanorods likely leads to enhanced charge separation and reduced non-radiative losses, thereby increasing the radiative recombination rate. The blue shift might be attributed to changes in the local environment of F8BT molecules, as ZnO nanorods can modify the polymer\u0026rsquo;s electronic structure by inducing strain or altering molecular packing[\u003cspan additionalcitationids=\"CR38 CR39\" citationid=\"CR37\" class=\"CitationRef\"\u003e37\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR40\" class=\"CitationRef\"\u003e40\u003c/span\u003e]. Adding silver nanoparticles (AgNP) to F8BT (F8BT/AgNP) results in a higher PL intensity, with the emission peak remaining at 547 nm, similar to F8BT/ZnONR. This enhancement is likely due to localized surface plasmon resonance (LSPR) effects from the AgNPs, which amplify the local electromagnetic field around the F8BT molecules, leading to increased radiative decay rates. However, the PL intensity is lower than F8BT/ZnONR, suggesting that while LSPR can boost emission, it may not be as effective as the exciton-surface state interaction seen with ZnO nanorods. Additionally, the nanoparticles may introduce non-radiative decay pathways or cause partial quenching of the excitons[\u003cspan additionalcitationids=\"CR42\" citationid=\"CR41\" class=\"CitationRef\"\u003e41\u003c/span\u003e\u0026ndash;\u003cspan citationid=\"CR43\" class=\"CitationRef\"\u003e43\u003c/span\u003e].The nanocomposite F8BT/ZnONR/AgNP, which includes ZnO nanorods and Ag nanoparticles, shows a moderate PL intensity. The peak moves slightly to 550 nm, indicating a small shift toward red compared to the separate ZnONR or AgNP composites. The increase in emissions in systems containing F8BT, ZnO nanoparticles, and silver nanoparticles can be attributed to several factors related to their interactions and properties. One significant factor is energy transfer mechanisms like F\u0026ouml;rster Resonance Energy Transfer (FRET), where non-radiative energy transfer occurs between a donor (F8BT) and an acceptor (ZnO or Ag NPs) when they are nearby and their energy levels align. This results in enhanced emission from the acceptor due to efficient energy transfer[\u003cspan citationid=\"CR44\" class=\"CitationRef\"\u003e44\u003c/span\u003e, \u003cspan citationid=\"CR45\" class=\"CitationRef\"\u003e45\u003c/span\u003e]. Additionally, improved charge separation and reduced recombination in hybrid systems play a role, where excited electrons in F8BT can be efficiently transferred to the conduction band minimum of ZnO or the Fermi level of Ag NPs. This efficient charge transfer minimizes non-radiative recombination and increases the radiative recombination rate, resulting in higher emission intensity. Furthermore, the presence of ZnO and Ag NPs can help passivate surface states and defects in F8BT, reducing non-radiative decay paths and enhancing photon emission[\u003cspan citationid=\"CR46\" class=\"CitationRef\"\u003e46\u003c/span\u003e, \u003cspan citationid=\"CR47\" class=\"CitationRef\"\u003e47\u003c/span\u003e].\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003c/div\u003e"},{"header":"4. Conclusions","content":"\u003cp\u003eThe research investigated the optical properties and work function of poly(9,9-dioctylfluorene-co-benzothiadiazole) (F8BT) and its nanocomposites with ZnO nanorods (ZnONRs) and silver nanoparticles (AgNPs) using Scanning Probe Microscopy (SPM) and optical spectroscopy techniques. Kelvin Probe Force Microscopy (KPFM) revealed a work function of approximately 4.484 eV for pure F8BT. The addition of ZnONRs and AgNPs resulted in significant changes in contact potential, suggesting their substantial influence on the electronic properties of the nanocomposites. Optical absorption measurements demonstrated that the presence of ZnONRs and AgNPs enhanced the light-absorbing properties of F8BT, resulting in an increase in band gap from 2.50 eV for pure F8BT to 2.63 eV with ZnONRs and further to 2.66 eV with AgNPs. This observation indicates a strong interaction between the polymer and the nanostructures. Furthermore, photoluminescence (PL) spectroscopy unveiled a remarkable enhancement in emission intensity for the F8BT/AgNP/ZnONR nanocomposite. This enhancement was attributed to exciton recombination and the effects of localized surface plasmon resonance (LSPR) induced by the AgNPs. In summary, the addition of ZnONRs and AgNPs significantly enhanced the optical and electronic properties of F8BT, making the resulting nanocomposites highly promising for various applications in optoelectronic devices, such as photovoltaics and light-emitting systems.\u003c/p\u003e "},{"header":"Declarations","content":"\u003cp\u003e\u003cstrong\u003eAuthors contribution\u003c/strong\u003e Ishaq Musa:Writing \u0026ndash; review \u0026amp; editing, Writing \u0026ndash; original draft, Visualization, Methodology, Investigation, Conceptualization,Formal analysis.\u0026nbsp;\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eData availability\u0026nbsp;\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eAll data in this study are available from the corresponding author upon request.\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eDeclaration\u0026nbsp;\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThe author has no conflicts of interest to declare that are relevant to the content of this article.\u003cstrong\u003e\u0026nbsp;\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eAcknowledgments\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThe author thanks Palestine Technical University\u0026mdash;Kadoorie (PTUK) and the Palestinian Ministry of Higher Education for facilities and support.\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eFUNDING DECLARATION\u0026nbsp;\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003e\u0026nbsp; \u0026nbsp;There was no Funding\u003c/p\u003e"},{"header":"References","content":"\u003col\u003e\u003cli\u003e\u003cspan\u003eM. 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Commun. \u003cb\u003e12\u003c/b\u003e, 1772 (2021)\u003c/span\u003e\u003c/li\u003e\u003c/ol\u003e"}],"fulltextSource":"","fullText":"","funders":[],"hasAdminPriorityOnWorkflow":false,"hasManuscriptDocX":true,"hasOptedInToPreprint":true,"hasPassedJournalQc":"","hasAnyPriority":false,"hideJournal":true,"highlight":"","institution":"","isAcceptedByJournal":false,"isAuthorSuppliedPdf":false,"isDeskRejected":"","isHiddenFromSearch":false,"isInQc":false,"isInWorkflow":false,"isPdf":false,"isPdfUpToDate":true,"isWithdrawnOrRetracted":false,"journal":{"display":true,"email":"[email protected]","identity":"researchsquare","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":true,"externalIdentity":"","sideBox":"","snPcode":"","submissionUrl":"/submission","title":"Research Square","twitterHandle":"researchsquare","acdcEnabled":true,"dfaEnabled":false,"editorialSystem":"","reportingPortfolio":"","inReviewEnabled":false,"inReviewRevisionsEnabled":true},"keywords":"F8BT, ZnONRs, AgNPs, KPFM, Optical spectroscopy","lastPublishedDoi":"10.21203/rs.3.rs-4989599/v1","lastPublishedDoiUrl":"https://doi.org/10.21203/rs.3.rs-4989599/v1","license":{"name":"CC BY 4.0","url":"https://creativecommons.org/licenses/by/4.0/"},"manuscriptAbstract":"\u003cp\u003eThe optical properties and work function of poly(9,9-dioctylfluorene-co-benzothiadiazole) (F8BT) and its nanocomposites with ZnO nanorods (ZnONRs) and silver nanoparticles (AgNPs) were extensively studied using techniques such as Scanning Probe Microscopy (SPM) and optical spectroscopy. Kelvin Probe Force Microscopy (KPFM) measurements revealed significant differences in contact potential and a work function of around 4.484 eV for pure F8BT. Furthermore, optical absorption measurements showed increased absorbance and noticeable changes in bandgap when AgNPs and ZnONRs were added, indicating improved light-absorbing properties of the nanocomposites. The band gap of F8BT is typically around 2.50 eV, but the introduction of ZnO nanorods increases it to 2.63 eV. This could be due to the interaction between F8BT and ZnONRs. Additionally, the incorporation of silver nanoparticles (AgNPs) further raises the band gap to 2.66 eV. Analysis of the Photoluminescence (PL) spectra reveals a significant increase in emission intensity for the F8BT/AgNP/ZnONR combination, attributed to exciton recombination and the impact of localized surface Plasmon resonance in the nanocomposites.\u003c/p\u003e","manuscriptTitle":"Investigation of Kelvin Probe Force Microscopy and Optical Properties of F8BT Polymer Incorporated with ZnONR/AgNP Nanocomposite","msid":"","msnumber":"","nonDraftVersions":[{"code":1,"date":"2024-10-03 00:32:39","doi":"10.21203/rs.3.rs-4989599/v1","editorialEvents":[{"type":"communityComments","content":0}],"status":"published","journal":{"display":true,"email":"[email protected]","identity":"researchsquare","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":true,"externalIdentity":"","sideBox":"","snPcode":"","submissionUrl":"/submission","title":"Research Square","twitterHandle":"researchsquare","acdcEnabled":true,"dfaEnabled":false,"editorialSystem":"","reportingPortfolio":"","inReviewEnabled":false,"inReviewRevisionsEnabled":true}}],"origin":"","ownerIdentity":"ccf2a19b-a260-4a50-951e-5155c4207e7c","owner":[],"postedDate":"October 3rd, 2024","published":true,"recentEditorialEvents":[],"rejectedJournal":[],"revision":"","amendment":"","status":"posted","subjectAreas":[],"tags":[],"updatedAt":"2024-10-12T02:38:13+00:00","versionOfRecord":[],"versionCreatedAt":"2024-10-03 00:32:39","video":"","vorDoi":"","vorDoiUrl":"","workflowStages":[]},"version":"v1","identity":"rs-4989599","journalConfig":"researchsquare"},"__N_SSP":true},"page":"/article/[identity]/[[...version]]","query":{"redirect":"/article/rs-4989599","identity":"rs-4989599","version":["v1"]},"buildId":"qtupq5eGEP_6zYnWcrvyt","isFallback":false,"isExperimentalCompile":false,"dynamicIds":[84888],"gssp":true,"scriptLoader":[]}