SnO2QDs Deposited on GO/PPy-Modified Glassy Carbon Electrode for Efficient Electrochemical Hydrogen Peroxide Sensor

In this present work, we demonstrate an efficient electrochemical sensor for the detection of hydrogen peroxide (H2O2) using a glassy carbon electrode (GCE) modified with a ternary nanocomposite of tin oxide QDs/GO/PPy (SGP2). An in situ chemical oxidative polymerization method was used to create the SGP2 nanocomposite. FTIR, XRD, HR TEM, CV, DPV, and impedance analysis were used to characterize the nanocomposite. The SGP2 nanocomposite modified GCE can be used to create an effective H2O2 electrochemical sensor with high sensitivity and a low detection limit (LOD). With SGP2 modified GCE, the electrochemical detection test for H2O2 was carried out using cyclic voltammetry (CV) and amperometric methods. The SGP2 modified GCE shows improved sensing capabilities, resulting in considerable sensitivity of 11.69 µA mM cm−2 and a very low limit of detection (LOD) of 0.758 µM for a broad linear range of H2O2 concentration from 0.1 mM to 0.8 mM with a correlation coefficient R2 = 0.9886. Additionally, the performance of the SGP2-modified GCE electrode is on par with or nonetheless superior to that of the other functional materials that have been reported for H2O2. As a result, our findings suggest that combining conductive polymer with metal oxide may be a useful method for producing sophisticated and affordable electrochemical sensors.


Introduction
Through a recognition element that connects the analyte with the transducer and displays an electrical signal, a sensor is a device that enables the transformation of a physicochemical process into an analytical signal. To ensure that the results of any investigation are both accurate and trustworthy, a sensor's design is crucial. Therefore, gadgets with diagnostic capabilities have been created by combining nanotechnology, electrochemistry, and analytical chemistry.
For the creation and implementation of analytical methodologies, electrochemical sensors benefit from the redox property of chemical species. The recognition element must be properly immobilised on the surface of an electrochemical sensor for it to function well, which makes the design and development of simple and compatible materials crucial. It is a developing field in nanotechnology to correctly mix organic and inorganic nanomaterials to achieve the latter goal's with maximum efficiency.
A ubiquitous disinfectant, hydrogen peroxide is also a crucial intermediary in the biochemical, pharmacological, therapeutic, industrial, and environmental sciences. Consequently, its analytical determination plays a vital role. H 2 O 2 is best known for its harmful effects on living things, but it also plays an important signalling role in a variety of biological processes, including immune stomata closure, cell activation, apoptosis, and root growth. H 2 O 2 results from many metabolic processes involving the oxidase enzymes (urate oxidase, cholesterol oxidase, alcohol oxidase, glucose oxidase, amino acid oxidase) [1]. H 2 O 2 , which is produced by a subclass of white blood cells known as neutrophils, serves as the first aqueous oxidizing agents and epitaxial chemical vapour deposition [21]. Due to its unique structure, high solution-processability, and ease of post-functionalization of GO, this wonderful material has a wide range of applications in various fields. Graphene has found uses in the production of electrochemical sensors, capacitors and biosensors because of its excellent conductivity [22][23][24].
In recent years, various types of nanostructured PPy combined with graphene, GO, or reduced GO (rGO) nanosheets have been prepared and used to fabricate electrodes due to polypyrrole's distinctive properties, including its higher conductivity, low cost, excellent thermal stability, rapid charge-discharge mechanism, and high energy density [25]. According to Gurusamy et al. [4], the electrochemical measurement of hydrogen peroxide (H 2 O 2 ), using a modified glassy carbon electrode (MWCNT/(BIM-Cu 2+ ) n @GCE) coordinated with poly(bisbenzimidazol at copper(II)), was proposed by Gurusamy et al. This form of coordination polymer web for peroxide sensing is documented. The electrode demonstrated an H 2 O 2 detection limit of 7.8 × 10 −7 M and a sensitivity of 5 nA µM −1 in amperometric sensing.
In this study, SGP2 ternary composites (polypyrrole, tin oxide quantum dots, graphene oxide, in the ratio 1:1:2 coded as SGP2) were made utilizing an in situ chemical oxidation approach, and tin oxide quantum dots were created using a conventional hydrothermal process, and graphene oxide was synthesized by the modified Hummer's method. To describe the oxidation state, chemical composition, and electrocatalytic capabilities of the SGP2 ternary material using several techniques such as Fourier Transform Infrared Spectrometer (FTIR), Transmission Electron Microscope (TEM), X-Ray diffraction (XRD), Cyclic Voltammetry (CV), Difference Pulse Voltammetry (DPV), Atomic Force Microscopy (AFM), and Electrochemical Impedance Spectroscopy (EIS) studies are applied. We looked at the ternary composites' optical, electrical, and sensor studies. The present ternary nanocomposite (SGP2) with higher sensitivity of 11.69 µA mM cm −2 and low limit of detection 0.758 µM is a better material for the H 2 O 2 sensor. The modification of the sensor electrode utilizing graphene oxide-decorated SnO 2 quantum dots/polypyrrole ternary composites has been developed to enhance the sensing capabilities of H 2 O 2 sensors.

Synthesis of Graphene Oxide
The modified Hummer's method was used for the synthesis of GO. In a conical flask held at 0 • C with continuous stirring, 1.5 g of NaNO 3 , 1.5 g of graphite powder, and 23 mL of concentrated H 2 SO 4 dissolved in 500 mL of deionized water were mixed. In addition, 2.5 g of KMnO 4 were added to the flask and stirred for 3 h. Dropwise, 46 mL of deionized water were added to the flask and heated at 60 • C for 2 h with constant stirring. With constant stirring for an hour, 10 mL of H 2 O 2 were added to the flask. Following the change in colour of the solution, the suspension was filtered and washed several times with deionized water before drying for 2 h at 50 • C.

Synthesis of SGP2 Ternary Composite
The SGP2 ternary composite was created using in situ polymerization of pyrrole with HCl and FeCl 3 as an initiator. Drop-by-drop additions of SnO 2 QDs and GO were made after 2 mL of pyrrole monomer were added to 1 M HCl (100 mL) and agitated for an hour. After being sonicated for 30 min, the above-mentioned suspension/solution was kept at 0 • C for 24 h. The pyrrole suspension was then kept at 0 • C with constant stirring for a day to allow for polymerization, and then 11.354 g of FeCl 3 were added drop-by-drop. A ternary composite powder made of SnO 2 QDs, graphene oxide, and PPy was formed after the suspension was centrifuged for 15 min at 3000 rpm. The schematic representation of synthesis of SGP2 ternary composite for electrochemical sensor was shown in Scheme 1. The 1.9 g of N2H4. H2O (0.3 M) and 3.79 g of SnCl4·5H2O (0.1 M) were mixed together in 200 mL of distilled water with constant stirring. SnCl4 reacted immediately with hydrazine hydrate (N2H4. H2O) to form a slurry-like white precipitate. After stirring for 20 min, the solution was placed in a Teflon-lined autoclave fixed at 180 °C for 24 h. SnO2QDs were created by centrifuging the mixture for 30 min at 3000 rpm, rinsing it with distilled water, and drying it for two hours at 50 °C.

Synthesis of Graphene Oxide
The modified Hummer's method was used for the synthesis of GO. In a conical flask held at 0 °C with continuous stirring, 1.5 g of NaNO3, 1.5 g of graphite powder, and 23 mL of concentrated H2SO4 dissolved in 500 mL of deionized water were mixed. In addition, 2.5 g of KMnO4 were added to the flask and stirred for 3 h. Dropwise, 46 mL of deionized water were added to the flask and heated at 60 °C for 2 h with constant stirring. With constant stirring for an hour, 10 mL of H2O2 were added to the flask. Following the change in colour of the solution, the suspension was filtered and washed several times with deionized water before drying for 2 h at 50 °C.

Synthesis of SGP2 Ternary Composite
The SGP2 ternary composite was created using in situ polymerization of pyrrole with HCl and FeCl3 as an initiator. Drop-by-drop additions of SnO2 QDs and GO were made after 2 mL of pyrrole monomer were added to 1 M HCl (100 mL) and agitated for an hour. After being sonicated for 30 min, the above-mentioned suspension/solution was kept at 0 °C for 24 h. The pyrrole suspension was then kept at 0 °C with constant stirring for a day to allow for polymerization, and then 11.354 g of FeCl3 were added drop-by-drop. A ternary composite powder made of SnO2 QDs, graphene oxide, and PPy was formed after the suspension was centrifuged for 15 min at 3000 rpm. The schematic representation of synthesis of SGP2 ternary composite for electrochemical sensor was shown in Scheme 1.

Characterization Techniques
The Fourier Transform Infrared Spectrometer (FTIR) model ATR ALPHA BRUKER and X-ray diffractometry (XRD) by Rigaku Miniflex-II (Tokyo, Japan) with Cu Kα radiation of wavelength λ = 1.5406 A • at a scan rate of 5 • min −1 with 2θ values from 2 • to 80 • were used to study the chemical change. The Transmission Electron Microscope was used to investigate the TEM (model JEOL, JEM-2100, Peabody, MA, USA), with the Schottky type field emission gun as an electron source, with nano and convergent beam modes as operating modes (Operating HT 80-200 kV), with lattice resolution as 0.1 nm. The CH166E electrochemical workstation was used to record the electrochemical measurements. The dielectric study was conducted by using the Wayne kerr 6500 B series Impedance Analyser, Hemer, Germany.

FTIR Study
In order to create a SnO 2 quantum dots hybrid complex, hydrazine hydrate interacts with tin chloride. This interaction results in vibrational bands in the FTIR spectra of SnO 2 QDs shown in Figure 1. The N-H is attributed to the peaks at 954 cm −1 that result from bending vibration. The twist and wag bands at 1505 cm −1 and 1219 cm −1 , respectively, are evident between two metal ions. The O-H vibration of the absorbed water contributes to the peak at 1621 cm −1 . The peaks at 2340 cm −1 , 3051 cm −1 , and 3714 cm −1 are evidence that SnO 2 quantum dots are in their crystalline form [26]. and X-ray diffractometry (XRD) by Rigaku Miniflex-II (Tokyo, Japan) with Cu Kα radia tion of wavelength λ = 1.5406 A° at a scan rate of 5° min −1 with 2θ values from 2° to 80 were used to study the chemical change. The Transmission Electron Microscope was use to investigate the TEM (model JEOL, JEM-2100, Peabody, MA, USA), with the Schottk type field emission gun as an electron source, with nano and convergent beam modes a operating modes (Operating HT 80-200 kV), with lattice resolution as 0.1 nm. The CH166 electrochemical workstation was used to record the electrochemical measurements. Th dielectric study was conducted by using the Wayne kerr 6500 B series Impedance Ana lyser, Hemer, Germany.

FTIR Study
In order to create a SnO2 quantum dots hybrid complex, hydrazine hydrate interact with tin chloride. This interaction results in vibrational bands in the FTIR spectra of SnO QDs shown in Figure 1. The N-H is attributed to the peaks at 954 cm −1 that result from bending vibration. The twist and wag bands at 1505 cm −1 and 1219 cm −1 , respectively, ar evident between two metal ions. The O-H vibration of the absorbed water contributes t the peak at 1621 cm −1 . The peaks at 2340 cm −1 , 3051 cm −1 , and 3714 cm −1 are evidence tha SnO2 quantum dots are in their crystalline form [26]. A distinctive peak at 3423 cm −1 caused by the O-H group's presence in the GO. Th peaks at 1733 cm −1 and 1047 cm −1 , respectively, indicate the COOH (carboxy) and C-O-(epoxide). In addition, 1494 cm −1 represents the remaining sp 2 carbon in graphite. The PP has two bands: one at 1034 cm −1 , which corresponds to the stretching vibration of the C-N in-plane ring vibration with high conjugation, and one at 1535 cm −1 , which corresponds t the C-C bending vibration [27]. Furthermore, =C-N out of plane deformation is repre sented by the band seen near 909 cm −1 [28]. The formation of polypyrrole is confirmed b the band at 3748 and 2329 cm −1 , which is due to the N-H and C-H stretching vibration [29]. The peak of SGP2 at 956 cm −1 can be attributed to the ring stretching mode of PP present in the composite and 1653 cm −1 assigned from the O-H stretching of SnO2 presen A distinctive peak at 3423 cm −1 caused by the O-H group's presence in the GO. The peaks at 1733 cm −1 and 1047 cm −1 , respectively, indicate the COOH (carboxy) and C-O-C (epoxide). In addition, 1494 cm −1 represents the remaining sp 2 carbon in graphite. The PPy has two bands: one at 1034 cm −1 , which corresponds to the stretching vibration of the C-N in-plane ring vibration with high conjugation, and one at 1535 cm −1 , which corresponds to the C-C bending vibration [27]. Furthermore, =C-N out of plane deformation is represented by the band seen near 909 cm −1 [28]. The formation of polypyrrole is confirmed by the band at 3748 and 2329 cm −1 , which is due to the N-H and C-H stretching vibrations [29]. The peak of SGP2 at 956 cm −1 can be attributed to the ring stretching mode of PPy present in the composite and 1653 cm −1 assigned from the O-H stretching of SnO 2 present in the composite. Therefore, FTIR results show the presence of SnO 2 , GO, PPy in the ternary SGP2 composite.

XRD Analysis
The XRD analysis depicted in Figure 2 was used to examine the polycrystalline phase of SnO 2 QDs. All the peaks indexed in the SnO 2 QDS were comparable with ICDD No. 41-1445 without the presence of impurities [30]. The average crystallite size was calculated by using the Scherrer equation, the curve divided by maximum height, in radian). The average crystallite size of SnO2 QDs obtained is 2.78 nm, which is well in agreement with the TEM data.
The graphene's oxygen functional group is indicated by the large diffraction peak at 2θ = 9.78° with (001) crystal plane [31]. The small peaks at 2θ = 20° and 42° indicate that graphene and an oxygen atom are not completely linked. The broad peak at approximately 2θ = 24.63° is responsible for the polypyrrole's amorphous character [28]. The SGP2 composite exhibits all the distinctive peaks of SnO2 QDs, GO, and PPy. The polymer and SnO2 QDs do not aggregate on the graphene oxide surface, and they are evenly distributed throughout the SGP2 composite, as seen by the broad peak at 2θ = 26.2°, which represents the polymer present in the composite.

TEM Analysis
SnO2 QDs are depicted in Figure 3a,b in their respective High Resolution-TEM and TEM images, and Figure 3c depicts the corresponding selected region electron diffraction patterns, which clearly demonstrate lattice fringes. The lattice spacing of around 0.33 nm was used to study the tetragonal crystal structure of SnO2 QDs, as illustrated in Figure 3a. L = kλ/βcosθ, where crystallite size (L), λ is the wavelength of Cu-kα radiation 1.5406 A • , θ the Bragg diffraction angle (in radian), and β the integral breadth (i.e., area under the curve divided by maximum height, in radian). The average crystallite size of SnO 2 QDs obtained is 2.78 nm, which is well in agreement with the TEM data.
The graphene's oxygen functional group is indicated by the large diffraction peak at 2θ = 9.78 • with (001) crystal plane [31]. The small peaks at 2θ = 20 • and 42 • indicate that graphene and an oxygen atom are not completely linked. The broad peak at approximately 2θ = 24.63 • is responsible for the polypyrrole's amorphous character [28]. The SGP2 composite exhibits all the distinctive peaks of SnO 2 QDs, GO, and PPy.
The polymer and SnO 2 QDs do not aggregate on the graphene oxide surface, and they are evenly distributed throughout the SGP2 composite, as seen by the broad peak at 2θ = 26.2 • , which represents the polymer present in the composite.

TEM Analysis
SnO 2 QDs are depicted in Figure 3a,b in their respective High Resolution-TEM and TEM images, and Figure 3c depicts the corresponding selected region electron diffraction patterns, which clearly demonstrate lattice fringes. The lattice spacing of around 0.33 nm was used to study the tetragonal crystal structure of SnO 2 QDs, as illustrated in Figure 3a.
In hydrothermal settings, the reaction temperature, reaction time, and solution pH all affect the size morphology of the QDs. The SnO 2 quantum dots change into larger sizes with a cubic shape when the pH value is altered [32]. Figure 3b exhibits spherical SnO 2 QDs with particle sizes ranging from 2 to 5 nm that were produced following a 24-h heating period at 180 • C and a pH of 10. The wellcrystallized state of the rutile tetragonal SnO 2 QDs is confirmed by the SAED pattern in Figure 3c. The TEM image of graphene oxide shows the transparent graphene sheet with a thin-film structure that is the result of the rapid elimination of intercalated oxygen caused by the exfoliation or sonication technique used to eliminate the multi layered disorganized graphene sheets shown in Figure 3d,e [33]. Figure 3f depicts the black dots array of SnO 2 quantum dots distributed across the graphene sheet as a result of the SnO 2 QDs and PPy's strong electrostatic attraction to one another. In the SGP2 nanocomposite, SnO 2 QDs were dispersed into the GO and PPy layers. The SnO 2 QDs are efficiently formed on the graphene nanosheets' surface, and these thin graphene layers can significantly increase the composite's electrical conductivity. Additionally, the graphene sheets' individual SnO 2 QDs can speed up the diffusion of the electrolyte away from the electrode. When the structures are utilized as electrochemical electrodes, restacking of the graphene layer renders the final material less porous and electrolyte infiltration more challenging. The attachment of SnO 2 QDs may prevent the restacking of graphene layers in composites. Electrochemical studies have proven that the intercalation of SnO 2 QDS improves the material's cyclic stability by facilitating the transport of electrolyte ions into electrodes. In hydrothermal settings, the reaction temperature, reaction time, and solution pH all affect the size morphology of the QDs. The SnO2 quantum dots change into larger sizes with a cubic shape when the pH value is altered [32]. Figure 3b exhibits spherical SnO2 QDs with particle sizes ranging from 2 to 5 nm that were produced following a 24-h heating period at 180 °C and a pH of 10. The well-crystallized state of the rutile tetragonal SnO2 QDs is confirmed by the SAED pattern in Figure  3c. The TEM image of graphene oxide shows the transparent graphene sheet with a thinfilm structure that is the result of the rapid elimination of intercalated oxygen caused by the exfoliation or sonication technique used to eliminate the multi layered disorganized graphene sheets shown in Figure 3d,e [33]. Figure 3f depicts the black dots array of SnO2 quantum dots distributed across the graphene sheet as a result of the SnO2 QDs and PPy's strong electrostatic attraction to one another. In the SGP2 nanocomposite, SnO2 QDs were dispersed into the GO and PPy layers. The SnO2QDs are efficiently formed on the graphene nanosheets' surface, and these thin graphene layers can significantly increase the composite's electrical conductivity. Additionally, the graphene sheets' individual SnO2QDs can speed up the diffusion of the electrolyte away from the electrode. When the structures are utilized as electrochemical electrodes, restacking of the graphene layer renders the final material less porous and electrolyte infiltration more challenging. The attachment of SnO2QDs may prevent the restacking of graphene layers in composites. Electrochemical studies have proven that the intercalation of SnO2QDS improves the material's cyclic stability by facilitating the transport of electrolyte ions into electrodes.

Fabrication of Sensor and Electrochemical Study
The glassy carbon electrode (GCE) was sonicated with water and ethanol before being polished with an alumina paste of 0.5 μM and 0.05 μM prior to electrode modification. Following thorough cleaning and polishing, the GCEs were changed by coating them with SGP2 active material and Polyvinylidene fluoride binder; 3 μL of SGP2 composite solution were drop-casted on the surface of clean GCE having 0.07 cm 2 active surface electrode area and allowed to adsorb upon drying in a vacuum oven. The CHI 660E electrochemical workstation was connected to a standard three-electrode setup with platinum wire as the

Fabrication of Sensor and Electrochemical Study
The glassy carbon electrode (GCE) was sonicated with water and ethanol before being polished with an alumina paste of 0.5 µM and 0.05 µM prior to electrode modification. Following thorough cleaning and polishing, the GCEs were changed by coating them with SGP2 active material and Polyvinylidene fluoride binder; 3 µL of SGP2 composite solution were drop-casted on the surface of clean GCE having 0.07 cm 2 active surface electrode area and allowed to adsorb upon drying in a vacuum oven. The CHI 660E electrochemical workstation was connected to a standard three-electrode setup with platinum wire as the counter electrode, Ag/AgCl as the reference electrode, and SGP2 modified GCE as the working electrode. For SGP2 modified GCE, several H 2 O 2 concentrations ranging from 0.  Figure 4a, in contrast to SGP2 GCE, which displays a peak current response of roughly 36 mA, the observed bare GCE and SGP2 GCE of the CV curve demonstrate the absence of analytes. In Figure 4b, bare GCE exhibits minimal electrocatalytic activity for the detection of H 2 O 2 , while SGP2 GCE exhibits a prominent oxidation peak in the presence of H 2 O 2 analyte and a maximum peak current response of 160 mM, which is a four times higher current rate than in the absence of analyte. Due to the functionality of graphene and oxygen, SGP2 GCE is quickly oxidized.
with SGP2 at a scan rate of 30 mVs in 0.1 M PBS solution without H2O2. Figure 4a, in contrast to SGP2 GCE, which displays a peak current response of roughly 36 mA, the observed bare GCE and SGP2 GCE of the CV curve demonstrate the absence of analytes. In Figure 4b, bare GCE exhibits minimal electrocatalytic activity for the detection of H2O2, while SGP2 GCE exhibits a prominent oxidation peak in the presence of H2O2 analyte and a maximum peak current response of 160 mM, which is a four times higher current rate than in the absence of analyte. Due to the functionality of graphene and oxygen, SGP2 GCE is quickly oxidized. CV curve in Figure 5a was measured in the presence of various concentrations of H2O2 from 0.1 mM to 0.8 mM with PBS electrolyte. As the concentration of analytes was increased, the oxidation peak gradually moved toward the higher current rate, and the CV curve maintained its shape at the higher current rate, indicating the high electrocatalytic activity in the fabricated SGP2 GCE. Figure 5b shows the SGP2 CV curve measured at various scan rates from 10 mV s −1 to 80 mV s −1 in the presence of H2O2. Since the peak current rate increased as the scan rate was changed, the CV curve remained the same shape while the oxidation current only changed, and the SGP2 GCE has good electroactive material for sensor applications. Figure 5c shows the SGP2 GCE's calibration curve when H2O2 is present. As the H2O2 concentration increases, the oxidation peak current becomes linearly proportional to the analyte species, yielding a regression value of R 2 at ~0.988. CV curve in Figure 5a was measured in the presence of various concentrations of H 2 O 2 from 0.1 mM to 0.8 mM with PBS electrolyte. As the concentration of analytes was increased, the oxidation peak gradually moved toward the higher current rate, and the CV curve maintained its shape at the higher current rate, indicating the high electrocatalytic activity in the fabricated SGP2 GCE. Figure 5b shows the SGP2 CV curve measured at various scan rates from 10 mV s −1 to 80 mV s −1 in the presence of H 2 O 2 . Since the peak current rate increased as the scan rate was changed, the CV curve remained the same shape while the oxidation current only changed, and the SGP2 GCE has good electro-active material for sensor applications. Figure 5c shows the SGP2 GCE's calibration curve when H 2 O 2 is present. As the H 2 O 2 concentration increases, the oxidation peak current becomes linearly proportional to the analyte species, yielding a regression value of R 2 at~0.988. The SGP2 GCE calibration plot in Figure 5d demonstrates that the scan rate is being increased, and the peak current is moving toward a higher current rate. The manufactured electrode also shows that the scan rate effect is good, with an observed regression value of R 2 at ~0.998. The SGP2 GCE calibration plot in Figure 5d demonstrates that the scan rate is being increased, and the peak current is moving toward a higher current rate. The manufactured electrode also shows that the scan rate effect is good, with an observed regression value of R 2 at~0.998. Figure 6a shows the DPV curve of the SGP2 GCE in the presence of various concentrations of H 2 O 2 analyte. As hydrogen peroxide was continuously added to the PBS electrolyte at concentrations ranging from 0.5 mM to 7.0 mM, the oxidation peak current rate increased. As a result, the SGP2 GCE quickly detected the analyte and provided a high current rate because of the layer-structured GO. Figure 6b

Differential Pulse Voltametry Analysis of SGP2 GCE
The SGP2 GCE exhibits a high sensitivity of 11.69 µ A mM cm −2 and a low limit of detection (LOD) of 0.758 µ M; these results suggest that the archived value is higher than the previously reported results as mentioned in literature [35][36][37]. In Table 1, a comparative study of the analytical performance of the proposed SGP2 modified GCE sensor with the previously published sensors for H2O2 detection is presented [4,[38][39][40][41]. To the best of our knowledge, the proposed SGP2 modified GCE has a suitable sensor electrode for various environmental and clinical diagnostic applications.

Electrochemical Impedance Spectroscopy (EIS)
The properties of the fabricated electrode interface are further analyzed using EIS. A typical Nyquist plot has a semicircle segment that represents the electron-transfer resistance (Rct) at higher frequencies and a linear section that represents the diffusion limiting process at lower frequencies. The Warburg resistance (ZW), which is caused by fre-a b The SGP2 GCE exhibits a high sensitivity of 11.69 µA mM cm −2 and a low limit of detection (LOD) of 0.758 µM; these results suggest that the archived value is higher than the previously reported results as mentioned in literature [35][36][37]. In Table 1, a comparative study of the analytical performance of the proposed SGP2 modified GCE sensor with the previously published sensors for H 2 O 2 detection is presented [4,[38][39][40][41]. To the best of our knowledge, the proposed SGP2 modified GCE has a suitable sensor electrode for various environmental and clinical diagnostic applications.

Electrochemical Impedance Spectroscopy (EIS)
The properties of the fabricated electrode interface are further analyzed using EIS. A typical Nyquist plot has a semicircle segment that represents the electron-transfer resistance (R ct ) at higher frequencies and a linear section that represents the diffusion limiting process at lower frequencies. The Warburg resistance (ZW), which is caused by frequency-related ionic diffusion in the electrolyte and electrode surface, represents the slope area. The impedance plot at low frequency should be linear as a result of the presence of a "constant phase element". Figure 7 depicts the charge transport procedures in the H 2 O 2 -containing SGP2 modified electrode, doped GCE electrode, and bare GCE electrode. To understand the process of electron transfer, the charge transfer resistance (R ct ) at the electrode-electrolyte interface is computed. The dielectric and insulating properties of the electrode affect the value of R ct . Rct is a crucial factor in determining the coated electrode material's effectiveness in transferring charges from a solution to an electrode. It has been noted that SGP2-doped GCE in the presence of H2O2 has an RCt value of 168.32 while bare and SGP2-doped GCE have Rct values of 180.40 and 171.01, respectively. This implies that getting a better sensor response is possible when PPY/GO and SnO2 are present in the composite. SnO2 QDS's greater conductivity improves the kinetics of charge transfer. The EIS results are accompanied by the CV data, which showed that the SGP2 nanocomposite in the presence of H2O2 exhibited higher peak current.

Selectivity Study SGP2 Glassy Carbon Electrode
Interference study is a useful method to check the selectivity of developed electrochemical sensor towards H2O2 detection based on SGP2 nanocomposites. Examination of the interference of SGP2 modified GCE for H2O2 was determined in the presence of 2-fold higher concentration of various interferences substances like urea, glucose, L-cysteine, KCl and alanine. The DPV curve (Figure 8a) shows the no extra peak observed in the figure, which indicates that, with the addition of different interference substances, no change in the DPV curve proves that the fabricated sensor had good selectivity towards the H2O2 determination. Figure 8b shows that the oxidation peak current of (I/Io) was examined by the presence of interference (I) and absence of interference (Io); this clearly shows that the interference substance has no effect on the H2O2 and an achieved RSD of less than 1%. A fabricated SGP2 modified GCE sensor is suitable for various clinical diagnosis applications. R ct is a crucial factor in determining the coated electrode material's effectiveness in transferring charges from a solution to an electrode. It has been noted that SGP2-doped GCE in the presence of H 2 O 2 has an R Ct value of 168.32 while bare and SGP2-doped GCE have R ct values of 180.40 and 171.01, respectively. This implies that getting a better sensor response is possible when PPY/GO and SnO 2 are present in the composite. SnO 2 QDS's greater conductivity improves the kinetics of charge transfer. The EIS results are accompanied by the CV data, which showed that the SGP2 nanocomposite in the presence of H 2 O 2 exhibited higher peak current.

Selectivity Study SGP2 Glassy Carbon Electrode
Interference study is a useful method to check the selectivity of developed electrochemical sensor towards H 2 O 2 detection based on SGP2 nanocomposites. Examination of the interference of SGP2 modified GCE for H 2 O 2 was determined in the presence of 2-fold higher concentration of various interferences substances like urea, glucose, L-cysteine, KCl and alanine. The DPV curve (Figure 8a) shows the no extra peak observed in the figure, which indicates that, with the addition of different interference substances, no change in the DPV curve proves that the fabricated sensor had good selectivity towards the H 2 O 2 determination. Figure 8b shows that the oxidation peak current of (I/Io) was examined by the presence of interference (I) and absence of interference (Io); this clearly shows that the interference substance has no effect on the H 2 O 2 and an achieved RSD of less than 1%. A fabricated SGP2 modified GCE sensor is suitable for various clinical diagnosis applications.

AFM Analysis
To evaluate the structural morphology and surface roughness of the SGP2 composites by AFM investigation (Figure 9), AFM images of the SGP2 composite show a spherical morphology, and AFM 3-D micrograph images of the SGP2 show a uniform and homogeneous morphology with high prominence, with an average roughness obtained from the topological study of 1.863 nm and a particle size of 0.3 to 5 nm. This result indicates the compatibility of the polymer matrix with nanoparticles [42].

Dielectric Study of SnO2, GO, SGP2 Composite Film
With a complex dielectric constant, the real and imaginary parts of the dielectric properties are typically examined using the equation ε* = ε′ − I ε″, where ε″ and ε′ are the imaginary and real parts, respectively [38]. In the presence of an external field, it releases stored and lost energy. The dipole moment polarizability is related to the dielectric constant shown in Figure 10. The plots of the frequency-related dielectric constant and dielectric loss (ε′ and ε″) demonstrate that the dielectric behaviour of polymer composites depends on a lower frequency and is independent of a higher frequency. Utilizing capacitance Cp and loss factor tan δ, the real and imaginary components of dielectric properties are computed using the Equations (2) and (3):

AFM Analysis
To evaluate the structural morphology and surface roughness of the SGP2 composites by AFM investigation (Figure 9), AFM images of the SGP2 composite show a spherical morphology, and AFM 3-D micrograph images of the SGP2 show a uniform and homogeneous morphology with high prominence, with an average roughness obtained from the topological study of 1.863 nm and a particle size of 0.3 to 5 nm. This result indicates the compatibility of the polymer matrix with nanoparticles [42].

AFM Analysis
To evaluate the structural morphology and surface roughness of the SGP2 compo sites by AFM investigation (Figure 9), AFM images of the SGP2 composite show a spher ical morphology, and AFM 3-D micrograph images of the SGP2 show a uniform and ho mogeneous morphology with high prominence, with an average roughness obtained from the topological study of 1.863 nm and a particle size of 0.3 to 5 nm. This result indicates the compatibility of the polymer matrix with nanoparticles [42].

Dielectric Study of SnO2, GO, SGP2 Composite Film
With a complex dielectric constant, the real and imaginary parts of the dielectric properties are typically examined using the equation ε* = ε′ − I ε″, where ε″ and ε′ are the imaginary and real parts, respectively [38]. In the presence of an external field, it releases stored and lost energy. The dipole moment polarizability is related to the dielectric con stant shown in Figure 10. The plots of the frequency-related dielectric constant and die lectric loss (ε′ and ε″) demonstrate that the dielectric behaviour of polymer composites depends on a lower frequency and is independent of a higher frequency. Utilizing capac itance Cp and loss factor tan δ, the real and imaginary components of dielectric properties are computed using the Equations (2)

Dielectric Study of SnO 2 , GO, SGP2 Composite Film
With a complex dielectric constant, the real and imaginary parts of the dielectric properties are typically examined using the equation ε* = ε − I ε , where ε and ε are the imaginary and real parts, respectively [38]. In the presence of an external field, it releases stored and lost energy. The dipole moment polarizability is related to the dielectric constant shown in Figure 10. The plots of the frequency-related dielectric constant and dielectric loss (ε and ε ) demonstrate that the dielectric behaviour of polymer composites depends on a lower frequency and is independent of a higher frequency. Utilizing capacitance Cp and loss factor tan δ, the real and imaginary components of dielectric properties are computed using the Equations (2) and (3): Lower frequency increases owing to the energy accumulation between the polyme composite and the electrode. However, charge carrier density increases at high tempera tures due to ion aggregation dissociation, which, as a result, increases both ε′ and ε shown in Figures 10 and 11. Thereby, due to chain scissioning in polymer composites, th increasing trend of ε′ at various temperatures indicates the generation of bandgap defect [43]. At low frequencies less than 100 Hz, the dielectric constant of all pure SnO2, GO, an SGP2 composites increased dramatically. Lower frequency increases owing to the energy accumulation between the polymer composite and the electrode. However, charge carrier density increases at high temperatures due to ion aggregation dissociation, which, as a result, increases both ε and ε shown in Figures 10 and 11. Thereby, due to chain scissioning in polymer composites, the increasing trend of ε at various temperatures indicates the generation of bandgap defects [43]. At low frequencies less than 100 Hz, the dielectric constant of all pure SnO 2 , GO, and SGP2 composites increased dramatically.
When compared to comparable polymer nanocomposite values in the literature, the dielectric constant for SnO 2 /GO/PPy ternary composites (SGP2) is in the region of 3.5 × 10 6 , which is high [44]. This might be because the composite contains GO and SnO 2 nanocrystals. This suggests that the substantial polarization delocalization [45] may be connected with the high dielectric response of SGP2 composites at low frequency (100 Hz-1 kHz). In comparison to pure SnO 2 film, the ε and ε" values of SGP2 composites are 2 to 3 times greater. Thus, the results demonstrate temperature-dependent variations of the dielectric parameters. All of the values rise with temperature, and for SGP2, as depicted in Figures 10 and 11c, the values are maximum at a certain temperature. This is explained by the interfacial polymerization of SGP2 composites from the external field at high temperatures. As a result, the ternary polymer composite is an effective material for studying how composites behave electrically. When compared to comparable polymer nanocomposite values in the literature, the dielectric constant for SnO2/GO/PPy ternary composites (SGP2) is in the region of 3.5 × 10 6 , which is high [44]. This might be because the composite contains GO and SnO2 nanocrystals. This suggests that the substantial polarization delocalization [45] may be connected with the high dielectric response of SGP2 composites at low frequency (100 Hz-1 kHz). In comparison to pure SnO2 film, the ε′ and ε″ values of SGP2 composites are 2 to 3 times greater. Thus, the results demonstrate temperature-dependent variations of the dielectric parameters. All of the values rise with temperature, and for SGP2, as depicted in Figures 10 and 11c, the values are maximum at a certain temperature. This is explained by the interfacial polymerization of SGP2 composites from the external field at high temperatures. As a result, the ternary polymer composite is an effective material for studying how composites behave electrically.

Modulus Study
To better understand the dielectric process, use the electric modulus M* = M′ + iM′′, where M′ and M′′ are real and imaginary components of the complex dielectric modulus M*, which may be computed from the ε′ and ε″ using the Equations (4) and (5) [46]:

Modulus Study
To better understand the dielectric process, use the electric modulus M* = M + iM , where M and M are real and imaginary components of the complex dielectric modulus M*, which may be computed from the ε and ε" using the Equations (4) and (5) [46]: Because of the suppression of electrode polarization at low frequencies, M approaches zero; however, M increases with frequency, indicating that the restoring force determines the mobility of charge carriers when an electric field is present. Due to the charge carrier's short-range mobility and the conduction electrons' storage mobility, M" reaches a maximum value of 1.46 × 10 −2 as illustrated in Figure 13c. Figure 14 shows the AC conductivity of the ternary composites of SnO 2 , GO, and SGP2. For SGP composites, the critical frequency is 2 kHz, after which there is a modest rise in conductivity with frequency but no appreciable change in conductivity. Because of the suppression of electrode polarization at low frequencies, M′ approaches zero; however, M′ increases with frequency, indicating that the restoring force determines the mobility of charge carriers when an electric field is present. Due to the charge carrier's short-range mobility and the conduction electrons' storage mobility, M′′ reaches a maximum value of 1.46 × 10 −2 as illustrated in Figure 13c.  Because of the suppression of electrode polarization at low frequencies, M′ approaches zero; however, M′ increases with frequency, indicating that the restoring force determines the mobility of charge carriers when an electric field is present. Due to the charge carrier's short-range mobility and the conduction electrons' storage mobility, M′′ reaches a maximum value of 1.46 × 10 −2 as illustrated in Figure 13c.   Figure 14 shows the AC conductivity of the ternary composites of SnO2, GO, and SGP2. For SGP composites, the critical frequency is 2 kHz, after which there is a modest rise in conductivity with frequency but no appreciable change in conductivity. Conductivity increases linearly with frequency and temperature beyond 2 kHz, and because of the free charges in the chain, it reaches the charge carrier's vibration frequency together with the polymer at this point. Due to active trapped charges, conductivity is almost independent at low frequencies and reliant on high frequencies. The AC conductivity was calculated by using the Equation (6), [47] σac = ωcpd tan δ/A (6) where A is the electrode area, d is the thickness of the sample, and ε0 is the dielectric permittivity in free space (8.85 × 10 −12 F/m). According to Figure 14, the conductivity rises with temperature and frequency. The conductivity of the ternary composite material is higher than that of pure SnO2 and GO. The σac values for SnO2, GO and SGP2 are −2.2 S/cm, −1.294 S/cm, and −1.07 S/cm, respectively. The higher chain order of the polymer composite caused by the significant intercalation between the pure SnO2QDs and GO with PPy is attributed to the SGP2's maximum value agreement with dielectric data and conductivity. As the SnO2 QD concentration rises, the ions in the polymer have more flexibility, which enhances conductivity. Conductivity increases linearly with frequency and temperature beyond 2 kHz, and because of the free charges in the chain, it reaches the charge carrier's vibration frequency together with the polymer at this point. Due to active trapped charges, conductivity is almost independent at low frequencies and reliant on high frequencies. The AC conductivity was calculated by using the Equation (6) [47], σ ac = ωc p d tan δ/A (6) where A is the electrode area, d is the thickness of the sample, and ε 0 is the dielectric permittivity in free space (8.85 × 10 −12 F/m). According to Figure 14, the conductivity rises with temperature and frequency. The conductivity of the ternary composite material is higher than that of pure SnO 2 and GO. The σ ac values for SnO 2 , GO and SGP2 are −2.2 S/cm, −1.294 S/cm, and −1.07 S/cm, respectively. The higher chain order of the polymer composite caused by the significant intercalation between the pure SnO 2 QDs and GO with PPy is attributed to the SGP2's maximum value agreement with dielectric data and conductivity. As the SnO 2 QD concentration rises, the ions in the polymer have more flexibility, which enhances conductivity.

Conclusions
In conclusion, SGP2 nanocomposites synthesized utilizing an in situ chemical oxidative polymerization process are used to manufacture a newly created and efficient hydrogen peroxide electrochemical sensor. The produced nanocomposites were examined utilizing impedance analysis, FTIR, XRD, and AFM. The measurement of the dielectric properties shows that the electrical and dielectric properties of polypyrrole and SnO 2 /GO are successfully combined in the synthesized SGP2 nanocomposite. The measurement of the dielectric properties shows that the electrical and dielectric properties of polypyrrole and SnO 2 /GO are successfully combined in the synthesized SGP2 nanocomposite. A cyclic voltammetry analysis revealed that the SGP2 modified glassy carbon electrode-based electrochemical sensor demonstrated an excellent electrocatalytic effect for H 2 O 2 . The current amperometric sensor made from SGP2 modified GCE has a low LOD of 0.758 µM and high sensitivity of 11.69 µA mM cm −2 throughout a broad linear range of 0.1 mM to 0.8 mM. According to our findings, conductive polymer and metal oxide combined together could provide an efficient method of fabricating advanced and cost-effective electrochemical sensors.