Rational Design of SnO2 Hollow Microspheres Functionalized with Derivatives of Pt Loaded MOFs for Superior Formaldehyde Detection

In this work, SnO2 hollow microspheres functionalized with different incorporated amounts of Pt@Co3O4 complex catalyst were innovatively designed by using an MOF template. The results show that sensor based on the optimal incorporated amount of Pt@Co3O4 not only greatly enhances the response value of SnO2 to formaldehyde (Rair/Rformaldehyde = 4240 toward 100 ppm) but also decreases the low detection limit (50 ppb), which is quite outstanding compared with other SnO2-based formaldehyde sensors. Further analysis proves that the content of oxygen vacancy and chemisorbed oxygen and the catalytic effect of ultra-small Pt play the key roles in improving the formaldehyde sensing performance. Meanwhile, this present work demonstrates that oxide semiconductors functionalized with the derivatives of MOF templated catalysts may lead to the discovery of new material systems with outstanding sensing performance.


Introduction
With the improvement of living standards, people are paying more and more attention to air quality. Among the different kinds of volatile organic compounds (VOCs), formaldehyde has been identified as a carcinogen and teratogenic substance by the US Environmental Protection Agency and the World Health Organization [1,2]. When its concentration in air is 0.4-1 ppm, it irritates the eyes, nose and throat. When its concentration continues to increase, exceeding 3 ppm, human cells and tissues are damaged [3,4]. Therefore, the detection of formaldehyde becomes particularly important. At present, infrared absorption spectroscopy, gas chromatography, ultraviolet absorption and chemiluminescence analysis have been developed and used in the detection of formaldehyde [5][6][7][8]. Although these instruments have high accuracy, they are not suitable for formaldehyde detection due to high cost, complex operation and difficult real-time online detection. In recent years, metal oxide semiconductor (MOS) gas sensors have become new hot spots in the research of formaldehyde detection. From a practical view point, MOS sensors need to meet the following key points: (1) high response and low detection limit, which means that the sensor needs to have an obvious response to low concentrations of formaldehyde; (2) high selectivity, which indicates that the sensor needs to have a specific recognition function for formaldehyde; (3) good stability, representing stable output capacity, which determines the effective life of the sensor.
Tin oxide (SnO 2 ), as a typical n-type semiconductor, is demonstrated to have excellent sensing properties for formaldehyde. However, pure SnO 2 sensing material still has many shortcomings, such as low response value, unsatisfactory detection limit and poor selectivity. In traditional approaches, noble metals, such as Pd, Au, Ag and Pt, incorporated into SnO 2 have been synthesized and the gas sensing properties toward formaldehyde have been evaluated. For instance, Ruan's group prepared Pd-decorated hollow SnO 2 nanofibers [9]. The results of sensing performance showed that the SnO 2 modified by Pd had high response to formaldehyde (18.8 toward 100 ppm) and low detection limit (5 ppm) at 160 • C. In Chung et al.'s work, a sensor based on a Au@SnO 2 core-shell structure was successfully built to detect formaldehyde gas [10]. The response value to 50 ppm formaldehyde was about 11 at room temperature. Dong and his colleagues also found that sensors based on Ag-decorated SnO 2 possessed enhanced response (14.4 toward 10 ppm) to formaldehyde compared with the pure SnO 2 [11]. Furthermore, sensors based on Pt incorporated into SnO 2 were also fabricated to detect formaldehyde in previous work [12,13]. They showed a higher response and lower detection limit to formaldehyde which was superior to Pd, Au and Ag-SnO 2 . Furthermore, apart from SnO 2 sensing materials, Pt had also been incorporated in other metal oxides when formaldehyde was selected as the target gas. For example, Dong et al. also found that sensors based on Pt-functionalized NiO possessed enhanced response to formaldehyde compared with the pure NiO [14]. Ultra-fast and highly selective room-temperature formaldehyde sensors have also been obtained by Pt-loaded MoO 3 nanobelts in Gu et al.'s work [15]. Hence, it seems that the incorporation of Pt can indeed improve the sensing characteristics of SnO 2 sensors for detecting formaldehyde. However, it is worth noting that the sizes of Pt nanoparticles obtained in the literature above are mostly greater than 5 nm. In general, the catalytic activity increases drastically as the particle size of noble metals decreases, leading to the significantly enhanced response. Therefore, finding an effective method to obtain ultra-small Pt nanoparticles and then to enhance the formaldehyde sensing properties of SnO 2 is imperative.
Cobalt oxide (Co 3 O 4 ), as a typical p-type semiconductor, is an attractive functional material in the field of gas sensing. Importantly, building a p-n heterojunction between Co 3 O 4 and an n-type MOS has attracted considerable interest in improving the sensing characteristic. Liu [17]. The as-prepared sensing materials displayed a high sensing response of 39 toward 200 ppm formaldehyde at 260 • C. However, incorporation of Co 3 O 4 into SnO 2 to form a heterostructure for formaldehyde sensing applications is rarely reported.
Inspired by the above, in order to further improve the sensing characteristics of formaldehyde, a novel material system of SnO 2 containing Co 3 O 4 and ultra-small Pt nanoparticles should be developed. In this work, an effective catalyst loading method by using MOF templated catalyst (Pt@ZIF-67) was adopted. TEM results indicated that fine Pt nanoparticles of~3 nm were uniformly encapsulated in ZIF-67 without agglomeration. Then, Pt@Co 3 O 4 complex catalysts were unprecedentedly functionalized on SnO 2 hollow microspheres through a solvothermal method followed by calcination. Consequently, as expected, an ultra-sensitive formaldehyde sensor based on Pt@Co 3 O 4 -SnO 2 hollow microspheres was achieved.

Preparation of ZIF-67
The preparation process of ZIF-67 was as follows. Firstly, Co(NO 3 ) 2 ·6H 2 O (582 mg) and 2-methylimidazole (656.8 mg) were added into 25 mL methanol solvent under stirring, respectively. After ten minutes, the two kinds of solution were mixed together. Next, the Nanomaterials 2022, 12, 1881 3 of 15 mixed solution continued to be stirred for half an hour and then aged for one day. The precipitate was collected by centrifugation (6000 r/min, 5 min) and washed with ethanol and dried at 60 • C for 15 h.

Preparation of Pt@ZIF-67
Pt@ZIF-67 was prepared by adopting an improved method as stated in reference [18]. ZIF-67 (40 mg) and (NH 4 ) 2 PtCl 6 (4 mg) were dispersed in 3 mL deionized water and stirred for six hours. During this process, platinum ions would enter the cavity of ZIF-67. Subsequently, sodium borohydride (1 mg/mL) solution was applied to reduce Pt 4+ to Pt 0 . Accordingly, ZIF-67 templated Pt (Pt@ZIF-67) nanoparticles were successfully collected by centrifugation (8000 r/min) and washed six times with deionized water and ethanol alternately, then dried in air at 60 • C for 20 h.

Preparation of Pt@Co 3 O 4 -SnO 2 Hollow Microspheres
The composites of Pt@Co 3 O 4 -SnO 2 hollow microspheres were prepared via a hydrothermal method. SnCl 4 ·5H 2 O (701.2 mg), oxalic acid (63 mg) and an appropriate amount Pt@ZIF-67 (3 mg, 6 mg and 9 mg, respectively) were added into 9 mL deionized water and 16 mL glycerol. After stirring for 15 min, the mixed solution was transferred into a 50 mL stainless steel autoclave lined with Teflon and kept at 160 • C for 12 h in an oven. After the temperature of the oven dropped, the precipitate could be collected by centrifugating (8000 r/min) and washing six times with deionized water and ethanol alternately, and then dried at 60 • C. Ultimately, the precursor was annealed in air at 500 • C for 2 h with a heating rate of 2 • C/min to obtain Pt@Co 3 O 4 -SnO 2 hollow microspheres. The obtained composites were denoted as S3 (3 mg Pt@ZIF-67), S4 (6 mg Pt@ZIF-67) and S5 (9 mg Pt@ZIF-67).
Co 3 O 4 @SnO 2 hollow microspheres (labeled as S2) were prepared through the same experimental procedure of S4 samples, except that the same amount of ZIF-67 was used instead of Pt@ZIF-67 for preparing precursor solution.
The preparation steps of pure SnO 2 hollow microspheres (labeled as S1) were the same as S2-S5 except that Pt@ZIF-67 or ZIF-67 was not added.

Material Characterization
The morphologies and surface characteristics of these samples were observed by scanning electron microscopy (SEM, Merlin Compact, Carl Zeiss NTS GmbH, Oberkochen, Germany). The crystallinity, purity and composition were examined by X-ray diffraction (XRD, Smartlab, Rigaku Corporation, Tokyo, Japan) with Cu-Kα1 radiation (λ = 0.15406 nm). The internal microstructures, crystal planes and element distribution of the samples were analyzed by transmission electron microscope (TEM, Titan G260-300, FEI, Hillsboro, OR, USA), high-resolution TEM (HRTEM) and energy-dispersive X-ray spectroscopy (EDS). Furthermore, the research of oxygen species in the samples and the study of valence states of Pt, Co and Sn were carried out by X-ray photoelectron spectroscopy (XPS, ESCALAB 250Xi, Thermo Scientific K-Alpha, Waltham, MA, USA) with a mono Al K α (1486.6 eV, 6 mA × 12 kV).

Measurement of Formaldehyde Gas Sensors
In this work, ceramic substrate with attached silver-palladium interdigitated electrodes (Ag-Pd IDEs) is adopted, whose specific parameters are shown in Figure 1a. The specific steps of the fabrication of the sensor devices are as follows to ensure that the consistency of the resistance baseline and response of multiple sensors are the same. An appropriate amount (3-5 mg) of the as-prepared samples is mixed with a certain amount (0.3-0.5 mL) of ethanol to form a uniform slurry. The slurry is then applied to the surface of the Ag-Pd IDEs with a small brush to form a dense sensing layer. Figure 1b shows the schematic illustration of the blank sensor coated with the sensing layer. Furthermore, the multifunctional gas sensing testing system, CGS-MT (Beijing Sino Aggtech, Beijing, China), which is composed of a temperature control system, test chamber (5 L) with two sensor channels ( Figure 1c) and circulating water system, is used to analyze the gas sensing performance of the as-obtained samples. The data acquisition is achieved through test software on the computer connected to the CGS-MT instrument. The sensing performance is studied under laboratory conditions (~15 RH%, 18 • C). Nanomaterials 2022, 12, x FOR PEER REVIEW 4 of 15 (0.3-0.5 mL) of ethanol to form a uniform slurry. The slurry is then applied to the surface of the Ag-Pd IDEs with a small brush to form a dense sensing layer. Figure 1b shows the schematic illustration of the blank sensor coated with the sensing layer. Furthermore, the multifunctional gas sensing testing system, CGS-MT (Beijing Sino Aggtech, Beijing, China), which is composed of a temperature control system, test chamber (5 L) with two sensor channels ( Figure 1c) and circulating water system, is used to analyze the gas sensing performance of the as-obtained samples. The data acquisition is achieved through test software on the computer connected to the CGS-MT instrument. The sensing performance is studied under laboratory conditions (~15 RH%, 18 °C). The corresponding gas concentration (e.g., formaldehyde) can be derived from the following Equation [19]: where C (ppm) and M (g/mol) are the concentration and the molecular weight of formaldehyde, respectively. φ and ρ (g/mL) represent the mass fraction (37%) and the density (0.82 g/mL) of the formaldehyde aqueous solution, respectively. V1 (μL) and V2 (5 L) are the volume of formaldehyde aqueous solution to be injected and the volume of the test chamber, respectively.
The details of the complete test procedure are as follows. First, open the circulating water system and put the fabricated sensors into an air-filled test chamber for aging for three days. Afterwards, the sensor resistances gradually tend to a stable value, usually represented by Ra. Second, inject a certain concentration of target gas into the closed chamber with a microliter syringe. After a while, the resistance stabilizes again and is abbreviated as Rg. Then, open the lid of the chamber to refill the entire chamber with fresh air, and the resistance returns to near Ra again. During the test process, the resistance and response change continuously with time and are recorded by the test software on the computer connected to the CGS-MT instrument. The response value and response/recovery times are defined as follows. Taking the n-type MOS sensor to detect reducing gas as an example, the response value is defined as Ra/Rg. The response (τres) and recovery (τrecov) times refer to the time periods from Ra changing to Ra − |Ra − Rg| × 90% and from Rg changing to Rg + |Ra − Rg| × 90%, respectively [15]. The corresponding gas concentration (e.g., formaldehyde) can be derived from the following Equation [19]:

Structural and Morphological Characteristics
where C (ppm) and M (g/mol) are the concentration and the molecular weight of formaldehyde, respectively. ϕ and ρ (g/mL) represent the mass fraction (37%) and the density (0.82 g/mL) of the formaldehyde aqueous solution, respectively. V 1 (µL) and V 2 (5 L) are the volume of formaldehyde aqueous solution to be injected and the volume of the test chamber, respectively. The details of the complete test procedure are as follows. First, open the circulating water system and put the fabricated sensors into an air-filled test chamber for aging for three days. Afterwards, the sensor resistances gradually tend to a stable value, usually represented by R a . Second, inject a certain concentration of target gas into the closed chamber with a microliter syringe. After a while, the resistance stabilizes again and is abbreviated as R g . Then, open the lid of the chamber to refill the entire chamber with fresh air, and the resistance returns to near R a again. During the test process, the resistance and response change continuously with time and are recorded by the test software on the computer connected to the CGS-MT instrument. The response value and response/recovery times are defined as follows. Taking the n-type MOS sensor to detect reducing gas as an example, the response value is defined as R a /R g . The response (τ res ) and recovery (τ recov ) times refer to the time periods from R a changing to R a − |R a − R g | × 90% and from R g changing to R g + |R a − R g | × 90%, respectively [15].  [20]. On the one hand, it indicates that the ZIF-67 synthesized in this work is pure phase. On the other hand, it shows that the encapsulation of noble metal Pt does not change the internal structure of ZIF-67. Figure 2b,c present the SEM images of ZIF-67 and Pt@ZIF-67, respectively. As can be seen, the morphologies of Pt@ZIF-67 do not match well with ZIF-67. Compared with the solid structure of ZIF-67 (Figure 2d), Pt@ZIF-67 shows an obvious core-shell structure (Figure 2e), indicating that the encapsulation of Pt into ZIF-67 destroys the original morphology of ZIF-67 [21,22]. The reason can be explained as follows. During the process of the Pt 4+ entering the ZIF-67 cavity, the NH 4+ coming from (NH 4 ) 2 PtCl 6 hydrolyzes to produce H + , which provides an acidic environment that can corrode and dissolve ZIF-67 from the outside to inside (NH 4

Structural and Morphological Characteristics
. Similar results appear in our previous work [20]. Meanwhile, the conclusion that ZIF-67 can be corroded and dissolved in an acidic environment has also been confirmed in the literature [22,23]. From Figure 2e, it can also be concluded that large numbers of dark nanoparticles of about 3 nm are evenly distributed on ZIF-67. Figure 2f proves that the interplanar spacing of well-distributed dark nanoparticles is 0.225 nm, which exactly corresponds to that of Pt (111) [24]. Figure 2a shows the XRD diffraction patterns of ZIF-67, Pt@ZIF-67 and simulated ZIF-67. The diffraction peaks of as-synthesized ZIF-67 and Pt@ZIF-67 are identical to the results of the published XRD data of simulated ZIF-67 [20]. On the one hand, it indicates that the ZIF-67 synthesized in this work is pure phase. On the other hand, it shows that the encapsulation of noble metal Pt does not change the internal structure of ZIF-67. Figure 2b,c present the SEM images of ZIF-67 and Pt@ZIF-67, respectively. As can be seen, the morphologies of Pt@ZIF-67 do not match well with ZIF-67. Compared with the solid structure of ZIF-67 (Figure 2d), Pt@ZIF-67 shows an obvious core-shell structure ( Figure  2e), indicating that the encapsulation of Pt into ZIF-67 destroys the original morphology of ZIF-67 [21,22]. The reason can be explained as follows. During the process of the Pt 4+ entering the ZIF-67 cavity, the NH 4+ coming from (NH4)2PtCl6 hydrolyzes to produce H + , which provides an acidic environment that can corrode and dissolve ZIF-67 from the outside to inside (NH4 + + H2O → NH3·H2O + H + ). Similar results appear in our previous work [20]. Meanwhile, the conclusion that ZIF-67 can be corroded and dissolved in an acidic environment has also been confirmed in the literature [22,23]. From Figure 2e, it can also be concluded that large numbers of dark nanoparticles of about 3 nm are evenly distributed on ZIF-67. Figure 2f proves that the interplanar spacing of well-distributed dark nanoparticles is 0.225 nm, which exactly corresponds to that of Pt (111) [24]. Figure 3a reveals the XRD diffraction patterns of the five samples. All the recorded diffraction peaks of S1-S5 are well indexed to the characteristic peaks of SnO2 (JCPDS: 77-447). It is remarkably observed that there are no characteristic peaks of Co3O4 or Pt in the XRD patterns, which is mainly due to their relatively small incorporated amounts. Importantly, the influence of the derivatives of ZIF-67 (Pt@ZIF-67) on the phase structures of SnO2 hollow spheres has been found from the 25.5° to 27.5° amplified diffraction peaks ( Figure 3b). It seems that the derivatives of ZIF-67 (Pt@ZIF-67) do not cause any shift in diffraction peaks due to the ultra-low incorporated concentration. Figure 3a reveals the XRD diffraction patterns of the five samples. All the recorded diffraction peaks of S1-S5 are well indexed to the characteristic peaks of SnO 2 (JCPDS: 77-447). It is remarkably observed that there are no characteristic peaks of Co 3 O 4 or Pt in the XRD patterns, which is mainly due to their relatively small incorporated amounts. Importantly, the influence of the derivatives of ZIF-67 (Pt@ZIF-67) on the phase structures of SnO 2 hollow spheres has been found from the 25.5 • to 27.5 • amplified diffraction peaks ( Figure 3b). It seems that the derivatives of ZIF-67 (Pt@ZIF-67) do not cause any shift in diffraction peaks due to the ultra-low incorporated concentration. The SEM results of S1-S5 are shown in Figure 4a-e. It can be clearly seen that the asprepared samples are highly uniform with a hollow sphere-like morphology, and the diameters are about 2 μm. Moreover, from the high-magnification SEM of the inserted images of S1-S5, the nanoparticles on the surface of S2-S4 samples are more dense and smaller compared to S1. In addition, the low-magnification panoramic SEM image of S4 The SEM results of S1-S5 are shown in Figure 4a-e. It can be clearly seen that the as-prepared samples are highly uniform with a hollow sphere-like morphology, and the diameters are about 2 µm. Moreover, from the high-magnification SEM of the inserted images of S1-S5, the nanoparticles on the surface of S2-S4 samples are more dense and smaller compared to S1. In addition, the low-magnification panoramic SEM image of S4 is given in Figure 4f, which not only indicates the good dispersity of these microstructures, but also confirms the porous and hollow property again. The SEM results of S1-S5 are shown in Figure 4a-e. It can be clearly seen that the a prepared samples are highly uniform with a hollow sphere-like morphology, and th diameters are about 2 μm. Moreover, from the high-magnification SEM of the inserte images of S1-S5, the nanoparticles on the surface of S2-S4 samples are more dense an smaller compared to S1. In addition, the low-magnification panoramic SEM image of is given in Figure 4f, which not only indicates the good dispersity of these microstructure but also confirms the porous and hollow property again.  The TEM image of Figure 5a clearly shows the hollow structure of S1 (pure SnO 2 ), which is consistent with the experimental result of the SEM. The inset in Figure 5a is the selected area electron diffractive (SAED) pattern, confirming that pure SnO 2 is polycrystalline in nature. The HRTEM result in Figure 5b reveals the lattice distances of 0.177 nm, 0.264 nm and 0.335 nm which correspond to the crystal plane of SnO 2 (211), (101) and (311), respectively. Figure 5c,d show the relevant TEM and HRTEM images of S4. Obviously, the porosity of the shell of S4 is significantly lower than that of S1, which is also consistent with the result of the SEM images. The EDS elemental mapping images exhibited in Figure 5e exhibited in Figure 5e-h confirm the presence of Sn, Co, O and Pt elements in the S4 samples. It is worth noting that Pt and Co exist in the section shown by the white rectangle, indicating that part of ZIF-67 has not been corroded and dissolved during the stirring and solvothermal process, while the Pt in the yellow rectangle is dispersed in SnO2 hollow microspheres in the form of ultra-small nanoparticles. Additionally, it can be clearly seen that other cobalt element are uniformly distributed in SnO2 hollow microspheres. In summary, both platinum and cobalt exist in two forms, one of them in which both are loaded on SnO2 in the form of Pt@Co3O4 complex catalyst, and the remaining platinum and cobalt are incorporated into the SnO2 hollow microspheres in the form of nanoparticles and doping. The chemical states of Sn, Co and Pt in S1-S5 are verified by the high-resolution XPS spectra in Figure 6a-c. Figure 6a shows the two characteristic peaks of Sn 3d at ~494.3 eV and ~486.1 eV for Sn 3d3/2 and Sn 3d5/2, respectively, suggesting that the chemical state of the Sn element is +4 [25,26]. Figure 6b shows that the valence states of Co in the samples are composed of +2 and +3. In particular, the binding energies of Co 2+ peaks are at ~780.3 eV and ~794.8 eV, and the binding energies corresponding to Co 3+ are ~776.0 eV and ~793.8 eV [27]. Figure 6c displays the valence states of Pt [28,29]. For the XPS peaks of Pt in S3 and S4, they are not obvious due to the ultra-low incorporated amount. Therefore, the high-resolution XPS peak of platinum in S5 is studied. As shown in Figure 6c, peaks of Pt 4f5/2 and Pt 4f7/2 are located at 73.3 and 70.0 eV (gap = 3.3 eV), respectively, illustrating the nature of metal platinum (Pt 0 ). There is no other obvious peak when the binding energy is greater than 75 eV, which also proves that Pt 2+ and Pt 4+ mostly do not exist in the sample [30][31][32]. Figure 6d reveals the high-resolution O 1s XPS analysis of S1-S5. The O 1s spectra can be classified into three oxygen species, named O1, O2 and O3, with binding energy of ~529.5, ~530.5 and ~532.0 eV, respectively. O1 is attributed to the lattice oxygen. O2 represents the hydroxyl groups bonded to the metal cations in the oxygen vacancy region. O3 corresponds to chemisorbed and dissociated oxygen from the water molecules unavoidably adsorbed on the surface [33][34][35][36]. Among them, O1 is relatively stable and The chemical states of Sn, Co and Pt in S1-S5 are verified by the high-resolution XPS spectra in Figure 6a-c. Figure 6a shows the two characteristic peaks of Sn 3d at~494.3 eV and~486.1 eV for Sn 3d 3/2 and Sn 3d 5/2 , respectively, suggesting that the chemical state of the Sn element is +4 [25,26]. Figure 6b shows that the valence states of Co in the samples are composed of +2 and +3. In particular, the binding energies of Co 2+ peaks are at 780.3 eV and~794.8 eV, and the binding energies corresponding to Co 3+ are~776.0 eV and 793.8 eV [27]. Figure 6c displays the valence states of Pt [28,29]. For the XPS peaks of Pt in S3 and S4, they are not obvious due to the ultra-low incorporated amount. Therefore, the high-resolution XPS peak of platinum in S5 is studied. As shown in Figure 6c, peaks of Pt 4f 5/2 and Pt 4f 7/2 are located at 73.3 and 70.0 eV (gap = 3.3 eV), respectively, illustrating the nature of metal platinum (Pt 0 ). There is no other obvious peak when the binding energy is greater than 75 eV, which also proves that Pt 2+ and Pt 4+ mostly do not exist in the sample [30][31][32]. Figure 6d reveals the high-resolution O 1s XPS analysis of S1-S5.
The O 1s spectra can be classified into three oxygen species, named O1, O2 and O3, with binding energy of~529.5,~530.5 and~532.0 eV, respectively. O1 is attributed to the lattice oxygen. O2 represents the hydroxyl groups bonded to the metal cations in the oxygen vacancy region. O3 corresponds to chemisorbed and dissociated oxygen from the water molecules unavoidably adsorbed on the surface [33][34][35][36]. Among them, O1 is relatively stable and does not have any influence on the response. O2, as active sites, can support the adsorption and chemical reaction of oxygen and formaldehyde gas, proving that an increase in O2 content can indeed enhance the response of the sensor [37][38][39]. O3, namely O − (ads), can directly participate in the oxidation-reduction with formaldehyde. Obviously, the total relative percentages of O2 and O3 in S4 have been greatly improved due to the incorporation of an appropriate amount of Pt-Co 3 O 4 in SnO 2 hollow microspheres, whose value has reached 27.5%.
does not have any influence on the response. O2, as active sites, can support the adsorption and chemical reaction of oxygen and formaldehyde gas, proving that an increase in O2 content can indeed enhance the response of the sensor [37][38][39]. O3, namely O -(ads), can directly participate in the oxidation-reduction with formaldehyde. Obviously, the total relative percentages of O2 and O3 in S4 have been greatly improved due to the incorporation of an appropriate amount of Pt-Co3O4 in SnO2 hollow microspheres, whose value has reached 27.5%.

Gas Sensing Characteristics
Firstly, the response influenced by the operating temperature is investigated. As shown in Figure 7a, S4 exhibits the best response to formaldehyde (Rair/Rformaldehyde = 4240 toward 100 ppm), which is 10.4 times that of pure SnO2 (408 toward 100 ppm). Within the temperature range of 200 to 350 °C, the optimum operating temperature of all sensors based on S1-S5 for detecting formaldehyde is the same, that is, 300 °C. Moreover, the incorporated amount of Pt@Co3O4 has a significant effect on the response of SnO2 toward formaldehyde. Specifically, when the amount of Pt@Co3O4 incorporated is increased in S4 from that in S3, the response of SnO2 toward formaldehyde is enhanced from 2990 to 4240. When the incorporated amount of Pt@Co3O4 continues to increase in S5, the response decreases instead, which is may be due to the saturation of catalytic sensitization and catalyst aggregation caused by the excessive amounts of noble metal Pt [40]. Figure 7b shows the response of the five sensors based on S1-S5 with respect to different gases at a concentration of 100 ppm at 300 °C, proving that all sensors, especially the S4 sensor, have good specific detection capabilities for formaldehyde. Figure 7c demonstrates the superior reliability of the five sensors by evaluating the transient response characteristics toward six cycles of 100 ppm formaldehyde at 300 °C. In addition, to optimize the sensing

Gas Sensing Characteristics
Firstly, the response influenced by the operating temperature is investigated. As shown in Figure 7a, S4 exhibits the best response to formaldehyde (R air /R formaldehyde = 4240 toward 100 ppm), which is 10.4 times that of pure SnO 2 (408 toward 100 ppm). Within the temperature range of 200 to 350 • C, the optimum operating temperature of all sensors based on S1-S5 for detecting formaldehyde is the same, that is, 300 • C. Moreover, the incorporated amount of Pt@Co 3 O 4 has a significant effect on the response of SnO 2 toward formaldehyde. Specifically, when the amount of Pt@Co 3 O 4 incorporated is increased in S4 from that in S3, the response of SnO 2 toward formaldehyde is enhanced from 2990 to 4240. When the incorporated amount of Pt@Co 3 O 4 continues to increase in S5, the response decreases instead, which is may be due to the saturation of catalytic sensitization and catalyst aggregation caused by the excessive amounts of noble metal Pt [40]. Figure 7b shows the response of the five sensors based on S1-S5 with respect to different gases at a concentration of 100 ppm at 300 • C, proving that all sensors, especially the S4 sensor, have good specific detection capabilities for formaldehyde. Figure 7c demonstrates the superior reliability of the five sensors by evaluating the transient response characteristics toward six cycles of 100 ppm formaldehyde at 300 • C. In addition, to optimize the sensing performance of the sensors at 300 • C, the explicit relationship between formaldehyde concentration and response is further investigated in detail. As shown in Figure 7d, the S4 sensor always shows the highest response toward 1-150 ppm of formaldehyde among the five sensors. The inset figure is the responses of the sensors toward low concentration (1-10 ppm) of formaldehyde. performance of the sensors at 300 °C, the explicit relationship between formaldehyde concentration and response is further investigated in detail. As shown in Figure 7d, the S4 sensor always shows the highest response toward 1-150 ppm of formaldehyde among the five sensors. The inset figure is the responses of the sensors toward low concentration (1-10 ppm) of formaldehyde. Subsequently, other sensing characteristics of the S4 sensor toward formaldehyde are further shown in Figure 8. First of all, compared with the pure SnO2 hollow microspheres (S1), the sensor based on S4 not only shows a higher response, but also shorter response time. As shown in Figure 8a, the response times of S1 and S4 toward 100 ppm formaldehyde at 300 °C are 26 s and 13 s, respectively, implying that SnO2 hollow microspheres functionalized with an optimal amount of Pt@Co3O4 are a key factor in achieving both an excellent response and response time. Secondly, the dynamic resistance variation curve of the S4 sensor toward 1-0.05 ppm of formaldehyde at 300 °C is exhibited in Figure 8b. The response of the S4 sensor toward 1 ppm formaldehyde at 300 °C is 16.5. Notably, the result reveals a noticeable response to a low concentration of formaldehyde and the detection limit is 50 ppb (Rair/Rformaldehyde = 1.9). Moreover, long-term stability of response and resistance of the S4 sensor for detecting 100 ppm formaldehyde at 300 °C is observed. As shown in Figure 8c, the results show that the attenuation rates of the response and resistance are 11% and 24%, respectively, indicating that the sensor based on S4 is of great significance to realize the accurate detection of formaldehyde gas. Importantly, the comparisons of response and limit of detection between the S4 sensor and other reported SnO2-based formaldehyde sensors are displayed in Table 1 [9,12,13,[41][42][43][44][45][46][47]. Mostly, the sensor fabricated in this work has outstanding advantages in terms of response and limit of detection. It is worth noting that the limits of detection of [12] (60 Subsequently, other sensing characteristics of the S4 sensor toward formaldehyde are further shown in Figure 8. First of all, compared with the pure SnO 2 hollow microspheres (S1), the sensor based on S4 not only shows a higher response, but also shorter response time. As shown in Figure 8a, the response times of S1 and S4 toward 100 ppm formaldehyde at 300 • C are 26 s and 13 s, respectively, implying that SnO 2 hollow microspheres functionalized with an optimal amount of Pt@Co 3 O 4 are a key factor in achieving both an excellent response and response time. Secondly, the dynamic resistance variation curve of the S4 sensor toward 1-0.05 ppm of formaldehyde at 300 • C is exhibited in Figure 8b. The response of the S4 sensor toward 1 ppm formaldehyde at 300 • C is 16.5. Notably, the result reveals a noticeable response to a low concentration of formaldehyde and the detection limit is 50 ppb (R air /R formaldehyde = 1.9). Moreover, long-term stability of response and resistance of the S4 sensor for detecting 100 ppm formaldehyde at 300 • C is observed. As shown in Figure 8c, the results show that the attenuation rates of the response and resistance are 11% and 24%, respectively, indicating that the sensor based on S4 is of great significance to realize the accurate detection of formaldehyde gas. Importantly, the comparisons of response and limit of detection between the S4 sensor and other reported SnO 2 -based formaldehyde sensors are displayed in Table 1 [9,12,13,[41][42][43][44][45][46][47]. Mostly, the sensor fabricated in this work has outstanding advantages in terms of response and limit of detection. It is worth noting that the limits of detection of [12] (60 ppb) and this work (50 ppb) are not greatly different. Compared with the doping amount (1 wt%) and particle size of Pt (>5 nm) in [12], the sensing properties of Pt@Co 3 O 4 -SnO 2 toward formaldehyde are significantly enhanced even by the quite low Pt loading (~0.3 wt%) due to the finer dispersion of Pt (~3 nm) attained by using Pt@ZIF-67. Therefore, the sensor fabricated in this work is more meaningful for eventual practical application due to the expensive price of noble metals. ppb) and this work (50 ppb) are not greatly different. Compared with the doping amo (1 wt%) and particle size of Pt (>5 nm) in [12], the sensing properties of Pt@Co3O4-S toward formaldehyde are significantly enhanced even by the quite low Pt loading ( wt%) due to the finer dispersion of Pt (~3 nm) attained by using Pt@ZIF-67. Therefore sensor fabricated in this work is more meaningful for eventual practical application to the expensive price of noble metals.

Discussion
SnO2 is one of the most widely researched n-type MOS materials, whose sen mechanism is related to the adsorption/desorption of formaldehyde on the surfac

Discussion
SnO 2 is one of the most widely researched n-type MOS materials, whose sensing mechanism is related to the adsorption/desorption of formaldehyde on the surface of sensitive materials and controlled by the chemical reaction between formaldehyde and chemically adsorbed oxygen [48,49]. Generally, for sensors based on SnO 2 in air, the oxygen molecules adsorbed (O 2 (ads)) on the surface of SnO 2 will remove electrons from the conduction band of SnO 2 , thereby resulting in a decrease in the numbers of carriers in SnO 2 . Then, the sensor remains in a high-resistance state (R a ). Meanwhile, the oxygen will become different kinds of chemically adsorbed oxygen (mainly O − (ads), O 2− (ads) and O − 2 (ads)), whose generating process can be expressed by the formulas below [50].
Considering the formulas above and the optimal temperature (300 • C) in this work, the chemically adsorbed oxygen mainly reacts with formaldehyde in the form of O − (ads). The reaction equation is as follows [51].
Accordingly, the generated electrons in the chemical reaction will return to the conduction band of SnO 2 , increasing the number of the carriers, thus leading to the sensor having a low-resistance state (R g ). According to the formula of response and response times, the specific value can be calculated. In this work, the enhanced formaldehyde sensing performance of S4 can be attributed to three main reasons.
(I) The large difference in charge carrier concentration in Pt@Co 3 O 4 -SnO 2 and SnO 2 plays a leading role in improving the formaldehyde sensing performance, which can be explained by the change in the initial resistance of the sensor in air (R a ). Figure 9 provides the resistances in air of the five sensors. The R a of the sensor based on S1 is 8.6 MΩ which is enhanced 28 times with Pt@Co 3 O 4 incorporation (S4, 242 MΩ). This is closely related to the existence of p-type Co 3 O 4 and ultra-small Pt nanoparticles. On one hand, p-n heterojunctions between p-Co 3 O 4 /n-SnO 2 can contribute to the enhancement of the resistance. The work function of p-Co 3 O 4 (6.1 eV) is larger than that of n-SnO 2 (4.91 eV) [52,53]. When the p-Co 3 O 4 grain encounters the n-SnO 2 grain, a p-n heterojunction is produced at the interface, causing the electrons in SnO 2 to be transferred to Co 3 O 4 and the holes in Co 3 O 4 to move to SnO 2 . Thus, a potential barrier will be created with energy band bending, directly increasing the R a value of the sensor. On the other hand, the spillover and catalytic effect of ultra-small Pt play important roles in regulating the R a value. It is well known that Pt can act as a specific site which is conducive to making the oxygen molecules in air easily adsorb and then transfer to chemisorbed oxygen, thus significantly increasing the amount of O − (ads), which can be confirmed by the high-resolution XPS spectra of O 1s ( Figure 10) [54]. As shown in Figure 6d, the relative content of O3 in S4 is the highest among the five samples, being consistent with the theoretical analysis above. According to the formula in (4), this process will cause more electrons to be extracted from the conduction band of SnO 2 . Therefore, the R a of SnO 2 further increases with the introduction of Pt. Since the sensor response is defined as the ratio of R a to R g (R a /R g ), a better response is usually accompanied by a higher initial resistance. Thus, it is reasonable that a sensor based on SnO 2 functionalized with Pt@Co 3 O 4 has a more excellent response. However, the response change trend of the S5 sensor is inconsistent with the change in R a , suggesting that it is not comprehensive enough to consider the influence of R a on response alone. As is well known, the incorporation of excessive noble metals will make the surface catalytic activity of the sensitive body excessively enhanced, resulting in the desorption rate of formaldehyde molecules being greater than the adsorption rate [55]. Consequently, fewer formaldehyde molecules will participate in the reaction with chemically adsorbed oxygen, and finally the response will be reduced instead.
(II) The increase in oxygen vacancy is considered to be another key reason to improve the response of the sensor. As shown in Figure 6d, it can be concluded that the percentage of oxygen vacancy (O2) in the S4 sample is also the highest. By combining that with the analysis above, it makes sense that the incorporation of an optimal amount of Pt@Co 3 O 4 can maximize the response of SnO 2 toward formaldehyde. fewer formaldehyde molecules will participate in the reaction with chemically adsorbed oxygen, and finally the response will be reduced instead.  (Ⅱ) The increase in oxygen vacancy is considered to be another key reason to improve the response of the sensor. As shown in Figure 6d, it can be concluded that the percentage of oxygen vacancy (O2) in the S4 sample is also the highest. By combining that with the analysis above, it makes sense that the incorporation of an optimal amount of Pt@Co3O4 can maximize the response of SnO2 toward formaldehyde.
(Ⅲ) The improved response times of the S4 sensor can be understood in relation to the catalytic effect of ultra-small Pt nanoparticles [56]. Due to the ultra-small Pt, formaldehyde molecules can be easily decomposed into many active groups, which will promote the sensing reaction between formaldehyde and chemically adsorbed oxygen (O -(ads). As a consequence, the response time value effectively decreases when Pt is incorporated into the SnO2 hollow microspheres.

Conclusions
In this work, we have prepared series of Pt@Co3O4-SnO2 hollow microspheres by using different incorporated amounts of Pt@ZIF-67. Compared with pure SnO2 (S1), the sensor based on Pt@Co3O4-SnO2 hollow microspheres (S4) showed the most excellent response to formaldehyde (S = 4240 toward 100 ppm), which is 10.4 times that of pure SnO2 (S1). Furthermore, the response time and selectivity are also enhanced after the fewer formaldehyde molecules will participate in the reaction with chemically adsorbed oxygen, and finally the response will be reduced instead.  (Ⅱ) The increase in oxygen vacancy is considered to be another key reason to improve the response of the sensor. As shown in Figure 6d, it can be concluded that the percentage of oxygen vacancy (O2) in the S4 sample is also the highest. By combining that with the analysis above, it makes sense that the incorporation of an optimal amount of Pt@Co3O4 can maximize the response of SnO2 toward formaldehyde.
(Ⅲ) The improved response times of the S4 sensor can be understood in relation to the catalytic effect of ultra-small Pt nanoparticles [56]. Due to the ultra-small Pt, formaldehyde molecules can be easily decomposed into many active groups, which will promote the sensing reaction between formaldehyde and chemically adsorbed oxygen (O -(ads). As a consequence, the response time value effectively decreases when Pt is incorporated into the SnO2 hollow microspheres.

Conclusions
In this work, we have prepared series of Pt@Co3O4-SnO2 hollow microspheres by using different incorporated amounts of Pt@ZIF-67. Compared with pure SnO2 (S1), the sensor based on Pt@Co3O4-SnO2 hollow microspheres (S4) showed the most excellent response to formaldehyde (S = 4240 toward 100 ppm), which is 10.4 times that of pure SnO2 (S1). Furthermore, the response time and selectivity are also enhanced after the (III) The improved response times of the S4 sensor can be understood in relation to the catalytic effect of ultra-small Pt nanoparticles [56]. Due to the ultra-small Pt, formaldehyde molecules can be easily decomposed into many active groups, which will promote the sensing reaction between formaldehyde and chemically adsorbed oxygen (O − (ads). As a consequence, the response time value effectively decreases when Pt is incorporated into the SnO 2 hollow microspheres.

Conclusions
In this work, we have prepared series of Pt@Co 3 O 4 -SnO 2 hollow microspheres by using different incorporated amounts of Pt@ZIF-67. Compared with pure SnO 2 (S1), the sensor based on Pt@Co 3 O 4 -SnO 2 hollow microspheres (S4) showed the most excellent response to formaldehyde (S = 4240 toward 100 ppm), which is 10.4 times that of pure SnO 2 (S1). Furthermore, the response time and selectivity are also enhanced after the incorporation of Pt@Co 3 O 4 into SnO 2 . These noticeably improved sensing properties are achieved by the p-n heterojunction between p-Co 3 O 4 and n-SnO 2 , the spillover and catalytic effect of ultra-small Pt and the increase in oxygen deficient. These results prove that the unique synthetic route of Pt@Co 3 O 4 complex catalyst incorporated into MOS is a highly effective way to fabricate chemiresistive sensors.