In Situ Local Oxidation of SnO Induced by Laser Irradiation: A Stability Study

In this work, semiconductor tin oxide (II) (SnO) nanoparticles and plates were synthesized at room conditions via a hydrolysis procedure. X-ray diffraction (XRD) and transmission electron microscopy (TEM) confirmed the high crystallinity of the as-synthesized romarchite SnO nanoparticles with dimensions ranging from 5 to 16 nm. The stability of the initial SnO and the controlled oxidation to SnO2 was studied based on either thermal treatments or controlled laser irradiation using a UV and a red laser in a confocal microscope. Thermal treatments induced the oxidation from SnO to SnO2 without formation of intermediate SnOx, as confirmed by thermodiffraction measurements, while by using UV or red laser irradiation the transition from SnO to SnO2 was controlled, assisted by formation of intermediate Sn3O4, as confirmed by Raman spectroscopy. Photoluminescence and Raman spectroscopy as a function of the laser excitation source, the laser power density, and the irradiation duration were analyzed in order to gain insights in the formation of SnO2 from SnO. Finally, a tailored spatial SnO/SnO2 micropatterning was achieved by controlled laser irradiation with potential applicability in optoelectronics and sensing devices.


Introduction
Tin oxide is a well-known semiconductor oxide that commonly appears in two crystalline forms, tin dioxide (SnO 2 , cassiterite) and tin monoxide (SnO, romarchite) [1], the former being most commonly used because it is the stable polymorphic form. Despite the potential applicability of SnO in some fields of research, its use is commonly hindered as it is easily oxidized to the most stable SnO 2 , which is indeed one of the most extensively used semiconducting oxides.
On the other hand, tin monoxide, (tin oxide II, stannous oxide) (SnO, Sn 2+ ) romarchite, possesses p-type conductivity and often exhibits a layered structure with tetragonal space group P4/nmn (129) with lattice parameters a = b = 3.803 Å and c = 4.838 Å, corresponding to a litharge structure with a variable optical bandgap, ranging between E G~2 .5-3.4 eV [1,3,7,8]. In recent years, SnO has generated increasing interest in photocatalysis [9,10] and as a potential thermoelectric material, supported by first principle calculations [11,12] in part due to its low toxicity and abundance compared with other raised to 100 • C for 2 h. The final product was centrifuged and washed several times until obtaining neutral pH; finally, it was dried at 50 • C for 12 h. The product was stored in glass vessels.

Characterization Techniques
The structural characterization of the nanoparticles was carried out by X-ray diffraction (XRD) in PANanalytical X'Pert Powder equipment (PANanalytical, Malvern, United Kingdom) using the copper Kα line λ Cu = 1.5404 Å. Thermo diffractograms were performed with a X'Celerator detector in the range of 23.009 • to 34.977 • , with a step of 0.017 • at controlled temperatures in the range of 25-900 • C, in steps of 50 • C between 50-200 • C (8 min rise, 4 min step), and in steps of 20 • C (4 min rise, 4 min step) between 200-800 • C, returning to steps of 50 • C from 800-900 • C. The microstructural analysis was carried out in a transmission electron microscope, by analyzing TEM images as well as selected area (electron) diffraction patterns (SAED/TEM) on a JEOL JEM 1400 plus (Jeol, Japan). Raman spectroscopy measurements were carried out at room temperature on a Horiba Jobin-Yvon LabRam Hr800 (Horiba, Kyoto, Japan) using both continuous wave He-Ne laser (λ = 633 nm) and He-Cd laser (λ = 325 nm). Different neutral filters were used to attenuate the total laser intensity, when necessary, diminishing the laser intensity from the nominal 5 mW or 13 mW (I 0 ), respectively, for the UV or red laser to approximately 0.5·I 0 (D03) , 0.25·I 0 (D06) , 0.1·I 0 (D1), or 0.01·I 0 (D2) with the use of neutral filters [24]. The laser was focused onto the sample surface using a 40× objective (numerical aperture = 0.5, Thorlabs LMU-40X-NUV), which led to a laser spot diameter around 1 µm for the UV laser and a few microns for the red laser. The scattered light was collected with the same objective and dispersed with a grating of 2400 L/mm for UV and 600 L/mm for VIS and finally acquired with an air-cooled CCD detector Synapse. Photoluminescence (PL) was studied at room temperature in the same confocal microscope with a He-Cd UV laser (λ = 325 nm) as excitation source. The grating used for PL luminescence was 600 L/mm, using the same objective and CCD detector.

TEM and XRD
XRD results confirmed that the synthesized nanoparticles mainly consisted of high crystalline romarchite SnO, with a dominant (101) peak. Only a weak maximum corresponding to SnO 2 (110) was observed at 26.5 • in the XRD diffractograms due to natural oxidation, while diffraction peaks related to metallic Sn or other Sn-based oxides were not detected in this case. The as-synthesized SnO was stable under room conditions. Figure S1 shows the XRD patterns acquired from SnO as synthesized and after 1 or 2 years of storage, when peaks from SnO still dominated the diffractograms after long storage and only a weak maximum from SnO 2 was observed at 26.5 • . In that time span, the weak contribution corresponding to SnO (001) was quenched, which may have been related to the formation of small domains of SnO 2 .
The lattice parameters a = 3.80 Å and c = 4.83 Å were estimated from the analysis of the corresponding XRD patterns using the SnO planes (101) and (002), as indicated in Table 1. Table 1. Averaged dimensions and lattice parameters for tin oxide (SnO) estimated from TEM and XRD measurements.
From the low magnification TEM images analysis, it could be observed that the dimensions of the nanoparticles ranged from 5 to 16 nm, with averaged dimensions around 9 nm, as confirmed in Figure 1a. In addition, larger plates with dimensions of hundreds of nm could be also observed ( Figure 1b). The SAED pattern included in the inset in Figure  1b confirmed that the nanocrystals corresponded to SnO, although a low amount of SnO2 was also observed in some regions, as confirmed by the weak spots in the SAED pattern, in agreement with the XRD results.

Thermo XRD
To analyze the temperature stability of SnO and its oxidation to SnO2, XRD patterns were acquired in situ during a controlled annealing process in air, as described in the Materials and Methods section. Figure 2a shows the diffraction patterns acquired in the range of angles 15-70° at two temperatures, 25 °C and 900 °C. Figure 2b represents the contouring plot of the intensities from the XRD signal between 23-35° corresponding to the different steps in the annealing process from 25 to 900 °C. A detailed graph with the diffractograms recorded at temperatures between 25 and 900 °C is shown in Figure S2.
Peaks in the analyzed diffractograms corresponded only to SnO or SnO2 as they can be indexed according to the Inorganic Crystal Structure Database (ICSD) files nº 01-072-1012 for SnO and nº 00-001-0625 for SnO2, respectively. Diffraction peaks from metallic Sn or other oxides such as Sn2O3 and Sn3O4 were not detected in the analyzed range for the annealing temperatures. Peaks at 39.4 and 45.8°, marked with * in Figure 2a, correspond to the Pt sample-holder. It could be observed that oxidation from the initial SnO nanopowder into SnO2 started at around 400 °C. This oxidation process was nearly completed at temperatures above 800 °C, as observed in Figure 2b. Diverse authors also reported the oxidation from SnO to SnO2 at temperatures in the range 400-700 °C, as a function of the annealing parameters and the characteristic of the initial SnO nanopowder [13,14]. In general, annealing at temperatures higher than 600 °C fully transforms the SnO nanoparticles into the rutile SnO2 phase [27]. Moreover, in some cases an oxidation process involving the formation of intermediate oxides such as Sn2O3 and Sn3O4 has been reported [28]. In the present work, based on the thermodiffraction measurements, a direct oxidation process from unstable SnO to the more stable SnO2 phase occurred, probably by nucleation From the low magnification TEM images analysis, it could be observed that the dimensions of the nanoparticles ranged from 5 to 16 nm, with averaged dimensions around 9 nm, as confirmed in Figure 1a. In addition, larger plates with dimensions of hundreds of nm could be also observed ( Figure 1b). The SAED pattern included in the inset in Figure  1b confirmed that the nanocrystals corresponded to SnO, although a low amount of SnO 2 was also observed in some regions, as confirmed by the weak spots in the SAED pattern, in agreement with the XRD results.

Thermo XRD
To analyze the temperature stability of SnO and its oxidation to SnO 2 , XRD patterns were acquired in situ during a controlled annealing process in air, as described in the Materials and Methods section. Figure 2a shows the diffraction patterns acquired in the range of angles 15-70 • at two temperatures, 25 • C and 900 • C. Figure 2b represents the contouring plot of the intensities from the XRD signal between 23-35 • corresponding to the different steps in the annealing process from 25 to 900 • C. A detailed graph with the diffractograms recorded at temperatures between 25 and 900 • C is shown in Figure S2.
Peaks in the analyzed diffractograms corresponded only to SnO or SnO 2 as they can be indexed according to the Inorganic Crystal Structure Database (ICSD) files nº 01-072-1012 for SnO and nº 00-001-0625 for SnO 2 , respectively. Diffraction peaks from metallic Sn or other oxides such as Sn 2 O 3 and Sn 3 O 4 were not detected in the analyzed range for the annealing temperatures. Peaks at 39.4 and 45.8 • , marked with * in Figure 2a, correspond to the Pt sample-holder. It could be observed that oxidation from the initial SnO nanopowder into SnO 2 started at around 400 • C. This oxidation process was nearly completed at temperatures above 800 • C, as observed in Figure 2b. Diverse authors also reported the oxidation from SnO to SnO 2 at temperatures in the range 400-700 • C, as a function of the annealing parameters and the characteristic of the initial SnO nanopowder [13,14]. In general, annealing at temperatures higher than 600 • C fully transforms the SnO nanoparticles into the rutile SnO 2 phase [27]. Moreover, in some cases an oxidation process involving the formation of intermediate oxides such as Sn 2 O 3 and Sn 3 O 4 has been reported [28]. In the Nanomaterials 2021, 11, 976 5 of 11 present work, based on the thermodiffraction measurements, a direct oxidation process from unstable SnO to the more stable SnO 2 phase occurred, probably by nucleation and growth process, without forming intermediate oxides. The thermodynamic phase diagram of the Sn-O system can be found in [1,29,30], which is in agreement with this work. and growth process, without forming intermediate oxides. The thermodynamic phase diagram of the Sn-O system can be found in [1,29,30], which is in agreement with this work. Based on the results depicted in Figure 2b, it was observed that when increasing the temperature up to 300 °C there was no strong oxidation or phase transition and, in addition to a weak SnO2 (110) maximum at around 26.5°, only minor shifts to lower angles in the XRD peaks from SnO were observed, mainly the peak corresponding to the SnO (101) planes. Actually, the (110) peak from SnO2 rutile appeared and became as significant as the (101) maximum from SnO romarchite around 400 °C [27].
The (101) maximum from SnO observed at 29.9°, which dominated the XRD pattern at room temperature, suffered a shift to lower angles as the temperature increased. At 480 °C this peak was placed at 29.4° and then it shifted again toward higher angles, finally reaching 29.9° at 800 °C, although at this high temperature the relative intensity of this peak was drastically decreased. The shift to lower angles could be related to a thermal lattice expansion up to 480 °C, where the SnO2 phase dominated the XRD pattern. During the annealing and oxidation process an arrangement of the ions in the SnO lattice may have taken place, leading to small variations in the lattice constants along to the formation of SnO2. In this regard, the XRD maximum which exhibits more variation in its position and intensity corresponds to the (101) planes in romarchite. F. Wang et al. [31] reported a process in which the chemical coordination of the interstitials Sn cations becomes more similar to that of cassiterite SnO2 during the oxidation process, which could be related to the SnO (101) shift during annealing.

Raman Spectroscopy
In order to study the stability of SnO under irradiation and the possible laser-induced formation of SnO2 from SnO, Raman spectra from SnO nanopowder were analyzed using either a red (λ = 633 nm) or a UV (λ = 325 nm) laser, as well as variable laser intensity based on the employed neutral filters and controlled irradiation exposure time. Tin dioxide (SnO2) presented two active IR modes (A2u and Eu), four Raman active modes (A1g,B1g,B2g, and Eg), and two inactive modes (A2g and B1u) [32]. It is commonly reported that Eg (490 cm −1 ), A1g (640 cm −1 ), and B2g (760 cm −1 ) modes dominate the SnO2 Raman spectra. These modes are associated with the movement of O anions along the c-axis (Eg) and Based on the results depicted in Figure 2b, it was observed that when increasing the temperature up to 300 • C there was no strong oxidation or phase transition and, in addition to a weak SnO 2 (110) maximum at around 26.5 • , only minor shifts to lower angles in the XRD peaks from SnO were observed, mainly the peak corresponding to the SnO (101) planes. Actually, the (110) peak from SnO 2 rutile appeared and became as significant as the (101) maximum from SnO romarchite around 400 • C [27].
The (101) maximum from SnO observed at 29.9 • , which dominated the XRD pattern at room temperature, suffered a shift to lower angles as the temperature increased. At 480 • C this peak was placed at 29.4 • and then it shifted again toward higher angles, finally reaching 29.9 • at 800 • C, although at this high temperature the relative intensity of this peak was drastically decreased. The shift to lower angles could be related to a thermal lattice expansion up to 480 • C, where the SnO 2 phase dominated the XRD pattern. During the annealing and oxidation process an arrangement of the ions in the SnO lattice may have taken place, leading to small variations in the lattice constants along to the formation of SnO 2 . In this regard, the XRD maximum which exhibits more variation in its position and intensity corresponds to the (101) planes in romarchite. F. Wang et al. [31] reported a process in which the chemical coordination of the interstitials Sn cations becomes more similar to that of cassiterite SnO 2 during the oxidation process, which could be related to the SnO (101) shift during annealing.

Raman Spectroscopy
In order to study the stability of SnO under irradiation and the possible laser-induced formation of SnO 2 from SnO, Raman spectra from SnO nanopowder were analyzed using either a red (λ = 633 nm) or a UV (λ = 325 nm) laser, as well as variable laser intensity based on the employed neutral filters and controlled irradiation exposure time. Tin dioxide (SnO 2 ) presented two active IR modes (A 2u and E u ), four Raman active modes (A 1g , B 1g , B 2g , and E g ), and two inactive modes (A 2g and B 1u ) [32]. It is commonly reported that E g (490 cm −1 ), A 1g (640 cm −1 ), and B 2g (760 cm −1 ) modes dominate the SnO 2 Raman spectra. These modes are associated with the movement of O anions along the c-axis (E g ) and elongation of O−Sn−O and movement of the anions in a symmetric (A 1g ) and asymmetric manner (B 2g ) orthogonal to the c-axis [2].
SnO, often shows two main Raman modes at around 110 and 208 cm −1 which correspond to the B 1g and A 1g modes, respectively [8,25]. However, there was still some controversy in the assignment of the Raman modes, as some authors assign the first peak to E g based on frozen-phonon DFT calculations [33]. Figure 3a shows Raman spectra acquired with the UV laser in different spots on the SnO sample using different neutral filters, which can tailor the laser power densities, and using irradiation times of 60 s. Raman peaks from romarchite SnO were not observed when irradiating with the UV laser, even with the lowest power density (0.1·I 0 ), at least within the resolution of the technique. As the laser power density increases, the Raman signal obtained with the UV laser is dominated only by vibrational modes from SnO 2 , the intensity of which rise, showing improved crystallinity of the formed SnO 2 . After the UV irradiation, the E g and A 1g modes from SnO 2 were clearly observed in the Raman spectra, but the former was slightly displaced to lower wavenumbers 468 cm −1 , probably due to the initial lower crystallinity of the formed SnO 2 or due to temperature shift of the phonon modes. As the irradiation density and duration increased, not only did the relative intensity of the Raman modes increase but also their positions were closer to the expected for SnO 2 . This formation of SnO 2 from SnO by laser irradiation was irreversible, as expected, due to the higher stability of SnO 2 . Figure S3 shows Raman spectra acquired using the same filter but with variable irradiation time (60 or 600 s) where peaks from SnO 2 increased for longer irradiation.  [2]. SnO, often shows two main Raman modes at around 110 and 208 cm −1 which correspond to the B1g and A1g modes, respectively [8,25]. However, there was still some controversy in the assignment of the Raman modes, as some authors assign the first peak to Eg based on frozen-phonon DFT calculations [33]. Figure 3a shows Raman spectra acquired with the UV laser in different spots on the SnO sample using different neutral filters, which can tailor the laser power densities, and using irradiation times of 60 s. Raman peaks from romarchite SnO were not observed when irradiating with the UV laser, even with the lowest power density (0.1·I0), at least within the resolution of the technique. As the laser power density increases, the Raman signal obtained with the UV laser is dominated only by vibrational modes from SnO2, the intensity of which rise, showing improved crystallinity of the formed SnO2. After the UV irradiation, the Eg and A1g modes from SnO2 were clearly observed in the Raman spectra, but the former was slightly displaced to lower wavenumbers 468 cm −1 , probably due to the initial lower crystallinity of the formed SnO2 or due to temperature shift of the phonon modes. As the irradiation density and duration increased, not only did the relative intensity of the Raman modes increase but also their positions were closer to the expected for SnO2. This formation of SnO2 from SnO by laser irradiation was irreversible, as expected, due to the higher stability of SnO2. Figure S3 shows Raman spectra acquired using the same filter but with variable irradiation time (60 or 600 s) where peaks from SnO2 increased for longer irradiation. As irradiation with a UV laser induces the oxidation from SnO to SnO2, a red laser was also employed to achieve a deeper understanding of the intermediate steps in the transition from romarchite SnO to cassiterite SnO2. Raman spectra acquired with the red laser (λ = 633 nm) and using diverse neutral filters to modify the laser power density are shown in Figure 3b. An irradiation time of 200 s was used for the spectra acquisition. In this case, when using the lowest laser power density (0.1·I0), the formation of SnO2 was avoided, as only Raman peaks from SnO centered at 110.5 cm −1 and 208.6 cm −1 [34] could be clearly distinguished in the corresponding Raman spectrum. However, when using higher laser power densities, in addition to these SnO vibrational modes, some other new Raman peaks could be observed, mainly in the range 100-200 cm −1 . Two main peaks centered at 136 and 165 cm −1 were clearly distinguished either using higher power intensity (I0) or increasing exposition time with lower power intensity (0.5·I0). Guillén et al. [35]  As irradiation with a UV laser induces the oxidation from SnO to SnO 2 , a red laser was also employed to achieve a deeper understanding of the intermediate steps in the transition from romarchite SnO to cassiterite SnO 2 . Raman spectra acquired with the red laser (λ = 633 nm) and using diverse neutral filters to modify the laser power density are shown in Figure 3b. An irradiation time of 200 s was used for the spectra acquisition. In this case, when using the lowest laser power density (0.1·I 0 ), the formation of SnO 2 was avoided, as only Raman peaks from SnO centered at 110.5 cm −1 and 208.6 cm −1 [34] could be clearly distinguished in the corresponding Raman spectrum. However, when using higher laser power densities, in addition to these SnO vibrational modes, some other new Raman peaks could be observed, mainly in the range 100-200 cm −1 . Two main peaks centered at 136 and 165 cm −1 were clearly distinguished either using higher power intensity (I 0 ) or increasing exposition time with lower power intensity (0.5·I 0 ). Guillén et al. [35] attribute these peaks to intermediate SnO x oxides, mainly to monoclinic Sn 3 O 4 , as also confirmed by other authors [36]. These results point out an intermediate oxidation from SnO to SnO 2 by the formation of intermediate Sn 3 O 4 when the red laser power density was not high enough. In addition, when the red laser power was maximum (I 0 ), formation of SnO 2 was promoted as wide modes appeared in the region between 450-700 cm −1 (inset in Figure 3b), which could be attributed to the E g and A 1g modes from SnO 2 , also observed by UV irradiation (Figure 3a), although with much lower intensity in this case. It should be noted that contrary to the direct formation of SnO 2 from SnO by thermal annealing, confirmed by XRD analysis, in this case either complete transition to SnO 2 or formation of intermediate SnO x phases could be also promoted as a function of the laser irradiation conditions.

Laser-Induced Phase Transition
Increasing UV laser irradiation was shown to induce a phase transition from SnO to SnO 2 with minimum exposure time. Increasing this time enhanced the oxidation process and promoted SnO 2 formation. SnO nanopowder was irradiated continuously with a UV laser using a power density of 0.5·I 0 , while Raman spectra were acquired in the same point each minute for 40 minutes. As observed in the inset in Figure 4a continuous laser irradiation led to higher intensity spectra and narrow and well-centered peaks corresponding to the SnO 2 modes, such as A 1g . Peak intensities as a function of the irradiation duration in Figure 4a could be fitted to the Johnson-Mehl-Avrami-Kolmogorov (JMAK) equation [37]: where, X is referred to the volume fraction that is transformed in the irradiation zone, K is the effective rate constant, and n is the Avrami exponent. This exponent depends on the mechanism of nucleation and growth. In this case we considered that the volume transformed was proportional to the measured Raman intensity obtained by subtraction of a linear profile background.
attribute these peaks to intermediate SnOx oxides, mainly to monoclinic Sn3O4, as also confirmed by other authors [36]. These results point out an intermediate oxidation from SnO to SnO2 by the formation of intermediate Sn3O4 when the red laser power density was not high enough. In addition, when the red laser power was maximum (I0), formation of SnO2 was promoted as wide modes appeared in the region between 450-700 cm −1 (inset in Figure 3b), which could be attributed to the Eg and A1g modes from SnO2, also observed by UV irradiation (Figure 3a), although with much lower intensity in this case. It should be noted that contrary to the direct formation of SnO2 from SnO by thermal annealing, confirmed by XRD analysis, in this case either complete transition to SnO2 or formation of intermediate SnOx phases could be also promoted as a function of the laser irradiation conditions.

Laser-Induced Phase Transition
Increasing UV laser irradiation was shown to induce a phase transition from SnO to SnO2 with minimum exposure time. Increasing this time enhanced the oxidation process and promoted SnO2 formation. SnO nanopowder was irradiated continuously with a UV laser using a power density of 0.5·I0, while Raman spectra were acquired in the same point each minute for 40 minutes. As observed in the inset in Figure 4a continuous laser irradiation led to higher intensity spectra and narrow and well-centered peaks corresponding to the SnO2 modes, such as A1g. Peak intensities as a function of the irradiation duration in Figure 4a could be fitted to the Johnson-Mehl-Avrami-Kolmogorov (JMAK) equation [37]: where, X is referred to the volume fraction that is transformed in the irradiation zone, K is the effective rate constant, and n is the Avrami exponent. This exponent depends on the mechanism of nucleation and growth. In this case we considered that the volume transformed was proportional to the measured Raman intensity obtained by subtraction of a linear profile background. The JMAK equation has often been employed to describe laser-induced phase transitions from metastable phases [24] or to describe crystallization kinetics. In this case the transformation from SnO to SnO2 could not be described with this equation as the transformation for high laser energy densities occurred very fast. However, evolution and crystallization of the SnO2 formed during the initial irradiation stages could be described with the fit depicted in Figure 4b. In this case, the calculated Avrami exponent had a value close The JMAK equation has often been employed to describe laser-induced phase transitions from metastable phases [24] or to describe crystallization kinetics. In this case the transformation from SnO to SnO 2 could not be described with this equation as the transformation for high laser energy densities occurred very fast. However, evolution and crystallization of the SnO 2 formed during the initial irradiation stages could be described with the fit depicted in Figure 4b. In this case, the calculated Avrami exponent had a value close to n = 1, which corresponds to a diffusion controlled bi-dimensional reaction with nucleation site saturation. Hence, increasing irradiation time enhanced SnO 2 crystallinity Advantage can be taken from the laser-induced oxidation from SnO to SnO 2 in order to achieve spatial controlled SnO/SnO 2 micropatterning. Using a monitored stage, the UV laser with the highest laser intensity I 0 could irradiate different areas in the sample with micrometric resolution as a function of the laser spot size, thus leading to a spatial controlled formation of SnO 2 . Following this process, SnO or SnO 2 regions could be promoted in the samples as a function of the selected patterning. In this case, Figure 5a shows the bright (SnO 2 ) or dark (SnO) stripe-patterning formed on the surface of the sample after a controlled irradiation with the UV laser only in the bright areas. After the controlled UV irradiation, Raman spectra were acquired in selected points from the regions in Figure 5a using the UV laser and the lowest power density (0.1·I 0 ) to avoid formation of SnO 2 during measurements. The spectra acquired in region (i) corresponded with the Raman signal from SnO 2 , confirming oxidation from SnO to SnO 2 only in the irradiated regions, as shown in Figure 5b. Therefore, the controlled UV laser irradiation could tailor the oxidation process leading to either n-type SnO 2 and/or p-type SnO spatial distribution following a micrometric patterning. The availability of both n and p type conductivity in Sn oxides allows the potential development of bipolar devices based on p-n heterojunctions controlled at the microscale. Moreover, intermediate SnO x oxides could be also formed if needed as a function of the irradiation conditions. Nanomaterials 2021, 11, x FOR PEER REVIEW 8 of 11 to n = 1, which corresponds to a diffusion controlled bi-dimensional reaction with nucleation site saturation. Hence, increasing irradiation time enhanced SnO2 crystallinity Advantage can be taken from the laser-induced oxidation from SnO to SnO2 in order to achieve spatial controlled SnO/SnO2 micropatterning. Using a monitored stage, the UV laser with the highest laser intensity I0 could irradiate different areas in the sample with micrometric resolution as a function of the laser spot size, thus leading to a spatial controlled formation of SnO2. Following this process, SnO or SnO2 regions could be promoted in the samples as a function of the selected patterning. In this case, Figure 5a shows the bright (SnO2) or dark (SnO) stripe-patterning formed on the surface of the sample after a controlled irradiation with the UV laser only in the bright areas. After the controlled UV irradiation, Raman spectra were acquired in selected points from the regions in Figure 5a using the UV laser and the lowest power density (0.1·I0) to avoid formation of SnO2 during measurements. The spectra acquired in region (i) corresponded with the Raman signal from SnO2, confirming oxidation from SnO to SnO2 only in the irradiated regions, as shown in Figure 5b. Therefore, the controlled UV laser irradiation could tailor the oxidation process leading to either n-type SnO2 and/or p-type SnO spatial distribution following a micrometric patterning. The availability of both n and p type conductivity in Sn oxides allows the potential development of bipolar devices based on p-n heterojunctions controlled at the microscale. Moreover, intermediate SnOx oxides could be also formed if needed as a function of the irradiation conditions.

Photoluminescence
SnO bandgap is commonly reported to be between 2.5 eV (~496 nm) and 3.4 eV (~364 nm), therefore, an UV laser of λ = 325 nm (~3.8 eV) was used as excitation source in order to get information from all the luminescent processes. The oxidation to SnO2 by UV irradiation took place very fast, as observed during Raman analysis; thus, the obtained photoluminescence signal resembled the characteristic luminescence spectrum from SnO2. In this case, neutral filters were also used to reduce the laser power intensity. Figure 6a shows PL spectra from SnO acquired with the UV laser using 0.1·Io laser power density in the same spot, before and after irradiating the sample with the maximum (Io) intensity for 10 s.
The total intensity of the PL signal was increased when using higher laser power densities, as expected. For the PL spectrum acquired with the highest laser intensity (I0), the dominant emission was centered at around 2.25 eV, as shown in Figure 6a. Deconvolution into Gaussian functions of the spectra shown in Figure 6a can be found in Figure  S4. Additionally, a shoulder at about 3 eV up to 3.5 eV, could be observed. This spectrum can be attributed to SnO2, as this material normally shows characteristic emissions at 1.94

Photoluminescence
SnO bandgap is commonly reported to be between 2.5 eV (~496 nm) and 3.4 eV (~364 nm), therefore, an UV laser of λ = 325 nm (~3.8 eV) was used as excitation source in order to get information from all the luminescent processes. The oxidation to SnO 2 by UV irradiation took place very fast, as observed during Raman analysis; thus, the obtained photoluminescence signal resembled the characteristic luminescence spectrum from SnO 2 . In this case, neutral filters were also used to reduce the laser power intensity. Figure 6a shows PL spectra from SnO acquired with the UV laser using 0.1·I o laser power density in the same spot, before and after irradiating the sample with the maximum (I o ) intensity for 10 s.
The total intensity of the PL signal was increased when using higher laser power densities, as expected. For the PL spectrum acquired with the highest laser intensity (I 0 ), the dominant emission was centered at around 2.25 eV, as shown in Figure 6a. Deconvolution into Gaussian functions of the spectra shown in Figure 6a can be found in Figure S4. Additionally, a shoulder at about 3 eV up to 3.5 eV, could be observed. This spectrum can be attributed to SnO 2 , as this material normally shows characteristic emissions at 1.94 eV and 2.25 eV associated with oxygen vacancies-related defects:~2.50 eV due to surface defect states [2,38] and~3 eV due to transitions involving Vo" levels.
pletely disregarded, as some authors reported emissions from SnO around 2 to 2.3 eV due to defects such as Sn vacancies and O vacancies, and at ~3 eV related to band-edge emissions [8,39]. The differences on the PL spectra acquired using different filters is shown in Figure 6b, represented as chromaticity coordinates calculated from the PL spectra according to the Comission Internationale de l'Eclairage (CIE 1931) standard [40,41]. In any case, careful attention should be paid during analysis of discussion of the PL signal from SnO, as possible formation of SnO2 during irradiation should be considered.

Conclusions
Crystalline SnO nanoparticles and plates were synthesized via a hydrolysis method that allowed achievement of a large amount of SnO nanopowder, avoiding an atmosphere-control during the synthesis. The nanoparticles dimensions ranged from 5 to 16 nm, as confirmed by TEM observations. XRD measurements confirmed the minor oxidation and stability of the as-synthesized SnO nanopowder stored at room conditions for up to 24 months. The oxidation from SnO to SnO2 was promoted by thermal annealing or by controlled laser irradiation. Temperatures above 300 °C were required to initiate the oxidation from SnO to SnO2 which was completed at 800 °C, following a nucleation and growth process without formation of intermediate SnOx, as confirmed by thermodiffraction measurements. On the contrary, by using UV or red laser irradiation the transition from SnO to SnO2 could be controlled, assisted by the formation of intermediate Sn3O4, as confirmed by Raman spectroscopy. Careful attention should be paid during the PL and Raman analysis, as the use of the laser as excitation source can induce formation of SnO2 during measurement, thus leading to possibly misleading results and discussion. In this work, the evolution from SnO to SnO2 was studied as a function of the laser excitation source (UV and red laser), the laser power density (controlled by using neutral filters), and the irradiation duration in order to achieve deeper knowledge and control of the oxidation process. The evolution of the oxidation of the SnO2 promoted by UV laser irradiation obeys Avrami behavior. Finally, advantage was taken from the controlled SnO oxidation and a tailored spatial SnO/SnO2 micropatterning was developed based on a controlled laser irradiation. This laser-induced micropatterning can be of potential interest Before the irradiation, the PL spectrum was characterized by two main emissions centered at around 2 and 2.3 eV. These emissions could be due to high defective SnO 2 , although the presence of SnO, not detected by UV Raman analysis, could not be completely disregarded, as some authors reported emissions from SnO around 2 to 2.3 eV due to defects such as Sn vacancies and O vacancies, and at~3 eV related to band-edge emissions [8,39]. The differences on the PL spectra acquired using different filters is shown in Figure 6b, represented as chromaticity coordinates calculated from the PL spectra according to the Comission Internationale de l'Eclairage (CIE 1931) standard [40,41]. In any case, careful attention should be paid during analysis of discussion of the PL signal from SnO, as possible formation of SnO 2 during irradiation should be considered.

Conclusions
Crystalline SnO nanoparticles and plates were synthesized via a hydrolysis method that allowed achievement of a large amount of SnO nanopowder, avoiding an atmospherecontrol during the synthesis. The nanoparticles dimensions ranged from 5 to 16 nm, as confirmed by TEM observations. XRD measurements confirmed the minor oxidation and stability of the as-synthesized SnO nanopowder stored at room conditions for up to 24 months. The oxidation from SnO to SnO 2 was promoted by thermal annealing or by controlled laser irradiation. Temperatures above 300 • C were required to initiate the oxidation from SnO to SnO 2 which was completed at 800 • C, following a nucleation and growth process without formation of intermediate SnO x , as confirmed by thermodiffraction measurements. On the contrary, by using UV or red laser irradiation the transition from SnO to SnO 2 could be controlled, assisted by the formation of intermediate Sn 3 O 4 , as confirmed by Raman spectroscopy. Careful attention should be paid during the PL and Raman analysis, as the use of the laser as excitation source can induce formation of SnO 2 during measurement, thus leading to possibly misleading results and discussion. In this work, the evolution from SnO to SnO 2 was studied as a function of the laser excitation source (UV and red laser), the laser power density (controlled by using neutral filters), and the irradiation duration in order to achieve deeper knowledge and control of the oxidation process. The evolution of the oxidation of the SnO 2 promoted by UV laser irradiation obeys Avrami behavior. Finally, advantage was taken from the controlled SnO oxidation and a tailored spatial SnO/SnO 2 micropatterning was developed based on a controlled laser irradiation. This laser-induced micropatterning can be of potential interest for the fabrication of p-n devices based in all Sn-oxides with applicability in electronic, optoelectronic, and sensing devices.

Supplementary Materials:
The following are available online at https://www.mdpi.com/article/10 .3390/nano11040976/s1, Figure S1: XRD patterns on the period span of 2 years, Figure S2: (a) Complete set of thermodiffractograms and (b) detailed region between 29 and 30 • , Figure S3: Raman spectra acquired using the same filter but with variable irradiation time (60 or 600 s), Figure S4: Photoluminescence deconvolution to Gaussian functions of SnO (a) before and (b) after irradiation.