Silver nanoparticles have been known for the variety of applications in various fields such as catalysis, electronics, optics, medicine, and environment. Particularly, Ag nanoparticles find applications in diagnostic biomedical optical imaging 1 , molecular labeling 2 , spectrally selective coating for the solar energy absorption 3 , cancer therapy 4 , and sensors for refractive index 5 , and ammonia 6 . Moreover, Ag nanoparticles are known for the antimicrobial 7 , surface-enhanced Raman scattering (SERS) 8 and metal-enhanced fluorescence properties 9 . Silver nanoparticles are also known for cytoprotective and post-infected anti-HIV-1 activities 10 . Ag nanorods have been synthesized by arc discharge technique 11 , polyol process 12 , hard template synthesis using porous materials such as mesoporous silica 13 , and carbon nanotubes 14 , using surfactants such as cetyl trimethyl ammonium bromide (CTAB) 15 , sodium dodecyl sulfonate 16 , and dodecyl benzene sulfonic acid sodium (DBS) 17 , seed-mediated 15 and seedless, and surfactantless wet chemical approach 18 . Even though various methods have been known, the facile, quick, and the cost-effective synthetic routes are still elusive. Since compounds of silver like silver oxalate (Ag₂C₂O₄) are photosensitive and yield metallic silver upon the exposure to UV light, those compounds can be photochemically decomposed to obtain Ag nanoparticles in the presence of capping agents. Synthesis of Ag nanoparticles from silver oxalate by thermal and microwave-assisted decomposition has been reported, as temperature needed for the decomposition of silver oxalate is as low as 140 °C 19 20. In this article, a fast synthesis of Ag nanospheres and nanorods by UV irradiation of silver oxalate in the presence of poly (vinyl pyrrolidone) (PVP) and cetyl trimethyl ammonium bromide (CTAB) as capping agents has been demonstrated.

UV-visible diffused reflectance spectrum (DRS) of silver oxalate was recorded using Thermo scientific Evolution 600 UV-visible spectrophotometer. The surface morphology of silver oxalate was analyzed with a FEI (Model: Quanta 200) scanning electron microscope operating at 30 kV. UV-visible spectra of silver colloids were recorded using Jasco V-530 spectrophotometer. HRTEM analyses were carried out using JEOL-3010 transmission electron microscopes working at 300 kV and Philips CM20 transmission electron microscope (TEM) with EDX mapping working at 200 kV. Samples for TEM analysis were prepared by dispersing Ag nanoparticles in ethanol followed by drop casting on a copper grid (400 mesh) coated with carbon film. Powder XRD patterns were recorded using a SHIMADZU XD-D1 diffractometer using Ni-filtered Cu K_αradiation (λ = 1.5406 Å) at the scan rate of 0.1°/s. To correct the instrumental broadening, Si standard was used.

As-synthesized Ag₂C₂O₄ has been confirmed by using XRD and TGA 20 . UV-visible diffuse reflectance spectrum of Ag₂C₂O₄ is shown in Fig. 1. A sharp absorption peak at 285 nm and two humps at 323 nm and 343 nm are observed in the spectrum. This indicates that Ag₂C₂O₄ absorbs in the UV region. The band gap of as-synthesized Ag₂C₂O₄ has been found to be 4.35 eV. SEM image of Ag₂C₂O₄ given in Fig. 2 shows irregular shaped particles of size in the range of 0.5–7.5 μm.

UV-visible spectra of synthesized Ag colloids are given in Fig. 3. UV-visible spectrum of Ag colloid synthesized using 1:5 of Ag₂C₂O₄ and PVP shows a single sharp SPR band centered at around 404 nm. This single sharp SPR band indicates the presence of spherical Ag nanoparticles with average size below 10 nm in the colloid 19 . The corresponding HRTEM images given in Fig. 4a, b shows highly dispersed Ag nanoparticles on the grid. Size of the Ag particles lies between 1 and 6 nm and the average size of Ag nanoparticles is around 2 nm. The lattice-resolved image of a single Ag nanoparticle (6.2 × 7.2 nm) given in Fig. 4c shows the cubic arrangement with inter planar d-spacings of 0.2 and 0.288 nm; these d values correspond to (200) and (110) planes of Ag metal, respectively. Hence, the exposed face is bound with (100) facet. These observations confirm the presence of silver in fcc arrangement. Since synthesis of fine and narrow dispersed particles has been achieved with 1:5 ratio of Ag₂C₂O₄ and PVP, further studies based on varying the ratio of Ag₂C₂O₄ and PVP have not been carried out.

In the case of 1:2 ratio of Ag₂C₂O₄ and CTAB, a single broad SPR band observed with λ_max at 429 nm indicates the presence of Ag particles with the wide distribution of size or anisotropic Ag nanoparticles 20 22. The corresponding HRTEM image is shown in Fig. 5, which shows the presence of spherical and quasi-spherical Ag nanoparticles with size in the range of 4–62 nm. Average size of Ag nanospheres is ~30 nm. Lattice-resolved images (Fig. 5b and c) of single Ag nanospheres show lattice fringes corresponding to (111) plane of Ag metal. SAED pattern of a Ag nanosphere given in Fig. 5d shows spots and the rings composed of spots. This pattern implies the polycrystalline nature of Ag nanospheres. The spots as well as rings are indexed to (111), (200), (220), (311), (222), (400), (331), (420), and (422) planes of silver with fcc structure (JCPDS file - 89-3722).

UV-visible spectrum corresponding to Ag colloid formed using 1:5 ratio of Ag₂C₂O₄ and CTAB shows a couple of SPR bands with λ_max at 400 and 631 nm. This implies the presence of anisotropic nanoparticles like nanorods and Ag spherical particles. SPR bands at 400 nm and at 631 nm correspond to transverse interaction and another to longitudinal interaction, respectively, of anisotropic Ag nanoparticles like rods with visible light 15 23. The corresponding HRTEM images in Fig. 6a, b show the presence of nanorods and anisotropic particles. The length of the nanorods is up to 61 nm and the aspect ratio of nanorods varies from 2 to 6. The nanorods are not uniform in thickness, non-straight, and consist of particles at the edge. The average thickness of Ag nanorods is around 6 nm. Some of the rods appear to have formed through the attachment of the particles. Lattice-resolved HRTEM image of the Ag nanorod is shown in Fig. 6c. Lattice fringes with a d value of 0.25 nm is observed at the middle part of the rod. This corresponds to 1/3{422} reflection of silver with fcc structure. In general, appearance of 1/3{422} reflection is forbidden for the perfect single crystalline fcc lattice. However, it is observed only in the case of nanoplates or thin films of Au and Ag metals bound by atomically flat surfaces 24 . The corresponding SAED pattern, recorded in the direction perpendicular to the surface of Ag nanorod, shows spots. This pattern reveals that middle part of Ag nanorod is single crystalline. The symmetric hexagonal spots observed are indexed to {220}, {331}, and {422} reflections. These observations, too, reveal that top and basal planes of the nanorod are bound with {111} facets 25 . A line in Fig. 6c indicates the presence of twin boundaries parallel to rod. At the edge of the nanorod, a particle with lattice fringes corresponding to (200) plane of Ag with fcc structure is observed. This shows that the nanorod has originated from the particle and hence the rod, as a whole, is polycrystalline. This observation implies that particles act as seeds for the formation of nanorods. In the case of 1:8 ratio of Ag₂C₂O₄ and CTAB, UV-visible spectrum shows SPR bands at 409, 517, and 725 nm, revealing the presence of anisotropic Ag nanoparticles. The corresponding HRTEM in Fig. 7 shows the presence of featureless nanorods. In Fig. 7b, a nanorod with diameter of ~44 nm and aspect ratio of around 5 is observed. In this case too, a particle is present at the end of the nanorod. However, the formation of monodispersed nanorods has not been achieved in the case of 1:8 ratio of Ag₂C₂O₄ and CTAB. Hence, it is clear that only 1:5 ratio of Ag₂C₂O₄ and CTAB is better optimal ratio to form nanorods than 1:2 and 1:8 ratios.

In order to understand the intermediate stage of the reaction, reaction mixture (1:8 ratio of Ag₂C₂O₄and CTAB) has been analyzed by HRTEM after 5 min of UV irradiation. The corresponding TEM images in Fig. 7c, d show the decomposed surface of Ag₂C₂O₄decorated with Ag nanoparticles_.The contrast between Ag metal core and Ag₂C₂O₄compound is clearly seen from Fig. 7d. However, after 10 min of irradiation, no Ag₂C₂O₄has been observed. This shows that 10 min of UV-irradiation is enough for complete decomposition of Ag₂C₂O₄dispersed in the solution. The decomposition of Ag₂C₂O₄is so rapid because the intensity of UV lamp employed is high.

XRD powder patterns of Ag nanospheres and Ag nanorods are shown in Fig. 8. The inter planar d-spacing of XRD peaks correspond to (111), (200), (220), (311), and (222) planes of Ag with fcc structure (JCPDS file no: 89-3722). Average crystallite size corresponding to each plane has been calculated from XRD patterns using Scherrer’s equation 26 and given in Fig. 9. The average crystallite size of the spherical Ag nanoparticles formed using PVP lies between 2.8 and 4.7 nm. However, as per HRTEM analysis, it is around 2 nm. This deviation is mainly due to the poor scattering ability of Ag particles of size below 3 nm. The average crystallite size of Ag nanospheres synthesized using 1:2 ratio of Ag₂C₂O₄ and CTAB lies between 25 and 32 nm and the corresponding particle size from HRTEM lies between 4 and 62 nm. This observation indicates the polycrystalline nature of Ag nanoparticles. In the case of spherical nanoparticles, average crystallite size decreases while moving from low to high Bragg angles. This reveals the isotropic nature of the nanocrystals. In the case of Ag nanorods, the average crystallite size lies in the range between 6.4 and 10.4 nm, and particle size observed from HRTEM is higher than that from XRD analysis. This reveals that Ag nanorods are polycrystalline as evidenced by HRTEM analysis where rods contain more than one crystallite (Fig. 6b). Moreover, the average crystallite size of (111) planes considerably deviates from that of other planes. This deviation reveals the faceting in the nanocrystals. Since (111) planes show higher value of average crystallite size than that of other planes, longitudinal direction of the rods is bound with {111} planes. This observation shows good agreement with HRTEM image (Fig. 6c).

Texture coefficient corresponding to each plane in XRD pattern has been calculated by Hall method to understand the faceting in nanoparticles and shown in Fig. 10. Texture coefficient (C _hkl ) has been calculated using the following Eq. 1 27 .

where, C _(hkl) is the texture coefficient of the facet (hkl), I _(hkl) is the intensity of the (hkl) reflection of the sample under analysis, I _o(hkl) is the intensity of the (hkl) reflection of a polycrystalline bulk sample, and ‘n’ is the number of reflections taken into account. By using this equation, the preferential orientation of the facets can be understood. C _(hkl) is expected to be unity for the facet, which does not have preferential orientation. If it is higher than unity, it is a preferentially grown (highly exposed to X-ray) facet. The reference (polycrystalline bulk) used for the calculation is JCPDS file 89-3722. In the case of texture coefficient, Ag nanorods exhibit the similar trend as observed in the case of crystallite size. In other words, C ₍₁₁₁₎ and C ₍₂₂₂₎ are above unity and deviate from that of others. This reveals the faceting of {111} planes in Ag nanorods. In the case of both the Ag nanospheres, texture coefficients increase while moving from planes of lower to higher Bragg angle. In other words, C ₍₂₂₀₎ C ₍₃₁₁₎, and C ₍₂₂₂₎ are higher than C ₍₁₁₁₎ and C ₍₂₂₂₎. This trend is attributed to the difference between the synthesized Ag nanospheres and polycrystalline bulk reference. This difference is due to the effect of particle size in X-ray scattering. In the case of nanospheres, peaks at higher Bragg angle shows higher intensity than in the case of bulk sample. Similar phenomenon has been observed for Pt and Pd nanoparticles 28 29. In fact, the particle size effect on scattering is observed within two spherical Ag nanoparticles synthesized with different sizes, where C ₍₁₁₁₎ of smaller Ag nanospheres (~2 nm) is lower than that of bigger Ag nanospheres (~30 nm). Moreover, C ₍₁₁₁₎ of Ag nanorods is smaller than C ₍₂₂₂₎ for the same reason.

In order to understand the contribution of strain in line broadening, line-broadening analysis was done by Williamson–Hall plot and shown in Fig. 11 30 . Williamson–Hall (WH) plot is the plot of the integral breadth in the reciprocal space (ΔK = βcosθ/λ, β-FWHM of XRD line) with respect to reciprocal lattice space (K = 2sinθ/λ). The slope corresponds to strain and the intercept corresponds to 0.9/D (D-crystallite size). The straight line (linear fit) was drawn using the least-square analysis. The correlation coefficient (R), the average crystallite size, and strain in lattice are given in Table 1. The R value of Ag nanocrystals are in the following order: nanospheres (~2 nm) < nanorods < nanospheres (~30 nm). The same is the order for the decrease of anisotropy in the broadening of nanocrystals. The microstrain in Ag nanocrystals are in the following order: nanospheres (~2 nm) > nanorods > nanospheres (~30 nm). This observation indicates that the defect density is higher in the nanospheres (~2 nm) than in nanorods 31 . Average crystallite size calculated using WH plot for nanospheres (~2 nm) and nanorod is slightly higher than that from Scherrer’s equation due to the contribution of strain in line broadening. This is mainly due to the defects in lattice of small Ag crystals.

Silver oxalate decomposes under UV irradiation to yield metallic silver and CO₂ gas. This is mainly owing to the high photosensitivity of Ag₂C₂O₄ 21 _. Since this decomposition of Ag₂C₂O₄ is thermodynamically favorable due to the suitable reduction potentials of oxalate 27 and 32 , decomposition occurs rapidly under UV radiation to yield metallic Ag as shown in Eq. 2.

Oxalate dianion in Ag₂C₂O₄ is getting excited under the UV light and decomposes into CO₂. During the decomposition, electrons are simultaneously transferred to Ag⁺ ions to form Ag metal 21 . Absorption of UV light by Ag₂C₂O₄ is clear from the UV-visible DRS in Fig. 1. Formation of CO₂ has been confirmed by the appearance of white precipitate when the outlet of the reaction was passed through baryta (Ba(OH)₂) solution 19 . Thus-formed Ag atoms nucleate after attaining a concentration and grow into particles. In the case of PVP as capping agent, formation of fine spherical particles only has been observed. This is due to the capping of PVP at all the crystal planes on Ag nuclei. Hence, faceting (anisotropic growth) of the crystals has not been observed. Formation of very fine particles (~2 nm) is due to the homogenous nucleation (yielding larger number of nuclei) followed by fast particle growth. Moreover, PVP, the macromolecular capping agent, prevents agglomeration of nanocrystals and makes the fine particles stable. However, in the case of CTAB as the capping agent (1:2 ratio of Ag₂C₂O₄ and CTAB), formation of spherical nanoparticles (~30 nm) has been observed. This is due to the poor capping ability of CTAB. Formation of nanorods in the case of 1:5 ratio of Ag₂C₂O₄ and CTAB is expected due to the suitable concentration of CTAB. Further increase in the concentration ratio (1:8) increases the length of the rods but featureless curvy nanorods are also observed. In general, formation of monodispersed Ag nanorods depends on the use of seed, pH of the medium, rate of the reduction of Ag⁺ ions or rate of generation of Ag atoms, and concentration of CTAB 33 . Ascorbic acid is preferred as a reducing agent in the synthesis of Ag and Au nanorods. It is because ascorbic acid is a weak reducing agent and hence, the controlled generation of Ag atom occurs. It is because controlled generation of Ag atoms is necessary for the formation of monodispersed Ag nanorods 33 . In the current method, Ag nanoparticles first generated act as seeds as observed in HRTEM image (Fig. 6c). However, further particle growth is so fast due to the fast generation of Ag atoms in the growth solution out of the rapid decomposition. Hence, the rate of generation of Ag atoms from the decomposition is expected to have a major role in the formation of nanorods along with nanospheres (polydispersity). Since the rate of decomposition is directly proportional to the intensity of the UV lamp, low-intensity UV lamp may be suitable for the synthesis of monodispersed Ag nanorods. Apart from the role of CTAB for the formation of Ag nanorods, there is a possibility for the formation of worm-like Ag nanorods by the mere UV irradiation. This phenomenon is well known in silver halide photography where formation of Ag filaments occurs upon the UV irradiation on KBr microcrystals 34 35 36. In such a case, small Ag nuclei formed on the surface of the silver halide microcrystals catalyze the reduction of Ag⁺ ions present in silver halide microcrystals and give rise to the formation of Ag filaments. However, these Ag filaments degrade to small Ag nanoparticles (size <5 nm) upon further exposure to UV light over a period of time 37 . Hence, the effect of the UV irradiation is also responsible for the polydispersity of Ag nanoparticles and Ag nanorods obtained in the current method. In general, UV-visible irradiation on Ag and Au nanoparticles leads to the explosion of bigger particles into small clusters and the sintering of the small clusters to bigger aggregates 37 38 39. These two processes competitively occur in presence of UV-visible light. In such cases, defects are created in the resulting Ag nanocrystals due to the heating effect of UV-visible irradiation. This phenomenon is also possible in the current synthesis because Hg lamp employed possesses some amount of visible light also. Based on the above observations, formation mechanism has been explained schematically as shown in Fig. 12.

A fast synthesis of ultra-fine Ag nanospheres and nanorods has been demonstrated from silver oxalate in the presence of UV irradiation by using PVP and CTAB as capping agents, respectively. Spherical Ag nanoparticles of average size around 2 nm have been synthesized with 1:5 (w/w) ratio of Ag₂C₂O₄and PVP. Ag nanorods of low aspect ratio have been obtained when ratio of Ag₂C₂O₄and CTAB is 1:5 (w/w) in the absence of seed mediation. The preferential orientation of {111} facets has been observed in the case of nanorods. The monodispersity of the rods has not been achieved due to the fast generation of Ag atoms at the expense of Ag₂C₂O₄. Hence, utilization of low-intensity UV lamps may give rise to the formation of monodispersed Ag nanorods. The synthesized Ag nanoparticles with smaller size are found to contain more defects in lattice than those with the bigger size. The synthesized fine Ag nanospheres and the Ag nanorods can be potential candidates for catalysis and biocidal activities.