Proficient One-Step Heat-Up Synthesis of Manganese Sulfide Quantum Dots for Solar Cell Applications

The necessity to develop renewable energy resources that are highly durable and flexible with superior energy density and capacitance ability has attracted considerable interest in the field of solar cell research. Semiconducting compound materials that are easily available, hazard-free and cost-effective are emerging as potential solutions to tackle this challenge. Herein, we present multiple molecular precursors used to grow manganese sulfide nanoparticles through a proficient one-step heat-up approach. For all of the tested samples, the X-ray diffraction peaks correspond to a γ-MnS hexagonal wurtzite structure. UV-Vis spectroscopy yielded absorption wavelengths of 359–420 nm and band-gap energies of 3.78–4.0 eV. Photoluminescence analysis shows characteristics of red and blue shift from 451–602 nm. High-resolution transmission electron microscopy (HRTEM) and selected-area electron diffraction (SAED) reveal a narrow size distribution with nanosticks and large contact areas, which are critical for improved catalytic performance. The current study provides an improved pathway to a well-grown and uniform nanocrystal structure for applications in energy devices.


Introduction
Semiconductor quantum dots (QDs) employed as photosensitizers with tunable band gaps as an alternative to dye-sensitized solar cells (DSCs) has attracted increasing attention from researchers in recent years. QDs have a unique absorption coefficient for large light, with high stability due to their tunable band gap [1][2][3][4][5]. The use of QD photosensitizers from inorganic semiconductors is gaining increasing attention, with more studies being conducted due to their advantages relative to homologue dyes [1][2][3]. Owing to their physical and chemical properties, chalcogenide metal compounds, such as manganese, have recently received a considerable amount of attention as modern, innovative technology in a variety of fields [6]. The growth conditions of QD semiconductors can be altered via techniques to attain desirable optical, structural, electrical and morphological properties [7,8]. Magnetic semiconductor manganese sulfide (MnS) has a band gap of (Eg = 3.1-3.7 eV) and considerable potential in applications such as blue-green light emitters, optoelectronic devices, solar cells, photoconductors, sensors, coatings and mass optical memories [9][10][11][12]. They grow at lower temperatures and come in three structural shapes: zinc-blende, rock-salt and wurtzite. The rock-salt MnS structure is more stable than both β and γ-MnS and can irreversibly transform into a stable form of rock-salt structure at high temperatures of 100-400 • C [13][14][15][16], accounting for the unique chemical properties displayed by metastable MnS as compared to the stable phase [8].
Various approaches have been reported for the preparation of MnS through hydrothermal, solvothermal, chemical bath deposition (CBD), chemical vapor deposition (CVD) and successive ionic layer adsorption and reaction (SILAR) [17,18]. A single-source method produces high-purity and cost-effective materials by incorporating the required elements into one compound [1][2][3]. This approach involves a simple decomposition of the molecular precursor, usually dithiocarbamate metal complexes, in an inert environment to the desired temperature [19][20][21]. Such approaches have been employed for the formation of metal oxides and metal chalcogenides with various morphologies for different nanomaterials, such as nanofabrics, nanodiscs, nanorods, nanospheres and nanowires [22,23]. In the present study, we report on the formation of MnS through a single-source precursor approach. We investigated roles of aromatic mixed and single ligands in the MnS structural, optical, morphological and thermal stability.

Thermogravimetric Analysis (TGA) of Precursors PR1, PR2 and PR3
Thermogravimetric elevation within the temperature range of 30-900 • C was carried out to determine the thermal properties of the complexes shown in Figure 1b [24]. molecular precursor, usually dithiocarbamate metal complexes, in an inert environment to the desired temperature [19][20][21]. Such approaches have been employed for the formation of metal oxides and metal chalcogenides with various morphologies for different nanomaterials, such as nanofabrics, nanodiscs, nanorods, nanospheres and nanowires [22,23]. In the present study, we report on the formation of MnS through a single-source precursor approach. We investigated roles of aromatic mixed and single ligands in the MnS structural, optical, morphological and thermal stability.

Thermogravimetric Analysis (TGA) of Precursors PR1, PR2 and PR3
Thermogravimetric elevation within the temperature range of 30-900 °C was carried out to determine the thermal properties of the complexes shown in Figure 1b

XRD
Dithiocarbamate complexes are suitable precursors that are usually stable at room temperature but decompose under high heat to form metal sulfide. The XRD reveals the structural pattern of the prepared MnS nanoparticles using three molecular precursors The diffraction peaks obtained from the XRD analysis are illustrated in Figure 2 for

XRD
Dithiocarbamate complexes are suitable precursors that are usually stable at room temperature but decompose under high heat to form metal sulfide. The XRD reveals the structural pattern of the prepared MnS nanoparticles using three molecular precursors. The diffraction peaks obtained from the XRD analysis are illustrated in Figure 2 for MnS_1, MnS_2 and MnS_3. The obtained peaks are consistent with the γ-MnS hexagonal wurtzite structure data standards (JCPDS Card No. . The XRD results obtained in this study are in agreement with previous reports [25][26][27] on the γ-MnS wurtzite phase. The XRD patterns of the three samples at 260 • C show disperity in intensity that can be attributed to differences in carbon ring molar concentration in the molecular precursor with manganese ions [28,29]. Furthermore, the γ-MnS phase, nanocrystalline reductions and structural distortion were previously reported as a result of the Jahn-Teller effect at room temperature, as well as the oxygen content [28,29].
Molecules 2022, 27, x FOR PEER REVIEW 3 of 13 attributed to differences in carbon ring molar concentration in the molecular precursor with manganese ions [28,29]. Furthermore, the γ-MnS phase, nanocrystalline reductions and structural distortion were previously reported as a result of the Jahn-Teller effect at room temperature, as well as the oxygen content [28,29].

FTIR
As shown in Figure 3, the three samples of MnS have the same intensities of vibrations at various peaks. The vibration peaks at 580 cm −1 are related to Mn-S vibration modes in all the samples, as similarly reported in [30]. The low-intensity bands observed around 400-500 cm −1 are attributed to the interaction between resonances of the sulfide ions. C-S linkage vibration modes are observed at 720 cm −1 for all the samples, whereas C-N peaks occur at 1471-1634 cm −1 [31]. The high-intensity bands observed around 2918-2852 cm −1 are ascribed to the sp 1 (C-H) group in phenyl units [30], whereas the peaks at 3314 cm −1 correlate to the N-H stretching modes for the three MnS samples.   Figure 3, the three samples of MnS have the same intensities of vibrations at various peaks. The vibration peaks at 580 cm −1 are related to Mn-S vibration modes in all the samples, as similarly reported in [30]. The low-intensity bands observed around 400-500 cm −1 are attributed to the interaction between resonances of the sulfide ions. C-S linkage vibration modes are observed at 720 cm −1 for all the samples, whereas C-N peaks occur at 1471-1634 cm −1 [31]. The high-intensity bands observed around 2918-2852 cm −1 are ascribed to the sp 1 (C-H) group in phenyl units [30], whereas the peaks at 3314 cm −1 correlate to the N-H stretching modes for the three MnS samples. attributed to differences in carbon ring molar concentration in the molecular precursor with manganese ions [28,29]. Furthermore, the γ-MnS phase, nanocrystalline reductions and structural distortion were previously reported as a result of the Jahn-Teller effect at room temperature, as well as the oxygen content [28,29].

FTIR
As shown in Figure 3, the three samples of MnS have the same intensities of vibrations at various peaks. The vibration peaks at 580 cm −1 are related to Mn-S vibration modes in all the samples, as similarly reported in [30]. The low-intensity bands observed around 400-500 cm −1 are attributed to the interaction between resonances of the sulfide ions. C-S linkage vibration modes are observed at 720 cm −1 for all the samples, whereas C-N peaks occur at 1471-1634 cm −1 [31]. The high-intensity bands observed around 2918-2852 cm −1 are ascribed to the sp 1 (C-H) group in phenyl units [30], whereas the peaks at 3314 cm −1 correlate to the N-H stretching modes for the three MnS samples.

UV-Vis Spectroscopy
The optical behavior of the fabricated MnS_1, MnS_2 and MnS_3 nanoparticles was evaluated via UV-Vis spectroscopy. Both MnS_2 and MnS_3 exhibit absorption properties at 402 nm with a wavelength in the visible regions, as indicated in Figure 4a,b, with a band-gap energy of 3.78 eV. Unlike the other two samples, MnS_1 displays a slit edge with an absorption response at 359 nm and 420 nm and an energy band gap at 4.0 eV. This slit edge can be linked to the carbon ring molar concentration in the molecular precursor with manganese ions, which is a similar trend as that observed in the XRD results.

UV-Vis Spectroscopy
The optical behavior of the fabricated MnS_1, MnS_2 and MnS_3 nanoparticles was evaluated via UV-Vis spectroscopy. Both MnS_2 and MnS_3 exhibit absorption properties at 402 nm with a wavelength in the visible regions, as indicated in Figure 4a,b, with a band-gap energy of 3.78 eV. Unlike the other two samples, MnS_1 displays a slit edge with an absorption response at 359 nm and 420 nm and an energy band gap at 4.0 eV. This slit edge can be linked to the carbon ring molar concentration in the molecular precursor with manganese ions, which is a similar trend as that observed in the XRD results.

PL
The photoluminescence spectra of MnS_1, MnS_2 and MnS_3 are shown in Figure 5. All the samples have the same emission peaks at 451 nm, 490 nm, 511 nm, 527 nm, 541 nm and 609 nm at 365 nm excitation. The observed emission peaks at 451 nm and 490 nm were assigned to the blue shift and band-edge emission involving the excited states of the Mn 2+ ions [27]. The emission peak at 511 nm was attributed to the green shift of manganese and sulphur vacancies associated with interstitial defects [32,33]. Three other peaks at 527 nm, 541 nm and 609 nm are ascribed to the octahedral-coordinated Mn 2+ ion excitation, which in agreement with the results reported in [32,33]. The emission peaks can be attributed to the radiative recombination of electrons in surface-state shallow traps with photogenerated holes caused by lattice-stacking faults, in agreement with the stacking faults identified by HRTEM [27,34].

PL
The photoluminescence spectra of MnS_1, MnS_2 and MnS_3 are shown in Figure 5. All the samples have the same emission peaks at 451 nm, 490 nm, 511 nm, 527 nm, 541 nm and 609 nm at 365 nm excitation. The observed emission peaks at 451 nm and 490 nm were assigned to the blue shift and band-edge emission involving the excited states of the Mn 2+ ions [27]. The emission peak at 511 nm was attributed to the green shift of manganese and sulphur vacancies associated with interstitial defects [32,33]. Three other peaks at 527 nm, 541 nm and 609 nm are ascribed to the octahedral-coordinated Mn 2+ ion excitation, which in agreement with the results reported in [32,33]. The emission peaks can be attributed to the radiative recombination of electrons in surface-state shallow traps with photogenerated holes caused by lattice-stacking faults, in agreement with the stacking faults identified by HRTEM [27,34].

UV-Vis Spectroscopy
The optical behavior of the fabricated MnS_1, MnS_2 and MnS_3 nanoparticles was evaluated via UV-Vis spectroscopy. Both MnS_2 and MnS_3 exhibit absorption properties at 402 nm with a wavelength in the visible regions, as indicated in Figure 4a,b, with a band-gap energy of 3.78 eV. Unlike the other two samples, MnS_1 displays a slit edge with an absorption response at 359 nm and 420 nm and an energy band gap at 4.0 eV. This slit edge can be linked to the carbon ring molar concentration in the molecular precursor with manganese ions, which is a similar trend as that observed in the XRD results.

PL
The photoluminescence spectra of MnS_1, MnS_2 and MnS_3 are shown in Figure 5. All the samples have the same emission peaks at 451 nm, 490 nm, 511 nm, 527 nm, 541 nm and 609 nm at 365 nm excitation. The observed emission peaks at 451 nm and 490 nm were assigned to the blue shift and band-edge emission involving the excited states of the Mn 2+ ions [27]. The emission peak at 511 nm was attributed to the green shift of manganese and sulphur vacancies associated with interstitial defects [32,33]. Three other peaks at 527 nm, 541 nm and 609 nm are ascribed to the octahedral-coordinated Mn 2+ ion excitation, which in agreement with the results reported in [32,33]. The emission peaks can be attributed to the radiative recombination of electrons in surface-state shallow traps with photogenerated holes caused by lattice-stacking faults, in agreement with the stacking faults identified by HRTEM [27,34].

HRTEM and SAED
HRTEM and selected area electron diffraction (SAED), as shown in Figure 6c,f,i were used to identify the crystalline structure and size distribution of well-grown MnS_1, MnS_2 Molecules 2022, 27, 6678 5 of 12 and MnS_3 nanoparticles. MnS_1 and MnS_3 exhibit a narrow size distribution between 13.5-23.88 nm and 15.52 nm with nanosticks, indicating improved catalytic performance due to the large contact area, as shown in Figure 6a,b,g,h. The inserted SAED shown in Figure 6c shows a lattice d spacing of 0.46 nm, which is indexed to the MnS crystal plane of 220. MnS_3 shows an interplanar distance of 0.32 nm as obtained from the lattice fringes (Figure 6i), corresponding to the 002 planes of MnS. This is also affirmed by the inserted image in Figure 6i of the SAED pattern. The inner hollow structure, as well as the outer and inner surfaces with a smooth and relatively dense surface, are confirmed by Figure 6d,e for MnS_2, with a particle size of 2.96-58.88 nm. The SAED pattern shown in the insert in Figure 6f indicates a high crystallinity. The lattice fringes shown in Figure 6e with a d spacing of 0.31 nm could be indexed to the 002 plane of the MnS crystal. The HR-TEM images are in conformity with the respective XRD planes and supported by the results of previous studies [34][35][36]. A summary of the samples prepared through the single-source precursor route is presented in Table 1.

FESEM and EDS
The microstructure and morphology of MnS_1, MnS_2 and MnS_3 nanoparticles were determined from SEM images and are displayed in Figure 7a-f. The FESEM images for MnS_1 reveal a spongy spherical microstructure with small nanoparticles (see Figure  6a

FESEM and EDS
The microstructure and morphology of MnS_1, MnS_2 and MnS_3 nanoparticles were determined from SEM images and are displayed in Figure 7a-f. The FESEM images for MnS_1 reveal a spongy spherical microstructure with small nanoparticles (see Figure 6a,b) in agreement with the HRTEM results. The FESEM morphology of the MnS_2 and MnS_3 samples consists of spherical shapes and other irregular elongated shapes of numerous particles, as shown in Figure 6c-f. The SEM results followed a similar pattern as the XRD, further affirming the SEM results. [37,38]. The quantitative and qualitative characteristics of the three samples were taken from the EDS spectrum to determine the elemental composition of the MnS nanoparticles, as shown in Figure 8a-c. The EDS clearly reveals the purity of the three MnS nanoparticles, with the presence of elements such as Mn, C and S with no other elements [37].
In this study, we employed a single-source precursor using MnCl 2 ·4H 2 O and TOPO as coordinating solvents in a single step to form γ-MnS nanoparticles, representing a cost-effective method to address the stoichiometry retention challenge of γ-MnS during the deposition process for enhanced and stable photovoltaic performance. Balpinar and Göde [39] reported an efficiency of 3.40-2.28% for CdS doped with Mn with a band gap of 2.41-2.43 eV. According to Akman's [40] research, doping the Mn/ZnO photoanode in solar cell applications resulted in stability and an improvement in efficiency of 2.11-4.20% for 3.34-3.19 eV. Fadaam et al. [41] demonstrated enhanced conversion for MnS through annealing at 300 • C with a band-gap energy of 2.9 eV. Cao et al. [42] reported on the heterojunction structure of NiS2/MnS with 6.44 % and 4.81% for MnS FTO as a potential counter electrode to replace Pt as a low-cost and highly efficient material for dye-sensitized solar cells. Based on electrochemical, structural and optical analyses, the γ-MnS phase was investigated as an anode material and as efficient visible light emitters with improved cycling stability for Li-ion batteries [43][44][45]. The band-gap energy at 3.78-4.0 eV and the high emission intensity in the present study are strong indications that these materials can absorb the entire solar spectrum, improving efficiency in solar cell applications. Furthermore, the irregular protrusions on the surface are vital aspects of materials that can enhance electrolyte transport and photoactivity and optimize light absorbance. the XRD, further affirming the SEM results. [37,38]. The quantitative and qualitative characteristics of the three samples were taken from the EDS spectrum to determine the elemental composition of the MnS nanoparticles, as shown in Figure 8a   In this study, we employed a single-source precursor using MnCl₂4 H₂O and TOPO as coordinating solvents in a single step to form γ-MnS nanoparticles, representing a cost-

Synthesis of Ammonium N-Piperidinyldithiocarbamate
Ammonium N-piperidinyldithiocarbamate was prepared according to the literature [1]. A volume of 9.9 mL (0.1 mol) of piperidine was added to 30 mL of ammonium solution with 6.04 mL (0.1 mol) of carbon disulfide in a dropwise reaction at 5 • C and stirred for 1 h to precipitate. A solid yellow precipitate was formed. The precipitate was filtered and washed with diethyl ester and dried in the air, which resulted in the final product of ammonium N-piperidinyldithiocarbamate labelled as

Synthesis of Bis(N-Piperl-N-p-Anisildithiocarbamato)Manganese(II) Complexes, Mn[N-Piper-N-p-Anisdtc] (PR1)
MnCl 2 ·4H 2 O salt (0.3147 g, 2.5 mmol) dissolved in (15 mL) was slowly added to (0.4459 g, 2.5 mmol and 0.5409 g, 2.5 mmol) N-anildtc and N-p-anisildtc ligands dissolved in 15 mL distilled water under stirring in a 1:1:1 ratio. A dark brown precipitate was observed. The mixture was stirred constantly at room temperature for 1 h. The dark brown precipitate was filtered and washed with distilled water three times and dried under a calcium vacuum overnight, as shown in

Synthesis of MnS Metals Sulfide Nanoparticles
The MnS metal sulfide nanoparticles were fabricated by a simple one-step, one-pot technique with the aid of three reagents in 2 h. In a typical synthesis under an inert atmosphere, 0.2 g of PR1 dissolved in 4 mL of oleic acid was mixed with 3 g of hot HDA coordination solvent inserted into a three-neck bottom flask with a magnetic stirrer, cooler reflux and a thermometer. The HDA was heated to between 20 and 30 degrees Celsius before being raised to 260 degrees Celsius. The reaction was maintained for 1 h at the desired temperature. The dark solution was collected by allowing the temperature to drop to 70 °C, then adding about 50 mL of methanol before undergoing centrifugation at 2000 rpm for 30 min to remove the excess coordinating solvent. Oleic acid was then dried in a vacuum. The final product of MnS was formulated as MnS_1. The same procedures were followed for MnS_2 from PR2 and MnS_3 from PR3, as shown in Scheme 1 [1][2][3].

Materials Characterizations
The optical properties, surface morphology, thermal stability, elemental compositions and thickness of the MnS nanoparticles were evaluated through the following techniques: field emission scanning electron microscopy (FE-SEM, S-4200, Hitachi, Munich, Germany) coupled with energy dispersive X-ray spectroscopy (EDS) on-system, operating at a voltage of 15 kV. The size distributions of the three samples were identified using a JEOL JEM 2100 high-resolution transmission electron microscope (HRTEM, Pleasanton, Scheme 1. Preparation of MnS_1, MnS_2 and MnS_3 QDs.

Synthesis of MnS Metals Sulfide Nanoparticles
The MnS metal sulfide nanoparticles were fabricated by a simple one-step, one-pot technique with the aid of three reagents in 2 h. In a typical synthesis under an inert atmosphere, 0.2 g of PR1 dissolved in 4 mL of oleic acid was mixed with 3 g of hot HDA coordination solvent inserted into a three-neck bottom flask with a magnetic stirrer, cooler reflux and a thermometer. The HDA was heated to between 20 and 30 degrees Celsius before being raised to 260 degrees Celsius. The reaction was maintained for 1 h at the desired temperature. The dark solution was collected by allowing the temperature to drop to 70 • C, then adding about 50 mL of methanol before undergoing centrifugation at 2000 rpm for 30 min to remove the excess coordinating solvent. Oleic acid was then dried in a vacuum. The final product of MnS was formulated as MnS_1. The same procedures were followed for MnS_2 from PR2 and MnS_3 from PR3, as shown in Scheme 1 [1][2][3].

Materials Characterizations
The optical properties, surface morphology, thermal stability, elemental compositions and thickness of the MnS nanoparticles were evaluated through the following techniques: field emission scanning electron microscopy (FE-SEM, S-4200, Hitachi, Munich, Germany) coupled with energy dispersive X-ray spectroscopy (EDS) on-system, operating at a voltage of 15 kV. The size distributions of the three samples were identified using a JEOL JEM 2100 high-resolution transmission electron microscope (HRTEM, Pleasanton, CA, USA) operating at 200 kV. Their structural patterns were established using X-ray diffraction (XRD, Cambridge, UK) analysis with Cu Ka radiation at 40 mA and 40 kV, respectively. ThermoGravimetric Analyser 4000 (TGA Perkin Elmer, Johannesburg, South Africa) was performed at temperatures ranging from 30 to 600 • C at a rate of 10 • C min −1 . Fourier transform infrared spectroscopy (FTIR) analysis was achieved with the aid of a Bruker Platinum ATR Model Alpha (Waltham, MA, USA). PerkinElmer LAMBDA 365 and LS 45 fluorimeters (Waltham, MA, USA) were used to understand the optical properties (UV-Vis and PL analysis) of the three samples. NMR analysis was carried out using a Bruker AV-400 spectrometer (Waltham, MA, USA), working at 400.13 MHz and 300 K, with a spinning rate of 4 kHz.

Conclusions
In conclusion, a heat-up approach with the aid of coordinating solvent was used to form γ-MnS hexagonal wurtzite structure quantum dots with varying morphologies. FTIR reveals vibration peaks related to MnS vibration modes in all the samples. SEM and HRTEM images reveal a spongy and irregular spherical microstructure with numerous small particles. UV-Vis and photoluminescence show a band-gap energy of 3.78-4.0 eV and emission peaks in the range of 451-602 nm. The purity of the three MnS nanoparticles confirms the presence of Mn and S elements. The well-grown and uniform nanocrystal with an inner hollow structure, smooth outer and inner surfaces and a relatively dense surface indicates that the formed γ-MnS can be explored for energy and storage-device applications.