Open Access

Solvothermal synthesis, growth mechanism, and photoluminescence property of sub-micrometer PbS anisotropic structures

Nanoscale Research Letters20127:668

DOI: 10.1186/1556-276X-7-668

Received: 24 September 2012

Accepted: 15 November 2012

Published: 6 December 2012


The sub-micrometer PbS with anisotropic microstructures including fishbone-like dendrites, multipods, cubes, corallines, and hopper cubes were successfully prepared by the solvothermal process. Different morphologies can be obtained by adjusting the reaction temperatures or using the nontoxic controlled reagents which can tune the relative growth rate in the <100> direction and the <111> direction of PbS nuclei. Based on the viewpoint of crystallography about face-centered cubic crystal structure, the possible formation mechanism for sub-micrometer anisotropic structures has been discussed. The difference between the enhanced growth rates on the {100} and {111} planes induced the change of ratio between the growth rates in the <100> and <111> directions, which resulted in the formation of the different PbS anisotropic microstructures. The PbS anisotropic structures exhibited the different visible emission with a peak in the red regions mainly attributed to the variation of shape, size, and the trap state of as-obtained PbS.


Nanostructures Semiconductors Chemical synthesis Crystal growth Photoluminescence


With a near-infrared direct narrow bandgap (0.41 eV at 300 K) and a large exciton Bohr radius (18 nm), lead sulfide (PbS) is an important π-π semiconductor material[1, 2]. The sub-micrometer structures of PbS, which display unique physical properties originating from the intrinsic nature of the bulk materials[3, 4], have been promising for optoelectronic devices such as Pb2+ ion-selective sensors[5, 6], near-IR communication and switches[7, 8], flame monitors[9, 10], photonic and optical switching devices[11, 12], etc. It is well known that the intrinsic properties of materials, including the micrometer- and nanometer-sized crystals, rely sensitively on their crystallinity, morphologies, and surfaces[1315]. Therefore, it is essential to design a reasonable synthetic process for the synthesis of micrometer- or nanometer-sized PbS crystals with desired morphology[16, 17].

Over the past few years, researches aiming at the possibility to control the microstructure of the crystals have been developed[1820]. Some special structures, such as wire-, rectangle-, rod-, star-, and cube-like crystals have been demonstrated[21, 22]. Various surfactants were used to change the microenvironment or affect the growth process for solution synthesis[23, 24] and then inorganic nanomaterials with different morphologies were obtained[25, 26]. For the synthesis, the general strategy is to handle specific inducing agent which can selectively combine with specific crystal facets[22, 27]. Thus, the growth rates on different facets can be enhanced or weakened and consequently produce final crystals with different morphologies[28, 29]. Recently, PbS nanocrystals with peculiar anisotropic morphology have aroused the interest, and some anisotropic structures were synthesized through a solution route[21, 30]. This special anisotropic structure may lead to the different physical and chemical characteristics from the bulk or one-dimensional structure. It inspired us to seek suitable reagent for the synthesis of anisotropic PbS microstructures in high yield.

Here, the sub-micrometer-sized PbS anisotropic structures with morphology of fishbone-like dendrites, multipods, cubes, corallines, and hoppers were successfully synthesized by adjusting the reaction temperature or employing the nontoxic reagent to vary the relative growth rate on different crystalline facets of PbS nucleating seeds under the solvothermal conditions. The structure evolution and formation mechanism of PbS anisotropic microstructures have been discussed. The photoluminescence property was also investigated.


In this paper, all the reagents were of analytical grade and were used without further purification. The synthesis of sample was carried out through the solvothermal process. In a typical experiment, 20 mL of 0.05 mol/L lead acetate solution was added into stirred 20 mL of 0.05 mol/L 1-pyrrolidine dithiocarboxylic acid ammonium salt solution in methanol. A thick suspension of white precipitate appeared immediately. Subsequently, the above dispersion was transferred into a 50-mL Teflon-lined stainless steel autoclave, sealed, and maintained at 165°C or 180°C for 12 h, respectively. As to the solvothermal route with surfactant sodium dodecylbenzenesulfonate (SDBS), different masses of SDBS were added into the above mother mixture solution, respectively, and maintained at 180°C for 12 h. Then the autoclaves were cooled to room temperature naturally. The collected products were then washed with distilled water and methanol several times and dried under vacuum at 60°C for 5 h before further characterization. The processes with other compounds cetytrimethylammonium bromide (CTAB), ethylenediamine tetraacetic acid (EDTA), sodium dodecyl sulfate (SDS), cellulose triacetate (CTA), and polyethylene glycol 400 (PEG-400) were similar to that of SDBS.

Powder X-ray diffraction (XRD), transmission electron microscopy (TEM), and scanning electron microscopy (SEM) were applied to characterize the crystallographic phase, size, and morphology evolution of the products. Powder XRD measurement was performed with a MXP18AHF X-ray diffractometer (MAC Science Co. Ltd., Tokyo, Japan) using CuKα radiation (λ = 0.154056 nm). TEM images were collected using HITACHI H-600 transmission electron microscope (Chiyoda, Tokyo, Japan) at the operating voltage of 75 kV. SEM images were conducted at 15 keV with a LEO 1430VP scanning electron microscope (Carl Zeiss AG, Oberkochen, Germany).

Results and discussion

Figure1 shows TEM and SEM images of PbS prepared at 165°C without surfactants. It is shown that the products are mainly fishbone-like dendritic structures. Each dendrite contains a main ‘trunk’ with small lateral ‘branches’ growing perpendicularly to the major trunk (Figure1a). The typical SEM of individual dendrite clearly reveals a view of its three-dimensional dendritic structure with four rows of branches. It can be also seen that the separation angle between the adjacent rows is 90°. Each row is composed of some branches. These branches are parallel to each other orderly and perpendicular to the trunk (Figure1b). The main trunks are similar to these branches in the shape. Each of them has a sharp cusp like a sword. The main trunk has the length of about 1.0 to 3.5 μm and the diameter of 100 nm. The branches are 50 to 500 nm in length and 50 to 80 nm in diameter. In addition, the further hierarchical dendritic structures constructed by fishbone-like dendrites formed in the process (Figure1c). Some incomplete dendrites were also observed in the sample. The growth of their branches aborted, while the trunks have been full-grown (Figure1d).
Figure 1

TEM and SEM images of the fishbone-shaped PbS crystals. Obtained via solvothermal route without surfactants at 165°C for 12 h. (a) Dendrites, (b) three-dimensional dendritic structures, (c) hierarchical dendritic structures, and (d) incomplete dendrites.

When the growth of the materials was carried out at 180°C, dramatic changes occurred to the structures of products. Figure2 shows the SEM and TEM images, which distinctly reveal the sizes and morphologies of the as-obtained products. It is seen that the product prepared at 180°C is composed of a majority of pod-based crystals without the lateral smaller ‘sticks’. It has structures ranging from monopodal to hexapodal shapes. Besides a number of monopods in Figure2a, cross-shaped structures are the main shape which consisted of two to six pods (Figure2b,c,d). Typical SEM images are present in Figure2e. Three-dimensional PbS crystals composed of six cross-shaped pods were vividly displayed. From Figure2f, it can be seen that the separation angle between the two adjacent crossed pods is 90°. It is estimated to be 1 to 3 μm in length and 200 to 500 nm in diameter for each pod. For a certain unit, the diameter of each pod is nearly identical. In addition, a few crucifix-shaped tetrapods can be found in this sample (Figure2d).
Figure 2

TEM and SEM images of the pod-shaped PbS microstructures. Obtained via solvothermal process without surfactant at 180°C for 12 h. (a) Monopods, (b, c, and d) cross-shaped structures, and (e and f) three-dimensional cross-shaped structures.

To explore the influence of the surfactant SDBS to the morphology of PbS microcrystals, the following experiments were carried out: Firstly, we designed several solvothermal processes in the presence of different concentrations of SDBS (its CMC is 1.2 × 10−3 M), respectively, at the reaction temperature of 180°C and holding time for 12 h. TEM and SEM images of the products indicated that the surfactant SDBS can induce new structures (Figure3) [Additional file1: Figure S1]. It is worth noting that all products prepared with different concentrations of SDBS contain the novel cubic structure. It is clearly shown in Figure3d,e that each cube has a perfect cubic frame with six pyramid-shaped hoppers negative toward the center on the {100} facets and eight elongated horns along the <111> directions. In addition, some hoppers exposed visual step-like faces, i.e., a family of {100} facets. The experimental data showed that the reaction with 3.6 × 10−3 M SDBS can produce this structure with high yield. Reactions with 0.8 × 10−3 M or 1.2 × 10−3 M or 7.2 × 10−3 M SDBS created farraginous structures, cubes, truncated cubes, particles, or shuttle-like crystals. Subsequently, the several reactions with 3.6 × 10−3 M SDBS were developed for different duration times to study the evolution of PbS microstructure with time. Figure3a,b,c presented the evolution of the structure from multipods to fat pods to final cubic frames along the duration time, and they indicated that the number of cubes with the hopper increased when the time was prolonged. Further investigation discovered that the shape evolution casts anchor at about 12 h. The exhaustion of as-obtained PbS monomer is responsible for the evolution abortion of some pods.
Figure 3

TEM and SEM images of the samples. Samples synthesized with 3.6 × 10−3 M SDBS at the reaction temperature of 180°C under different duration times of (a) 3 h, (b) 6 h, and (c, d, and e) 12 h. (I to III) Schematic illustration of the evolution process of the PbS hopper cubic structures: from (I) primal octapod (corresponding to the object marked by blue circle in image e) to (II) transitional octapod (corresponding to the object marked by red circle in image e) to (III) final cube (corresponding to the object marked by yellow arrow in image e).

Indeed, the route in this work was a thermal decomposition of uni-precursor {[Pb(C5H8NS2)2]2} through a solvothermal reaction. When the lead acetate (Pb(AC)2) solution was added into 1-pyrrolidine dithiocarboxylic acid ammonium salt (C5H12N2S2) solution, the thick suspension of white precipitate came into being. We separately prepared the precursor with identical solutions and manipulation. The TG-DTA and element analyses of precursor were described in details in the Additional file1.

The formation of PbS sub-micrometer structures involves nucleation and subsequent growth processes of nuclei. The rock salt structure of the PbS seed crystallite formed during the nucleation process is the initial factor responsible for the final shape of the PbS structures. It is generally considered that these PbS seeds are tetradecahedrons (truncated cube), exposing six {100} facets and eight {111} facets. According to the literature, the final shape of a PbS nanocrystal was mainly determined by the ratio of the growth rate in the <100> direction to that in the <111> direction. From the viewpoint of crystallography, the {111} facets of a rock salt structure intrinsically have a higher surface energy than that of the {100} facets, and the growth kinetic energy barrier of the crystal facet is inversely proportional to the surface energy. This suggests that the growth rate along the <111> direction is higher than that of the <100> direction. However, the growth environment can influence the formation of anisotropic structures, dendrites, multipods, and cube with hoppers. Lifshitz mentioned that the main environmental parameters are as follows: (a) the stabilizing surfactants which can enhance or block the growth of specific facets, (b) the reaction temperature and reaction duration which determined the choice of thermodynamic or kinetic growth, and (c) a large concentration of the precursors to enable a fast kinetic growth and Ostwald ripening effect[21]. In a word, the final structure of a NaCl-type PbS crystal can be controlled by modulation of the ratio (R) between the growth rates in the <100> and <111> directions. As illustrated by Wang[31], the R for the formation of octahedra is 1.73, and that for the perfect cubes shape is 0.58.

In this work, when the reaction temperature was 165°C and 180°C, the growth rates were fast. This led to a preferential kinetic growth of branches. The difference between the enhanced growth rates on the {100} and {111} planes induced the ratio R to have a value of more than 1.73, which resulted in the formation of the dendrites as shown in Figure1a,c. As to the disappearance of the lateral smaller sticks at 180°C, the higher temperature may be an important factor. The relatively higher growth rate in <100> direction than that in <111> direction leads to the formation of the pods. Further exploration to this behavior is progressing in our laboratory.

In some corresponding reports, the synthesis of special PbS nanostructures was usually achieved with the stabilizing surfactants. These surfactants are mostly amine compounds, such as ethylene diamine (en). Ma et al. proposed that the amine molecules stabilize the {100} surfaces and, thus, enhance the natural habit of the rock salt structure to react faster along the <111> direction[30]. In our work, we found that the surfactant SDBS can also play the same role. When it was added to the reaction system, SDBS can rapidly increase the growth kinetic coefficient between the pods. However, the {100} surfaces of the original tetradecahedron were still blocked by the surfactant SDBS molecules, and the rate R was reduced to 0.58. The evolution of microstructures from octapod to final cube was schematically illustrated in Figure3. The primal octapod (I) had a central cube with eight centrosymmetric pods pullulating along the apex. It was clearly shown in the SEM photograph (marked with the blue continuous circle in Figure3e). These octapods gradually grew into intermediate shape (II) and ripened to final cubes when the reaction proceeded. Some transitional shapes evolved between the octapods, and the ripe cubes were mostly generated in the products obtained at 3 and 6 h (Figure3a,b). They were also confirmed by the SEM micrograph (marked with the red dot circle in Figure3e). These structures formed by growing the space between the pods without further growth of the central cube, and their pods kept on stretching to the eight apexes of the central cube. Thus, it was doubtless that the pods gradually gathered flesh and pullulated to become developmental fat octapods. The distance from the neighboring pods is about 2 μm (Figure3). The continuative growth of the aforementioned mode resulted in the formation of final sculpturesque cubes (III) by filling the space between the arms without further growth of the {100} facets of the central cube. These cubes are about 2.5 × 2.5 μm in size.

The crystallinity of the as-prepared dendrites, multipods, and hopper cubes are clearly illustrated by their distinct XRD patterns shown in Figure4. All the peaks can be indexed as face-centered cubic structure with the Fm3m space group (JCPDS no. 05–592). The high intensity of the diffraction patterns suggests that the samples have been well crystallized. The XRD pattern of cubic crystal gives an average lattice parameter of 0.5927 nm (calculated from (200) and (111) peaks in Figure4c), which is in good agreement with the JCPDS no. 05–592 database (a = 0.5936 nm).
Figure 4

X-ray powder diffraction patterns of microstructures. (a) Fishbone-shaped, (b) pod-shaped, and (c) hopper cubic microstructures.

In addition, the present works indicated that the compounds of CTAB, EDTA, SDS, CTA, and PEG-400 can also modulate the relative growth rate on the different surfaces of NaCl-type PbS crystals. Some novel anisotropic microstructures have been created through the solvothermal processes with their assistant. When CTAB was added into the system, dendritic PbS microcrystals were obtained (Figure5a). The cross-shaped PbS with plump pods responded to surfactant SDS (Figure5b). The present work showed that the EDTA can decrease the R between the growth rates in the <100> and <111> directions. The full cubic structure would come into being with them (Figure5c). As to CTA, it can diminish the size of the products. The nanocubes or nanobars synthesized with CTA are about 70 to 150 nm in width (Figure5d). The vivid coralloid structures were fabricated with the nonionic surfactant PEG-400 (Figure5e). Figure5f clearly revealed that the buds of the coralline were the PbS nanocubes or nanobars grafted on the PbS stakes. Furthermore, under the same experimental condition (the reaction temperature, duration time, and solvents are equal to the aforementioned process without surfactants), the molar ratio of Pb2+/S2− source (1:1) were replaced by 2:1 and 3:1. The results showed that the molar ratio of Pb2+/S2− weakly affects the final morphologies of PbS crystals in the present case.
Figure 5

TEM and SEM images of the PbS microstructures. Obtained with different surfactants via solvothermal processes at 180°C for 12 h, respectively. (a) CTAB, (b) SDS, (c) EDTA, (d) CTA, and (e and f) PEG-400.

Figure6 shows the room-temperature photoluminescence (PL) spectra of the PbS microstructures obtained by different processes. It is harvested that these PL spectra show a clear shape- and size-dependent features. With the excitation wavelength of 485 nm, the emission maximums of the PL spectra of T165, T180, and T180SDBS are around 692, 716, and 721 nm with a near equal narrow FWFM of approximately 20 nm, while the intensities of T180 and T180SDBS are stronger than T165. A great deal of investments suggested that the PL performances of nanoparticles are generally impacted by the shape, dimensions, size, size distribution, or density of defects. In the present work, the sharp optical spectra in three PL imply the narrow size distribution and blueshift compared to the bulk counterpart (NIR region) suggesting the strong degree of confinement. The samples T180 and T180SDBS should hold better crystallinity than T165 and possess lower density of defects. The opportunities of nonradiative recombination of photoinduced electron–hole pairs will be depressed, so the intensities of their PL spectra are higher than T165. It is considered that the differences of emission peaks are mainly attributed to the variation of shape, size, and the trap state of as-obtained PbS. The lower wavelengths of T165 and T180 implied the stronger confinement than T180SDBS, which can be understood from the fact that T165 and T180 are composed of one-dimensional units with smaller sizes simultaneously, while the T180SDBS has no one-dimensional structures.
Figure 6

Photoluminescence spectrum of PbS microstructures obtained with different processes. (a) Without surfactant at 165°C for 12 h (T165), (b) without surfactant at 180°C for 12 h (T180), and (c) with 3.6 × 10−3 M SDBS at 180°C for 12 h (T180SDBS).


In conclusion, the solvothermal route has been successfully developed to prepare sub-micrometer PbS anisotropic structures with different morphology. The solvothermal synthesis of PbS anisotropic structures including fishbone-like dendrites, multipods, cubes, corallines, and hoppers has been facilely applied by adjusting the reaction temperature or using the different nontoxic reagents. The results indicated that the modulation of reaction condition with different surfactants, which can adjust the ratio between the growth rates in the <100> and <111> directions, is the key for the fabrication of the NaCl-type PbS microstructures.



This work was financially supported by the Scientific Research Projects for University of Xinjiang Education Department (no. XJEDU2012I03), the Doctoral Start Foundation of Xinjiang University (no. BS100129), the National Natural Science Foundation of China (nos. 21101132, 21061013, and 21271151), Xinjiang Autonomous Region with Science and Technology Project Plan (no. 200991101), and Autonomous Regions High Technology Research and Development Program (no. 201016118).

Authors’ Affiliations

Key Laboratory of Advanced Functional Materials of Autonomous Region, Institute of Applied Chemistry, Xinjiang University
Key Laboratory of Clean Energy Material and Technology of Ministry of Education, Institute of Applied Chemistry, Xinjiang University
Laboratory for Microstructures, Shanghai University


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© Cao et al.; licensee Springer. 2012

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