# Room Temperature Ferromagnetic and Optical Properties of Chrome Doped ZnS Nanorods Prepared by Hydrothermal Method

Authors: Wenhua Zhao; Zhiqiang Wei; Li Zhang; Xiaojuan Wu; Xuan Wang; Jinlong Jiang
Journal: Journal of Nanomaterials
 (2017)

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## Abstract

Cr dopedZn1-xCrxS nanorods with different concentration ratio (x=0, 0.01, 0.03, and 0.05) were successfully synthesized by hydrothermal method. The crystal microstructure, morphology, chemical composition, and optical and magnetic properties of the samples were characterized by X-ray diffraction (XRD), field-emission scanning electron microscopy (FESEM), high-resolution transmission electron microscopy (HRTEM), X-ray energy dispersive spectrometry (XEDS), diffuse-reflectance spectroscopy (DRS), photoluminescence (PL) spectra, and the vibrating sample magnetometer (VSM). All the samples synthesized by this method exhibited single-phase wurtzite structure with good crystallization as demonstrated by XRD studies, which indicated that all Cr ions successfully substituted for the lattice site of Zn2+ and generated single-phase Zn1-xCrxS. DRS revealed the band gap of doped Zn1-xCrxS underwent blue shift compared to that of the bulk ZnS. PL spectra showed obvious ultraviolet emission peak at 375 nm and two blue emissions appear about 500 and 580 nm. The blue emissions intensity of doped samples improved with the increase of Cr concentration, comparing to pure ZnS. Magnetic measurements indicated that the undoped and doped ZnS nanorods exhibited well-defined ferromagnetic behavior at room temperature. The saturation magnetization weakened significantly with increasing Cr concentration comparing to pure ZnS and reached minimum for 3% Cr.


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## Body

## 1. Introduction

Diluted magnetic semiconductors (DMS) are referred to as nonmagnetic semiconductors in which a small fraction of host cations are replaced by transition metal or rare-earth ions, with both spin and charge degrees of freedom in a single material [1]. DMS has attracted enormous interest due to the exchange interactions between the spins of the dopant atoms and the carriers in the semiconductor host, as they are expected to bring global ferromagnetic order in the entire lattice at room temperature. ZnS is a kind of the II–VI semiconductor materials with direct wide band gap energy (3.7 eV), and it is a versatile and multifunctional semiconductor material, which has good piezoelectric, ferromagnetic, photoelectric, and photosensitive properties [2, 3]. The investigations for ZnS diluted magnetic semiconductor (DMS) nanocrystals have attracted considerable attention due to their novel properties and broad application prospect in diverse areas, such as spin-polarized light emitting diode, spin field-effect transistors, field-emission devices, optical isolator, and quantum computer [4–8].In recent years, single transition metal doped ZnS have been extensively investigated by various methods, and the electrical, magnetic, and optical properties of ZnS can be modified by controlling the preparation process, changing the kinds of doping elements and doping amount. Transition metals (TMs) (e.g., Nd [9], Mn [10], Co [11], Cu [12], Fe [13], and Ni [14–16]) doped ZnS based diluted magnetic semiconductors (DMS) are potential candidate for luminescent properties and room temperature ferromagnetism. Many experimental results have observed the room temperature ferromagnetism (RTFM) and extraordinary photoluminescence (PL) primarily depending on the synthesis method as well as processing conditions [17–19]. But, to the best of our knowledge, there are no reports on the effect of the structural, optical, and magnetic properties for Cr doped ZnS nanorods.Hence, the understanding of FM origination in Cr doped ZnS nanorods is still in urgent demand.In the present work, undoped and Cr doped ZnS nanorods were synthesized by hydrothermal method using ethylenediamine as modifier. The samples were characterized by X-ray diffraction (XRD), field-emission scanning electron microscopy (FESEM), high-resolution transmission electron microscopy (HRTEM), X-ray energy dispersive spectrometry (XEDS), diffuse-reflectance spectroscopy (DRS), photoluminescence (PL) spectra, and the vibrating sample magnetometer (VSM) to investigate the crystal microstructure, morphology, constituent elements, and optical and magnetic properties.


## 2. Materials and Methods

Z
n
1
-
x
C
r
xS nanorods (x=0, 0.01, 0.03, and 0.05) were successfully synthesized by hydrothermal method. All raw materials used in this work were of analytical grade and without further purification. In the synthesis process, a required amount of ethylenediamine (C2H8N2) was dissolved in deionized water. Meanwhile, weighed zinc acetate (Zn(CH3COO)2·2H2O) and chrome chloride (CrCl3·6H2O) according to the chemical formula and the mole ratio of the metal cation of undoped ZnS and Cr doped ZnS mixed together and dissolved into the mixed solvent to obtain a solution of 0.015 mol/L. Then a certain amount of thiourea (NH2)2CS was added to the above solution, and the mixture was magnetically stirred at room temperature for 30 min. Finally, the prepared solution was transferred into a 100 ml Teflon lined stainless steel autoclave, and the hydrothermal synthesis was heated at 200°C for 12 h in an oven and then cooled to room temperature naturally. Thereafter, the resulting precipitate was separated centrifugally and washed with distilled water and absolute alcohol several times, respectively. The obtained products were dried in oven at 60°C for 10 h. Thus, Zn1-xCrxS nanocrystals were collected and used for further studies.The structural analysis of as-synthesized samples was examined by a powder X-ray diffractometer (Japan Rigaku D/Max-2400) with CuKa radiation at λ=1.54056 Å. The samples were scanned in the angular range from 10 to 90° (2θ) with scanning rate 0.005°/s and step size 0.02°. The average crystalline grain size of the products was estimated from the half maximum width and the peak position of an XRD line broadened according the Scherrer formula. The morphology and microstructure of the samples were observed by field-emission scanning electron microscope (FESEM, 200 FEG) and high-resolution transmission electron microscopy (HRTEM, JEM-2010). The chemical composition of the products was verified by X-ray energy dispersive spectroscopy (XEDS) at an acceleration voltage of 200 keV in TEM. The optical properties of the samples were analyzed using ultraviolet-visible (UV-VIS, TU-1901) spectrophotometer. Photoluminescence (PL) spectra were recorded on a PerkinElmer fluorescence spectrometer with the excitation wavelength of 320 nm. Magnetic hysteresis loops were investigated at room temperature using a vibrating sample magnetometer (VSM, Lakeshore 7304) with an applied field from −8000 Oe to 8000 Oe.


## 3. Results and Discussion

### 3.1. Structural Analysis

The XRD patterns of different doping concentration ratioZn1-xCrxS (x=0.01, 0.03, and 0.05) nanorods compared with pure ZnS are shown in Figure 1. It is obvious that the diffraction peaks located at 2θ = 26.91°, 28.50°, 30.53°, 39.61°, 47.56°, 51.78°, and 56.39° correspond to (100), (002), (101), (102), (110), (103), and (112) planes, respectively. All the diffraction peaks can be well indexed with the single-phase hexagonal wurtzite ZnS structure, which are readily matched with the standard spectrum (JCPDS 36-1450). In addition, no extra diffraction peaks assigned to other secondary phases such as metal clusters or metal oxides are detected from the XRD patterns, which confirms that the samples are pure single phase. Thus, it indicates that Cr3+ is effectively substituted into Zn2+ ions sites within the ZnS crystal lattice without changing the wurtzite structure of the parent ZnS.Figure 1
XRD patterns ofZn1-xCrxS (x=0, 0.01, 0.03, and 0.05) nanorods.Based on the XRD results, the average crystalline size of pure ZnS and doped ZnS nanorods can be calculated from the full width at half maximum (FWHM) of the most intense diffraction peak (002) according to Scherrer formula as follows:D=Kλ/Bcos⁡θ, where D represents the average crystalline size, K=0.89 is the Scherrer constant, λ is X-ray wavelength (Cu Ka, 1.54056 Å), θ is the diffraction angle, and B is FWHM of (002) diffraction peak in radians. The (002) diffraction peak FWHM of pure ZnS is greater than that of doped ZnS samples, which is indicating the incorporation of dopant ions as substituents in the lattice of the host material. It is evident that the increase slightly of FWHM with increasing Cr dopant concentration is in turn increase of the crystallite size. Comparing the doped samples and pure ZnS, the results suggest that the doping concentration influences the crystallites size.The corresponding parameters of the main diffraction peak (002) for undoped ZnS and Cr doped ZnS samples are listed in Table1. The (002) diffraction peak position for Zn1-xCrxS samples evidently shifts to higher angle, comparing to pure ZnS. In addition, the peak positions of synthesized Zn1-xCrxS nanorods shift to higher angles with the concentration of Cr doping increasing. When there is a small amount of Cr doping (x=0.03), the diffraction peak position of the doped ZnS nanorods reaches maximum. Shift of peak position towards higher angle is explained from lattice constant shrinkage, which is attributed to the substitution of the Zn2+ ions by the smaller Cr3+ ions. According to the Bragg formula: 2dhklsin⁡θ=λ, where dhkl denotes the crystalline plane distance for indices (hkl) and θ is the diffraction angle of the (002) peak. Plainly, the decrease of the crystalline plane distances will result in the increase of the diffraction angles. From Table 1, it can be found that d values of pure ZnS are greater than that of doped ZnS samples, while d value of doped samples decrease with the increase of Cr doped content. The lattice constants a and c are calculated by the following formula: a=dhkl4/3h2+hk+l2+(a/c)2l2, the lattice constant a is obtained for the (100) plane through the relation a=λ/3sin⁡θ, and the lattice constant c is derived for the (002) plane using the relation c=λ/sin⁡θ, respectively. The calculation results are given in Table 1. The lattice constants of the doped ZnS are smaller than that of pure ZnS, and the lattice constants a and c and their interplanar distance of doped ZnS decrease with the increase of Cr doped content, reaching minimum for 3% Cr. It can be attributed that the ionic radius of the Cr3+ (0.69 Å) is smaller than that of the Zn2+ (0.74 Å), which revealed that Cr ions occupy Zn ions sites in the wurtzite structure, causing lattice distortion [20].Table 1
Parameters of the XRD patterns for Zn1-xCrxS (x=0, 0.01, 0.03, and 0.05) nanorods.
Sample
2θ (°)
FWHM (°)
d
h
k
l (Å)
a (Å)
c (Å)
Cell volume (Å3)
D (nm)
Pure ZnS
28.500
0.269
3.129
3.829
6.258
79.45
30
Zn0.99Cr0.01S
28.520
0.213
3.127
3.828
6.254
79.36
34
Zn0.97Cr0.03S
28.618
0.245
3.117
3.799
6.233
77.90
36
Zn0.95Cr0.05S
28.539
0.258
3.125
3.824
6.250
79.15
39The volume of unit cell of hexagonal system is evaluated from equation:V=3a2c/2=0.866a2c. As the doping concentration is increasing, the volume of the unit cell of the doped nanorods dramatically decreases comparing to pure ZnS. When there is a small amount of Cr doping (x=0.03), the volume of the unit cell of the doped nanorods reaches maximum, which is shown in Table 1. It indicates that the changes in peak position, peak width, and peak intensity depend on the lattice parameter and cell volume, which is mainly attributed to the successful incorporation of Cr3+ ions into ZnS lattice.


### 3.2. Morphological Studies

The morphology of pure ZnS and doped ZnS samples is studied by FESEM and HRTEM. Figure2 shows the FESEM images of the undoped ZnS and Zn0.95Cr0.05S samples, respectively. Figure 2(a) shows FESEM images of undoped ZnS sample, and it is observed that pure ZnS nanorods possess one-dimensional rod-like shape. The diameter of the samples ranges from 30 to 40 nm, with an average diameter approximately 30 nm and the length about 200–300 nm. The micrograph clearly indicates the presence of weak aggregation between the rods. Figure 2(b) shows the FESEM micrograph of Zn0.95Cr0.05S sample, which shows the presence of large roughly one-dimensional rod-like structure with regular length distribution. Cr doped ZnS system does not change the morphology of the samples, but the diameter slightly increases and the length decreases with the increase of Cr concentration. From the above observations, it can be noticed that the doping concentration of Cr affects the parent ZnS, and the nanorods are in the nanoscale region. Comparing with pure ZnS samples, the morphology of doped samples becomes shorter and wider, and the rod length diameter ratio becomes lower.Figure 2
FESEM images of (a) pure ZnS and (b) Zn0.95Cr0.05S nanorods.Figure3 displays the HRTEM micrographs of Zn0.95Cr0.05S sample. From this figure, it can be found that Zn0.95Cr0.05S nanorods are the same as the FESEM images, possessing roughly one-dimensional rod-like structure and well dispersed with clear edge and smooth surface. The average diameter of the nanorods is about 30 nm, and the length ranges from 200 to 300 nm. Figure 3(b) displays the typical HRTEM image of Zn0.95Cr0.05S nanorods, and it reveals the clear lattice fringe, with no obvious defects. The interplanar distance is about 0.312 nm, which is in good agreement with the d-spacing of (002) plane of hexagonal wurtzite ZnS structure. The value of lattice spacing is smaller than that of bulk ZnS, and the crystal lattice has tendency to shrink, which can be attributed to the difference of ion radius of Zn2+ (0.74 Å) comparing with that of Cr3+ (0.69 Å). Therefore, it is evident that Cr doping influences the morphology of the samples. The HRTEM analysis is in good agreement with the FESEM and XRD results, which further indicates that all Cr3+ successfully substituted for the lattice site of Zn2+ and generated single-phase Zn1-xCrxS [21].Figure 3
HRTEM micrographs and SAED patterns of Zn0.95Cr0.05S.The corresponding selected area electron diffraction (SAED) patterns of Zn0.95Cr0.05S sample are shown in Figure 3(c), and the SAED pattern consists of many regular diffraction rings with different radius and one center. These rings correspond to (100), (002), (101), (102), (110), (103), and (112) planes of Zn0.95Cr0.05S nanorods from inner to exterior, respectively. The SAED pattern also confirms that Zn0.95Cr0.05S nanorods are wurtzite structure, belonging to polycrystalline structure, which is in agreement with the result of XRD. It indicates that the Cr3+ ions do not degrade the crystallinity of ZnS nanorods.


### 3.3. Chemical Characterization

In order to confirm the existence of the Cr elements of the doped samples, XEDS analysis is recorded. Figure4 shows the XEDS patterns of the undoped ZnS and Zn0.92Cr0.05S nanorods. From Figure 4(a), it can be found that the undoped ZnS nanorods mainly contain S and Zn two elements. Figure 4(b) obviously confirms the presence of Cr elements besides S and Zn elements for Zn0.95Cr0.05S nanorods, whereas the spectrum of pure ZnS did not find the presence of Cr elements. The quantitative atomic and weight percentage of the compositional elements are indicated in the inset of Figure 4. The calculated weight and atomic percentage are nearly equal to their nominal stoichiometry within the experimental error. The XEDS results further verify XRD conclusion, which indicates that Cr doped ZnS diluted magnetic semiconductors are successfully synthesized by hydrothermal method, and Cr3+ are successfully substituted as dopant in ZnS matrix.Figure 4
XEDS patterns of pure ZnS (a) and Zn0.95Cr0.05S (b).
(a)
(b)


### 3.4. Optical Properties

The diffuse-reflectance spectra are employed to investigate the effect of Cr doping on the optical characteristics ofZn1-xCrxS nanorods. The DRS of the pure ZnS and doped ZnS nanorods are depicted in Figure 5(a). The characteristic absorption edges band at ultraviolet (UV) region lies in the range of 330–390 nm, which shows that all samples possess wide absorption. The absorption coefficients are different, and there is an effect on the position of the absorption peaks. For analysis purposes the diffuse-reflectance (R) of the sample can be related to the Kubelka-Munk function F(R) by the relation F(R)=1-R2/2R. The band gap of the Zn1-xCrxS nanorods is estimated from the diffuse-reflectance spectra by plotting the square of the Kubelka-Munk function FR2 versus energy and extrapolating the linear part of the curve to FR2=0, which is shown in Figure 5(b). The absorption edges for Zn1-xCrxS samples are seen to be evidently shifted towards lower wavelengths comparing with pure ZnS and are shown in Figure 5(b). The measured values of optical band gap energy for pure ZnS are showed in Table 2, and Zn0.99Cr0.01S, Zn0.97Cr0.03S, and Zn0.95Cr0.05S are 3.729 eV, 3.737 eV, 3.743 eV, and 3.732 eV, respectively, which indicates that the Cr ions replace the Zn ions in the ZnS lattice, and the band gap of Cr doped ZnS samples is greater than that of pure ZnS. The band gap energy gradually increases with the increase of Cr concentration, up to a maximum 3.743 eV for 3% Cr. Furthermore, the band gap values estimated for these samples are in the range of 3.729–3.743 eV that are slightly greater than that of bulk ZnS (3.7 eV), which is manifested in the fact that the band gap energy undergoes blue shift in the doped ZnS system. The increase in the band gap energy with the decrease in the lattice parameters (a, c, and V) is due to the effect of doping, which are strongly supported by XRD results and associated with the variation of the lattice parameters. It can be explained that the increase of optical band gap may be attributed to the sp-d spin-exchange interactions between the band electrons of host matrix and the localized d electrons of the transition metal ion substituting the captions. Thus, the s-d and p-d exchange interactions between the band electrons of ZnS and localized d electrons of Cr give rise to change in the energy band structure, which can increase the band gap.Table 2
Band gap and magnetic moments of Zn1-xCrxS (x=0, 0.01, 0.03, and 0.05) nanorods.
Sample
Band gap (eV)
Magnetic moments (emu/g)
Saturation magnetization
Remanent magnetization (10−4)
Coercivity (Oe)
Pure ZnS
3.729
0.0117
6.415
46.71
Zn0.99Cr0.01S
3.737
0.0111
5.122
40.26
Zn0.97Cr0.03S
3.743
0.0097
5.339
41.22
Zn0.95Cr0.05S
3.732
0.0105
5.376
42.74Figure 5
UV-Vis diffuse-reflectance spectra (a) and (F(R)hν)2 versus hν curves (b) of Zn1-xCrxS (x=0, 0.01, 0.03, and 0.05) nanorods.
(a)
(b)PL spectra of pure ZnS and Cr doped ZnS nanorods are shown in Figure6. It is observed that PL intensity of doped samples is higher than pure ZnS sample. The ZnS samples exhibit three obvious broad emission peaks at 375 nm, 500 nm, and 580 nm, respectively. The obvious UV emission can be attributed to originate from excitonic recombination corresponding to the near-band-edge emission (NBE) of wide band gap of ZnS due to the quantum confinement effect [22]. The blue-green emission bands centered at 500 nm for samples may be attributed to S vacancies in ZnS nanorods and Zn vacancy related defects [23, 24]. The green emission peak at 580 nm is possibly assigned to positively charged electron transition and surface traps mediated by defects in the band gap [25]. The origin of this peak is still not clear and needs further study.Figure 6
PL spectra ofZn1-xCrxS (x=0, 0.01, 0.03, and 0.05) nanorods.The doped samples exhibit similar ultraviolet (UV) emission band at 375 nm to compare with pure ZnS, which illustrates that the doped samples display nearly the same structure of pure ZnS. As the doping concentration increases, the intensity of PL emission of the doped nanorods dramatically increases comparing to pure ZnS. When there is a small amount of Cr doping (x=0.03), the intensity of the peak of the PL spectrum reaches maximum. It is observed that the particle sizes of the doped samples increase with the increasing of Cr concentration from Table 1, which corresponds with XRD data. The increase in particle size results in enhanced surface defects leading to an increase in the PL intensity as chrome content is increased. It is because Cr3+ acts as a sensitizing agent and enhances the radiative recombination processes. Thus, the PL intensity of doped Zn1-xCrxS nanorods is higher than that of pure ZnS [26]. These results are in good agreement with XRD, EDX, and UV-visible studies.


### 3.5. Magnetic Studies

Figure7 presents the RT magnetic hysteresis (M-H) loops of the undoped ZnS and Zn1-xCrxS (x=0.01, 0.03, and 0.05) nanorods measured with the applied magnetic field of 8 kOe. It has deducted the contributions from the diamagnetism of the Si substrate and the paramagnetism of the sample holder during VSM measurement. The M-H curves show that all the samples exhibit obvious ferromagnetic behaviors. The ferromagnetism of undoped ZnS sample is attributed to the fact that sulfur vacancies boost both the emission and the magnetism, which is revealed d0 ferromagnetism [27], and the stronger exchange interactions between these sulfur vacancies weakened the saturation magnetization (Ms). From XRD results of doped ZnS nanorods, it is suggested that there are no traces of impurity or secondary phases, thus removing the possibility of ferromagnetism due to the clusters of transition elements or secondary phases in the samples. Hence, the room temperature ferromagnetism of Cr doped ZnS samples could arise from intrinsic magnetic property.Figure 7
M
-
H curves of Zn1-xCrxS (x=0, 0.01, 0.03, and 0.05) nanorods.TheM-H curves indicate the saturation magnetization values of 0.0117 emu/g, 0.0111 emu/g, 0.0097 emu/g, and 0.0105 emu/g for pure ZnS, Zn0.99Cr0.01S, Zn0.97Cr0.03S, and Zn0.95Cr0.05S nanorods, respectively. In view of the Cr3+ ions substituted into ZnS lattice, the origin of magnetism in the samples is due to the exchange interaction between local spin-polarized electrons (such as the electrons of Cr3+ ions) and the conductive electrons. Such interaction can lead to the spin polarization of conductive electrons. Consequently, the spin-polarized conductive electrons undergo an exchange interaction with local spin-polarized electrons of other Cr3+ ions. Thus, after a successive long-range exchange interaction, almost all Cr3+ ions exhibit the same spin direction, resulting in the ferromagnetism of the material. Poornaprakash et al. also report [28] the magnetic property in Cr doped ZnS nanoparticles by hydrothermal method. Therefore, there is an increase in the intensity of the peak with increase in dopant content in that report.The saturation magnetization of doped samples is smaller than that of pure ZnS, and the values of saturation magnetization decrease with the increase of Cr doping concentration. It is interesting that the ferromagnetism is suppressed with the Cr concentration increasing. In addition, the saturation magnetization ofZn1-xCrxS samples decreases with the increase of Cr concentration comparing to pure ZnS and reaches minimum for 3% Cr. It is because the Cr3+ ions substitute the Zn ions, with the local hole concentration at the anion increasing. As the Cr concentration increases, the distance between the Cr atoms and each other is closer and the super exchange interaction between the neighboring Cr atoms is antiferromagnetic in nature. When there is an increase of Cr doping concentration, the enhanced antiferromagnetic interaction is attributed to the decreased volume and the ferromagnetic ordering is suppressed [29].The variation of coercivity (Hc) and remanent magnetization (Mr) with Cr concentration ofZn1-xCrxS nanorods are indicated in the inset of Figure 7. It is observed that the values of Ms, Hc, and Mr of Cr doped ZnS samples are lower than that of pure ZnS, respectively. In order to investigate the magnetic properties in Zn1-xCrxS nanorods clearly, the magnetic moments values are shown in Table 2. Furthermore, the Hc and Mr gradually increase in doped samples with the increase of Cr concentration. When Hc is smaller, the synthesized ZnS nanorods show soft magnetic properties.


## 3.1. Structural Analysis

The XRD patterns of different doping concentration ratioZn1-xCrxS (x=0.01, 0.03, and 0.05) nanorods compared with pure ZnS are shown in Figure 1. It is obvious that the diffraction peaks located at 2θ = 26.91°, 28.50°, 30.53°, 39.61°, 47.56°, 51.78°, and 56.39° correspond to (100), (002), (101), (102), (110), (103), and (112) planes, respectively. All the diffraction peaks can be well indexed with the single-phase hexagonal wurtzite ZnS structure, which are readily matched with the standard spectrum (JCPDS 36-1450). In addition, no extra diffraction peaks assigned to other secondary phases such as metal clusters or metal oxides are detected from the XRD patterns, which confirms that the samples are pure single phase. Thus, it indicates that Cr3+ is effectively substituted into Zn2+ ions sites within the ZnS crystal lattice without changing the wurtzite structure of the parent ZnS.Figure 1
XRD patterns ofZn1-xCrxS (x=0, 0.01, 0.03, and 0.05) nanorods.Based on the XRD results, the average crystalline size of pure ZnS and doped ZnS nanorods can be calculated from the full width at half maximum (FWHM) of the most intense diffraction peak (002) according to Scherrer formula as follows:D=Kλ/Bcos⁡θ, where D represents the average crystalline size, K=0.89 is the Scherrer constant, λ is X-ray wavelength (Cu Ka, 1.54056 Å), θ is the diffraction angle, and B is FWHM of (002) diffraction peak in radians. The (002) diffraction peak FWHM of pure ZnS is greater than that of doped ZnS samples, which is indicating the incorporation of dopant ions as substituents in the lattice of the host material. It is evident that the increase slightly of FWHM with increasing Cr dopant concentration is in turn increase of the crystallite size. Comparing the doped samples and pure ZnS, the results suggest that the doping concentration influences the crystallites size.The corresponding parameters of the main diffraction peak (002) for undoped ZnS and Cr doped ZnS samples are listed in Table1. The (002) diffraction peak position for Zn1-xCrxS samples evidently shifts to higher angle, comparing to pure ZnS. In addition, the peak positions of synthesized Zn1-xCrxS nanorods shift to higher angles with the concentration of Cr doping increasing. When there is a small amount of Cr doping (x=0.03), the diffraction peak position of the doped ZnS nanorods reaches maximum. Shift of peak position towards higher angle is explained from lattice constant shrinkage, which is attributed to the substitution of the Zn2+ ions by the smaller Cr3+ ions. According to the Bragg formula: 2dhklsin⁡θ=λ, where dhkl denotes the crystalline plane distance for indices (hkl) and θ is the diffraction angle of the (002) peak. Plainly, the decrease of the crystalline plane distances will result in the increase of the diffraction angles. From Table 1, it can be found that d values of pure ZnS are greater than that of doped ZnS samples, while d value of doped samples decrease with the increase of Cr doped content. The lattice constants a and c are calculated by the following formula: a=dhkl4/3h2+hk+l2+(a/c)2l2, the lattice constant a is obtained for the (100) plane through the relation a=λ/3sin⁡θ, and the lattice constant c is derived for the (002) plane using the relation c=λ/sin⁡θ, respectively. The calculation results are given in Table 1. The lattice constants of the doped ZnS are smaller than that of pure ZnS, and the lattice constants a and c and their interplanar distance of doped ZnS decrease with the increase of Cr doped content, reaching minimum for 3% Cr. It can be attributed that the ionic radius of the Cr3+ (0.69 Å) is smaller than that of the Zn2+ (0.74 Å), which revealed that Cr ions occupy Zn ions sites in the wurtzite structure, causing lattice distortion [20].Table 1
Parameters of the XRD patterns for Zn1-xCrxS (x=0, 0.01, 0.03, and 0.05) nanorods.
Sample
2θ (°)
FWHM (°)
d
h
k
l (Å)
a (Å)
c (Å)
Cell volume (Å3)
D (nm)
Pure ZnS
28.500
0.269
3.129
3.829
6.258
79.45
30
Zn0.99Cr0.01S
28.520
0.213
3.127
3.828
6.254
79.36
34
Zn0.97Cr0.03S
28.618
0.245
3.117
3.799
6.233
77.90
36
Zn0.95Cr0.05S
28.539
0.258
3.125
3.824
6.250
79.15
39The volume of unit cell of hexagonal system is evaluated from equation:V=3a2c/2=0.866a2c. As the doping concentration is increasing, the volume of the unit cell of the doped nanorods dramatically decreases comparing to pure ZnS. When there is a small amount of Cr doping (x=0.03), the volume of the unit cell of the doped nanorods reaches maximum, which is shown in Table 1. It indicates that the changes in peak position, peak width, and peak intensity depend on the lattice parameter and cell volume, which is mainly attributed to the successful incorporation of Cr3+ ions into ZnS lattice.


## 3.2. Morphological Studies

The morphology of pure ZnS and doped ZnS samples is studied by FESEM and HRTEM. Figure2 shows the FESEM images of the undoped ZnS and Zn0.95Cr0.05S samples, respectively. Figure 2(a) shows FESEM images of undoped ZnS sample, and it is observed that pure ZnS nanorods possess one-dimensional rod-like shape. The diameter of the samples ranges from 30 to 40 nm, with an average diameter approximately 30 nm and the length about 200–300 nm. The micrograph clearly indicates the presence of weak aggregation between the rods. Figure 2(b) shows the FESEM micrograph of Zn0.95Cr0.05S sample, which shows the presence of large roughly one-dimensional rod-like structure with regular length distribution. Cr doped ZnS system does not change the morphology of the samples, but the diameter slightly increases and the length decreases with the increase of Cr concentration. From the above observations, it can be noticed that the doping concentration of Cr affects the parent ZnS, and the nanorods are in the nanoscale region. Comparing with pure ZnS samples, the morphology of doped samples becomes shorter and wider, and the rod length diameter ratio becomes lower.Figure 2
FESEM images of (a) pure ZnS and (b) Zn0.95Cr0.05S nanorods.Figure3 displays the HRTEM micrographs of Zn0.95Cr0.05S sample. From this figure, it can be found that Zn0.95Cr0.05S nanorods are the same as the FESEM images, possessing roughly one-dimensional rod-like structure and well dispersed with clear edge and smooth surface. The average diameter of the nanorods is about 30 nm, and the length ranges from 200 to 300 nm. Figure 3(b) displays the typical HRTEM image of Zn0.95Cr0.05S nanorods, and it reveals the clear lattice fringe, with no obvious defects. The interplanar distance is about 0.312 nm, which is in good agreement with the d-spacing of (002) plane of hexagonal wurtzite ZnS structure. The value of lattice spacing is smaller than that of bulk ZnS, and the crystal lattice has tendency to shrink, which can be attributed to the difference of ion radius of Zn2+ (0.74 Å) comparing with that of Cr3+ (0.69 Å). Therefore, it is evident that Cr doping influences the morphology of the samples. The HRTEM analysis is in good agreement with the FESEM and XRD results, which further indicates that all Cr3+ successfully substituted for the lattice site of Zn2+ and generated single-phase Zn1-xCrxS [21].Figure 3
HRTEM micrographs and SAED patterns of Zn0.95Cr0.05S.The corresponding selected area electron diffraction (SAED) patterns of Zn0.95Cr0.05S sample are shown in Figure 3(c), and the SAED pattern consists of many regular diffraction rings with different radius and one center. These rings correspond to (100), (002), (101), (102), (110), (103), and (112) planes of Zn0.95Cr0.05S nanorods from inner to exterior, respectively. The SAED pattern also confirms that Zn0.95Cr0.05S nanorods are wurtzite structure, belonging to polycrystalline structure, which is in agreement with the result of XRD. It indicates that the Cr3+ ions do not degrade the crystallinity of ZnS nanorods.


## 3.3. Chemical Characterization

In order to confirm the existence of the Cr elements of the doped samples, XEDS analysis is recorded. Figure4 shows the XEDS patterns of the undoped ZnS and Zn0.92Cr0.05S nanorods. From Figure 4(a), it can be found that the undoped ZnS nanorods mainly contain S and Zn two elements. Figure 4(b) obviously confirms the presence of Cr elements besides S and Zn elements for Zn0.95Cr0.05S nanorods, whereas the spectrum of pure ZnS did not find the presence of Cr elements. The quantitative atomic and weight percentage of the compositional elements are indicated in the inset of Figure 4. The calculated weight and atomic percentage are nearly equal to their nominal stoichiometry within the experimental error. The XEDS results further verify XRD conclusion, which indicates that Cr doped ZnS diluted magnetic semiconductors are successfully synthesized by hydrothermal method, and Cr3+ are successfully substituted as dopant in ZnS matrix.Figure 4
XEDS patterns of pure ZnS (a) and Zn0.95Cr0.05S (b).
(a)
(b)


## 3.4. Optical Properties

The diffuse-reflectance spectra are employed to investigate the effect of Cr doping on the optical characteristics ofZn1-xCrxS nanorods. The DRS of the pure ZnS and doped ZnS nanorods are depicted in Figure 5(a). The characteristic absorption edges band at ultraviolet (UV) region lies in the range of 330–390 nm, which shows that all samples possess wide absorption. The absorption coefficients are different, and there is an effect on the position of the absorption peaks. For analysis purposes the diffuse-reflectance (R) of the sample can be related to the Kubelka-Munk function F(R) by the relation F(R)=1-R2/2R. The band gap of the Zn1-xCrxS nanorods is estimated from the diffuse-reflectance spectra by plotting the square of the Kubelka-Munk function FR2 versus energy and extrapolating the linear part of the curve to FR2=0, which is shown in Figure 5(b). The absorption edges for Zn1-xCrxS samples are seen to be evidently shifted towards lower wavelengths comparing with pure ZnS and are shown in Figure 5(b). The measured values of optical band gap energy for pure ZnS are showed in Table 2, and Zn0.99Cr0.01S, Zn0.97Cr0.03S, and Zn0.95Cr0.05S are 3.729 eV, 3.737 eV, 3.743 eV, and 3.732 eV, respectively, which indicates that the Cr ions replace the Zn ions in the ZnS lattice, and the band gap of Cr doped ZnS samples is greater than that of pure ZnS. The band gap energy gradually increases with the increase of Cr concentration, up to a maximum 3.743 eV for 3% Cr. Furthermore, the band gap values estimated for these samples are in the range of 3.729–3.743 eV that are slightly greater than that of bulk ZnS (3.7 eV), which is manifested in the fact that the band gap energy undergoes blue shift in the doped ZnS system. The increase in the band gap energy with the decrease in the lattice parameters (a, c, and V) is due to the effect of doping, which are strongly supported by XRD results and associated with the variation of the lattice parameters. It can be explained that the increase of optical band gap may be attributed to the sp-d spin-exchange interactions between the band electrons of host matrix and the localized d electrons of the transition metal ion substituting the captions. Thus, the s-d and p-d exchange interactions between the band electrons of ZnS and localized d electrons of Cr give rise to change in the energy band structure, which can increase the band gap.Table 2
Band gap and magnetic moments of Zn1-xCrxS (x=0, 0.01, 0.03, and 0.05) nanorods.
Sample
Band gap (eV)
Magnetic moments (emu/g)
Saturation magnetization
Remanent magnetization (10−4)
Coercivity (Oe)
Pure ZnS
3.729
0.0117
6.415
46.71
Zn0.99Cr0.01S
3.737
0.0111
5.122
40.26
Zn0.97Cr0.03S
3.743
0.0097
5.339
41.22
Zn0.95Cr0.05S
3.732
0.0105
5.376
42.74Figure 5
UV-Vis diffuse-reflectance spectra (a) and (F(R)hν)2 versus hν curves (b) of Zn1-xCrxS (x=0, 0.01, 0.03, and 0.05) nanorods.
(a)
(b)PL spectra of pure ZnS and Cr doped ZnS nanorods are shown in Figure6. It is observed that PL intensity of doped samples is higher than pure ZnS sample. The ZnS samples exhibit three obvious broad emission peaks at 375 nm, 500 nm, and 580 nm, respectively. The obvious UV emission can be attributed to originate from excitonic recombination corresponding to the near-band-edge emission (NBE) of wide band gap of ZnS due to the quantum confinement effect [22]. The blue-green emission bands centered at 500 nm for samples may be attributed to S vacancies in ZnS nanorods and Zn vacancy related defects [23, 24]. The green emission peak at 580 nm is possibly assigned to positively charged electron transition and surface traps mediated by defects in the band gap [25]. The origin of this peak is still not clear and needs further study.Figure 6
PL spectra ofZn1-xCrxS (x=0, 0.01, 0.03, and 0.05) nanorods.The doped samples exhibit similar ultraviolet (UV) emission band at 375 nm to compare with pure ZnS, which illustrates that the doped samples display nearly the same structure of pure ZnS. As the doping concentration increases, the intensity of PL emission of the doped nanorods dramatically increases comparing to pure ZnS. When there is a small amount of Cr doping (x=0.03), the intensity of the peak of the PL spectrum reaches maximum. It is observed that the particle sizes of the doped samples increase with the increasing of Cr concentration from Table 1, which corresponds with XRD data. The increase in particle size results in enhanced surface defects leading to an increase in the PL intensity as chrome content is increased. It is because Cr3+ acts as a sensitizing agent and enhances the radiative recombination processes. Thus, the PL intensity of doped Zn1-xCrxS nanorods is higher than that of pure ZnS [26]. These results are in good agreement with XRD, EDX, and UV-visible studies.


## 3.5. Magnetic Studies

Figure7 presents the RT magnetic hysteresis (M-H) loops of the undoped ZnS and Zn1-xCrxS (x=0.01, 0.03, and 0.05) nanorods measured with the applied magnetic field of 8 kOe. It has deducted the contributions from the diamagnetism of the Si substrate and the paramagnetism of the sample holder during VSM measurement. The M-H curves show that all the samples exhibit obvious ferromagnetic behaviors. The ferromagnetism of undoped ZnS sample is attributed to the fact that sulfur vacancies boost both the emission and the magnetism, which is revealed d0 ferromagnetism [27], and the stronger exchange interactions between these sulfur vacancies weakened the saturation magnetization (Ms). From XRD results of doped ZnS nanorods, it is suggested that there are no traces of impurity or secondary phases, thus removing the possibility of ferromagnetism due to the clusters of transition elements or secondary phases in the samples. Hence, the room temperature ferromagnetism of Cr doped ZnS samples could arise from intrinsic magnetic property.Figure 7
M
-
H curves of Zn1-xCrxS (x=0, 0.01, 0.03, and 0.05) nanorods.TheM-H curves indicate the saturation magnetization values of 0.0117 emu/g, 0.0111 emu/g, 0.0097 emu/g, and 0.0105 emu/g for pure ZnS, Zn0.99Cr0.01S, Zn0.97Cr0.03S, and Zn0.95Cr0.05S nanorods, respectively. In view of the Cr3+ ions substituted into ZnS lattice, the origin of magnetism in the samples is due to the exchange interaction between local spin-polarized electrons (such as the electrons of Cr3+ ions) and the conductive electrons. Such interaction can lead to the spin polarization of conductive electrons. Consequently, the spin-polarized conductive electrons undergo an exchange interaction with local spin-polarized electrons of other Cr3+ ions. Thus, after a successive long-range exchange interaction, almost all Cr3+ ions exhibit the same spin direction, resulting in the ferromagnetism of the material. Poornaprakash et al. also report [28] the magnetic property in Cr doped ZnS nanoparticles by hydrothermal method. Therefore, there is an increase in the intensity of the peak with increase in dopant content in that report.The saturation magnetization of doped samples is smaller than that of pure ZnS, and the values of saturation magnetization decrease with the increase of Cr doping concentration. It is interesting that the ferromagnetism is suppressed with the Cr concentration increasing. In addition, the saturation magnetization ofZn1-xCrxS samples decreases with the increase of Cr concentration comparing to pure ZnS and reaches minimum for 3% Cr. It is because the Cr3+ ions substitute the Zn ions, with the local hole concentration at the anion increasing. As the Cr concentration increases, the distance between the Cr atoms and each other is closer and the super exchange interaction between the neighboring Cr atoms is antiferromagnetic in nature. When there is an increase of Cr doping concentration, the enhanced antiferromagnetic interaction is attributed to the decreased volume and the ferromagnetic ordering is suppressed [29].The variation of coercivity (Hc) and remanent magnetization (Mr) with Cr concentration ofZn1-xCrxS nanorods are indicated in the inset of Figure 7. It is observed that the values of Ms, Hc, and Mr of Cr doped ZnS samples are lower than that of pure ZnS, respectively. In order to investigate the magnetic properties in Zn1-xCrxS nanorods clearly, the magnetic moments values are shown in Table 2. Furthermore, the Hc and Mr gradually increase in doped samples with the increase of Cr concentration. When Hc is smaller, the synthesized ZnS nanorods show soft magnetic properties.


## 4. Conclusions

(1)
Pure ZnS and dopedZn1-xCrxS nanorods with different concentration ratio (x=0, 0.01, 0.03, and 0.05) were successfully synthesized by hydrothermal method. All the samples synthesized by this method exhibit single-phase wurtzite structure with good crystallization. All Cr ions successfully substituted for the lattice site of Zn2+ and generate single-phase Zn1-xCrxS, the lattice constant underwent distortion, and the grain size increased with increasing Cr doping concentration. The morphology of all the samples is one-dimensional rod-like shape with good dispersion.
(2)
The band gap of dopedZn1-xCrxS nanorods underwent blue shift compared to that of the bulk ZnS. PL spectra show obvious ultraviolet emission peak at 375 nm and two blue emissions appear about 500 and 580 nm, and the blue emissions intensity of doped samples improves with the increase of Cr concentration comparing to pure ZnS and reaches maximum for 3% Cr.
(3)
Magnetic measurements indicate that the undoped and Cr doped ZnS samples exhibit ferromagnetic behavior at room temperature, and the saturation magnetization weakened significantly with increasing Cr concentration comparing to pure ZnS and reached minimum for 3% Cr. The variation of coercivity and remanent magnetization of Cr doped ZnS samples is lower than that of pure ZnS, respectively. The Hc and Mr gradually increase with the increase of Cr concentration.



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*Source: 9378349-2017-03-27.xml*