# Synthesis and the Structural Transformation offcc to hcp in Ni-Graphene Nanocomposite by Simple Chemical Route via Sonication

Authors: N. K. Mahale; R. D. Ladhe; S. B. Attarde; S. T. Ingle
Journal: Journal of Nanoparticles
 (2014)

---

## Abstract

We report the synthesis and structural transformation offcc to hcp in Ni-graphene (Ni-Gr) composite by simple chemical route via sonication. The syntheses of Ni-Gr composite by simultaneous reduction method, and the effect of different composition ratio on morphology and crystal structure were examined in our present study. The results indicated that the graphene ratio played an important role in crystal structure and d-spacing in nickel crystals. Different compositions have shown different behavior. The nanonickel clusters of various shapes with coated graphene and decorated as nickel on graphene sheets are observed. The synthesized composites were characterized using X-ray diffraction (XRD), field emission scanning electron microscopy (FE-SEM), and transmission electron microscope (TEM). The XRD patterns indicated crystal lattice modifications in some composites while composites with a higher graphene ratio produced very small crystals with uniform lattice parameter and d-spacing. FE-SEM images indicated the growth of Datura fruit like shapes of nickel clusters in higher composition of nickel while the composites with least concentration of nickel were composed of cubical nanoparticles grown on graphene sheets. TEM analysis revealed many Ni nanoparticles surrounding the smooth petals like surface of graphene, with average diameters of spiky nickel nanoparticles being about 50 nm and 124 nm, respectively, on 200 nm of scale.


---

## Body

## 1. Introduction

By virtue of large surface to volume ratio, nanoparticles are currently enjoying broad aspects of research. Graphene’s importance has been well accepted after exploration of its extraordinary physical properties of high conductivity, high surface area, and exceptional mechanical properties. The common methods of graphene production includes micromechanical exfoliation, thermal expansion of graphite [1–3], chemical vapor deposition [4, 5], and solution-based chemical reduction of exfoliated graphite oxide [4, 6–9]. At the same time in the world of material science, nanonickel is also having unique place with variety of applications in chemical cell, batteries, nanoelectronics, and fuel cell and especially as a catalyst; but both graphene and nickel have excellent performances as a composite material in supercapacitors, photovoltaics, and batteries [4]. Moreover nickel nanoparticles have wide scope in different disciplines including magnetic fluids [10], data storage [11], biotechnology [12], catalysis [13, 14], and magnetic resonance imaging [15, 16]; it is also applicable as catalysts for hydrogenation of nitrobenzene [17] and thermal decomposition of ammonium perchlorate [18]. Many methods have been used to synthesize the metal nanoparticles, namely, chemical reduction [19–28], photochemical reduction [29, 30], sonochemical method [31], microemulsion technique [32], polyol process [33, 34], alcohol reduction [35], heat evaporation [36, 37], and electrochemical reduction [27, 28]. Though nickel nanoparticles are synthesized by reduction of metal salts using reducing agents as NaBH4, hydrazine, and polyols, these processes can produce stable nanoparticles without agglomeration, but particle surfaces are often found to be rough and exhibit spiky surface morphology [38].In this work we have attempted to study higher control over structural, morphological, and compositional properties with a high specific surface area and overall composition and control over their resultant catalytic and other physical properties.


## 2. Experimental Details

### 2.1. Preparation of Graphite Oxide

Graphite oxide was prepared with modified Hummer’s method, by stirring 100 mg graphite powder and 50 mg sodium nitrate in 3 mL sulphuric acid. The above suspension was kept in round bottom flask (RBF) under ice bath with vigorous agitation, and RBF was kept under ice bath with addition of potassium permanganate (KMnO4) over 30 minutes. The rate of addition of KMnO4 was maintained enough to control the temperature of suspension from exceeding 20°C. After 30 minutes ice bath was removed and the temperature was allowed to rise up to 35°C for 2 hours and as the reaction progressed the mixture became a brownish grey paste. At the end of 2 hours, 100 mL distilled water was added drop by drop for 15 minutes and the temperature of the reaction was maintained at 90–95°C. After distilled water addition, the suspension turned brown in color, and then 100 mL 30% hydrogen peroxide (H2O2) was added to minimize the concentration of residual permanganate and manganese dioxide to colorless soluble manganese sulfate. After treatment with H2O2, the suspension turned bright yellow color.The filtration and washing of graphite oxide (GO) are very difficult due to its lower molecular size and suspension which takes lot of time to settle, in case of filtration clogging of filter paper makes it messy. To get rid of this problem the best way we adopted by transferring synthesized suspension in separating funnel of 500 mL capacity and kept it aside up to settling; after that we got a transparent layer upper layer and the bottom layer filled of graphite oxide suspension and then separated these two layers by transferring the GO suspension slowly without mixing the upper one with a lower layer in another separating funnel. For collection of the GO paste, centrifuged it at 9000 RPM for 15–20 min. The supernatant from centrifuged was discarded and collected the graphite oxide. The GO paste was washed by 10% hydrochloric acid and subsequently by distilled water till it becomes neutral (pH 7); mother liquor was tested by atomic absorption spectrophotometer (Thermo) to ensure the filtrate is completely manganese free and then transformed it into powder form by evaporating the water. The quantity of graphite oxide required for the whole experiment was produced under different batches with the same method.


### 2.2. Synthesis of Nanonickel Graphene Composite

Individual nickel nanoparticles were synthesized by reduction method using hydrazine hydrate (N2H4·H2O). The use of hydrazine hydrate in aerobic condition leads to the formation of nickel oxide nanoparticles by chelation; Ni nanoparticles formation takes place through reduction of Ni+2 by N2H4·H2O and here molar ratio of Ni : N2H4 : NaOH must be 1 : 6.4 : 5.1; out of these trio, if ratio of NaOH and N2H4·H2O is disturbed, then the nickel hydrazine chloride complex forms. In this case first the bis- and trisnickel hydrazine chloride complex of purple and blue color are formed and then at 60–70°C they get reduced in presence of sodium hydroxide.We decorated nickel nanoparticles on graphene by simultaneous sonication and reduction of nickel salt solution and graphite oxide; this method is more facile than conventional. Total of nine composites were prepared of different ratios of Ni : Gr, that is, 9 : 1, 8 : 2, 7 : 3, 6 : 4, 5 : 5, 4 : 6, 3 : 7, 2 : 8, and 1 : 9. As said above the molar ratio of the reactant was maintained except that the quantity of hydrazine hydrate was kept constant for all composites, that is, 10 mL. Hydrazine hydrate (N2H4·H2O) was used to reduce Ni+2 ion solution of various concentrations. 100 mL reagent-grade nickel chloride solution was prepared in water produced by a Milli-Q SP Ultrapure-Water Purification System; all used reagents were of analytical grade provided by Fisher Scientific Company. The sodium hydroxide and nickel chloride solutions of various concentrations were prepared as given in Table 1, and the quantity of graphite oxide was suspended in sodium hydroxide solution for uniform dispersion it was sonicated. The 10 mL hydrazine hydrate was taken in Erlenmeyer conical flask of 250 mL capacity and kept in sonicator bath (750 watts, 50 kHz, Ultrasonic cleaner, Lab Hosp, Mumbai); when the temperature in sonicator reached 45–50°C, drop by drop addition of graphite oxide suspended sodium hydroxide and nickel chloride was started simultaneously and sonicated throughout the experiment. First the bis- and trisnickel hydrazine chloride complex of purple and blue color are formed at 60–70°C; within 5–10 seconds solution turns black and it represents the formation of metal nickel nanoparticles. Being sonicated the aggregation of the particles was avoided. After finishing the reaction the composites were collected by centrifugation at 9000 rpm, paste was washed several times to make it free of base and nonreacted material. On achieving the neutral pH of composite paste it was transferred to Petri plates, allowed to dry, and then stored in cramped vials.Table 1
Chemical composition applied for composite synthesis.
Composite
Graphite oxide (gm)
NiCl2·6H2O %w/v (aq.)
NaOH%w/v (aq.)
N2H4·H2O (mL)
A
0.1
3.644
0.15
10
B
0.2
3.239
0.13
10
C
0.3
2.834
0.11
10
D
0.4
2.429
0.010
10
E
0.5
2.024
0.08
10
F
0.6
1.619
0.06
10
G
0.7
1.214
0.05
10
H
0.8
0.809
0.03
10
I
0.9
0.409
0.01
10


### 2.3. Characterization of Composites

The XRD patterns were obtained using the Brucker D8 Advance powder diffractometer operating in the reflection mode with CuKa radiation (40 kV, 40 mA) and diffracted beam monochromator, using a step scan mode with the step of 0.020 and 0.5 s per step. Divergence slit 1.200 and antiscatter slit 0.600 were used. Diffraction patterns of powders were compared with ICCD reference database. The Scherrer equation was applied to estimate a crystallite size. The SEM micrographs were obtained using Hitachi High Tech S-4800 Type II equipped with EDX Brucker-X Flash Detector 5030. The TEM micrographs were analyzed on Philips CM200 TEM, having operating voltage range of 20–200 kv with resolution: 2.4Å. The powder samples were studied in native form without coating by conductive metal layers. The sample for electron microscopy was prepared by dispersing the powder in propanol by sonication and applying a drop of very dilute suspension on carbon-coated grids. The suspensions were dried by slow evaporation at ambient temperature.


## 2.1. Preparation of Graphite Oxide

Graphite oxide was prepared with modified Hummer’s method, by stirring 100 mg graphite powder and 50 mg sodium nitrate in 3 mL sulphuric acid. The above suspension was kept in round bottom flask (RBF) under ice bath with vigorous agitation, and RBF was kept under ice bath with addition of potassium permanganate (KMnO4) over 30 minutes. The rate of addition of KMnO4 was maintained enough to control the temperature of suspension from exceeding 20°C. After 30 minutes ice bath was removed and the temperature was allowed to rise up to 35°C for 2 hours and as the reaction progressed the mixture became a brownish grey paste. At the end of 2 hours, 100 mL distilled water was added drop by drop for 15 minutes and the temperature of the reaction was maintained at 90–95°C. After distilled water addition, the suspension turned brown in color, and then 100 mL 30% hydrogen peroxide (H2O2) was added to minimize the concentration of residual permanganate and manganese dioxide to colorless soluble manganese sulfate. After treatment with H2O2, the suspension turned bright yellow color.The filtration and washing of graphite oxide (GO) are very difficult due to its lower molecular size and suspension which takes lot of time to settle, in case of filtration clogging of filter paper makes it messy. To get rid of this problem the best way we adopted by transferring synthesized suspension in separating funnel of 500 mL capacity and kept it aside up to settling; after that we got a transparent layer upper layer and the bottom layer filled of graphite oxide suspension and then separated these two layers by transferring the GO suspension slowly without mixing the upper one with a lower layer in another separating funnel. For collection of the GO paste, centrifuged it at 9000 RPM for 15–20 min. The supernatant from centrifuged was discarded and collected the graphite oxide. The GO paste was washed by 10% hydrochloric acid and subsequently by distilled water till it becomes neutral (pH 7); mother liquor was tested by atomic absorption spectrophotometer (Thermo) to ensure the filtrate is completely manganese free and then transformed it into powder form by evaporating the water. The quantity of graphite oxide required for the whole experiment was produced under different batches with the same method.


## 2.2. Synthesis of Nanonickel Graphene Composite

Individual nickel nanoparticles were synthesized by reduction method using hydrazine hydrate (N2H4·H2O). The use of hydrazine hydrate in aerobic condition leads to the formation of nickel oxide nanoparticles by chelation; Ni nanoparticles formation takes place through reduction of Ni+2 by N2H4·H2O and here molar ratio of Ni : N2H4 : NaOH must be 1 : 6.4 : 5.1; out of these trio, if ratio of NaOH and N2H4·H2O is disturbed, then the nickel hydrazine chloride complex forms. In this case first the bis- and trisnickel hydrazine chloride complex of purple and blue color are formed and then at 60–70°C they get reduced in presence of sodium hydroxide.We decorated nickel nanoparticles on graphene by simultaneous sonication and reduction of nickel salt solution and graphite oxide; this method is more facile than conventional. Total of nine composites were prepared of different ratios of Ni : Gr, that is, 9 : 1, 8 : 2, 7 : 3, 6 : 4, 5 : 5, 4 : 6, 3 : 7, 2 : 8, and 1 : 9. As said above the molar ratio of the reactant was maintained except that the quantity of hydrazine hydrate was kept constant for all composites, that is, 10 mL. Hydrazine hydrate (N2H4·H2O) was used to reduce Ni+2 ion solution of various concentrations. 100 mL reagent-grade nickel chloride solution was prepared in water produced by a Milli-Q SP Ultrapure-Water Purification System; all used reagents were of analytical grade provided by Fisher Scientific Company. The sodium hydroxide and nickel chloride solutions of various concentrations were prepared as given in Table 1, and the quantity of graphite oxide was suspended in sodium hydroxide solution for uniform dispersion it was sonicated. The 10 mL hydrazine hydrate was taken in Erlenmeyer conical flask of 250 mL capacity and kept in sonicator bath (750 watts, 50 kHz, Ultrasonic cleaner, Lab Hosp, Mumbai); when the temperature in sonicator reached 45–50°C, drop by drop addition of graphite oxide suspended sodium hydroxide and nickel chloride was started simultaneously and sonicated throughout the experiment. First the bis- and trisnickel hydrazine chloride complex of purple and blue color are formed at 60–70°C; within 5–10 seconds solution turns black and it represents the formation of metal nickel nanoparticles. Being sonicated the aggregation of the particles was avoided. After finishing the reaction the composites were collected by centrifugation at 9000 rpm, paste was washed several times to make it free of base and nonreacted material. On achieving the neutral pH of composite paste it was transferred to Petri plates, allowed to dry, and then stored in cramped vials.Table 1
Chemical composition applied for composite synthesis.
Composite
Graphite oxide (gm)
NiCl2·6H2O %w/v (aq.)
NaOH%w/v (aq.)
N2H4·H2O (mL)
A
0.1
3.644
0.15
10
B
0.2
3.239
0.13
10
C
0.3
2.834
0.11
10
D
0.4
2.429
0.010
10
E
0.5
2.024
0.08
10
F
0.6
1.619
0.06
10
G
0.7
1.214
0.05
10
H
0.8
0.809
0.03
10
I
0.9
0.409
0.01
10


## 2.3. Characterization of Composites

The XRD patterns were obtained using the Brucker D8 Advance powder diffractometer operating in the reflection mode with CuKa radiation (40 kV, 40 mA) and diffracted beam monochromator, using a step scan mode with the step of 0.020 and 0.5 s per step. Divergence slit 1.200 and antiscatter slit 0.600 were used. Diffraction patterns of powders were compared with ICCD reference database. The Scherrer equation was applied to estimate a crystallite size. The SEM micrographs were obtained using Hitachi High Tech S-4800 Type II equipped with EDX Brucker-X Flash Detector 5030. The TEM micrographs were analyzed on Philips CM200 TEM, having operating voltage range of 20–200 kv with resolution: 2.4Å. The powder samples were studied in native form without coating by conductive metal layers. The sample for electron microscopy was prepared by dispersing the powder in propanol by sonication and applying a drop of very dilute suspension on carbon-coated grids. The suspensions were dried by slow evaporation at ambient temperature.


## 3. Result and Discussion

### 3.1. X-Ray Diffraction Study

Figure1 shows the XRD pattern of composites A to H. As shown in the figure peaks can be indexed to face centered cubic phase (space group Fm-3m (225)) of Ni JCPDS number 01-077-9326. The XRD clearly showed that, as the Ni ratio decreased in composite ratio, the position and intensities of the XRD peaks are varied, possibly due to their size and morphology. The sharp peaks demonstrated that the synthesized nickel is well crystallized. The FE-SEM results showed that the graphene oxide or graphite oxide percentage played an important role in the final morphology of Ni-nanocrystal. It should be noted here that such a novel morphology has been reported earlier, and we are the first to introduce the new morphologies in composite regime. The FE-SEM results showed that the nickel nanoparticles may grow like cube as the graphite oxide percentage is increased. The XRD results of composites formed at various compositions; out of them most has showed high intensity at 43.5° (2θ) that evidently confirmed the growth of nanocubes. Composites A and B have almost constant lattice parameter. A has 13.0 Å while B has 8.75 Å, but the composite C shows thehcp phases a=b=3.6 and  c=1.78. Composite D has normally grown the nickel nanoparticles with constant lattice parameter. Lattice expansion can be seen in all composites except for composite A, though there are some composites with different parameters, but either lattice distortion or expansion is obvious in the composites. According to previous reports lattice distortion in various nanocrystalline materials processed using different methods is revealed by significant change in the lattice parameter [39, 40].Figure 1
XRD pattern of composites A to H.Composites G and C show higher degree of lattice distortion as compared to the other composites. Composites G and C withhcp regime can be understood with the work explained by Datta et al. [41]. They have reported that the structural transformation offcc tohcp in Ni(Si) below the critical size of ~10 nm by the mechanical instability concept calculations based on the equation of state shows 37% reduction in tetragonal shear modulus of nanocrystallinefcc Ni(Si) at onset of transformation suggesting defect induced melting offcc Ni(Si) to amorphous structure of zero shape modulus which is expected to be relaxed tohcp structure of molar volume of 7.57 cm3/moL and is in good agreement with the molar volume of liquid at the melting point of Ni. According to Chatterjee et al. [42], the expansion of lattice parameter also has been detected in nanocrystallinebcc (Cr, Fe, and Nb) andfcc (Ni, Cu, Ag, and Pd) metal synthesized using different approaches [43].In case of crystal size and molar volume of the composite, result shows crystal size reduced greatly with increasing graphene ratio. As per the crystal size determined by Scherrer equation the lowest crystal size is observed at composite H, that is, 0.07Å. The refinement of crystal size has been explained by considering the presence of a stress field at the core due to presence of vacancy or vacancy cluster situated at grain boundary in nanocrystalline material which mainly depends on the volume fraction of the interface that is inversely related to crystallite size [44].


### 3.2. Scanning Electron Microscopic Study

Scanning electron micrograph of the composites can be seen in Figure2. Figure 2(a) shows effect of simultaneous reduction of Ni+2 and GO in composite A. On an average of 50 nm spherical particle embedded in graphene coating. The particle formation of both Ni and graphene at the same time has made uniform coating on one another. At microlevel the nanoclusters of the composite are observed. In case of composite B the increased amount of graphene can be seen apparently in Figure 2(b). The clusters are grown like Datura fruit; spiky nickel nanoparticles spherical cluster is surrounded by petals of graphene. Not only the clusters are on graphene but also the metal nanoparticles are embedded in nanopetals of graphene. Thin film has covered the nanoclusters of nickel containing both spherical and spiky nanoparticles.SEM micrograph of composites A (Ni 9 : 1 graphene), B (8 : 2), C (7 : 3), D (6 : 4), E (5 : 5), F (4 : 6), G (3 : 7), and H (2 : 8).
(a)
(b)
(c)
(d)
(e)
(f)
(g)
(h)The thick film of graphene on nickel clusters is more vivid in scanning electron micrograph of composite C in Figure2(c); it is the effect of higher percentage of graphene in the Ni : Gr (3 : 7) ratio. Every Ni particle gets embedded as soon as it is formed and a very good and uniform covering of graphene is observed in composite C. About all the nanoclusters are of the same size, interconnected, and covered by graphene. With reduction in Ni+2 ions and increase in graphite oxide, the cluster size increased and spiky shape of Ni nanoparticles tends towards being more spherical. The graphene and cluster contacts are also thick compared to the previous composites. The coating of the graphene over nickel nanoclusters has become heavier and thick; the previous composites have shown nearly transparent coating over nickel nanoclusters.The increasing amount of graphite oxide and the reduced Ni is showing great impact on the site of the nanoclusters growth in composite E. The nickel nanoparticle growth is preferred more on the edges of the graphene sheet. This is maybe due to the fact that the site for nucleation provided by hydroxyl group is present at the verge of reduced graphite oxide. This composite having 50 : 50 proportion of Ni and graphene shows that the epoxy, hydroxyl, and pairwise carboxyl groups are available for further reaction with graphite oxide. A single formation at the edge and its magnetic attraction gives rise to cluster formation up to some extent. The composite F that is, 6: 4, in this composite nickel nanoclusters are formed like a chain of clusters connected by graphene, can be seen in Figure2(f). The graphene coating of a cluster avails the site for nucleation of another cluster and so on. Such behavior may reduce the resistance in the composite and could serve as a better catalyst. Around 40–100 nm size and sphere were formed on graphene surface; not only surface edge but also all the available space was used by nickel nanoparticles. This ratio 7 : 3, that is, composite G, is more perfect from the point of crystal lattice andd-spacing though it has low quantity of nickel, but it has occupied nearly all the surface available with graphene sheet. The largest diameter of nickel nanoparticles was found to be 573 nm. The spike of nanonickel pixels/cubes has seen on the corners of graphene sheet. As in the previous composites the graphene was showing Datura fruit like morphology along with Ni nanoparticles, but in composite graphene show the cabbage like morphology and Ni nanocubes of size ranging from 12 to 100 nm on graphene surface. In composite G approximately all the sheets of graphene and maximum surface of sheets have been covered by cubes of Ni. In composite I, that is, Ni : Gr (1 : 9), sporadically scattered growth of nickel nanoparticles has occurred. The amount of nickel in ratio that is 10% is not enough to cover the large surface area of graphene.


### 3.3. Transmission Electron Microscopic Study

A TEM image recorded from two spherical clusters of spiky nickel on the thick surface of graphene is displayed in Figure3(a). Apparently there are many nanoparticles surrounding the smooth petals like surface of graphene; the average diameters of spiky nickel nanoparticles are about 50 nm and 124 nm, respectively, on 50 nm of scale. Not only the clusters are on graphene but also the metal nanoparticles are embedded in nanopetals of graphene. This formation of the nickel nanoparticles was observed by FESEM and previously was confirmed by TEM. Figure 3(c) is the corresponding selected area electron diffraction pattern with the interplanar spacings of the nanoparticles being 2.5 nm and 5.4 nm, consisting of the spacings of the (1 1 1) and (2 0 0) plane of nickel and graphene.(a) TEM images of Ni nanoparticles surrounded by graphene in composite H. (b) Average diameters of nickel nanoparticles of composite H. (c) SAED of composite H.
(a)
(b)
(c)


## 3.1. X-Ray Diffraction Study

Figure1 shows the XRD pattern of composites A to H. As shown in the figure peaks can be indexed to face centered cubic phase (space group Fm-3m (225)) of Ni JCPDS number 01-077-9326. The XRD clearly showed that, as the Ni ratio decreased in composite ratio, the position and intensities of the XRD peaks are varied, possibly due to their size and morphology. The sharp peaks demonstrated that the synthesized nickel is well crystallized. The FE-SEM results showed that the graphene oxide or graphite oxide percentage played an important role in the final morphology of Ni-nanocrystal. It should be noted here that such a novel morphology has been reported earlier, and we are the first to introduce the new morphologies in composite regime. The FE-SEM results showed that the nickel nanoparticles may grow like cube as the graphite oxide percentage is increased. The XRD results of composites formed at various compositions; out of them most has showed high intensity at 43.5° (2θ) that evidently confirmed the growth of nanocubes. Composites A and B have almost constant lattice parameter. A has 13.0 Å while B has 8.75 Å, but the composite C shows thehcp phases a=b=3.6 and  c=1.78. Composite D has normally grown the nickel nanoparticles with constant lattice parameter. Lattice expansion can be seen in all composites except for composite A, though there are some composites with different parameters, but either lattice distortion or expansion is obvious in the composites. According to previous reports lattice distortion in various nanocrystalline materials processed using different methods is revealed by significant change in the lattice parameter [39, 40].Figure 1
XRD pattern of composites A to H.Composites G and C show higher degree of lattice distortion as compared to the other composites. Composites G and C withhcp regime can be understood with the work explained by Datta et al. [41]. They have reported that the structural transformation offcc tohcp in Ni(Si) below the critical size of ~10 nm by the mechanical instability concept calculations based on the equation of state shows 37% reduction in tetragonal shear modulus of nanocrystallinefcc Ni(Si) at onset of transformation suggesting defect induced melting offcc Ni(Si) to amorphous structure of zero shape modulus which is expected to be relaxed tohcp structure of molar volume of 7.57 cm3/moL and is in good agreement with the molar volume of liquid at the melting point of Ni. According to Chatterjee et al. [42], the expansion of lattice parameter also has been detected in nanocrystallinebcc (Cr, Fe, and Nb) andfcc (Ni, Cu, Ag, and Pd) metal synthesized using different approaches [43].In case of crystal size and molar volume of the composite, result shows crystal size reduced greatly with increasing graphene ratio. As per the crystal size determined by Scherrer equation the lowest crystal size is observed at composite H, that is, 0.07Å. The refinement of crystal size has been explained by considering the presence of a stress field at the core due to presence of vacancy or vacancy cluster situated at grain boundary in nanocrystalline material which mainly depends on the volume fraction of the interface that is inversely related to crystallite size [44].


## 3.2. Scanning Electron Microscopic Study

Scanning electron micrograph of the composites can be seen in Figure2. Figure 2(a) shows effect of simultaneous reduction of Ni+2 and GO in composite A. On an average of 50 nm spherical particle embedded in graphene coating. The particle formation of both Ni and graphene at the same time has made uniform coating on one another. At microlevel the nanoclusters of the composite are observed. In case of composite B the increased amount of graphene can be seen apparently in Figure 2(b). The clusters are grown like Datura fruit; spiky nickel nanoparticles spherical cluster is surrounded by petals of graphene. Not only the clusters are on graphene but also the metal nanoparticles are embedded in nanopetals of graphene. Thin film has covered the nanoclusters of nickel containing both spherical and spiky nanoparticles.SEM micrograph of composites A (Ni 9 : 1 graphene), B (8 : 2), C (7 : 3), D (6 : 4), E (5 : 5), F (4 : 6), G (3 : 7), and H (2 : 8).
(a)
(b)
(c)
(d)
(e)
(f)
(g)
(h)The thick film of graphene on nickel clusters is more vivid in scanning electron micrograph of composite C in Figure2(c); it is the effect of higher percentage of graphene in the Ni : Gr (3 : 7) ratio. Every Ni particle gets embedded as soon as it is formed and a very good and uniform covering of graphene is observed in composite C. About all the nanoclusters are of the same size, interconnected, and covered by graphene. With reduction in Ni+2 ions and increase in graphite oxide, the cluster size increased and spiky shape of Ni nanoparticles tends towards being more spherical. The graphene and cluster contacts are also thick compared to the previous composites. The coating of the graphene over nickel nanoclusters has become heavier and thick; the previous composites have shown nearly transparent coating over nickel nanoclusters.The increasing amount of graphite oxide and the reduced Ni is showing great impact on the site of the nanoclusters growth in composite E. The nickel nanoparticle growth is preferred more on the edges of the graphene sheet. This is maybe due to the fact that the site for nucleation provided by hydroxyl group is present at the verge of reduced graphite oxide. This composite having 50 : 50 proportion of Ni and graphene shows that the epoxy, hydroxyl, and pairwise carboxyl groups are available for further reaction with graphite oxide. A single formation at the edge and its magnetic attraction gives rise to cluster formation up to some extent. The composite F that is, 6: 4, in this composite nickel nanoclusters are formed like a chain of clusters connected by graphene, can be seen in Figure2(f). The graphene coating of a cluster avails the site for nucleation of another cluster and so on. Such behavior may reduce the resistance in the composite and could serve as a better catalyst. Around 40–100 nm size and sphere were formed on graphene surface; not only surface edge but also all the available space was used by nickel nanoparticles. This ratio 7 : 3, that is, composite G, is more perfect from the point of crystal lattice andd-spacing though it has low quantity of nickel, but it has occupied nearly all the surface available with graphene sheet. The largest diameter of nickel nanoparticles was found to be 573 nm. The spike of nanonickel pixels/cubes has seen on the corners of graphene sheet. As in the previous composites the graphene was showing Datura fruit like morphology along with Ni nanoparticles, but in composite graphene show the cabbage like morphology and Ni nanocubes of size ranging from 12 to 100 nm on graphene surface. In composite G approximately all the sheets of graphene and maximum surface of sheets have been covered by cubes of Ni. In composite I, that is, Ni : Gr (1 : 9), sporadically scattered growth of nickel nanoparticles has occurred. The amount of nickel in ratio that is 10% is not enough to cover the large surface area of graphene.


## 3.3. Transmission Electron Microscopic Study

A TEM image recorded from two spherical clusters of spiky nickel on the thick surface of graphene is displayed in Figure3(a). Apparently there are many nanoparticles surrounding the smooth petals like surface of graphene; the average diameters of spiky nickel nanoparticles are about 50 nm and 124 nm, respectively, on 50 nm of scale. Not only the clusters are on graphene but also the metal nanoparticles are embedded in nanopetals of graphene. This formation of the nickel nanoparticles was observed by FESEM and previously was confirmed by TEM. Figure 3(c) is the corresponding selected area electron diffraction pattern with the interplanar spacings of the nanoparticles being 2.5 nm and 5.4 nm, consisting of the spacings of the (1 1 1) and (2 0 0) plane of nickel and graphene.(a) TEM images of Ni nanoparticles surrounded by graphene in composite H. (b) Average diameters of nickel nanoparticles of composite H. (c) SAED of composite H.
(a)
(b)
(c)


## 4. Conclusions

We have successfully synthesized and achieved structural transformation offcc tohcp in Ni-graphene (Ni-Gr) composite by simple chemical route via sonication. As a result we found nonmagnetic nickel and also decorated the graphene clusters with Ni cubes and Datura fruit like morphologies by changing GO ratio in Ni : Gr composites. The composition of Ni+2 and GO and their effect on growth and morphology were investigated. The GO played a major role in formation of various microstructures of composite. The XRD pattern showed the formation of well crystallized nickel nanoparticles on smooth amorphous graphene surface. The FE-SEM and TEM images showed that the clusters and the coating of graphene over Ni nanoparticles are self-assembled by reduction and sonication process. The composites are prepared by hydrazine hydrate and sonication method which is one of its kind and significant morphologies have been synthesized and showed new material for further variety of applications in chemical cell, batteries, nanoelectronics and fuel cell and especially as a catalyst.



---

*Source: 305637-2014-06-23.xml*