Synthesis and Electro-Magneto-Mechanical Properties of Graphene Aerogels Functionalized with Co-Fe-P Amorphous Alloys

Graphene aerogels (GAs) are functionalized with Fe-Co-P alloy using an electro-deposition method. The Fe-Co-P alloy coated on the graphene nanosheets is found to possess an amorphous structure and a nanoporous architecture of GAs. The electro-mechanical properties of GAs are significantly affected by the Fe-Co-P nanoparticles embedded inside GAs. The electro-mechanical responses of GA/Fe-Co-P nanoporous hybrid structures are sensitive to an applied magnetic field, demonstrating that they are promising for electro-magneto-mechanical applications. The light-weight, high-strength and nanoporous GAs functionalized with Fe-Co-P amorphous alloys are desirable sensors, actuators, and nano-electro-mechanical systems that could be controlled or manipulated by mechanical, electric and magnetic fields.

Because of their exceptionally large surface areas (as large as 2630 m 2 /g) and good electrical conductivity (~10 2 S/m), GAs are desirable supports for micro-and nano-sized metals, oxides, magnets, photo-catalysts and electro-catalysts, which have significantly enhanced performances compared with their pristine counterparts [9][10][11][12][13][14][15][16][17][18]. In particular, owing to their super-elasticity (up to 200% in compression) and stress-dependent electrical conductivity, GAs are suitable nano-electro-mechanical sensors and devices for various applications, such as micro-or nano-sized strain gauges, stress and pressure sensors. However, there are two major drawbacks of GAs which will prevent them from wide-spread applications. First, the high porosity of GAs usually results in significant reduction of their mechanical strength [1][2][3][4]. Second, the graphene nanosheets in GAs are reduced graphene oxides, which have low electrical conductivity [5][6][7]. Hence, graphene aerogel with improved mechanical and electrical performances are urgently needed.
In this work, we investigate GAs functionalized with Fe-Co-P alloys. The nanoporous structures of samples and the phases of Fe-Co-P embedded inside GAs are characterized. The mechanical as shown in the inset in Figure 1b. It can be seen in Figure 1 that the nanoporous architectures of GA are preserved in the GA/Co-Fe-P hybrid structures (Sample-h14) and the Co-Fe-P fully coated on the graphene nanosheets consists of a lot of nanoparticles. Figure 2 shows the SEM images of all GA/Co-Fe-P samples. The sizes and contents of Co-Fe-P nanoparticles in the hybrid structures can be found to increase with increasing deposition time. It seems that the Co-Fe-P alloys fully coated on the graphene nanosheets in Sample-h14 could result from the growth of Co-Fe-P nanoparticles whose sizes can be as small as 20-30 nm, as shown in Figure 2a for Sample-h2.
Micromachines 2016, 7, 117 3 of 8 as shown in the inset in Figure 1b. It can be seen in Figure 1 that the nanoporous architectures of GA are preserved in the GA/Co-Fe-P hybrid structures (Sample-h14) and the Co-Fe-P fully coated on the graphene nanosheets consists of a lot of nanoparticles. Figure 2 shows the SEM images of all GA/Co-Fe-P samples. The sizes and contents of Co-Fe-P nanoparticles in the hybrid structures can be found to increase with increasing deposition time. It seems that the Co-Fe-P alloys fully coated on the graphene nanosheets in Sample-h14 could result from the growth of Co-Fe-P nanoparticles whose sizes can be as small as 20-30 nm, as shown in Figure 2a for Sample-h2.   Figure 3 shows the XRD patterns of GA/Co-Fe-P samples. In comparison with those of GA and Co-Fe-P foils prepared by the same electrodeposition conditions, the XRD peaks for Sample-h14 demonstrate that the Co-Fe-P alloys coated on the graphene nanosheets is amorphous, as shown in  as shown in the inset in Figure 1b. It can be seen in Figure 1 that the nanoporous architectures of GA are preserved in the GA/Co-Fe-P hybrid structures (Sample-h14) and the Co-Fe-P fully coated on the graphene nanosheets consists of a lot of nanoparticles. Figure 2 shows the SEM images of all GA/Co-Fe-P samples. The sizes and contents of Co-Fe-P nanoparticles in the hybrid structures can be found to increase with increasing deposition time. It seems that the Co-Fe-P alloys fully coated on the graphene nanosheets in Sample-h14 could result from the growth of Co-Fe-P nanoparticles whose sizes can be as small as 20-30 nm, as shown in Figure 2a for Sample-h2.   Figure 3 shows the XRD patterns of GA/Co-Fe-P samples. In comparison with those of GA and Co-Fe-P foils prepared by the same electrodeposition conditions, the XRD peaks for Sample-h14 demonstrate that the Co-Fe-P alloys coated on the graphene nanosheets is amorphous, as shown in  Figure 3 shows the XRD patterns of GA/Co-Fe-P samples. In comparison with those of GA and Co-Fe-P foils prepared by the same electrodeposition conditions, the XRD peaks for Sample-h14 demonstrate that the Co-Fe-P alloys coated on the graphene nanosheets is amorphous, as shown in Figure 3b. The intensity of the broad peak at 44.7˝for the amorphous phase of Co-Fe-P indicates that its content dramatically increases when the electrodeposition time is larger than 8 h, as shown in Figure 3a for Sample-h2, h4 and h8 and in Figure 3b for Sample-h14. Figure 3b. The intensity of the broad peak at 44.7° for the amorphous phase of Co-Fe-P indicates that its content dramatically increases when the electrodeposition time is larger than 8 h, as shown in Figure 3a for Sample-h2, h4 and h8 and in Figure 3b for Sample-h14.  Table 1 lists the results of analysis on the nanoporous structures of GA/CO-Fe-P samples. As indicated by the specific surface area (SSA) and volume (Vtotal), the Co-Fe-P nanoparticles embedded on the graphene nanosheets significantly reduce the SSA and Vtotal of Sample-h2 and Sample-h4. With the evolution of Co-Fe-P nanoparticles throughout the graphene nanosheets, the SSA and Vtotal of Sample-h8 and Sample-h14 increase, suggesting that the Co-Fe-P amorphous alloy tends to form film-like coating on the surfaces of graphene nanosheets when the content of Co-Fe-P increases. As listed in Table 1, the average size of nano-pores of the hybrid structures increases with increasing content of Co-Fe-P. Table 1. The composition, specific surface area (SSA) and volume (Vtotal), and pore width of GA and GA/Co-Fe-P samples.
Raman spectra of the GA/Co-Fe-P samples are shown in Figure 4. The D-band (1327 cm −1 ) represents the defects in the graphene or amorphous carbon; the G-band (1593 cm −1 ) is caused by the in-plane vibration of graphite with an E2g-symmetry intra-layer mode. The intensity ratio of D-band to G-bands (Id/Ig) is higher in Sample-h2 than those of any other samples, suggesting that the defective carbon structures can be induced in Sample-h2 where Co-Fe-P nanoparticles with sizes of 20-30 nm might interact with the graphene nanosheets or their junctions. Becasue the surfaces of Co-Fe-P nanoparticles are less active toward the bonding with carbon atoms of the graphene nanosheets when the sizes of nanoparticles are increased, therefore the ratio Id/Ig could decrease to that of graphene with increasing sizes of nanoparticles.

Samples
Co   Table 1 lists the results of analysis on the nanoporous structures of GA/CO-Fe-P samples. As indicated by the specific surface area (SSA) and volume (V total ), the Co-Fe-P nanoparticles embedded on the graphene nanosheets significantly reduce the SSA and V total of Sample-h2 and Sample-h4. With the evolution of Co-Fe-P nanoparticles throughout the graphene nanosheets, the SSA and V total of Sample-h8 and Sample-h14 increase, suggesting that the Co-Fe-P amorphous alloy tends to form film-like coating on the surfaces of graphene nanosheets when the content of Co-Fe-P increases. As listed in Table 1, the average size of nano-pores of the hybrid structures increases with increasing content of Co-Fe-P. Raman spectra of the GA/Co-Fe-P samples are shown in Figure 4. The D-band (1327 cm´1) represents the defects in the graphene or amorphous carbon; the G-band (1593 cm´1) is caused by the in-plane vibration of graphite with an E 2g -symmetry intra-layer mode. The intensity ratio of D-band to G-bands (I d /I g ) is higher in Sample-h2 than those of any other samples, suggesting that the defective carbon structures can be induced in Sample-h2 where Co-Fe-P nanoparticles with sizes of 20-30 nm might interact with the graphene nanosheets or their junctions. Becasue the surfaces of Co-Fe-P nanoparticles are less active toward the bonding with carbon atoms of the graphene nanosheets when the sizes of nanoparticles are increased, therefore the ratio I d /I g could decrease to that of graphene with increasing sizes of nanoparticles.

The Electro-Mechanical Properties of GA/Co-Fe-P Samples
The compressive strength of Sample-h2, h4, h8 and h14 are determined from the compression tests to be 0.2, 3.8, 22 and 620 kPa, respectively. Except for Sample-h2 whose fracture strength is smaller than that of GA (0.6 kPa), the GA/Co-Fe-P samples exhibit much improved strength as compared with the monolith GA. The small mechanical strength of Sample-h2 might be related with the disorder graphene nanosheets induced by the embedded Co-Fe-P nanoparticles with sizes of 20-30 nm. When the Co-Fe-P amorphous alloys fully coat the graphene nanosheets inside GA, as shown in Figure 1b for Sample-h14, the mechanical properties of GA/Co-Fe-P hybrid structure are mainly determined by the Co-Fe-P amorphous alloys. Therefore the fracture strength of GA/Co-Fe-P hybrid structure increases with the increasing content of Co-Fe-P in a non-linear manner.
The GA/Co-Fe-P hybrid structures are placed along the horizontal direction between two copper plates. Thin copper wires are attached to the two copper plates which are separately contacted with the top and bottom electrodes of the samples. The copper plates are driven to move horizontally in the opposite directions, leading to the compression on the samples. When the samples are compressed by a uniaxial compressive strain ε, the electrical resistances R(ε) of the samples are measured. Figure 5 shows the repeatable change of electrical resistance ∆R = |R − R(ε)| of the GA/Co-Fe-P samples (Sample-h4 and Sample-h8) with ε, which is cyclic between 0 and εm. R is the electrical resistance at ε = 0. A linear relation between ∆R/R and ε changing from 0 to εm and then back to 0 can be observed, the ∆R/R~ε relations for Sample-h2 and Sample-h14 are not shown either because they have εm < 2% (Sample-h2) or the change in ∆R/R is less than 1% (Sample-h14).
The repeatable changes of electrical resistances under applied strains in Sample-h4 and Sample-h8 indicate that they have better electro-mechanical performances or sensitivities compared to monolith GA. Combined with its high mechanical strength and light weight, Sample-h8 has the best performance in nano-electro-mechanical applications.

The Electro-Magneto-Mechanical Properties of GA/Co-Fe-P Samples
The electro-deposited Co-Fe-P alloy foils have been well studied to have excellent soft magnetic properties [19]. Although in the GA/Co-Fe-P hybrid structures only Sample-h14 is found to exhibit magnetic properties which are detectable by the VSM, as shown in Figure 6a, other GA/Co-Fe-P hybrid structures containing Fe-Co-P magnetic materials could be also sensitive to an

The Electro-Mechanical Properties of GA/Co-Fe-P Samples
The compressive strength of Sample-h2, h4, h8 and h14 are determined from the compression tests to be 0.2, 3.8, 22 and 620 kPa, respectively. Except for Sample-h2 whose fracture strength is smaller than that of GA (0.6 kPa), the GA/Co-Fe-P samples exhibit much improved strength as compared with the monolith GA. The small mechanical strength of Sample-h2 might be related with the disorder graphene nanosheets induced by the embedded Co-Fe-P nanoparticles with sizes of 20-30 nm. When the Co-Fe-P amorphous alloys fully coat the graphene nanosheets inside GA, as shown in Figure 1b for Sample-h14, the mechanical properties of GA/Co-Fe-P hybrid structure are mainly determined by the Co-Fe-P amorphous alloys. Therefore the fracture strength of GA/Co-Fe-P hybrid structure increases with the increasing content of Co-Fe-P in a non-linear manner.
The GA/Co-Fe-P hybrid structures are placed along the horizontal direction between two copper plates. Thin copper wires are attached to the two copper plates which are separately contacted with the top and bottom electrodes of the samples. The copper plates are driven to move horizontally in the opposite directions, leading to the compression on the samples. When the samples are compressed by a uniaxial compressive strain ε, the electrical resistances R(ε) of the samples are measured. Figure 5 shows the repeatable change of electrical resistance ∆R = |R´R(ε)| of the GA/Co-Fe-P samples (Sample-h4 and Sample-h8) with ε, which is cyclic between 0 and ε m . R is the electrical resistance at ε = 0. A linear relation between ∆R/R and ε changing from 0 to ε m and then back to 0 can be observed, the ∆R/R~ε relations for Sample-h2 and Sample-h14 are not shown either because they have ε m < 2% (Sample-h2) or the change in ∆R/R is less than 1% (Sample-h14).
The repeatable changes of electrical resistances under applied strains in Sample-h4 and Sample-h8 indicate that they have better electro-mechanical performances or sensitivities compared to monolith GA. Combined with its high mechanical strength and light weight, Sample-h8 has the best performance in nano-electro-mechanical applications.

The Electro-Magneto-Mechanical Properties of GA/Co-Fe-P Samples
The electro-deposited Co-Fe-P alloy foils have been well studied to have excellent soft magnetic properties [19]. Although in the GA/Co-Fe-P hybrid structures only Sample-h14 is found to exhibit magnetic properties which are detectable by the VSM, as shown in Figure 6a, other GA/Co-Fe-P hybrid structures containing Fe-Co-P magnetic materials could be also sensitive to an applied magnetic field. Therefore, the repeatable changes of electrical resistances of the GA/Co-Fe-P samples under applied strains could be affected by the applied magnetic fields.
Micromachines 2016, 7, 117 6 of 8 applied magnetic field. Therefore, the repeatable changes of electrical resistances of the GA/Co-Fe-P samples under applied strains could be affected by the applied magnetic fields.   Figure 6b shows the ∆R/R~ε relations for Sample-h4 and Sample-h8 with and without a magnetic field of 10 Oe applied along the compression direction. Both samples have enhanced electro-mechanical sensitivity when a magnetic field is applied. Remarkably, the electro-mechanical responses under a magnetic field can be as high as 3 times of those of Sample-h4 without an applied magnetic field. Although the effects of nanoporous structures of GA/Co-Fe-P and the sizes of Co-Fe-P nanoparticles embedded on the graphene nanosheets on the electro-magneto-mechanical properties are yet to be further explored, the results suggest that the GA/Co-Fe-P hybrid structures have outstanding electro-magneto-mechanical responses and could be promising nano-electro-mechanical systems controlled or manipulated by multiple applied fields. applied magnetic field. Therefore, the repeatable changes of electrical resistances of the GA/Co-Fe-P samples under applied strains could be affected by the applied magnetic fields.   Figure 6b shows the ∆R/R~ε relations for Sample-h4 and Sample-h8 with and without a magnetic field of 10 Oe applied along the compression direction. Both samples have enhanced electro-mechanical sensitivity when a magnetic field is applied. Remarkably, the electro-mechanical responses under a magnetic field can be as high as 3 times of those of Sample-h4 without an applied magnetic field. Although the effects of nanoporous structures of GA/Co-Fe-P and the sizes of Co-Fe-P nanoparticles embedded on the graphene nanosheets on the electro-magneto-mechanical properties are yet to be further explored, the results suggest that the GA/Co-Fe-P hybrid structures have outstanding electro-magneto-mechanical responses and could be promising nano-electro-mechanical systems controlled or manipulated by multiple applied fields.  Figure 6b shows the ∆R/R~ε relations for Sample-h4 and Sample-h8 with and without a magnetic field of 10 Oe applied along the compression direction. Both samples have enhanced electro-mechanical sensitivity when a magnetic field is applied. Remarkably, the electro-mechanical responses under a magnetic field can be as high as 3 times of those of Sample-h4 without an applied magnetic field. Although the effects of nanoporous structures of GA/Co-Fe-P and the sizes of Co-Fe-P nanoparticles embedded on the graphene nanosheets on the electro-magneto-mechanical properties are yet to be further explored, the results suggest that the GA/Co-Fe-P hybrid structures have outstanding electro-magneto-mechanical responses and could be promising nano-electro-mechanical systems controlled or manipulated by multiple applied fields.

Conclusions
We investigate GAs functionalized with Fe-Co-P alloys, which are promising materials for nano-electro-mechanical systems and nano-devices. The GA/Co-Fe-P hybrid structures synthesized by electrodeposition are found to have nanoporous structures and contain amorphous Fe-Co-P nanoparticles embedded on the graphene nanosheets. The relations between the electrical resistances of samples and the applied strains and magnetic fields are determined. The results demonstrate that GAs functionalized with Fe-Co-P amorphous alloys are suitable for electro-magneto-mechanical applications in micro-machine and nano-devices.