Leila
Haghighi Poudeh
a,
Burcu
Saner Okan
*b,
Jamal
Seyyed Monfared Zanjani
a,
Mehmet
Yildiz
a and
Yusuf
Menceloglu
a
aFaculty of Engineering and Natural Sciences, Sabanci University, Tuzla, Istanbul 34956, Turkey. E-mail: meyildiz@sabanciuniv.edu
bSabanci University Nanotechnology Research and Application Center, SUNUM, Tuzla, Istanbul 34956, Turkey
First published on 16th October 2015
Two dimensional graphene oxide sheets are converted into three dimensional (3D) hollow and filled microspheres by using three different carrying polymers through one-step core–shell electrospraying technique without applying any post treatments. Electrospraying process prevents the aggregations and crumbling of graphene sheets by constructing 3D interconnected framework, and provides homogeneous dispersion of graphene sheets in polymer solution under electric field, and allows the polymer chains to crawl into graphene layers forming intercalated structure. The proper polymer concentration and solution viscosity are determined by using Mark–Houwink–Sakurada equation to produce an ideal graphene based polymeric sphere structure via electrospraying. Graphene based polymeric spheres with controllable hollowness are successfully fabricated by changing core solvents. The connectivity of graphene sheets in polymeric shell is improved by increasing carbon networks after carbonization process. Morphology, shrinkage behaviour and structural properties of spheres are evaluated by tailoring polymer type, polymer concentration, graphene amount, flow rate and applied voltage.
For the production of hollow 3D graphene structures, sphere-like templates such as polystyrene (PS), silicon dioxide (SiO2), and titanium dioxide (TiO2) were used in several published techniques. In one of the works, graphene hollow spheres were prepared by covering PS balls with graphene oxide (GO) sheets and then calcination was applied at 420 °C for 2 h to remove PS from the core.22 In another work, graphene-based hollow spheres were fabricated by electrostatic assembly of GO sheets on polyethylenimine covered SiO2 spheres in solution phase, and subsequently followed by washing with hydrofluoric acid and annealing processes to get hollow structure.23 In order to improve the catalytic properties of hollow spheres, Pd nanoparticles were decorated in double-shelled hollow carbon spheres by using SiO2 nanospheres as template during in situ process.24 In the mentioned processes, the size of spheres directly depends on the templates. It is not an easy process to control the shape of spheres and hollowness and get higher yield of graphene balls due to the recovery process in wet-chemical methods.
Electrospinning is one of widely used techniques to produce fibers and spherical or bead-like structures with the diameters ranging from few micrometers to nanometer by adjusting the surface tension of the droplet and viscosity of the solution under electric field.25 Recently, co-axial electrospinning process has received great attention due to its ability to produce core–shell 3D structures with different functionalities which have distinct advantages in comparison to structures fabricated by regular electrospinning technique.26 In this technique, two dissimilar solutions in concentric tubes flow under a high electric field, which is applied between the tip of the nozzle and collector. As a result, the surface tension of a compound droplet at the tip of the nozzle is overcome whereby the droplet stretches and forms a continuous jet which is collected on the electrically grounded plate as a fiber.27 In electrospinning and electrospraying, the final morphology of the product is affected by solution properties (such as viscosity and electrical conductivity) and process parameters (such as voltage, flow rate, and distance between collector and nozzle). There are few attempts for the integration of graphene into the fiber structure by using classic and co-axial electrospinning techniques. In one of the studies, Promphet et al.28 fabricated graphene based nanoporous fibers by electrospinning of graphene/polyaniline/polystyrene mixture to be used as an electrochemical sensor to detect heavy metals. In another work, aligned poly(3-hexylthiophene)–graphene nanofibers produced via two-fluid coaxial electrospinning technique were integrated into high-performance field effect transistors since graphene acts as an electronically conducting bridge between the polymer domains in the structure.29 Shilpa et al.30 synthesized core–shell composite nanofibers as an anode electrode for Li-ion batteries by co-axial electrospinning of rGO–polyacrylonitrile (PAN) solution as shell and zinc oxide with polymethyl methacrylate (PMMA) as core and then applied carbonization and calcination processes to this fiber mat. In all above mentioned relevant studies, for preserving the intrinsic properties of graphene materials in the bulk matrix, GO and rGO are incorporated into the fiber structure by electrospinning technique in one-step process.
One can conclude from literature that so far, considerable amount of works have focused on the production of polymeric bead structures and core–shell microcapsules and the investigation of their morphological changes by tailoring electrospinning parameters.31,32 In the present work, thermally exfoliated graphene oxide (TEGO) sheets are converted into 3D spheres with controlled hollowness and porosity by using three different carrier polymers through core–shell electrospraying technique. The effect of electric field on the exfoliation of graphene sheets is investigated by spectroscopic techniques to understand graphene dispersion behavior in polymeric shell during electrospraying process. In this study, shell polymers namely PS and PMMA are chosen due to their ease for the formation of spherical topology during electrospinning process since these two polymers are widely used as a template material for the production of 3D structures. Additionally, PAN polymer is used to form carbon network because of its high carbonization degree. The appropriate concentration for the production of spheres is verified by using Mark–Houwink–Sakurada equation. Hollowness of these spheres is controlled by changing core solvent and its flow rate. The dimension and morphology of graphene based spheres are investigated and optimized by tailoring the parameters of polymer type, polymer concentration, solution viscosity, TEGO amount, solvent evaporation rate and flow rate.
Fig. 1 Schematic representation of fabrication of graphene based spheres by tri-axial electrospraying technique. |
Fig. 2 SEM images of (a) as received TEGO sheets, (b) sonicated TEGO sheets in DMF, and (c) electrosprayed TEGO sheets in DMF without polymer. |
In order to detect the changes in the number of graphene layers, Raman spectroscopy analysis was conducted for as received, sonicated and electrosprayed TEGO sheets and the results are presented in Fig. 3. Raman spectrum of TEGO has three sharp main peaks: 1338 cm−1, 1577 cm−1, and 2750 cm−1, refer to as D, G, and 2D peaks, respectively.36 D peak is related to disorderness and its intensity changes with the defects in the structure. G peak corresponds to in-plane vibrations of sp2 bonded carbon atoms and its intensity is altered due to the variation in the number of graphene layers.36,37 It is known from literature, as the ratio of D to G intensities (ID/IG) increases, sp2 bonds are broken implying that there are more sp3 bonds and more defects in the structure.36 In the current study, after the sonication process, there is a slight decrease in ID/IG of untreated TEGO sample from 0.2 to 0.1. After electrospraying of TEGO sheets, D band completely disappears indicating that defect-free multi-layer graphene sheets are obtained. This decrease in D band intensity comes from the reduction in the thickness of graphene layers which is due to the deformation of solvent. In addition, shape, width and position of 2D peak determine the graphene layers.36 The reduction in the intensity ratio of G to 2D peaks (IG/I2D) indicates the decrease in the number of graphene layers. IG/I2D values of untreated TEGO and sonicated TEGO, and electrosprayed TEGO are 2.3, 2.0 and 2.0, respectively. This shows that the sonication process breaks down graphene layers, which are bonded by weak van der Waals forces, and then initiates the exfoliation process. On the other hand, multi-layer structure is still preserved after electrospraying process because there is no notable change in IG/I2D value. Furthermore, the intensity values of 2D peak increases after each process, and 2D peak of electrosprayed TEGO gets sharper and thus number of graphene layers decreases slightly when compared to sonicated TEGO. The peak positions and intensity ratios are given in Table S2.†
Fig. 3 (a) Raman spectra of as received TEGO, sonicated TEGO and electrosprayed TEGO and (b) the comparison of 2D peak intensities. |
Polymer type | M w (g mol−1) | M n (g mol−1) | PDI | Intrinsic viscosity (dL g−1) |
---|---|---|---|---|
PMMA | 41645 | 20798 | 2.00 | 0.3404 |
PS | 49283 | 29686 | 1.66 | 0.0781 |
PAN | 44489 | 32293 | 1.38 | 0.7261 |
Selected polymers can form spherical structures by the optimization of the system (applied voltage, syringe and collector distance, flow rate) and solution parameters (polymer concentration and TEGO content). In addition to these mentioned parameters, polymer chain entanglements affect the structural formations during electrospinning process. The degree of entanglement is determined by calculating two limiting concentrations, C* and Ce. C* corresponds to the solution concentration where the hydrodynamic volumes begin to overlap and Ce is the entanglement concentration which separates the semi-dilute unentangled and semi-dilute entangled regimes. C* is calculated using the following equation:
C* = 1/[η] | (1) |
Moreover, the optimum concentration for the fabrication of polymer based TEGO spheres was investigated by using Mark–Houwink–Sakurada equation (eqn (2)):
[η] = KHMa | (2) |
C* = 4 × 104Mw−0.625, PMMA | (3) |
C* = 3.15 × 104Mw−0.603, PS | (4) |
C* = 5.65 × 104Mw−0.780, PAN | (5) |
Fig. 4 shows the entanglement concentration Ce = 10C* as a function of molecular weight of PMMA, PS, and PAN polymers. Solid lines represent the concentration threshold of each polymer obtained from eqn (3) (black line), eqn (4) (red line) and eqn (5) (blue line), and each point corresponds to the polymer concentrations which are selected for the fabrication of spheres. As seen in Fig. 4, all of the corresponding points attributed to the used polymer concentrations stay on the lower region of threshold line (Ce) where bead formation is dominant.
Fig. 4 Entanglement concentration Ce = 10C* as a function of the molecular weight of PMMA, PS, and PAN polymers. |
Polymeric solutions were purged through outer syringe by keeping core syringe empty during co-axial electrospraying. Table 2 summarizes the synthesis conditions and characteristic properties of spheres made of PMMA and PS polymers and shrinkage percentages of polymeric spheres after the integration of TEGO into the structure. By the addition of TEGO in electrospun solutions, there is a significant decrease in the diameter of TEGO based spheres when compared to neat polymeric spheres. Herein, TEGO sheets start the shrinkage of the spheres under electric field since the surface forces increase on droplets. After increasing the amount of TEGO, a gradual increase is observed in sphere diameter. For instance, as seen in Table 2, PMMA spheres shrink by about 38% through the addition of 0.005 wt% TEGO and the shrinkage values decreases down to 29% and 20% with 0.01 wt% and 0.02 wt% TEGO loadings, respectively. The decrease in diameter shows the dense stacking of graphene layers in polymeric shell. It is known that oxygen functional groups of GO in aqueous and organic solutions are negatively charged,39 and hence, the electrostatic interaction between these negatively charged GO sheets and positively charged polymers minimizes the size of the spherical structure. Carbon/oxygen ratio of GO is changed regarding the type of chemical exfoliation process.35,40 Most of surface oxygen functional groups can be removed by applying thermal treatment and hydrophilicity of GO decreases and this allows for controlling the surface chemistry of graphene.41 In addition, thermal treatment extends the distance between graphene layers and ease intercalation process is achieved during electrospraying process. Therefore, TEGO is preferred as filler for the production of composite spheres. Increasing TEGO amount in electrospun solution gradually imbalances the electrostatic interaction between charges, and enlarges the sphere diameter.
TEGO amount (wt%) | Average diameter of spheres (μm) | Average shrinkage of spheres (%) | |
---|---|---|---|
PMMA | 0 | 4.7 | — |
0.005 | 2.9 | 38 | |
0.01 | 3.4 | 29 | |
0.02 | 3.8 | 20 | |
PS | 0 | 4.5 | — |
0.005 | 2.2 | 51 | |
0.01 | 2.6 | 42 | |
0.02 | 3.1 | 32 |
Fig. 5 exhibits SEM images of spheres sprayed by using air at atmospheric pressure in the core of the syringe. After electrospraying process without any core materials, it is observed that all types of polymers form porous and filled sphere structures. After the addition of TEGO into the polymer, it is noted that the diameter of these spheres decreases. Furthermore, Fig. 6 presents SEM images of neat PS spheres and TEGO based PS spheres at higher magnification. By the incorporation of TEGO, the porosity of spheres decreases and the surface becomes smoother.
Fig. 5 SEM images of spheres produced by (a) PMMA, (b) PMMA-0.01 wt% TEGO, (c) PMMA-0.02 wt% TEGO, and (d) PS, (e) PS-0.005 wt% TEGO, (f) PS-0.02 wt% TEGO. |
XRD characterization was performed in order to prove the presence of TEGO in polymer spheres. In Fig. 7, TEGO has a characteristic 002 peak at 26.5°. In the XRD analysis of polymer–graphene based nanocomposites, 002 peak can either completely disappear or shift to the lower region due to the intercalation of polymeric chains into graphene sheets.42,43 In Fig. 7a, PMMA shows a wide diffraction peak spanning from 10° to 20° with a maximum intensity at 2θ ≈ 14.4° and the intensity of this peak decreases as TEGO amount increases and 2θ shifts to lower angel values due to the complete coating of multi layer graphene by polymer chains. Also, the diffraction peak broadens and its intensity decreases by the incorporation of TEGO and thus composite becomes completely amorphous structure. In Fig. 7b, PS has a broad diffraction peak between 15° and 25° and as the value of TEGO increases, PS diffraction peak shifts towards lower angles and its peak becomes wider by increasing TEGO amount. Table S4 of ESI† also shows the values of polymer peak intensity and 2θ values. One can note that in the produced spheres, 002 peak of TEGO disappears. The slight shifting of polymer diffraction peak to the lower angle region and the disappearance of 002 peak of TEGO bespeak that the electric field enhances the distribution of graphene sheets in polymer solution so that multi-layer graphene sheets are completely coated by polymer during sphere formation. Fig. 8 also shows schematically how complete coverage occurs between TEGO and polymer chains and avoids restacking of multi-layer graphene sheets under electric field.
Fig. 8 Schematic illustration of interactions between polymeric chains and TEGO sheets during sphere formation. |
Fig. 9 shows Raman spectra of TEGO, PS, and PS–TEGO spheres. PS has characteristic Raman peaks at 3050 cm−1 and 2900 cm−1 due to the vibration of C–H bonds, 1600 cm−1 attributed to CC vibrations and 995 cm−1 related to aromatic carbon rings.44 In the Raman spectrum of the PS-0.02 wt% TEGO, the characteristic peaks of TEGO do not appear because of the low amount of TEGO in the polymeric spheres and overlapping of polymer main peaks with TEGO peaks. On the other hand, significant decrease in Raman peaks of PS was observed by the integration of TEGO (see Table S5 in ESI†) which also proves the presence of TEGO in the spheres.
The produced spheres were cut by using an ion beam source of FIB-SEM instrument to investigate the inside of microstructures. Fig. 10 displays FIB-SEM images of 0.02 wt% TEGO + PMMA spheres produced utilizing the methanol as core solvent with the lowest flow rate. Before the ion bombardment, spherical structure is clearly seen in Fig. 10a. After the ion bombardment, the shell material starts to melt upon increasing the current of the ion beam whereby one can clearly observe the hollowness within the sphere as seen in Fig. 10b. Fig. 11 yields the FIB-SEM images of TEGO based PMMA spheres produced with a flow rate of 2 μL min−1 during the ion beam bombardment process. The porous core structure is detected at the end of complete melting of shell materials as seen in Fig. 11c. This proves that increasing the flow rate of core solvent facilitates the penetration of core solvent through shell and induces phase separations and thus leads to porous core structure. The average diameter of spheres changes from 3.4 μm to 4.6 μm by increasing the flow rate of core material because higher flow rate speeds up the evaporation process of solvent. Spraying methanol with a high flow rate of 5 μL min−1 totally changes the morphology and fiber formation is detected among spheres, which are shown in Fig. S2.†
Fig. 10 FIB-SEM images of PMMA spheres containing 0.02 wt% TEGO using methanol as a core material and a flow rate of 0.5 μL min−1 (a) before and (b) after ion bombardment. |
Fig. 11 FIB-SEM images of PMMA spheres containing 0.02 wt% TEGO using methanol as a core material and a flow rate of 2 μL min−1 (a) before and (b) during and (c) after ion bombardment. |
In addition, FIB-SEM technique is used for the observation of porous core in PMMA spheres produced by using atmospheric air in core syringe. Fig. 12 displays FIB-SEM images of these spheres after the ion bombardment. The structure of spheres is noticeably porous even at longer bombardment period.
Fig. 12 FIB-SEM images of 20 wt% PMMA spheres containing 0.02 wt% TEGO by using atmospheric air as a core material (a) and (b) after ion bombardment. |
At the initial step of our process, 5 wt% PAN, 5 wt% PAN-0.02 wt% TEGO and 3.5 wt% PAN-0.05 wt% TEGO solutions were sprayed separately without using any core material to produce PAN-based spheres. Fabricated spheres containing 5 wt% PAN and 5 wt% PAN-0.02 wt% formed half hollow spheres (donut-shaped structures) and carbonization does not affect the morphologies of these structures as seen in Fig. 13. The reason for donut-shaped formation might be due to the combined effects of low polymer concentration, high intrinsic viscosity and applied electric forces. Thus, a rather interesting sphere structure is formed during the discharge process of the polymeric mixture from the tip of syringe. Average diameters of 5 wt% PAN and 5 wt% PAN-0.02 wt% TEGO spheres are about 1.6 μm and 2.9 μm, respectively. The incorporation of TEGO enlarges the diameter of spheres, which might stem from better dispersion and alignment of multi-layer graphene sheets in higher viscosity of PAN solution during electrospraying process when compared to the results of PMMA and PS solutions.
Fig. 13 SEM images of 5 wt% PAN spheres (a) before and (b) after carbonization, and 5 wt% PAN-0.02 wt% TEGO spheres (c) before and (d) after carbonization. |
After the carbonization process, both neat PAN and TEGO based PAN spheres shrink about 75%, and the diameters of PAN and TEGO based PAN spheres decrease down to nanometer scale and become 400 and 700 nm, respectively. Carbonization leads to the formation of more packed spheres having less porosity (Fig. 13b and d).
In another PAN sphere production, TEGO amount increased up to 0.05 wt% and polymer concentration decreased down to 3.5 wt% in order to investigate the changes in morphologies of spheres. By increasing TEGO content, the zero shear viscosity of electrospun solution is expected to increase which will require larger electric field strength to deform the droplet whereby the diameter of spheres gets bigger. Fig. 14 shows SEM images of 3.5 wt% PAN-0.05 wt% TEGO before and after carbonization. The average diameter of spheres before carbonization is about 6.5 μm. In Fig. 14b and c, one can immediately notice an interesting microstructure composed of two disjointed spheres which might have been formed due to phase separation because of high TEGO amount in electrospun solution. EDX results confirm that the average carbon wt% in outer sphere shell is about 71 whereas the inner sphere shell has 62% carbon. High carbon content in outer sphere and the wrinkles in Fig. 14b point to the high amount of graphene sheets and less polymer intercalation in the outer part of the structure. Consequently, TEGO starts phase separation after the complete diffusion of polymer chains through graphene layers and spheres are entwined together and isolated from each other. Moreover, since the inner layer should have smaller viscosity than the outer layer referring to the graphene content as measured by the EDX, during electrospraying process, the inner layer should be deformed much easier than the outer layer by the combined surface forces (i.e., electric and surface tension forces).
After heat treatment, TEGO based PAN spheres collapses totally and the boundaries on the surface of layers and the smooth surfaces are clearly seen in Fig. 14d. When compared to the results having high polymer concentration and low TEGO amount given in Fig. 13, the porosity of surfaces in Fig. 14 decreases significantly by increasing TEGO and reducing polymer concentration. These results confirmed the significance of solvent evaporation rate, solution viscosity, polymer concentration and TEGO amount on sphere morphology.
Raman spectra of TEGO and 5 wt% PAN-0.02 wt% TEGO spheres before and after carbonization are shown in Fig. 15a. In the Raman spectrum of carbonized TEGO based PAN spheres, two peaks appears: the peak at ∼1340 cm−1 related to D band of graphene and the peak around ∼1580 cm−1 attributed to G band. ID/IG ratio of carbonized spheres is approximately 0.9 higher than ID/IG ratio of TEGO as 0.2 which shows the growing of graphene-like structures and reordering of aromatic groups towards graphene networks at higher temperatures.46Fig. 15b shows FTIR spectra of TEGO and produced PAN spheres. In the FTIR spectrum of TEGO, there is no sharp peak since thermal exfoliation of GO removes most of the oxygen functional groups and the resultant material has high carbon content. Only a weak peak at around 1722 cm−1 appears which is assigned to carbonyl stretching of CO.47 PAN spheres show characteristic peaks at 2930 cm−1, 2250 cm−1, and 1450 cm−1 which are associated with C–H bonds in CH2, nitrile bond (CN), and tensile vibration of CH2, respectively.48 By the incorporation of TEGO into the structure, a sharp peak at 1720 cm−1 can be distinguished easily related to the stretching vibration from carbonyl group (CO) of TEGO. Thus, this confirms the presence of TEGO in the structure. After applying heat treatment, the reduction in peak intensities at 2930 cm−1 and 1450 cm−1 and the disappearance of the peak at 2250 cm−1 indicate the cyclization and dehydrogenation of TEGO based PAN spheres during carbonization process.
Footnote |
† Electronic supplementary information (ESI) available: The chemical structures of (a) PMMA, (b) PS, and (c) PAN polymers, table of electrospraying parameters of PS–TEGO, PMMA–TEGO, and PAN–TEGO spheres, table of positions and intensities of D, G, 2D peaks, ID/IG and IG/I2D values of untreated TEGO, sonicated and electrosprayed TEGO, table of Mark–Houwink–Sakurada constants for PMMA, PS, and PAN polymers at room temperature, table of XRD diffraction peak intensities and positions of TEGO based PMMA and PS based spheres, table of Raman peak intensities of PS and PS-0.02 wt% TEGO spheres, and SEM image of PMMA spheres containing 0.02 wt% TEGO using methanol as a core material with the flow rate of 5 μL min−1. See DOI: 10.1039/c5ra19581k |
This journal is © The Royal Society of Chemistry 2015 |