Abstract
In this paper, the 3D pore structure of CuCr powders were obtained by pre-press shaping process, and finally the 3D interconnected carbon nanotubes/copper (CNTs/Cu) composites with excellent properties were insitu synthesized by chemical vapor deposition (CVD) and spark plasma sintering (SPS) technique. The morphology and structure of CNTs/ Cu composites are characterized by scanning electron microscopy (SEM), Raman spectra, transmission electron microscopy (TEM), X-ray diffraction (XRD) and X-ray photoelectron spectroscopy (XPS), and the results showed that the quality of CNTs and the interfacial bonding strength of CNTs/ Cu composites can be improved owing to the 3D pore structure. Meanwhile, the 3D pore structure was favorable to avoid pollution of CNTs during the synthesis process. The tensile strength of CNTs/ Cu composites increased to 421.2 MPa, with 47.6% enhancements compared to CuCr. Furthermore, the coefficient of friction (COF) reduced to 0.22 and the corrosion resistance were increased by 51.86% compared to CuCr. Consequently, our research provides a novel and an effective method for the synthesis of high quality CNTs/ Cu composites.
1 Introduction
CNTs/Cu composites have attracted increasing attention in the aerospace and ground transportation because of their excellent properties in many aspects, such as super mechanical strength and high electrical conductivity [1, 2, 3]. The key techniques of the synthesized CNTs/Cu composites mainly include the uniform dispersion of CNTs in the Cu matrix and good interfacial bonding, which can exert the full potential of CNTs as a reinforcement in the Cu matrix [4, 5, 6, 7]. The existing reports for the CNTs/ Cu composites focused mainly on electrochemical deposition [8], powder metallurgy [9], fusion casting [10] and stirring casting [11]. Walid et al. [12] investigated the mechanical properties of CNTs/Cu composites prepared by electroless deposition and spark plasma sintering (SPS), and the electrical conductivity reached 72%IACS, the Vickers hardness achieved 108 HV, as well as 341.2 MPa for yield strength. Shukla et al. [13] investigated the tensile strength of CNTs/ Cu composites prepared via mechanical alloying and hot pressing sintering, the results showed that the tensile strength of CNTs/Cu composites reached 330 MPa. However, the above-stated method cannot be achieved the uniform dispersion of CNTs in the Cu matrix and the good interfacial bonding between the CNTs and Cu, which will result in the failure of realization of CNTs as a reinforcement [14, 15, 16]. Therefore, it is necessary to investigate a novel method to disperse CNTs uniformly in the Cu matrix, and to improve the interfacial bonding between CNTs and Cu matrix.
In this paper, a new idea of combining pre-compression with CVD to achieve the in-situ grown CNTs in the voids of pre-compressed 3D interpenetrating CuCr alloy powders to form 3D interconnected CNTs/Cu composited was first proposed and realized. The method firstly pre-compacted CuCr alloy powders at a pressure of 50 MPa at room temperature to form the CuCr pre-compacted bulk with 3D pore structure, and secondly synthesized CNTs on the CuCr pre-compacted bulk by CVD, and finally formed CNTs/ Cu composites by SPS [17]. The method of pre-compacting into bulk materials not only avoids the instability of the atmosphere in the process of directly synthesizing CNTs and uneven dispersion of CNTs as well as the problem of easy-contaminated, but also significantly improves the interfacial bonding of the composites. In addition, CVD avoids the structural damage and contamination of CNTs under the high-energy and high-temperature generated by the conventional external addition method, and achieves the uniform dispersion and in-situ growth of the CNTs in the copper matrix [18, 19, 20]. The combination of the pre-compacting and CVD provides excellent 3D interconnected CNTs/ Cu composites, which provides a new and effective way for the preparation of high performance copper-based composites.
2 Experiment
2.1 Preparation of 3D interconnected CNTs/Cu pre-compressed bulk
Firstly, 15g CuCr (200 mesh, Shanghai Sinopharm Chemical Reagent Co., Ltd, 0.6 wt% Cr) alloy powders were taken a tube furnace for solution-aging treatment to achieve the homogeneous precipitation of catalyst Cr particles. Then the CuCr alloy powders were pre-compacted at room temperature, and the pressure was 50MPa. Then a CuCr pre-compressed bulk was formed, which had 3D void structure of 30 mm in diameter and 3 mm in height. Then CNTs/ Cu pre-compacted bulk was obtained at 800∘C for 60 min.
2.2 Preparation of 3D interconnected CNTs/Cu composites
The 3D interconnected CNTs/ Cu pre-compacted bulk was loaded into a graphite mold (inner diameter ø30 mm) and sintered in a spark plasma sintering furnace to get the 3D interconnected CNTs/Cu composites. The heating rate was 100∘C/ min, the sintering pressure was 30 MPa, the sintering temperature was 900∘C, and the sintering time was 10 min. The experimental process is shown in Figure 1. Finally, the composites were hot rolled (850∘C, 60% deformation) to increase its relative density.
Schematic illustration of the preparation process of 3D interconnected CNTs/Cu composites
2.3 Characterization
The morphology of the materials was characterized by scanning electron microscopy (SEM, QUANTA FEG 450). The graphite-amorphous carbon features of CNTs in the composites were characterized by Raman spectroscopy (Raman Station 400F) with a wavelength of 532 nm. Elemental composition and chemical bonds were characterized by X-ray photoelectron spectroscopy (Thermo ES-CALAB 250). The tensile strength, hardness and electrical conductivity of the composites were tested using a Zwick precision line vario, a microhardness tester (HX-1000TM/LCD) and a digital metal conductivity tester (D60K). The density of the composites was measured by the Archimedes drainage method. The corrosion resistance and tribological properties of the composites were investigated using a friction wear machine (HIIT-2II) and an electrochemical workstation (CHI 660D, CHI 1140C), respectively.
3 Results and discussion
3.1 Microstructural characterization of the 3D interconnected CNTs/Cu composites
Figure 2 shows the surface and internal morphology of the 3D CNTs/Cu bulk materials. Figure 2a and the inset a1 show that the number of CNTs on the surface of the 3D pore structure is small. The average outer diameter of the CNTs is 20-40 nm, the length is about 1400 nm. But the distribution is uneven, and there are more defects. The reasons are that C2H4 and H2 flow through the surface of the substrate directly and quickly, leading to the CVD reaction incompletely and formation of impurities such as amorphous carbon easily. What’s worse, it is more susceptible to be contaminated due to a large exposed surface area. From Figure 2b and the inset b1, we can see that the CNTs are evenly distributed in the bulk. In addition, the walls of CNTs are clean, and there are no defects and amorphous carbon. The average outer diameter of the CNTs is 20-30 nm and the length is increased to about 1800 nm. This is because the gas flow in the 3D porous structure is relatively stable, and the reaction is relatively sufficient. Furthermore, the interior is not easily contaminated, so the matrix is clean. The average gap of the adjacent copper powder in the pre-compressed bulk is 712 nm, that is, the porosity is 71.81%. But the porosity of the pre-compressed bulk reduced to 66.43% after the in-situ synthesis of CNTs. The CNTs connected to the matrix to realize the cross-link of Cu and CNTs as well as CNTs and CNTs. At the same time, the pre-compression form will have a copper-copper connection, so the three kinds of connections are evenly distributed to form a 3D interconnected network structure.
(a) SEM image of the 3D CNTs/Cu surface morphology (b) SEM image of the 3D CNTs/Cu internal morphology (c) Percentage of CNTs of different diameters
Figure 3 shows the Raman spectrum of the surface and interior of 3D interconnected CNTs/Cu composites. The synthesis environment of surface CNTs is similar to the direct synthesis one. The peak ratio (ID/IG) of the D peak near 1347.39 cm−1 and the G peak near 1593.01 cm−1 is 1.017, indicating the CNTs having more amorphous structures and defects. But for the internal materials, due to the existence of 3D pores, the synthesis environment of CNTs is relatively stable, and the peak ratio (ID/IG) of the generated CNTs is significantly reduced to 0.941. The defects density of CNTs is reduced and the degree of graphitization is enhanced [21, 22, 23, 24]. It indicates that pre-compacted to the 3D porous structure to grow carbon nanotubes can effectively suppress the formation of amorphous carbon, thereby improving the purity of CNTs.
Raman spectrum of surface and interior of CNTs/Cu composites
In order to study the microstructure of 3D CNTs/Cu composites, XRD and XPS tests were performed. Figure 4a shows the XRD pattern of the 3D CNTs/Cu composites and CuCr. The composites exhibited only three characteristic peaks corresponding to Cu (PDF No. 851, 326), and showed no peaks of CNTs and Cr. The possible reason is that the strong diffraction peaks of Cu covered the signals of CNTs and Cr. Except for the copper peak, no other peaks were found, indicating the good chemical stability between copper matrix and carbon nanotubes [20].
(a) XRD patterns of the 3D interconnected CNTs/Cu composites and CuCr (b) XPS wide scan of the 3D interconnected CNTs/Cu composites and CuCr (c) Cu 2p XPS map of the 3D interconnected CNTs/Cu composites (d) C 1s XPS map of the 3D interconnected CNTs/Cu composites
XPS test was performed to study the chemical composition and oxidation state of the 3D interconnected CNTs/Cu composites. Figure 4b shows the main elemental composition and the content of two samples. Figure 4c shows the XPS core level Cu2p spectrum of two composite powders with two Cu peaks with binding energies of 952.3 eV and 932.6 eV, respectively, corresponding to Cu2p1/2 and Cu 2p3/2 [25]. There are also satellite peaks in the Cu2p spectrum, declaring that the presence of a small amount of CuO in the composites due to surface exposure of the 3D surface structure leading to slight oxidation of the copper matrix [26]. Figure 4d shows the C 1s spectrum of the sample. In order to study the structure of the CNTs, the fitted peaks in the linear are attributed to sp2 hybridization and sp3 hybridized carbon, respectively [27]. It is clear that the percentage of sp2 hybrid carbon sample is higher, which means it has a higher degree of graphitization and fewer CNTs lattice defects [28]. This confirms that pre-compressing the alloy powders into a 3D loose and porous structure firstly, and then in-situ growing carbon nanotubes to form a 3D interconnected composites is beneficial to the growth of CNTs and contributes to the improving the properties of the materials.
The interfacial bonding between carbon nanotubes and copper matrix and the one between copper and copper have a significant effect on the properties of composites. HRTEM was used to study the interfacial bonding of the 3D interconnected CNTs/Cu composites. Figure 5 is the TEM images of the interface for 3D interconnected CNTs/ Cu composites. Figure 5a shows that the CNTs are uniformly dispersed in the Cu matrix and the CNTs are not aggregated and the tube walls are clean. Figure 5b is a high-magnification TEM image of the interface between CNTs and Cu. The CNTs are tightly bound to the Cu matrix, with no obvious physical gaps and no intermediate compounds [29, 30, 31]. This result indicates that the good interfacial bonding between CNTs and Cu are well retained in the 3D interconnected structure. At the same time, the interface between copper and copper is very good, and a large amount of mutual diffusion occurs among the copper atoms, the atomic level bonding is achieved at the interface. The combination of the interface greatly improves the strength of the matrix, and eliminates the disadvantage of the weak interfacial bonding between copper and copper as well as the unrealizable atomic level bonding prepared by the conventional method, thereby the tensile strength of the composites is improved.
(a) TEM topography of 3D interconnected CNTs/Cu composites (b) HRTEM morphology of the 3D interconnected CNTs/Cu composites
3.2 Performance of the 3D interconnected CNTs/Cu composites
Figure 6 shows the tensile stress-strain curve after rolling of the 3D interconnected CNTs/Cu composites. For comparison, the tensile stress-strain curve of CuCr was also tested. The yield strength, elongation, hardness and relative density are summarized in Table 1. The average yield strength of CuCr is 285.4 MPa, and the elongation is about 21.7%, which is plastic fracture. The elongation of the 3D interconnected CNTs/Cu composites decreased from 21.7% to 17.9% compared with CuCr, but its strength and hardness were greatly improved, and the tensile strength was 47.6% higher than that of CuCr. There are two main reasons for this. One is the in-situ synthesized carbon nanotubes act as the reinforced phase, which further improves the tensile strength and hardness. The other one is that CNTs and CNTs, CNTs and copper, copper and copper are interconnected, forming 3D network structure, which increases the resistance to dislocation motion, and reduces the peeling speed and slows the destruction rate of materials. Mean-while, the strengthening and toughening effect of carbon nanotubes hinders the extension of cracks [32].
Tensile stress-strain curve of the 3D interconnected CNTs/Cu composites and CuCr after rolling
Properties of the 3D interconnected CNTs/Cu composites and CuCr
| Sample | Tensile Strength | Starin | Vickers Hardness | Relative density (%) | Conductiviy (%IACS) |
|---|---|---|---|---|---|
| (MPa) | (%) | (HV) | |||
| CuCr | 285.4 | 21.7 | 122.2 | 99.2 | 85.7 |
| CNTs/Cu | 421.2 | 17.9 | 130.2 | 98.9 | 84.6 |
The conductivity of the 3D interconnected CNTs/ Cu composites and CuCr was measured by eddy current method. The results are shown in Table 1. The conductivity of CNTs/ Cu (85.7%) decreased only slightly compared to CuCr (84.6% IACS). The slight decrease in conductivity mainly caused by two reasons. First, the mean free path (MFP) of the charge carriers is reduced due to the reduction in matrix particle size and the increase in dislocation density [33]. Second, the voids formed during the sintering process become an insulating barrier for the current [34]. However, the conductivity decreases little and is negligible in this study. The prepared CNTs/Cu composites are still highly conductive materials. This is because the method of pre-pressurizing then growth CNTs is adopted, which can effectively reduce the voids in the final materials and increase the density of the materials. At the same time, the structural features of the interconnected structure and the copper-copper combination are more conducive to current transfer.
Carbon nanotubes are considered to be a new type of solid lubricant in previous studies [35, 36, 37]. Figure 7 shows the SEM images of the wear surface for the 3D interconnected CNTs/Cu composites and CuCr. The relative friction pair is stainless steel ball. The load is 10 N and the sliding speed is 0.03 m/s. The CuCr has a large wear width, and the surface has obvious plastic deformation marks and obvious furrows and sticking pits, and a large piece of debris is peeled off. The wear surface of the 3D interconnected CNTs/Cu composites is improved compared with CuCr, and the lamellar cracking phenomenon was greatly reduced. The wear width was reduced from 965 μm to 836 μm, so the wear resistance was significantly improved. The coefficient of friction (COF) and wear of the two materials are summarized in Table 2. The 3D interconnected CNTs/Cu composites exhibited better anti-friction properties (COF ≈ 0.22) compared the COF for Cu is 0.55. What’s more, the wear loss was reduced from 1.9mg for CuCr to 0.8 mg for 3D interconnected CNTs/ Cu composites. This is because that the distribution of the CNTs in the 3D interconnected structure is more uniform and the material has higher relative density. CNTs plays a self-lubricating role in the matrix during the friction and wear process, some protective films are formed on the worn surface, which reduces the friction coefficient of the composites [38]. At the same time, the interconnected 3D structure hinders the wear and tear of the material during the rubbing process.
Low-magnification SEM image of friction and wear surface for CuCr (a) and 3D interconnected CNTs/Cu (c); High-magnification SEM image of friction and wear surface for CuCr (b) and 3D interconnected CNTs/Cu (d)
Friction and wear properties of 3D interconnected CNTs/Cu composites and CuCr
| Sample | Friction coefficient | Wear loss (mg) |
|---|---|---|
| CuCr | 0.51 | 1.9 |
| CNTs/Cu | 0.22 | 0.8 |
Figure 8 is the Tafel curve for 3D interconnected CNTs/Cu composites and CuCr (the area is 1 cm2) in a 3.5 wt% NaCl solution. In general, the more positive the self-corrosion potential and the lower the self-corrosion current density, indicting the better corrosion resistance of the material [39, 40]. Compared to CuCr, the polarization curve (Ecoor) of the 3D interconnected CNTs/Cu composites exhibits a considerable positive shift, showing better corrosion resistance. The corrosion current density (Icoor) of CNTs/ Cu composites is significantly lower than that of CuCr, which indicates that the existence of 3D interconnected structures and the addition of CNTs have a significant effect on slowing down the corrosion process.
Tafel curve of CNTs/Cu composites and CuCr in 3.5wt.% NaCl solution
The protection efficiency (PE) is calculated from the measured Icorr value and equation (1) [41, 42]:
In addition, the corrosion rate (CR) can be estimated from the corrosion current value according to the standard equation (equation (2)) [43].
In the equation, z is the valence, equal to 2, ρ is the density of materilas, equal to 8.97 g/cm3, K is the corrosion rate constant, equal to 3.27×10−3 mm·g /(μA·cm·year),Mis the atomic weight, equal to 63.5.
The electrochemical parameters obtained from the polarization curves are shown in Table 3. It can be seen from the results that the corrosion resistance of CNTs/Cu composites is much higher than that of CuCr. This is because the structure of the CNTs/Cu composites is better, and the CNTs is cleaner and more uniformly dispersed in the matrix. This work promoted a corrosion rate reduction of 51.86%, greatly improving corrosion resistance.
Corrosion parameters of CNTs/Cu composites and CuCr in 3.5wt.% NaCl solution
| Sample | Ecorr (V) | Icorr | CR | PE (%) |
|---|---|---|---|---|
| (μA/cm2) | (mm/year) | |||
| CuCr | −0.39 | 20.99 | 0.243 | - |
| CNTs/Cu | −0.36 | 10.13 | 0.117 | 51.86% |
4 Conclusion
3D interconnected CNTs/Cu composites were prepared by pre-compressing CuCr alloy powders into 3D pore structure by CVD and SPS. This method provides a stable environment for the growth of carbon nanotubes and improves the quality and distribution of CNTs. At the same time, the 3D interconnected composites prepared by the method exhibits excellent performance in terms of strength and corrosion resistance, and meanwhile the problem of decreased conductivity caused by the addition of carbon nanotubes was solved. Presented work provides a new and an effective way to prepare copper-based composites with excellent mechanical properties and high electrical conductivity.
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