Research Article | Open Access
Pyry-Mikko Hannula, Minttu Junnila, Dawid Janas, Jari Aromaa, Olof Forsén, Mari Lundström, "Carbon Nanotube Fiber Pretreatments for Electrodeposition of Copper", Advances in Materials Science and Engineering, vol. 2018, Article ID 3071913, 8 pages, 2018. https://doi.org/10.1155/2018/3071913
Carbon Nanotube Fiber Pretreatments for Electrodeposition of Copper
There is increasing interest towards developing carbon nanotube-copper (CNT-Cu) composites due to potentially improved properties. Carbon nanotube macroscopic materials typically exhibit high resistivity, low electrochemical reactivity, and the presence of impurities, which impede its use as a substrate for electrochemical deposition of metals. In this research, different CNT fiber pretreatment methods, such as heat treatment, immersion in Watts bath, anodization, and exposure to boric acid (H3BO3), were investigated to improve the electrochemical response for copper deposition. It was shown that these treatments affect the surface activity of CNTs, including electrical resistivity, polarization resistance, and active surface area, which influence the electrodeposition process of copper. Properties of CNT structures and CNT-Cu composites were researched by electrochemical impedance spectroscopy (EIS), galvanostatic copper deposition, scanning electron microscope (SEM), and four-point electrical resistance measurements. Heat treatment, Watts bath, anodization, and boric acid treatments were shown to be effective for modifying the CNT surface reactivity for subsequent electrochemical deposition of copper.
The exceptional properties of carbon nanotubes (CNTs), such as stiffness, low density, high mechanical strength, and excellent electrical and thermal conductivity, have attracted researchers to utilize them in various structures. While individual nanotubes exhibit extraordinary properties, they are difficult to transfer to macroscopic CNT materials due to the existence of unoptimal contact junctions between nanotubes, warranting the research for composite structures. One particular class of such composites is based on carbon nanotubes surrounded by a copper matrix [1–3]. Low-density CNT composites with significantly increased conductivity, current-carrying capacity, and mechanical properties could revolutionize many different industry sectors with applications in electrical wiring, microelectronics, and power transfer [4–6]. Such composites can be formed by utilizing carbon nanotube wires, such as fibers or films, as the base material [7–10].
An important issue of producing CNT material on a large scale is that the manufacturing techniques generate many impurities and unwanted CNT types creating an inhomogeneous mixture of components. Undesirable impurities include, for example, soot, amorphous carbon, metal catalysts (such as Fe), carbon nanoparticles, and other unwanted particles. As made, CNT structures are typically improved by procedures that clean the CNT sidewalls of unwanted impurities and add additional reactivity by modification and introduction of new functionalities, such as oxygen-containing functional groups [11, 12]. Other methods include densifying the CNT material, either by organic solvents  or mechanical application , effectively bridging the distance between individual nanotubes to decrease contact resistances. Doping with halogen gases and organic and ionic species have also been explored to alter the carrier density, and thus electrical resistance and activity of CNT material . Modification or purification of CNT base material is routinely applied before producing composite structures [16–19].
Previously, Xu et al.  reported using anodization as a pretreatment method for producing functionalized CNT-Cu composites. The method combined continuous fiber spinning from CNT array, fiber anodization, and finally copper deposition. The anodized CNT surfaces were shown to exhibit stronger bonding with the deposited copper compared to unanodized surfaces due to the effect of functional groups. CNT fiber coated with 1 μm copper cladding after anodization resulted in a strength of about 800 MPa, whereas without anodization, the corresponding value was 611 MPa. Additionally, the conductivity of anodized CNT composite was shown to be almost four times higher. However, the effect of anodization on the electrochemical polarization of the CNT fiber was not described.
Electrochemical impedance spectroscopy (EIS) has not been conventionally applied for CNT research. However, it allows for the investigation of CNT material electrochemical properties. Properties, which affect the electrochemical reactivity, such as electrical resistivity, polarization resistance, and surface area can be compared by EIS investigation. It is important to compare these properties as pretreatment modification of CNT fiber structures is likely to affect many properties simultaneously.
The aim of this study was to investigate pretreatment methods, which can be used to positively affect the electrochemical activity of CNT material before electrochemical deposition of copper. Carbon nanotube-copper composites were also produced, and their microstructure and specific conductivity were described.
2. Materials and Methods
2.1. CNT Materials
Different lengths (10–350 mm) of CNT fibers and yarns were used. Diameter of fibers was 10 µm, while yarns were 150–200 µm in diameter. CNT material consists mainly of multiwalled carbon nanotubes (MWCNTs) with a small percentage of double-walled (DWCNTs) and single-walled carbon nanotubes (SWCNTs). Yarn samples consist of a plethora of fibers rolled together and treated with acetone to densify and bundle them together to form yarns . The CNT samples were produced by dry spinning directly from a CVD reactor. Pristine CNT materials were unfunctionalized and contained approximately 15% of carbonaceous impurities and catalyst metals .
Macroscopic objects made of CNTs have very low weight (a fiber sample 2 cm in length weighs less than 10 µg), and so it is a challenging sample material to work with, easily floating or breaking. The tests were conducted by using sample holders, and the schematics are presented in Figure 1. The PVC sample holder (a) was made by gluing a copper wire to the plastic holder, and the glass-plate sample holder (b) was made with conductive Foil Shielding Tape no. 1183 (resistance 0.005 Ω) manufactured by 3 M on the glass plate. The electrical contact to the fiber in both sample holders was made with conductive silver paste (42469, Alfa Aesar).
Table 1 shows the employed bath compositions. Copper sulfate bath was used to electrodeposit fibers with copper. Watts bath is typically used to electrodeposit nickel, but here it was used without applied current or voltage, that is, as an immersion bath for Ni and B doping. Anodizing bath was used to electrooxidize the CNT material by anodization. Boric acid bath contains equal concentration of boric acid compared to Watts bath, in order to observe changes in CNT material by just boric acid application method. All chemicals used were of pro-analysis grade. Solutions were made in distilled water.
2.3. Electrochemical Cell Setup
Electrochemical tests were carried out using ACM Instruments Gill AC potentiostat with Gill AC Sequencer software. A standard three-electrode cell was used (Figure 2). The reference electrode was a calomel electrode (SCE, Radiometer 401) placed close to the CNT sample using a protective Schott tube with Pt frit (Schott B281). The anode was a copper electrode made of 0.5 mm thick sheet. In anodization, the counter electrode was an inert platinum electrode.
EIS tests were carried out in copper sulfate bath before and after different treatments in order to observe changes in CNT materials. The behavior of single CNT fibers were tested as CNT fiber material is inhomogeneous and by using this method the change in properties could be reliably measured. First, the EIS measurement of a single CNT fiber was conducted in copper sulfate solution. Then, the sample was rinsed with copious amounts of water to remove electrolyte from the surface. The sample was then immersed in the studied bath or heat treated for designated time. Afterwards, the sample was lightly rinsed with deionized water by dipping into deionized water. EIS measurement was then performed again in copper sulfate solution. Thus, the effect of different treatments on the properties of a single CNT fiber in copper sulfate electrolyte could be compared pre- and posttreatments.
Electrochemical impedance spectroscopy results were presented as Bode plots. Polarization resistance, solution resistance, and capacitance were calculated with the relative change of results. Results can be compared as EIS measurements do not disturb the sample composition or properties. Solution resistance (RΩ) was determined at high frequency (100,000 Hz). Polarization resistance (Rp) was determined from the difference between impedance at high (100,000 Hz) and low frequency (0.01 Hz). Capacitance (Cdl) was calculated using the following equation :where ωmax is the angular speed corresponding to phase angle maximum, Rp is the polarization resistance, and RΩ is the solution resistance.
2.5. CNT Material Pretreatment Methods
Heat treatment, Watts nickel bath, anodization, and boric acid treatment were investigated as potential CNT fiber activation methods. Treatment methods and parameters are listed in Table 2. The heat treatment (treatment no. 1) was carried out in furnace under oxygen flow, samples 2–6 were immersed completely in the selected solutions. In the anodization test (no. 6), CNT fiber sample was immersed in 10 wt.% H2SO4 solution and anodized at 2500 mV versus SCE for 50 s.
2.6. Copper Deposition
Carbon nanotube fibers were electrodeposited with copper in order to estimate the kinetics of the reaction. The electrical resistance of samples was measured by four-point electrical resistance measurement (Fluke 8846a Multimeter). Copper cladding growth rates were determined as a function of current, sample length, deposition time, and copper cladding length.
3. Results and Discussion
3.1. Effect of CNT Pretreatment Methods
CNT materials behave as inhomogeneous resistive substrates rather than metallic substrates and exhibited significant terminal effect. The analysis by Alkire and Varjian  and Matlosz et al.  shows that the electrochemical copper deposition overpotentials change along electrically resistive wires. Closest to the current feed point, the activation polarization and ohmic resistance polarization are the strongest. As the distance along the wire increases, the effect of substrate resistance becomes larger causing the activation and electrolyte ohmic polarization to decrease. After a certain distance, the driving force of the deposition, that is, the activation overpotential, becomes too small to support deposition. This effect is decreased during electrodeposition, when the growing metal on the surface of the substrate provides additional conductivity and thus the deposition can progress further. Thus, the copper growth on CNT fibers progresses further from close to the electrical contact as the deposition is continued. Improving the conductivity and activity of the substrate through pretreatments is expected to increase this deposition speed. The effect of different pretreatment methods on these surface properties were studied using electrochemical impedance spectroscopy (EIS). Table 3 shows the relative changes in the CNT fiber polarization resistance, solution resistance, and capacitance based on EIS results after different treatments.
The following reasoning was used to analyze the results: The polarization resistance is a measure of the CNT surface that supports charge-transfer reaction for copper deposition. The ohmic resistance describes sample resistivity, but it includes both the sample resistance and the uncompensated solution resistance. The uncompensated resistance was not considered significant because of concentrated test solutions, small distance between reference electrode and sample, and small applied currents. The measured capacitance results from the adsorbed species in the electrochemical double layer. The capacitance was considered to describe the electrochemically active area. Changes in the measured capacitance can result from a variety of causes, which change the surface area of CNT fibers.
Relative resistance change ∆Rp < 1 indicates improved CNT surface activity, and relative ohmic resistance ∆RΩ < 1 indicates improved conductivity, whereas values above 1 for ∆Rp and ∆RΩ indicate impaired properties. If relative value of Cdl was <1, the active area was reduced and if Cdl was >1, the active area had increased. The typical double layer capacitance of metals and CNT in electrolyte is about the same, about 10–50 mF/cm2, and the capacitance value can be used as a measure of electrochemically active area [23, 24]. As the polarization resistance (Ω·cm2) and capacitance (F/cm2) have opposite relation to surface area, the relative changes can be used to estimate if the changes result from surface activation or surface area changes.
From Table 3, it can be observed that the heat treatment strongly affects both the polarization resistance and solution resistance of the sample (sample 1). This indicates the positive effect of heat treatment on CNT surface activity and conductivity. This result is attributed to the small amount of functional groups generated during mild heat treatment at low temperatures and the removal of less-conductive amorphous carbon particles. The decrease in capacitance indicates decreased active area, possibly due to removal of large impurity particles. The decrease in both polarization resistance and capacitance indicates that while the total surface area was decreased, the surface was more active due to the decrease in resistance and addition of oxygen-containing functional groups.
The purpose of the immersion in the Watts bath was to dope the CNT material surface with Ni and B. The effect of Watts bath treatment was shown to activate CNT surface significantly (samples 2, 3 and 4), similarly to heat treatment. The Bode plot of EIS before and after Watts bath immersion for fiber sample 3 is shown in Figure 3. After 60-minute immersion in Ni- and B-containing bath, the ohmic resistance decreased to 16% of the original value indicating improved conductivity of CNTs as noted previously for CNTs and graphene [25–27]. The decrease in polarization resistance indicates activation of the CNT fiber surface by providing more electrochemically active sites. The capacitance decreased, indicating a decrease of active surface area. The immersion time also had an effect; during longer times, the fiber was doped more heavily, leading to more pronounced decrease in ohmic resistance and polarization resistance. This result is further confirmed by rinsing the sample with copious amounts of water after immersion in Watts bath (sample 4), which then produced much smaller effect. This result stems from the removal of activity and conductivity increasing dopants. The improved electrochemical response of CNT fibers immersed in Watts bath before electrodeposition is also shown later by galvanostatic copper deposition tests (Figure 7).
EIS for sample 5 before and after boric acid immersion is shown in Figure 4. This test was conducted to observe the changes made by B doping only. In our case, the resistivity of CNT fiber was only slightly decreased after B doping due to the small immersion time and low concentration of boric acid. However, the impedance and phase angle were reduced and polarization resistance decreased significantly after boric acid treatment. Analogous to our work, CNTs doped with boron have shown increased electrochemical activity for oxygen reduction reaction . Based on the pretreatment results by Watts bath and boric acid, it can be concluded that both Ni and B doping showed an improvement in increasing the electrochemical reactivity of CNT material. Doping with both elements simultaneously and for longer times (until 72 h) gave the best results.
Anodization at 2.5 V versus SCE is a highly oxidizing procedure that strongly affects the surface structure of nanotube material, sample 6. Strong anodization introduced oxygen-containing functional groups at the CNT material surface, which then reduced the charge-transfer resistance of the CNT fiber . At the same time, the sample resistance increased as the anodization process was so severe that the mean free path of electrons was decreased due to deterioration of nanotube sidewalls . Finally, the active surface area of the fiber increased considerably likely due to the decrease in hydrophobicity by large additions of functional groups.
3.2. Electrochemical Deposition for CNT-Cu Production
CNT-Cu composite samples were produced by electrodeposition on CNT yarns in copper sulfate electrolyte (Figure 5). Samples were produced up to 30 centimeters in length with a typical diameter of approximately 150 µm. Density of produced composite samples varied from 3.0 to 6.5 g/cm3, increasing with the amount of copper deposited. Samples in Figures 5(b) and 5(c) were fractured by bending to observe the composite wire insides. The surface of yarns was covered by a continuous copper cladding, while copper also penetrated inside the CNT material (Figure 5(c)).
The specific electrical conductivities of produced composite samples are shown in Figure 6. Specific conductivities normalized by the sample weight were used as the cross-sectional area of CNT material and resulting composite are never uniform. The specific conductivity of pristine CNT yarns is also shown for comparison (data point at 100 wt.% CNT). The specific conductivity of CNT-Cu composites strongly increases with the amount of copper. The conductivity is increased approximately tenfold when comparing 5 wt.% CNTs to the pure CNT yarn. The results are in line with the previously published values of CNT-Cu wires [7, 9,10] The specific conductivity reported here decreases less as the weight percentage of CNTs increases compared with thinner fibers . This result is attributed to the difficulty of depositing continuous copper layers inside thick and dense yarn matrices. Thus, in comparison, more copper is deposited as a continuous cladding on top of the yarn surface leading to an improvement in the electrical conductivity.
Finally, galvanostatic deposition tests were performed on carbon nanotube fibers. Due to the previously mentioned terminal effect causing the localized plating phenomenon on CNT fibers, the plating speed could be determined. Deposition speed rate is calculated from optical microscopy inspection of deposit length after deposition test. First, CNT fibers were deposited at varying applied current to observe the plating kinetics of nonmodified materials. Then, the fiber samples were pretreated by immersion in Watts bath for 60 minutes before copper deposition. This test was conducted twice to confirm the effect of Watts bath. The plating rate results are shown in Figure 7. It was observed that the highest coating rates were for samples immersed in Watts bath, confirming the results from EIS measurements. At the same applied potential, the deposition speed was approximately five times higher for Watts bath–pretreated samples. The deposition speed was higher at over 10 times less applied current, exhibiting the powerful effect of Ni and B doping provided by the Watts bath immersion. Similar copper deposition enhancement has been shown for oxygen-functionalized CNT materials elsewhere .
In conclusion, we studied improving the electrochemical deposition of copper on CNT fibers by various treatments. These treatments changed the conductivity, polarization resistance, and active surface area of the samples. The copper deposition rate was enhanced considerably by Ni and B doping from Watts bath without the need for harsh treatments, such as oxidation, that are known to deteriorate the nanotube properties . Previously, similar improvements in enhancing the copper deposition rate on CNT macrostructures have been attained by utilizing harsh oxidation as a pretreatment method [7, 16]. In this case, we used a “soft” doping method, which had a positive effect on the CNT material conductivity. The specific conductivity of thick CNT-Cu yarn composites (90% of Cu at ca. 5 wt.% CNTs) decreased less than previously shown  thinner CNT-Cu fibers (50% of Cu at ca. 5 wt.% CNTs), likely due to less penetration of copper inside the thick CNT matrix.
Carbon nanotube (CNT) fibers were pretreated by various solutions and oxidative treatments. These treatments were shown to change the electrochemical response of CNT fibers for copper deposition. Surface properties of CNT fibers were characterized by electrochemical impedance spectroscopy (EIS) to observe changes in polarization resistance, ohmic resistance, and capacitance. The deposition rates of pristine and Watts bath–immersed samples were compared by galvanostatic copper deposition and it was found that the deposition rate increased drastically with pretreatment in Watts bath as predicted by EIS measurements. The specific electrical conductivity of carbon nanotube-copper composite samples with various CNT wt.% were reported. The highest specific conductivity was found to be at 87 wt.% of copper at 4.7 wt.% of CNTs. The results show that the pretreatments can be used to tune the electrochemical response of CNT fibers for copper deposition. Simple immersion in Watts bath before deposition was shown to increase the deposition rate on CNT fibers by approximately fivefold. The study demonstrated that with careful optimization, it is possible to obtain CNT-Cu composites at a high rate. As indicated by the literature, such materials (Cu reinforced with nanocarbon) could show improved electrical, thermal, or mechanical properties as compared with pure copper. Further experiments are under way to determine it.
Conflicts of Interest
The authors declare that they have no conflicts of interest.
This work has been supported by the FP7 FundRef identification ID: European project Ultrawire (Grant Agreement 609057) and by the Finnish Academy NoWaste project FundRef identification ID: (Grant Agreement 297962). RawMatTERS Finland Infrastructure (RAMI) supported by the Academy of Finland is greatly acknowledged. Dawid Janas would like to thank the National Science Center, Poland (under the Polonez program, Grant Agreement UMO-2015/19/P/ST5/03799) and the European Union’s Horizon 2020 Research and Innovation Programme (Marie Sklodowska-Curie Grant Agreement 665778). Dawid Janas would also like to acknowledge Foundation for Polish Science for START scholarship (START 025.2017) and the Silesian University of Technology in Gliwice for funding the research in the framework of habilitation grant (04/020/RGH17/0050).
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