Carbon nanotubes (CNTs), since the moment of discovery (Iijima 1991), have enjoyed the attention of scientists, because they demonstrate unique mechanical (Gonnet et al. 2006), thermal (Berber et al. 2000; Fujii et al. 2005; Kumanek and Janas 2019) and electrical (Chen et al. 2008; Brady et al. 2016; Friedman et al. 2017) properties. They may have metallic and semiconductor properties (McEuen et al. 2002) depending on the particular way the carbon atoms are arranged at the nanoscale. This means that the geometry of nanotubes, in particular their internal structure, affects their thermal and electrical conductivity. Individual CNTs are characterized by the carrier mobility of up to 10,000 cm2/V s at 50 K (Zhou et al. 2005) which is much higher than in the case of silicon, and the electrical current density of up to 4 × 109 A/cm2 (Javey et al. 2004), which is better than the properties of a typical metal such as copper or aluminum by as much as three orders of magnitude (Hong and Myung 2007). Due to their properties, CNTs are applied as very sensitive electrochemical sensors (Gao et al. 2012), biosensors (Wang 2005), batteries (Landi et al. 2009), energy devices (Blackburn et al. 2018), transparent conductors (Wu et al. 2004) and others (Blackburn et al. 2018).

All the time, there is a growing demand for semiconductors or conductors with improved electrical properties, and so, given their characteristics, it is not surprising that nanocarbon materials are envisioned as one of the most promising candidates on this front. What is even more beneficial is that rich chemistry of carbon enables one to tweak their electrical properties with ease. One of the simplest methods of doing so is introduction of a dopant in onto the surface of a CNT or into the structure. The dopant affects the distribution of the electron charge of the nanotube when it is physically or chemically bonded with it, which directly affects its Fermi level. Doping may be conducted using encapsulation (Fukumaru et al. 2015), via modification of crystal structure of carbon nanotubes by heteroatoms (Liu et al. 2016b) or by exposure of the surface of carbon nanotubes to the doping agents (Janas et al. 2013b, 2014; Tonkikh et al. 2015; Zhao et al. 2011; Lee et al. 1997). The injected heteroatom or compound could be classified as an electron-donor (n-type) or electron-acceptor (p-type). In the literature, halogens (Janas et al. 2014; Tonkikh et al. 2015; Zhao et al. 2011), interhalogens (Janas et al. 2017a) or strong acids (Janas et al. 2013b; Lee et al. 1997) are mainly used as p-type dopants and nitrogen compounds (Janas 2018) or alkali metals (Lee et al. 1997) as n-type dopants. To this day, one of the highest gain in electrical conductivity was obtained by doping carbon nanotubes with halogens to create cables exceeding specific electrical conductivity of metals (Zhao et al. 2011).

Modifications of CNT ensembles using halogen compounds may be conducted in different ways. One of the simple techniques involves exposing CNTs to chlorine, bromine or iodine vapours (Janas et al. 2014; Qiu et al. 2018). Another method is immersing CNTs in a solution containing halogen compounds such as: SOCl2 (Dettlaff-Weglikowska et al. 2005), I2 (Janas et al. 2014), PBr3 (Fanchini et al. 2007) or ICl (Janas et al. 2014). Finally, it can be realized by Hunsdiecker reaction with oxidized CNTs (Janas et al. 2014), which results in favorable chemical modification. These processes suffer many disadvantages, such as the requirement of large excess of halogen-bearing reagent, the necessity to employ harsh reaction conditions (which demands appropriate health and safety measures) or long processing times. Furthermore, handling gaseous halogens is problematic because these compounds are toxic, corrosive and demand challenging conditions to introduce these atoms into the structure of CNTs. Despite this restriction, halogen doping is an effective way of improving electrical conductivity of CNT films and iodine compounds play a special role in this field because of their strong action on the electrical properties of nanocarbon materials (Janas et al. 2014; Zhan et al. 2015). Therefore, the search for mild approaches how to bring iodine and carbon nanomaterials together is of great interest.

Recently, new reports about effective, mild and safe iodination procedures emerged for arenes (Espuña et al. 2004; Barluenga et al. 2007; Racys et al. 2016) and heterocycles (Barluenga et al. 1993; Hamri et al. 2012; Przypis and Walczak 2019). In this subject, hypervalent iodine reagents have been at the forefront of synthetic methodology developments in the past 20 years (Merritt and Olofsson 2009; Yoshimura and Zhdankin 2016). Multiple examples of iodonium salt usage in organic synthesis have been reported in recent literature (Barluenga et al. 1993; Espuña et al. 2004; Hamri et al. 2012; Borzenko et al. 2015; Racys et al. 2016; Iskra and Murphree 2017; Liu et al. 2017; Przypis and Walczak 2019). Aryliodonium and diaryliodonium salts play a special role in this field because they are air- and moisture stable and soluble in many organic solvents despite their reactive framework. The idea to use iodonium salt in the nanocarbon realm was recently explored by He and Swager (2016), who employed them for introduction of the aryl moiety into their structure mediated by sodium naphthalide. Herein, we present another facet of iodonium salts, which we successfully employed for modification of CNT electronic properties by iodine under mild conditions.

The research described by us constitutes an alternative pathway to the previously taken routes of halogen introduction into the CNT network and solve the drawbacks described above. For this purpose, we designed and synthesized three different iodonium salts: Barluenga’s reagent (bispyridineiodonium tetrafluoroborate, IPy2BF4), pyridine iodine monochloride (IPyCl) and diphenyliodonium chloride (DPIC) of various electronic and structural characteristics. Tailor-made iodine-bearing compounds were very successful in doping CNT films as compared with iodine monochloride, which we used as reference. Because of their high stability in the ambient and elimination of the common problem of desorption, evaporation or sublimation of halogen species from the doped material, these compounds appear as very attractive agents to tailor the electronic properties of nanocarbon materials.


Doping of SWCNT films with iodonium salts

Thin free-standing CNTs films were obtained using a method reported previously by us (Janas et al. 2017b) from high-quality single-walled carbon nanotubes (SWCNTs; Tuball™) purchased from OCSiAl. In brief, this method involved dispersing nanocarbon material in an acetone/toluene mixture assisted by the presence of ethyl cellulose (EC). After sonication, during which the mixture reached uniform dispersion, it was gradually placed in the form of several layers on Kapton foil. After evaporation of the whole solvent, the dry film, which formed on the substrate, was delicately peeled off. Then, the CNT film was cleaned of EC by rapid thermal annealing (Janas and Stando 2017). The obtained CNT film was immersed in 0.1-M solution of selected iodonium salt in CH2Cl2 for 60 s, and then placed in a vacuum desiccator to evaporate the solvent. Information about the method of synthesis of iodonium salts can be found in the included Supplementary Information file. Figure 1 depicts the structure of the doping agents obtained for the study.

Fig. 1
figure 1

Structure of iodonium salts: diphenyliodonium chloride (DPIC), bispyridine iodonium tetrafluoroborate (IPy2BF4) and pyridineiodonium chloride (IPyCl)

Characterization of CNT films

To fully characterize the obtained pristine and doped SWCNTs films, the following methods were employed.

Raman spectroscopy (Alpha 300 Witec, Germany) with a confocal microscope and an Nd-YAG laser (532 nm, max. power 23 mW, power of measurements 2.3 mW) were used to analyze the surface of the pristine and doped CNTs. The measurement was conducted with static mode centered at 1500 cm−1 (which corresponds to acquisition window from 0 to 3500 cm−1) with 25 accumulations and integration time of 10 s to obtain a signal essentially without noise. The intensity ratio ID/IG, which informs us about the degree of structural perfection of the material, was calculated.

Scanning electron microscopy (FEI Quanta 250 FEG) was used to characterize morphologies of pristine CNTs and CNTs after doping. The micrographs of samples were taken in high vacuum using field emission gun operated at 15 kV.

Thermogravimetric analysis (TGA2 Mettler Toledo) was performed from 25 to 1000 °C, with heating rate 10 °C/min and in the stream of air of 30 ml/min.

X-ray photoemission and Auger spectra were obtained using PREVAC EA15 hemispherical electron Energy analyzer equipped with X-ray source (PREVAC dual-anode XR-40B, Al-Ka line, energy 1486.60 eV) and 2D-MCP detector. The measurements were carried out using the following conditions: 0.9 eV scanning step, 200 eV pass energy and 2 × 10−8 Pa system base pressure. The binding energy (BE) scale was calibrated by positioning the reference peaks of Au 4f7/2 (84.0 eV). The data recorded were fitted using CASA XPS embedded algorithms as well as relative sensitivity factors. Background modelled by the Shirley function was subtracted. It was determined that the estimated uncertainty for the energy position of components amounted to 0.1 eV.

X-ray powder diffraction (XRD) was used to detect impact of iodonium salts on the crystallinity of CNTs. The analysis was obtained using an X-ray diffractometer Empyrean (PANAlytical equipped with a PIXcel3D detector). The measurements were taken using Bragg–Brentano configuration. Conditions of the measurement: Cu Kα λ = 1.5406 Å, 40 kV, 30 mA.

The electrical conductivity measurement was made with a 4-point method using a Keithley 2450 SourceMeter. A CNT cut film with dimensions of 3 mm × 60 mm was placed, using silver paste, on the copper electrodes to eliminate the problem of contact resistance. The whole measurement set-up was placed on an insulating glass substrate (Fig. 2). The value of electrical resistivity under electric current of 100 mA was measured, and then the value of electrical conductivity was calculated by taking into the account the dimensions of the samples obtained from optical microscope. At least five measurements were made for each sample. The results were averaged and statistical error was calculated.

Fig. 2
figure 2

Set-up with a sample for measurement of electrical conductivity

Thermal conductivity was measured using steady-state method with infrared thermography (Wang et al. 2008; Zhang et al. 2012; Liu et al. 2016a). The measurement consisted in recording the temperature profile along the whole length of the sample, while direct current of specific parameters flows through it. The temperature of the sample as a function of its length was recorded using an IR thermometer (FLIR ETS 320) and modeled using the following equation:

$$ \kappa = \frac{U \times I \times 0.5L}{{4 \times w \times d \times \left( {T_{\text{m}} - T_{0} } \right)}}, $$

where κ is thermal conductivity, U is voltage, l is current, L, w and t are length, width and thickness of the sample, respectively. To is temperature on ends of the sample and Tm is temperature in the middle of the sample. The measurements were conducted in a vacuum chamber designed and constructed by us to eliminate the impact of the ambient environment, which would otherwise cause convection of heat to the surroundings. Figure 3 depicts an IR image of the sample taken during thermal conductivity measurements. The temperature measurement points were marked: Sp1—middle of the sample and Sp2—end of the sample.

Fig. 3
figure 3

Infrared thermograph of the measured samples

At least five measurements were made for each sample. The results were averaged and statistical error was calculated. The measurement temperature was assumed to be the temperature of the warmer end of the sample to underestimate the reported results.

Results and discussion

The obtained CNT film prepared for the doping tests was first subject to morphology and spectroscopy tests to validate its suitability for the study. The SEM micrographs (Fig. 4) present the material at 250× magnification of the parent powder and in the form of free-standing films obtained from them.

Fig. 4
figure 4

SEM micrographs of a parent CNT powder and b freestanding film made from it at ×250 magnification

As can be seen in the micrographs, the manufacture process affects the microstructure to a large extent. The obtained material is of a relatively homogenous and continuous character essentially without voids. No non-CNT clusters composed of amorphous carbon or other adulterants were detected, which illustrates highly pristine nature of this material.

To study how addition of various iodonium salts impacts the morphology the material was characterized by SEM at 100,000× magnification (Fig. 5).

Fig. 5
figure 5

SEM micrographs of films from a pristine CNT and doped by iodine compounds, b CNT-DPIC, c CNT-IPy2BF4 and d CNT-IPyCl at ×100,000 magnification

The pristine CNT film (Fig. 5a) was once again characterized by few defects and contaminants (mostly remnants of the catalyst from the synthesis). The constituting CNTs were in very close contact with each other, which translated to a reduced number of voids (and hence the starting material had relatively high electrical conductivity as compared with as will be shown in the further parts of the manuscript). Upon addition of DPIC, the microstructure of the film remained principally unchanged despite the appearance of brighter fragments, similar to mist, which is probably associated with the presence of the DPIC compound on the surface of the film (Fig. 5b). In the case of the films doped with IPy2BF4 and IPyCl, the structure of which are presented as Fig. 5c, d, the character of the surface is different—small pearls made of the iodine compounds are situated among carbon nanotubes. The SEM structural analysis confirmed that doped films contain the structures other than those typical for the pristine film and, additionally, indicated that the nature of the DPIC compound is different from that of the IPy2BF4 and IPyCl compounds, as they look different in the micrographs. After doping by these two iodonium salts, the internal structure of the films changed. Between the bundles, there was created open space supposedly caused by intercalation of these species. As will be shown in the section on electronic and thermal properties of these materials, differences in the internal structures will play an important contribution to the recorded electrical and thermal performance.

We then decided to look into the influence of these compounds on the composition of the nanocarbon material by carrying out Raman spectroscopy (Fig. 6). The ID/IG ratio, which is a common way to gauge the level of crystallinity in carbon materials, was calculated and the location of maximum of G peak was analyzed for every sample. Structural imperfections in the form of Csp3 groups are detected as so-called D-peak about 1300 cm−1; whereas, the atoms forming Csp2 lattice give a G peak about 1600 cm−1. The ID/IG ratio of the neat CNT films was found to be as low as 0.035, which once again validates very low level of disorder in the starting material.

Fig. 6
figure 6

Raman spectra of undoped and doped SWCNT films

To our delight, we did not observe any change to the value of ID/IG ratio in the case of the films doped with iodonium salts. This means that the doping technique elaborated by us has non-destructive character on the structure of CNTs. It should be noted that the maximum of G peak shifted from 1586 to 1589 cm−1, i.e., by + 4 cm−1 (Fig. 6, inset). This blue shift strongly suggests charge transfer from the nanotube to the dopant (Janas 2018) as expected from the p-doping agents prepared by us for the study.

To get a more detailed insight regarding the chemical composition and type of bonds in the materials, we employed XPS analysis. First, an Auger electron spectrum analysis was conducted to determine the difference (described as D parameter) between the maximum and minimum derivatives of C KLL spectra, in the energy scope of between 1240 and 1190 eV. In the case of ideal graphitic structure, its value is 21.4 (Mezzi and Kaciulis 2010; Haerle et al. 2001). Our base CNT film reached the same value, which again confirms that it is free of defects (Fig. S7).

The analysis of the photoemission peak of C1s (Fig. 7) provided proof that the starting material mainly contains carbon–carbon bonds with sp2 hybridization, as indicated by the signal at 248.7 eV.

Fig. 7
figure 7

C1s spectra of a pristine CNT film, b CNT-DPIC, c CNT-IPy2BF4 and d CNT-IPyCl

Additionally, there are present minute amounts of functional groups containing oxygen atoms such as C–O (287 eV), C=O or O–C=O (289 eV), COOH (290 eV) and π–π* shake-up (291.4 eV). In the case of the samples doped with iodine compounds in the C1s spectrum, an additional signal of the energy of 286 eV is visible, apart from the regular signals visible in the pristine material. It results from the C–I and C–N type bonds, the peaks of which coincide in this range. It proves that iodine compounds are present in the CNT film and that doping is permanent even under high-vacuum conditions of the XPS.

The doped films were also subject to the study of the photoemission peak of I 3d (Fig. 8).

Fig. 8
figure 8

I 3d spectra of a CNT-DPIC, b CNT-IPy2BF4 and c CNT-IPyCl

This step was carried out to learn about the character of the iodine bonds in the material. The results depicted in the Fig. 8 clearly demonstrate that the maxima of peaks in the DPIC compound spectrum (Fig. 8a) are shifted towards higher energies than for the IPy2BF4 and IPyCl compounds (Fig. 8b, c, respectively). This indicates that the electronic configuration in those compounds is different from that of DPIC. Most probably, this is caused by the type of bond between the atoms of iodine and carbon present in the structure of this doping compound. In the case of DPIC, we deal with a covalent bond, so the maximum of the peak can be located at higher energy values than in the case of the coordination bond present in IPy2BF4 and IPyCl compounds, which justifies the observed shift. Additionally, it may be observed that in the IPyCl compound spectrum, the ratio of intensity of the I 3d signal components is opposite to that in the spectra of the other two compounds. That phenomenon probably results from the fact that the compound is more prone to development of coordination bonds with nanotubes than the two previous ones, because it does not have such a strong steric effect, as its structure only contains one aromatic ring, not two. As a consequence, we may suspect that IPyCl will most readily influence the properties of the CNTs.

Thermogravimetric analysis was used to determine the thermal stability of obtained iodonium salts as such (Fig. 9a) and when incorporated into the CNT networks (Fig. 9b). Each of the thermograms of the iodine compounds displays a single relatively large combustion peak at around 200 °C, which corresponds to complete loss of mass on heating. Nevertheless, up to about 100 °C, the thermograms remain relatively flat, so the doping compounds are not prone to desorption in this temperature regime. Thermal analysis was also applied to determine thermal stability of the CNT film and the impact of doping on that (Fig. 9b). The pristine CNT films are characterized by the thermal stability up to 450 °C, and then the oxidation accelerates rapidly as expected for single-walled CNTs. In the case of the films doped with iodine compounds, we observe more complex relation between mass loss and temperature. The first significant change is observable at about 150 °C. That is probably related to the initiation of degradation or desorption of the dopant, which is in accordance with the result obtained during thermogravimetric analysis of pure iodine substances.

Fig. 9
figure 9

TGA curves of a iodonium salts and b the CNT film before and after doping

The XRD analysis indicated that the applied doping with iodonium salts does not affect the crystallographic structure of CNTs. The doped CNT films do not demonstrate additional reflexes that would illustrate such change (Fig. S8).

The start of second notable change in mass of CNT samples can be ascribed to about 550 °C, which demonstrates that doping increases the thermal stability of films by about 100 °C (pristine CNT film started the decomposition at circa 450 °C). This can be explained by the observed modification of the microstructure as visualized earlier by electron microscopy. Our previous studies show that the packing degree can have a strong effect on the shape of the thermograms (Janas et al. 2013a). From the chemical point of view, it is important to consider that halogen-bearing species can purify the material from low-molecular weight contamination, which effectively increases its thermal stability (Janas et al. 2014) and that is what we witnessed.

To demonstrate that the change of microstructure and electronic structure upon doping gives rise to tangible enhancement of the properties of the CNT films, we evaluated their electrical and thermal conductivity. The measurements on the electrical front showed that the CNT film doped with a DPCI compound has gained just slight improvement of electrical conductivity (348 ± 18 S/cm vs. 245 ± 32 S/cm for the untreated film, Fig. 10).

Fig. 10
figure 10

Electrical conductivity of measured CNT films

The boost was on the same level as when iodine monochloride (reported previously as strong doping agent of nanocarbon (Janas et al. 2014, 2017a) was employed as reference, which improved electrical conductivity of the CNT film up to 335 ± 15 S/cm. The IPy2BF4 and IPyCl compounds demonstrated much greater improvement of electrical conductivity, i.e., by 224% and 322% in comparison with the starting material (reaching 794 ± 9 S/cm and 1034 ± 19 S/cm, respectively). Various degree of enhancement of electrical conductivity of CNT films stems from the differences between their structures and type of C–I bonding. As indicated by XPS analysis, the IPy2BF4 and IPyCl compounds have similar electron structure with labile iodine atom, and so adding them to SWCNTs resulted in a significant improvement of electrical conductivity. It was more profound in the case if IPyCl because there was no steric hindrance and the I+ cation was more likely to interact with the carbon lattice because of higher “unsaturation” of its electronic shell. In the case of DPCI and iodine chloride, their electron structure is also similar. Iodine atoms are bound with strong covalent bonds, so the impact on the improvement of electrical conductivity is not as strong as in the case of IPy2BF4 and IPyCl, wherein coordination bonds are present. Furthermore, as can be seen in SEM micrographs, the microstructural changes that appeared after doping with IPy2BF4 and IPyCl are analogous. Based on the change in the microstructure, we suspect that these chemical species can more readily cause intercalation of the CNT network with iodine atoms, which is responsible for the higher increase in electrical conductivity.

Finally, the steady-state method with infrared thermography was used to measure thermal conductivity of the CNT films before and after doping (Fig. 11). The thermal conductivity of pristine film was found to be about 77 ± 15 W/mK. Our result match the thermal conductivity of the CNT systems similar to ours, also created from isotropically distributed single-walled carbon nanotubes, which were measured by the same method (Feng et al. 2018; Wang et al. 2008; Nasibulin et al. 2011). What is more, the value of thermal conductivity of the films doped with compounds of DPCI and IPy2BF4 stayed at the same level as measured for the pristine film (89 ± 9 W/mK and 75 ± 1 W/mK, respectively). On the other hand, in the case of IPyCl doping, we observed an increase in the value of thermal conductivity by over 50% reaching 117 ± 8 W/mK. As discussed before, IPyCl geometry and electronic structure are somewhat unique and can readily donate iodine atoms to the CNT ensemble because of the type of C–I bonding and lack of steric hindrance. Previous results indicate that doping of SWCNTs with iodine can markedly increase thermal conductivity of CNT networks (Behabtu et al. 2013; Mayhew and Prakash 2014). It appears that using our compounds can also be beneficial in this regard but the effect is most profound in the case of IPyCl doping because of the aforementioned justification why it is most compatible with nanocarbon due to its electronic and structural features.

Fig. 11
figure 11

Thermal conductivity of measured CNT films


In summary, we have developed an efficient and convenient method for the modification of properties of CNT films by means of doping with iodonium salts. Our methodology provides a novel approach to obtain iodine-doped CNTs, which hitherto are limited by previous conventional methods.

The highest increase in electrical and thermal conductivity was observed for the SWCNTs doped with IPyCl, which enhanced them by over 4× and 1.5× times, respectively, as compared with un-doped SMCNT films. Both the electronic structure and open geometry of a IPyCl molecule make doping with that compound most effective in terms of improvement of the transport properties of the explored nanocarbon material. In the case of other employed iodine compounds (IPy2BF4 and DPIC), we also noted improvements to the properties of the CNT films, but they were much less notable. This was caused by the presence of a stronger C–I covalent bond and/or the steric hindrance, which limited the lability of the iodine atoms which can cause intercalation of the CNT films.

Based on these results, we can state that out of the iodine compounds which we synthesized, IPyCl is most promising to effectively improve the overall performance of the CNT network. We believe that synthesis of IPyCl analogues could lead to similar favorable improvements, and so the direction proposed by us to the nanocarbon society could be an attractive alternative as compared with the use of iodine vapors or hazardous iodine chemicals to reach the same goal. From the practical point of view, incorporation of stable iodine species into the CNT network to tune the transport performance could be an important route towards design of high-performance components for microelectronics based on a wider spectrum of nanocarbon materials.