Geometric parameters of the VA CNTs determined by the SEM method.

## Abstract

This chapter presents the results of experimental studies of the electrical, mechanical and geometric parameters of vertically aligned carbon nanotubes (VA CNTs) using scanning probe microscopy (SPM). This chapter also presents the features and difficulties of characterization of VA CNTs in different scanning modes of the SPM. Advanced techniques for VA CNT characterization (the height, Young’s modulus, resistivity, adhesion and piezoelectric response) taking into account the features of the SPM modes are described. The proposed techniques allow to overcome the difficulties associated with the vertical orientation and high aspect ratio of nanotubes in determining the electrical and mechanical parameters of the VA CNTs by standard methods. The results can be used in the development of diagnostic methods as well as in nanoelectronics and nanosystem devices based on vertically aligned carbon nanotubes (memory elements, adhesive structures, nanoelectromechanical switches, emission structures, etc.).

### Keywords

- nanotechnology
- carbon nanotube
- scanning probe microscopy
- resistivity
- Young’s modulus
- adhesion
- piezoelectric response

## 1. Introduction

Precise parameters of vertically aligned carbon nanotubes (VA CNTs) control geometric parameters, resistivity, Young’s modulus, adhesion, strength, and so on, and are a prerequisite for the devices of nanoelectronics and nanosystems creation on their basis with reproducible and stable characteristics [1, 2, 3, 4]. However, the determination of these parameters in the carbon nanotubes (CNTs) by standard diagnostic methods is difficult due to the vertical orientation and the high aspect ratio of the nanotubes.

Thus, the application of traditional experimental methods for determining mechanical parameters (direct tensile load, pulsed dynamic method, etc.) is complicated due to the size of the VA CNT and also because of the need to fasten nanotubes on the substrate. In addition, as shown by the analysis of published data, the Young’s modulus (one of the main mechanical parameters of CNTs) has a wide range of values in the range 0.4–6.85 TPa [5, 6, 7, 8, 9, 10, 11, 12, 13]. The values of the Young’s modulus obtained experimentally are 2–3 times smaller [5, 7, 8, 9, 10] calculated on the basis of theoretical models [11, 12, 13]. This may be due to the fact that the Young’s modulus of CNTs depends essentially on the thickness of the CNT wall, which in practice is several times larger than values used in theoretical calculations [14].

The most widely used methods for investigating the electrical properties of microstructures require the formation of contact areas of several micrometers in size at the tops of the VA CNTs. This fact significantly limits the possibilities of using these methods to determine the electrical parameters of individual vertically aligned nanotubes because of their small transverse dimensions [15]. The work on quantitative evaluation and study of VA CNT adhesion to substrate is not numerous due to the complicated nature of interaction between the substrate, the catalytic center and the nanotube during the growth of the carbon nanotubes and also the need to manipulate individual nanotubes during experimental studies [16, 17, 18].

Thus, the tasks associated with development of new nanodiagnostic techniques to determine the geometric, mechanical and electrical parameters of VA CNTs are relevant in connection with the need to control and study parameters of individual vertically aligned carbon nanotubes, elements and devices on their basis and also in connection with requirements for development of metrological support for nanotechnologies.

A promising method for developing such nanodiagnostic techniques is a scanning probe microscopy (SPM) method [19, 20, 21, 22, 23, 24, 25]. This method does not require additional fixation of VA CNTs, special sample preparation and formation of contact areas on their tops. However, the determination of quantitative values of individual carbon nanotube parameters based on results obtained by SPM requires analysis of measurement process and development on its basis of techniques for determining parameters of CNTs taking into account the features of the SPM method.

This chapter describes unique techniques for determining the height, Young’s modulus, bending stiffness, resistivity and adhesion to a substrate of vertically aligned carbon nanotubes, based on the methods of scanning probe microscopy. Described techniques can be used for nanodiagnostics of parameters of individual vertically aligned carbon nanotubes and for creation of nanoelectronic elements and devices on their basis [1, 11, 21, 23, 25, 26, 27, 28, 29].

## 2. Scanning probe techniques for characterization of vertically aligned carbon nanotubes

### 2.1. Experimental samples and equipment

The experimental samples of vertically aligned carbon nanotubes were grown using the NANOFAB NTC-9 nanotechnology multi-functional complex (NT-MDT, Russia) using the plasma-enhanced chemical vapor deposition (PECVD) method [2, 25, 30, 31]. A silicon wafer with a deposited titanium film and a nickel catalytic film with thicknesses of 20 and 10 nm, respectively, was used as the initial substrate. Acetylene was used as the reaction gas. The growth of VA CNT arrays was carried out at a pressure of 4.5 Torr and a temperature of 750°C. The growth parameters for experimental samples were characterized by the growth time, the acetylene feed rate and current flowing in the system. The structural analysis of the VA CNT arrays was conducted by the transmission electron microscopy (TEM) using Tecnai Osiris (FEI, Netherlands) and the Raman spectrometer Renishaw InVia Reflex (Renishaw plc, UK). Analysis of TEM images and Raman spectra showed that the experimental samples were multi-walled carbon nanotubes [3]. Surface investigations of the obtained VA CNT arrays were carried out using a scanning electron microscope (SEM) Nova Nanolab 600 (FEI Company, Netherlands).

Experimental studies of geometric, mechanical, electrical and adhesive properties of VA CNT arrays were carried out using the Ntegra probe nanolaboraty (PNL) (NT-MDT, Russia). To process the experimental data, the ImageAnalysis application package was used. A commercially available silicon cantilever of the NSG 20 brand was used as the probe of the atomic force microscope in developing the technique for determining the height of the VA CNT array. Investigations of the mechanical properties of carbon nanotube were carried out at Ntegra PNL by an integrated scanning hardness nanotester. The indenter was a diamond triangular pyramid of Berkovich with an angle at the vertex between the edge and height * θ* = 70°. Investigations of the electrical parameters of VA CNTs were carried out by scanning tunneling microscopy (STM) method in spectroscopy mode with a distance between the STM probe and the VA CNT top equal to 0.5 nm. A tungsten probe made by an electrochemical method was used as a STM probe. Experimental studies of the VA CNT adhesion to a substrate were carried out by atomic-force microscopy (AFM) in current spectroscopy mode, with a distance between CNT top and an AFM probe equal to 1 nm. Experimental studies of piezoelectric response of VA CNT were performed by the AFM method in force spectroscopy mode. A commercially available silicon cantilever with a platinum coating of NSG11/Pt brand with a tip radius of 20 nm was used as an AFM probe.

### 2.2. A technique for determining the height of a vertically aligned carbon nanotube array

One of the promising methods for studying nanoscale structures is the atomic force microscopy, which allows one to determine the parameters of nanostructures without special sample preparation and to modify them by probe nanolithography methods [25]. The main difficulty in the study of VA CNT arrays by the AFM method is the mobility of nanotubes in their interaction with the probe. In addition, at a high density of carbon nanotubes in the array, the depth of penetration of the AFM probe between the individual nanotubes is limited by the parameters of the probe itself (the radius of curvature and aspect ratio of tip sides), which can lead to the display on AFM images of nonindividual nanotubes in the array and their bundles [25].

The study of influence of AFM scanning mode (contact, semi-contact and noncontact) on the quality of the image obtained on the surface of VA CNT array (with a diameter * D* = 80 nm, length

*= 2 μm and density of nanotubes in the array*L

*= 30 μm*n

^{−2}) shows that the carbon nanotubes “detach” from substrate-surface VA CNTs in AFM contact mode ( Figure 1a ). As a result, the AFM contact mode cannot be used for nanodiagnostics and for determining the VA CNT geometric parameters [25]. The study of the VA CNT array in the semi-contact mode shows that the individual VA CNTs are combined into bundles when the probe is exposed ( Figure 1b ). The main disadvantage of AFM images of VA CNT array obtained in a semi-contact mode is the presence of a number of scanning artifacts caused by the high mobility of nanotubes during mechanical contact with the probe, and as a consequence, the relatively low resolution of this AFM mode ( Figure 1b ).

In addition, a partial destruction of the VA CNT array is possible when scanning in a semi-contact mode with a pressing force of the AFM probe to surface more than 10 μN and scanning frequency more than 1 Hz ( Figure 2 ).

The usage of the AFM noncontact mode at which the probe interacts with the array surface only due to van der Waals forces [32] made it possible to obtain AFM images of bundles of vertically aligned carbon nanotubes with a higher resolution, without explicit artifacts ( Figure 1c ). In the noncontact mode, the individual nanotubes were also combined into bundles with a diameter of about 300 nm ( Figure 1c ) under the action of van der Waals forces [25]. Statistical processing of AFM images showed that the maximum height of the bundle was 2.52 μm, the average height was 1.27 ± 0.35 μm and the density of individual VA CNT bundles in the array was about 1.68 μm^{−2} [25].

Thus, it has been shown that the optimal scanning mode for determination of the geometric parameters of vertically aligned carbon nanotubes is the AFM noncontact mode, which allows one to obtain AFM images with a higher resolution resolving and without destroying the VA CNT structure. The results obtained by the AFM noncontact mode correlate well with the values of the geometrical parameters of the VA CNT determined by the SEM method.

Based on the obtained results, a technique for measuring a VA CNT array height was developed. This technique was based on sequential scanning in contact, then in semi-contact or noncontact modes of a VA CNT array with different areas [25]. So, the VA CNT array were scanned with an area of 10 × 10 μm^{2} and then 30 × 30 μm^{2} ( Figure 3a , b ). The analysis of the profilogram of the scanning area allowed to determine the maximum height of the VA CNT array equal to 1.98 μm and the average height of VA CNTs in the array equal to 1.12 ± 0.45 μm ( Figure 3c ).

The developed technique for measuring the VA CNT array height allows to determine the height value with a higher reliability than a semi-contact or noncontact mode in that the measurement of this parameter is made relative to substrate’s surface and not the greatest penetration depth of the AFM probe into the array. Moreover, the developed technique makes it possible to obtain and automatically process a statistical set of the geometric parameters’ values of carbon nanotubes in contrast to the SEM method.

### 2.3. A technique for determining the Young’s modulus and bending stiffness of vertically aligned carbon nanotubes

One of the promising methods for determining the Young’s modulus of vertically aligned CNTs is the nanoindentation method based on indenting a solid needle (indenter) into the array by applying an external load and obtaining the dependence of the penetration depth of the indenter into the array from nanoindentation force [11, 22]. A schematic process of nanoindentation of a vertically aligned carbon nanotubes array is shown in Figure 4 . Initially, the indenter is in the approached state, then the load is applied and the indenter interacts with the array surface and touches the first VA CNT at the depth * h*; with a further increase in the load, the first nanotube begins to bend and the indenter touches the second tube at the depth

_{1}

*( Figure 4a ). At a given depth h, the indenter interacts with the i-number of VA CNTs, each of which is deflected by a distance*h

_{2}

*( Figure 4b ), depending on the initial touch depth of the indenter with the i-tube and the geometry of the indenter [13]:*w

_{0}

On the other hand, the nanoindentation process can be considered using a micromechanical model. This model is based on the beam theory, according to which an individual vertically aligned nanotube is an elastic hollow cylindrical rod fixed at one end. In this case, the elastic deflection * w*of a carbon nanotube with an outer diameter

_{0}

*and a height*D

*when an external load is applied is described by the equation [11]:*L

where * P*and

*are the forces acting on the nanotube parallel and perpendicular to its axis, respectively ( Figure 4a );*T

*= (*k

*)*P/(YI)

_{eff}

^{1/2},

*is the effective bending stiffness of a VA CNT with an effective moment of inertia equal to*(EI)

_{eff}

*≈*I

_{eff}

πD

^{4}/64 [11].

Earlier, a method was developed for determining the mechanical parameters of a VA CNT based on the nanoindentation using a micromechanical model [11]. The main shortcoming of this method was the use of bending stiffness as a rigidity parameter of theoretical and experimental dependencies, from which the value of the Young’s modulus of the VA CNT is calculated [11] This fact significantly reduced the reliability of the obtained results. To eliminate this shortcoming, we proposed a technique for determining the bending stiffness * (EI)*for each i-tube interacting with the indenter using experimental dependences [22, 28, 29]. For this the force

_{eff}

*acting on one CNT was represented as [22]:*P

where * P*is the indentation force representing the vector sum of the forces

_{IND}

*and*P

*( Figure 4a ),*T

*is the indentation force corresponding to the depth hi of touching of the*P

_{i}

*-tube and*i

*is the number of nanotubes interacting with the indenter at the*i

*. The values of the*P

_{IND}

*and*P

_{IND}

*forces are determined from the experimental dependences obtained in the nanoindentation process of the VA CNT array.*P

_{i}

Thus, Young’s modulus is determined from the following expression based on the technique developed by us [22]:

The number of nanotubes * i*interacting with the indenter for a given indentation force is defined as the product of the total interaction area of the indenter S at penetration depth h and density of the VA CNTs in an array. The total area

*is the sum of the cross-section area of the indenter*S

*at depth*S

_{ind}

*, the interaction area by the perimeter of indenter*h

*and the cross-sectional area of the nanotube*S

_{per}

*. Due to the fact that the Berkovich indenter is a regular triangular pyramid with the angle at the vertex*S

_{CNT}

*= 70°, the height of the triangle lying at the base of the pyramid is*θ

*=*a

*and the value of the edge of the base is*1.5 h∙tg70°

*. The interaction area of the indenter*c = 2a∙tg30°

*at the penetration depth*S

*with one tube is [22]:*h

This dependence allows us to determine not only the number of tubes interacting with the indenter at a depth * h*but also the depth

*at which the indenter touches the*h

_{i}

*-tube.*i

The technique proposed by us technique makes it possible to calculate the Young’s modulus of individual VA CNT directly from a set of the experimental dependences obtained in the nanoindentation process [22] The limits of applicability of the technique are determined by the aspect ratio of vertically aligned carbon and the nanotube deflection value. The maximum value of the deflection of CNTs in the nanoindentation process, in which the interaction of the indenter with the VA CNT array is still described by the beam theory, depends on the length of the carbon nanotube and is determined by the following expression [22]:

where 0.2 * L*is the maximum penetration depth determined from the experimental dependences.

For the approbation of the developed technique, three experimental samples of VA CNT arrays with various geometric parameters were studied ( Figure 5 ). Analysis of SEM images made it possible to estimate the diameter and height of carbon nanotubes, as well as the density of nanotubes in the array. The values of these parameters are presented in Table 1 .

Parameter | VA CNTs No 1 | VA CNTs No 2 | VA CNTs No 3 |
---|---|---|---|

Height , nm | 650 | 1210 | 930 |

Diameter , nm | 44 | 36 | 51 |

Aspect ratio | 15 | 34 | 13 |

The VA CNTs density in array , μm^{−2} | 82 | 72 | 69 |

Using the obtained values of the geometric parameters of carbon nanotubes, their mechanical properties were investigated by the developed technique. The maximum value of an indentation force was 100 μN. The nanoindentation was carried out at six different points separated from each other by a distance of about 5 μm for each VA CNT array. Figure 6 shows the experimental dependences obtained for three arrays of VA CNT.

Analysis of the dependences showed that the curve of the penetration depth of the indenter into the array on the indentation force is nonlinear. Two sections of the curve can be distinguished: the elastic (from 0 to 250 nm for the first mass, from 0 to 175 nm for the second mass, and from 0 to 250 nm for the third one) and inelastic (from 250 to 330 nm for the first array, from 175 to 275 nm for the second one and from 250 to 600 nm for the third one) interaction. Therefore, only the first section of the curves was used to calculate the Young’s modulus of VA CNTs as the beam theory describes only small elastic deflections. Based on this, the total penetration depth of the indenter into the first array * h*was 250 nm, into the second one was 175 nm and into the third one was 250 nm. The corresponding indentation forces of

*were about 8, 10 and 3 μN, respectively ( Figure 6 ).*Р

_{IND}

Using the developed technique, the bending stiffness and Young’s modulus were determined for each i-nanotube of the VA CNT interacting with the indenter at a depth * h*and the average values of these parameters were obtained for each VA CNT arrays. The results are shown in Table 2 . The obtained values of the mechanical parameters of the VA CNT correlate well with the literature data [5, 6, 7, 9, 11, 22, 28].

Mechanical parameters | VA CNTs No 1 | VA CNTs No 2 | VA CNTs No 3 |
---|---|---|---|

Bending stiffness, N∙nm^{2}Young’s modulus, TPa | 0.112 ± 0.004 1.15 ± 0.05 | 0.106 ± 0.005 1.29 ± 0.08 | 0.195 ± 0.007 0.59 ± 0.12 |

An analysis of the results showed that the Young’s modulus of a VA CNT increases with the increase in its length. This fact can be associated with decreasing the structural defects of the nanotube with increasing length. Analysis of the bending stiffness values showed that the value of this parameter increases with increasing diameter of the nanotubes. This is probably due to an increase in the number of inner layers in multi-walled carbon nanotubes and an increase in Van der Waals forces between layers, which leads to an additional resistance of the carbon nanotube to bending deformations during indentation [14].

Thus, the developed technique can be successfully used to measure the mechanical parameters of vertically aligned carbon nanotubes by the nanoindentation, as well as to study the effect of the geometric parameters of VA CNT on their Young’s modulus [22, 28]. The developed technique can be used to determine the mechanical properties of nanotubes and nanowires from other materials [21].

### 2.4. A technique for determining the resistivity of vertically aligned carbon nanotubes

Scanning probe microscopy is a precision method for studying the electrical properties of horizontal carbon nanotubes [33, 34, 35]. However, the study of vertically aligned carbon nanotube has difficulties due to the mobility of nanotubes upon contact with the SPM probe and the formation of VA CNT bundles on the application of an electric field [36]. In addition, the determination of the VA CNT resistivity based on the current–voltage characteristics (CVC) obtained by the SPM method requires an analysis of the measuring process the CVCs and the development of a technique taking into account the features of the SPM [23]. Earlier, it was shown that the value of the VA CNT resistivity obtained on the basis of CVCs obtained by the AFM method is higher [23] than the value presented in the literature [37]. This is due to the influence of contact of the AFM probe on the VA CNT top and the appearance of additional resistance in the measuring system. In addition, as a result of preliminary scanning of the VA CNT array in an AFM semi-contact mode, nanotubes form bundles, which makes it difficult to localize the probe over an individual VA CNT top and to study its electrical properties. The determination of the resistance of an individual VA CNT by the scanning tunneling microscopy (STM) method allows to overcome these difficulties because the resistance of the tunnel contact of the STM probe with the VA CNT top at a voltage of more than 1 V becomes insignificant and does not significantly affect the overall resistance of the system “STM probe/VA CNT/conductive layer/VA CNT array/contact.” In addition, the formation of VA CNT bundles does not occur during the preliminary scanning by the STM method [23].

The schematic and the equivalent circuit of the measuring system of the VA CNT by the STMs method are shown in Figure 7 . According to Figure 7b , the total resistance of the system

where * R*, the contact materials

_{sub}

*and the STM probe*R

_{Me}

*determined by STM spectroscopy of the array area without the VA CNTs ( Figure 7c , d );*R

_{CNTs/Me}+ R

_{CNTs}+ R

_{CNTs/sub},

*—resistance of the tunnel contact between the STM probe and VA CNT;*R

_{tun}

*is the total resistance of an individual vertically aligned carbon nanotube and the contact between the VA CNT and the conductive layer [23].*R

_{CNT}+ R

_{CNT/sub}

Earlier, it was shown that the contribution of the resistance of the tunnel contact decreases with increasing electric field strength and at large values of the strength one can take * R*~ 0 [38], where the total resistance of the individual VA CNT and the contact to the conductive layer can be taken as [23]:

_{tun}

The resistance * R*~ 0 ( Figure 7d ) and the CVC obtained at the modified area of the VA CNT array. The resistivity of an individual VA CNT was defined as

_{tun}

*=*ρ

_{el}

*.*S/L

The experimental approbation of the proposed technique was carried out on an experimental sample of VA CNT array (* D* = 70–120 nm,

*= 2.2 μm,*L

*= 8 μm*n

^{−2}). The distance between the STM probe and the VA CNT top was 0.5 nm. To localize the probe at the VA CNT top, a preliminary scanning of the array surface was performed using the STM method. The resulting STM image and the CVC of the VA CNT (solid line) are shown in Figure 8 . The resistance of the “STM probe/conductive layer/VA CNT array/contact“ system ( Figure 7c ) was measured additionally to exclude the resistance of the STM probe, the conductive layer, the contact material and the nanotube array below it from the total resistance system. To measure this resistance, the VA CNT array was previously scanned in the AFM contact mode using the technique presented in Section 2.2. The CVC of the modified area is shown in Figure 8b (dashed line).

Analysis of the obtained STM image of the VA CNT array showed that individual nanotubes are not combined into bundles due to the low density of VA CNTs in the array ( Figure 8a ). It allows investigating the electrical properties of individual VA CNTs. The diameter of the VA CNT is 118 ± 39 nm. The height of the VA CNT is not displayed correctly on the STM image due to the peculiarities of measuring the VA CNT array by the STM [36]. Based on the CVC of the individual VA CNT ( Figure 8b ), it can be concluded that the individual VA CNT exhibits two conduction states: high resistance when the voltage is varied from 0 to 10 V and low resistance when the voltage varies from 10 to 0 V, which is due to the manifestation of a memristor effect in VA CNT [3, 26, 29, 39, 40]. The low-resistance state of the VA CNT was used to determine the resistance of the nanotube, since there is no additional resistance in VA CNT associated with the internal electric field in the nanotube [3, 40].

The resistance of ^{2} (1.186·10^{−9} Ω cm^{2}) [23]. Therefore, the resistance of the contact for the VA CNTs under study changes in the range * R* = 4.1–12.8 Ω. Thus, we have

_{CNTs/sub}

*< <*R

_{CNTs/sub}

^{−4}Ωm. The obtained value of the resistivity of multi-walled VA CNT correlates well with the literature data [41].

### 2.5. A technique for determining the adhesion of vertically aligned carbon nanotube to a substrate

The adhesion of VA CNT to a substrate * W*quantitatively characterized by the work of breaking the adhesive bond per unit area was assumed to be equal to the work of the internal elastic forces arising at the base of the VA CNT at the moment of detachment from substrate [42]:

_{a}

where * σ* =

*—mechanical stress arising in a VA CNT as a result of elongation;*kΔL

_{0}/S

*is a VA CNT elongation at the point*ΔL

_{0}

*= 0.01*x

_{0}

*at*L

*.*t = t

_{0}

From a practical point of view, the adhesion strength and the corresponding detachment force (the maximum force that can be applied along the axis of the nanotube without detaching it from the substrate) are of great importance. These parameters allow optimizing the design and operating parameters of emitters and memory elements based on VA CNT to prevent a VA CNT detaching from the substrate. The adhesion strength * f*was defined as the force required for breaking the adhesive bond of the VA CNT with the substrate referred to the area of the adhesive contact. The value of adhesive strength is sensitive to the determination method and depends on the type of external load causing destruction of the adhesive contact. When applying a mechanical load to the VA CNT, the external force is expended on the deformation of VA CNT (

_{0}

*) and the break of the adhesion bond with the substrate (*F

_{x}

*), and the adhesion strength of the VA CNT bond to the substrate is determined as [42]:*F

_{a}= W

_{a}∙S/ΔL

_{0}

When applying an external electric field, the adhesive strength _{0} by applying a mechanical load due to the attraction force * F*arising under the action of an external electric field which is expended not only on the deformation of VA CNT and the break of adhesive bond with the substrate but also on the polarization and creation of the conduction current VA CNT. The adhesive strength

_{at}(t)

Thus, the value of the maximum force that can be applied to the “VA CNT/substrate” system without its destruction will be different for devices functioning in the field of mechanical loads of high electric field.

Experimental studies of adhesion were carried out on a VA CNT array (* D* = 70—120 nm,

*= 2.2 μm and*L

*= 8 μm*n

^{−2}) when voltage pulses U were applied with an amplitude of 10 V to 30 V and duration of 1 s. The detachment of the VA CNT from the substrate was fixed by the absence of current on the reverse branch of the CVC (with the voltage from the maximum value to zero) obtained in the “substrate/VA CNT/AFM probe” system in the AFM spectroscopy mode ( Figure 9 ). The nanotube is retained on the surface of the AFM probe by the van der Waals forces after removal of the external electric field [19]. This effect was used to create critical-dimension atomic-force microscopy (CD-AFM) probes by depositing a carbon nanotube from a VA CNT array on the tip [19]. As shown by experimental studies, the detachment of a vertically aligned carbon nanotube from the substrate did not occur at U = 10 V; a single nanotube was detached with a reproducibility of about 30% at U = 15 V; a constant detachment of one or two VA CNTs was recorded at U = 20 V; several nanotubes were detached at U > 20 V. The voltage at which the detachment of a single VA CNT from the substrate was observed was likely to vary with the diameter of the nanotube. It should be noted that only van der Waals forces (~ 15 nN [3]).

Further, a modeling of the VA CNT deformation under the action of an external electric field was carried out to determine the quantitative values of the adhesion of VA CNTs to the substrate [3, 29, 40]. The results of the modeling showed that the VA CNT deformation increases with increasing voltage from 10 V to 30 V. So the elongation at the VA CNT base (x = 0.01 L) * ΔL*is 0.037, 0.0391, 0.0404, 0.0419, 0.0441 and 0.0445 nm for a VA CNT with

_{0}

*= 70, 80, 90, 100, 110 and 120 nm, respectively, at corresponding voltage at the detachment ( Figure 10 ). The elongation at the VA CNT top (*D

*=*x

*)*L

*is 1.25, 1.31, 1.36, 1.41, 1.48 and 1.49 nm, respectively ( Figure 10 ). An analysis of the dependence of the elongation of a vertically aligned carbon nanotube (at*ΔL

_{max}

*=*x

*) on its diameter showed that at a voltage of 15 V*L

*of the VA CNT with a diameter of 70 nm is 1.24 nm and the*ΔL

_{max}

*increases to 1.49 nm with an increase in the diameter of VA CNT to 120 nm. Thus, voltage at the detachment of a VA CNT with*ΔL

_{max}

*= 80 nm is equal to 16.3 V; with*D

*= 90 nm,*D

*= 17.5 V; with*U

*= 100 nm,*D

*= 18.7 V; with*U

*= 110 nm,*D

*= 19.6 V and; with*U

*= 120 nm,*D

*= 20 V ( Figure 10 ) [42].*U

Taking into account the results of modeling, the adhesion of VA CNT (* D* = 70—120 nm)

*increases from 0.55 to 1.19 mJ/m*W

_{a}

^{2}with the increase in diameter according to Eq. (10). This fact probably connected with the increase in the number of carbon atoms interacting with the substrate per unit area of the adhesive contact, when the diameter of the VA CNT is increased and as a result of the increase in the layers of the multi-walled carbon nanotube. The corresponding adhesion force

*of the individual VA CNT with increasing diameter varied from 92.5 nN to 226.1 nN. According to Eq. (11), the adhesive strength of the VA CNT to the substrate*F

_{a}

*is 714.1 ± 138.4 MPa when a mechanical load is applied. The corresponding detachment force*f

_{0}

*varies from 1.93 to 10.33 μN depending on the diameter of the VA CNT ( Figure 11 , dependence 1).*F

_{0}

The detachment force * F*exceeds the adhesion force

_{0}

*by tens of times due to the considerable internal elastic forces arising in VA CNT under tension. According to Eq. (12), the adhesion strength of the VA CNT to the substrate*F

_{a}

*at the moment of nanotube detachment from the substrate (varies from 3.83 μN to 20.02 μN for VA CNT with a diameter of 70–120 nm) ( Figure 11 , the dependence of 2) [42].*F

_{at}(t

_{0})

Thus, the adhesion strength of a VA CNT to the substrate when applying an external electric field * f*. It allows using a VA CNT with diameter from 70 to 120 nm grown by PECVD in the development and creation of emitters and memory elements with an electric field strength up to 10

_{0}

^{10}V/m. The calculated adhesion force and adhesion strength are well correlated with available literature data [17, 18], which confirms the reliability of the results obtained.

### 2.6. A technique for determining the piezoelectric response of vertically aligned carbon nanotubes

Recent work in the field of investigation of electromechanical properties of carbon nanostructures has shown the possibility of manifesting flexoelectric and piezoelectric effects in them [3, 43, 44, 45, 46]. In this connection, an urgent task was the development of a technique for determining the piezoelectric response of vertically aligned carbon nanotubes because the use of the piezoresponse force microscopy in this case is difficult.

To study the piezoelectric response of VA CNT, we proposed a technique based on AFM power spectroscopy with parallel detection of a current flowing in the “lower electrode/VA CNT/AFM probe” system using an AFM oscilloscope. As a result, deformation of VA CNTs was formed in the AFM force spectroscopy mode by mechanical pressing of the probe to its top and the current value generated by VA CNT was detected at a known mechanical load. Schematic of the measurement process is shown in Figure 12a .

The results of study of the VA CNT array (* D* = 34 ± 3 nm,

*= 370 ± 40 nm and*L

*= 47 μm*n

^{−2}) on the basis of the proposed technique showed that the current in the “lower electrode/VA CNT/AFM probe” system did not flow when an AFM probe is approached to an individual nanotube; with increasing the pressing force of the probe from 0 to 0.5 μN, a current appeared the value of which varied from 0 to −24 nA, respectively; the current value decreased back to zero at the subsequent removal of the pressing force ( Figure 12b ).

To exclude the influence of the measurement system and the substrate on the measurement results, it is also necessary to carry out similar measurements on a substrate mechanically purified from VA CNT using the AFM contact mode. For this sample, the measurements of the substrate showed the absence of a piezoelectric response when it deformed. The current flowing in the measurement system was constant and amounted to about 60 pA, which can be attributed to the systematic error of the PNL Ntegra measurement system.

Thus, the developed technique allows us to experimentally estimate the value of a current generated by deforming a carbon nanotube as a result of a direct piezoelectric effect. The obtained results correlate with the experimental and theoretical studies carried out by us earlier [3, 44].

## 3. Conclusion

Thus, unique techniques for nanodiagnostics of geometric, mechanical, electrical and adhesion properties of vertically aligned carbon nanotubes have been developed. The developed techniques were used for experimental investigations of the VA CNT. The obtained values of Young’s modulus, bending stiffness, resistivity and adhesion of VA CNTs correlate well with the published data [5, 6, 7, 9, 11, 17, 18, 22, 28, 41], which confirm the reliability of the developed techniques. The developed techniques do not require additional sample preparation and can be used as express techniques for quality control of grown VA CNTs and elements of nanoelectronics and nanosystems based on them. The obtained results can be used for the development of nanodiagnostic methods, as well as for the design and fabrication of resistive energy-efficient memory elements with a high density of cells, adhesive structures, nanoelectromechanical switches and emission structures based on vertically aligned carbon nanotubes. Application of the developed techniques at the stage of interoperational control of the technological process of manufacturing such devices will increase reproducibility of their parameters and stability of operation.

The results were obtained using the equipment of Research and Education Center and the Center for collective use “Nanotechnologies” of Southern Federal University.

## Acknowledgments

This work was financially supported by Russian Foundation for Basic Research (project No. 16-29-14023 ofi_m) and Internal grant of the Southern Federal University (project No. VnGr-07/2017-2026).