# Young's Modulus of Single-Crystal FullereneC70 Nanotubes

Authors: Tokushi Kizuka; Kun'ichi Miyazawa; Takayuki Tokumine
Journal: Journal of Nanotechnology
 (2012)

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## Abstract

We performed bending tests on single-crystal nanotubes composed of fullerene C70 molecules by in situ transmission electron microscopy with measurements of loading forces by an optical deflection method. The nanotubes with the outer diameters of 270–470 nm were bent using simple-beam and cantilever-beam loading by the piezomanipulation of silicon nanotips. Young's modulus of the nanotubes increased from 61 GPa to 110 GPa as the outer diameter decreased from 470 nm to 270 nm. Young's modulus was estimated to be 66% of that of single-crystal C60 nanotubes of the same outer diameter.


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## Body

## 1. Introduction

There have been many investigations of crystal morphologies and structures of fullerene C60 molecules since the first report on the crystallization of fullerene C60 molecules. C60 crystals have been shown in the forms of plates, films, and rods [1–13]. In particular, single-crystal fullerene nanowhiskers (NWs) with high length-to-diameter aspect ratios have been synthesized by a liquid–liquid interfacial precipitation (LLIP) method [14, 15]. In addition, tubular fullerene NWs, that is, single-crystal fullerene nanotubes (NTs) have been synthesized by the same method [16]. The mechanical properties of NWs and NTs have been investigated for application to structural materials and functional devices. Buckling tests of C60 NWs and NTs have been performed by in situ transmission electron microscopy (TEM), and their Young’s moduli were estimated to be 53–69 GPa and 62–107 GPa, respectively [17–19]. Fullerene NWs and NTs can be synthesized using another well-known fullerene molecule, that is, C70 [15, 20]. The mechanical nature of fullerene NWs and NTs can be controlled by selecting their constituent molecules, as demonstrated in fullerene films [21, 22]. In this study, we performed bending tests on C70 NTs by in situ TEM.


## 2. Experimental

We synthesized C70 NTs by the LLIP method using a saturated solution of C70 molecules in pyridine and 2-propanol [16]. The solution, including precipitated C70 NTs, was added dropwise to the edge of a gold plate. The plate was mounted on a specimen holder of the transmission electron microscope equipped with a piezomanipulation system at the University of Tsukuba [23–26]. A silicon microcantilever with a nanometer-sized tip used for contact-type atomic force microscopy (AFM) was fixed onto a cantilever holder. Both the specimen and the cantilever holders were inserted into the microscope. The cantilever tip was brought into contact with individual NTs fixed on the plate edges by piezomanipulation inside the microscope. The tip was then pressed on the NTs for bending with simple-beam- and cantilever-beam-type loading. The cantilever tip was then pulled back to release the force. A series of these manipulations were performed several times at room temperature in a vacuum of 1 × 10−5 Pa using the same NT. The deformation process was observed in situ using a television and video capture system with a time resolution of 17 ms. At the same time, the force applied to the NTs was measured by optical detection of the cantilever deflection used in AFM. The spring constant of the cantilever was measured to be 4.7 N/m.


## 3. Results

Figure1 shows a time-sequence series of the bright-field images of the bending process of a C70 NT protruding from an edge of the gold plate. The dark triangular region in the upper part of each frame of Figure 1 is the cantilever tip. The brighter region around the NT is the vacuum. The outer and inner diameters of the NT in Figure 1 are 270 nm and 100 nm, respectively. The length of the deformed part is 2.5 μm. The crystal structure of the NT was tetragonal. This crystal structure has been observed in dried C70 NWs, C60 NWs, and NTs synthesized by LLIP methods [18–20]. Polymerized C70 crystals under hydrostatic compression have an orthorhombic structure with similar lattice constants a and c, which is comparable to the tetragonal structure [27]. The longer growth axis of the NT is aligned parallel to the [110] direction. The left side of the NT was fixed on the gold plate, as shown in Figure 1. In this bending test, the cantilever tip was initially placed in contact with the NT (Figure 1(a)). Then, force was exerted on the NT in the direction indicated by the arrow in Figure 1(a) and was bent (Figure 1(b)). Thus, bending of the NT was performed using cantilever-beam-type loading. Subsequently, the tip was released, and the NT recovered its initial straight shape (Figure 1(c)). This observation shows that the bending is an elastic deformation. This bending and recovery cycle was repeated several times using the same NT. Figure 2 shows the relationship between the force and the flexure during the bending process depicted in Figure 1. The points indicated by arrowheads a–c in Figure 2 correspond to the TEM images in Figures 1(a)–1(c). The maximum flexure and loading at the free end of the NT were 467 nm and 431 nN, respectively. A hysteresis is observed in Figure 2 during the pressing and pulling of the cantilever tip. This is attributed to the bonding of the cantilever tip with the NT surface [28]. Sawtooth-like variations are observed in both the pressing and pulling processes. The decrease in force during the pressing process and the increase in force during the pulling process are caused by the rotation of the cantilever tip due to slip of the contact region between the cantilever tip and the NT surface [28]. The increase in force during the pulling process arises from the recovery of deflection of the AFM cantilever beam by increase in the recovery shift of the NT due to slip. The other changes in the exerted force, that is, the increase during the pressing process and the decrease during the pulling process, are not significantly  influenced by slip events. On the basis of the relationships among force, flexure, and Young’s modulus in cantilever-beam loading, we estimated that Young’s modulus of the NTs is 68–110 GPa from the slope of the force curve in these regions. We performed a bending test with the same type loading for another NT with an outer diameter of 470 nm and an inner diameter of 230 nm. Its Young’s modulus was estimated to be 61±5 GPa.A time-sequence series image and the separation like galley is forbidden. Time-sequence series of bright-field images of cantilever-beam-type loading bending of single-crystal C70 nanotube with outer diameter of 270 nm and inner diameter of 100 nm. One end of the nanotube is fixed on a gold plate. The arrow indicates the direction of loading imparted by the tip of AFM cantilever. This bending test was performed in the vacuum.
(a)(b)(c)Figure 2
Force-flexure curve of C70 nanotube during bending shown in Figure 1. Points a–c correspond to the states shown in Figures 1(a)–1(c). The arrows indicate the time path of recording.Figure3 shows a time-sequence series of the bright-field images of the bending process of a C70 NT, both ends of which were fixed on the gold plate. The outer and inner diameters of the NT are 340 nm and 80 nm, respectively. The length of the region of deformation was 3.5 μm. The loading was performed at the center of the deformation region by the cantilever tip. Thus, this loading was simple-beam-type loading. Figure 4 shows the relationship between the force and the flexure during the bending process presented in Figure 2. The maximum flexure and loading at the free end were 123 nm and 6.8 μN, respectively. Similar to the cantilever-beam-type bending in Figure 1, a hysteresis is observed. The pressing process from state (a) to (b) in Figure 4 is approximated by one slope. In contrast, the pulling process from state (b) to (c) in Figure 4 is composed of two slopes. The lower slope from state (b) in the pulling process is attributed to the friction between the cantilever tip and the NT surface. This is because the rotation of the cantilever tip, that is, the change in cantilever-beam deflection, is suppressed by the friction [28]. From the slope during the pressing process from state (a) to (b) in Figure 4, we estimated Young’s modulus of the NTs to be 82±5 GPa on the basis of the relationships among force, flexure, and Young’s modulus in simple-beam loading.Time-sequence series of bright-field images of loading of simple-beam-type bending of single-crystal C70 nanotube with outer diameter of 340 nm and inner diameter of 80 nm. The nanotube is supported on a gold plate with two fulcra indicated by the triangles. The arrow indicates the loading direction by the tip of the AFM cantilever. This bending test was performed in the vacuum.
(a)(b)(c)Figure 4
Force-flexure curve of C70 nanotube during bending shown in Figure 3. Points a–c correspond to the states shown in Figures 3(a)–3(c), respectively. The arrows indicate the time path of recording.In Figure5, we plotted Young’s modulus of these C70 NTs against their outer diameters. Young’s modulus increases as the outer diameter decreases. The relationship between Young’s modulus E (GPa) of C70 NTs and the outer diameters d(nm) is approximated by a straight line, E=-0.143d+129, as shown in Figure 5. As the thickness of the NTs used in this study is 85–130 nm, the tubular structure does not occur when the minimum outer diameter decreases less than 170–260 nm. From this minimum diameter, the maximum Young’s modulus of C70 NTs is estimated to be 92–105 GPa. Kizuka et al. reported that Young’s modulus of a C60 NT with an outer diameter of 510 nm is 84.5 GPa [18]. From the linear approximation in Figure 5, Young’s modulus of a C70 NT with the same outer diameter, that is, 510 nm, is calculated to be 56 GPa. Thus, Young’s modulus of the C70 NT is 66% of that of a C60 NT of the same outer diameter.Figure 5
Young’s modulus of single-crystal C70 nanotubes plotted against outer diameter. The values observed in the present study are indicated by the filled circles. The solid line indicates a linear approximation. For reference, Young’s moduli of single-crystal C60 nanotubes and nanowhiskers are represented with rhombus and open circles, respectively    [18, 19, 29].


## 4. Discussion

### 4.1. Young’s Modulus of C70 NTs and Films

Young’s moduli of C70 NTs estimated in this study are 7–28 times larger than those of crystalline C70 films (4–9 GPa) [21, 22]. The crystal lattice of the C70 NTs studied here is tetragonal, whereas crystal structure of C70 crystalline films is the face-centered-cubic structure [21, 22]. The averaged center-to-center distance between adjoining C70 molecules in the NTs along the growth direction is 3% smaller than that of C70 NTs with a face-centered-cubic structure [15]. According to Miyazawa et al., this difference can be attributed to the polymerization of the molecules [14]. Thus, it is deduced that the increase in Young’s modulus observed in this study originates from the effect of the polymerization of the constituent C70 molecules, as previously discussed for the bending tests of C60 NTs [18].


### 4.2. Young’s Modulus of C70 NTs and C60 NTs

The estimated Young’s moduli of C70 NTs are larger than those of the crystalline C70 films, whereas the modulus obtained for the C70 NT with an outer diameter of 510 nm is 66% of that of a C60 NT with the same diameter. Kolomenskii et al. and Murugavel et al. reported a similar quantitative relationship of Young’s moduli in crystalline C70 and C60 films [21, 22]. They attribute this relationship to the difference in molecular densities of crystalline C70 and C60 films.


### 4.3. Dependency of Young’s Modulus on the Outer Diameter

As shown in Figure5, Young’s modulus increases as the outer diameter decreases. Saito et al. observed a similar relationship between Young’s modulus and the outer diameter of C60 NWs [19]. They discussed the relationship on the basis of a core-shell structure model of C60 NWs. Ringor and Miyazawa investigated the incubation process of C60 NWs in solution and revealed that C60 NTs were formed owing to the elution of the interior regions [30]. Kato and Miyazawa pointed out from the cross-sectional TEM that the density of pores in the interior region of C60 NWs is higher than that in the region near the surfaces [31]. Their result also supports the core-shell structure of NWs. The dependency of the Young’s modulus on the outer diameter, as shown in Figure 5, infers that the core component remained in the C70 NTs and the larger Young’s modulus of thinner NTs is attributed to a smaller amount of the core component, which leads to a lower density of the NT.


## 4.1. Young’s Modulus of C70 NTs and Films

Young’s moduli of C70 NTs estimated in this study are 7–28 times larger than those of crystalline C70 films (4–9 GPa) [21, 22]. The crystal lattice of the C70 NTs studied here is tetragonal, whereas crystal structure of C70 crystalline films is the face-centered-cubic structure [21, 22]. The averaged center-to-center distance between adjoining C70 molecules in the NTs along the growth direction is 3% smaller than that of C70 NTs with a face-centered-cubic structure [15]. According to Miyazawa et al., this difference can be attributed to the polymerization of the molecules [14]. Thus, it is deduced that the increase in Young’s modulus observed in this study originates from the effect of the polymerization of the constituent C70 molecules, as previously discussed for the bending tests of C60 NTs [18].


## 4.2. Young’s Modulus of C70 NTs and C60 NTs

The estimated Young’s moduli of C70 NTs are larger than those of the crystalline C70 films, whereas the modulus obtained for the C70 NT with an outer diameter of 510 nm is 66% of that of a C60 NT with the same diameter. Kolomenskii et al. and Murugavel et al. reported a similar quantitative relationship of Young’s moduli in crystalline C70 and C60 films [21, 22]. They attribute this relationship to the difference in molecular densities of crystalline C70 and C60 films.


## 4.3. Dependency of Young’s Modulus on the Outer Diameter

As shown in Figure5, Young’s modulus increases as the outer diameter decreases. Saito et al. observed a similar relationship between Young’s modulus and the outer diameter of C60 NWs [19]. They discussed the relationship on the basis of a core-shell structure model of C60 NWs. Ringor and Miyazawa investigated the incubation process of C60 NWs in solution and revealed that C60 NTs were formed owing to the elution of the interior regions [30]. Kato and Miyazawa pointed out from the cross-sectional TEM that the density of pores in the interior region of C60 NWs is higher than that in the region near the surfaces [31]. Their result also supports the core-shell structure of NWs. The dependency of the Young’s modulus on the outer diameter, as shown in Figure 5, infers that the core component remained in the C70 NTs and the larger Young’s modulus of thinner NTs is attributed to a smaller amount of the core component, which leads to a lower density of the NT.


## 5. Conclusion

We performed bending tests on individual C70 NTs by in situ TEM. From the measurements of the force-flexure relationships of C70 NTs, Young’s modulus was estimated to be 61–110 GPa. Young’s modulus increased as the outer diameter decreased. From this relationship, the Young’s modulus of a C70 NT was estimated to be 66% of that of a C60 NT of the same outer diameter, that is, 510 nm. The maximum Young’s modulus of C70 NTs was estimated to be 92–105 GPa from the limit of the thickness of the tubular structure.



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*Source: 969357-2011-09-28.xml*