Morphology, Structure, and Properties of Conductive Polylactide Fibers Prepared Using Polyvinyl Acetate and Multiwalled Carbon Nanotubes

: Two kinds of conductive polylactide ﬁbers—polylactide pre-oriented yarns (PLA-POY) and PLA-drawn textured yarns (PLA-DTY) are prepared by coating method using ethyl acetate as solvent, multiwalled carbon nanotubes (MWCNTs) as conductive ﬁller, and polyvinyl acetate (PVAc) as dispersing agent and coating agent. The PLA ﬁbers are characterized by scanning electron microscope (SEM), Fourier-transform infrared spectroscopy (FTIR), di ﬀ erential scanning calorimetry (DSC), resistance meter, and tensile test. The results show that PLA-POY and PLA-DTY have been coated successfully by PVAc and MWCNTs. After PLA-POY ﬁbers are treated by ethyl acetate, the highly porous structures form because of swelling and the subsequent solvent-induced crystallization of PLA-POY ﬁbers with low crystallinity. This causes the tensile force to decrease. However, PVAc can improve the tensile force of the treated PLA-POY ﬁbers. For PLA-DTY ﬁbers, the e ﬀ ect of ethyl acetate on surface morphology is small. Therefore, the treated PLA-DTY ﬁbers own higher tensile properties than original PLA-DTY ﬁbers due to the existence of PVAc. With the increase of PVAc and MWCNTs, the conductive properties of the PLA ﬁbers will increase. The electrical conductivity of PLA-POY and PLA-DTY ﬁbers can reach 0.53 and 0.13 µ s / cm, respectively.


Introduction
Polylactide (PLA) is a type of biodegradable polyester with thermoplastcity, biodegradability, and biocompatibility [1,2]. PLA has been extensively used for fiber materials due to its similarity with polyethylene terephthalate (PET) fibers, ecofriendly nature, and ease of processing [3]. The melt-spinning method is optimal for manufacturing PLA fibers because of its thermoplastcity [3] and a wide melt-processing window.
The effects of processing conditions on the structure and properties of melt-spun PLA fibers have been studied widely [4][5][6]. Especially, Liu et al. [3] studied the effect of air drawing on structure and properties of PLA fibers. Solarski et al. [7] introduced plasticizer and clay to PLA and manufactured PLA fibers by melt-spinning process. The obtained PLA fibers presented an improvement in thermal and shrinkage properties. Polylactide/poly (3-hydroxybutyrate-co-3-hydroxyvalerate) (PLA/PHBV) First, PVAc was added to ethyl acetate and dissolved by stirred for 3 h with a magnetic stirrer to prepare PVAc in ethyl acetate solution. Second, the required amounts of MWCNTs were added into PVAc in ethyl acetate solution, stirred for 30 min by a magnetic stirrer, and then sonicated for 2 h to obtain the suspension of MWCNTs and PVAc in ethyl acetate. Here, the concentration of MWCNTs and PVAc in ethyl acetate is 2-10 and 10-50 mg/mL, respectively. Last, conductive PLA fibers were prepared by coating method; the coating method is shown in Figure 1. The temperature of the water bath in the ultrasonic cleaner was room temperature. The take-up speed of conductive fibers was ~1 m/min. The obtained conductive fibers were dried naturally in fume hood. The treated PLA-POY and PLA-DTY fibers are denoted by OCxPy and TCxPy, respectively. Here, the letter "O" in OCxPy and the letter "T" in TCxPy stand for PLA-POY and PLA-DTY, respectively. C and x stand for MWCNTs and the concentration of MWCNTs, respectively. P and y stand for PVAc and the concentration of PVAc, respectively.

Differential Scanning Calorimetry
The crystallization behaviors and melting behaviors of the samples were characterized by differential scanning calorimetry that used a DSC Q200 (TA Instruments ® , Inc., New Castle, DE, USA). Nitrogen was used at a flow rate of 50 mL/min. The instrument was calibrated with In and Pb. The weight of the samples was between 4 and 6 mg. Each sample was heated from 0 to 200 °C at 10 °C/min.

Scanning Electron Microscope
Scanning electron microscopy (SEM) measurements of the longitudinal surface and cross section of fibers were carried out by a Model SU1510 scanning electron microscope (Hitachi, Tokyo, Japan). The samples were sputtered with gold before the SEM observation. The morphologies of the cross sections of samples were observed at a working voltage of 5 kV. Here, the fiber bundles first are embedded by using collodion. Then, cross-section slices were prepared by using Y172 Hardy's thin cross-section device (Changzhou Depu Textile Technology Co., Ltd., Changzhou, China).

Fourier Transform Infrared-Attenuated Total Reflection Spectroscopy
The spectra of Fourier transform infrared-attenuated total reflection (FTIR-ATR) were recorded on a Nicolet FTIR spectroscope (Nexus 670, Waltham, MA, USA). Each spectrum was recorded with a total of 16 scans from 4000 to 500cm −1 ; each scan had a resolution of 4 cm −1 at room temperature. The spectra were subtracted against a background air spectrum. OMNIC Nicolet Software (version 8.1) was used for spectra analysis.

Differential Scanning Calorimetry
The crystallization behaviors and melting behaviors of the samples were characterized by differential scanning calorimetry that used a DSC Q200 (TA Instruments ® , Inc., New Castle, DE, USA). Nitrogen was used at a flow rate of 50 mL/min. The instrument was calibrated with In and Pb. The weight of the samples was between 4 and 6 mg. Each sample was heated from 0 to 200 • C at 10 • C/min.

Scanning Electron Microscope
Scanning electron microscopy (SEM) measurements of the longitudinal surface and cross section of fibers were carried out by a Model SU1510 scanning electron microscope (Hitachi, Tokyo, Japan). The samples were sputtered with gold before the SEM observation. The morphologies of the cross sections of samples were observed at a working voltage of 5 kV. Here, the fiber bundles first are embedded by using collodion. Then, cross-section slices were prepared by using Y172 Hardy's thin cross-section device (Changzhou Depu Textile Technology Co., Ltd., Changzhou, China).

Fourier Transform Infrared-Attenuated Total Reflection Spectroscopy
The spectra of Fourier transform infrared-attenuated total reflection (FTIR-ATR) were recorded on a Nicolet FTIR spectroscope (Nexus 670, Waltham, MA, USA). Each spectrum was recorded with a total of 16 scans from 4000 to 500cm −1 ; each scan had a resolution of 4 cm −1 at room temperature. The spectra were subtracted against a background air spectrum. OMNIC Nicolet Software (version 8.1) was used for spectra analysis.

Conductive Properties
The conductive properties of the treated PLA fibers with high resistivity were tested by Keithley 65167B high resistance meter (Cleveland, OH, USA). The conductive properties of the treated PLA fibers with low resistivity were tested using a TENMARS TM-87 digital multimeter (Taipei, Taiwan). The length of the tested fibers is 0.08m. The electrical resistivity of the untreated PLA fibers was characterized by a YG321 fiber-specific resistance tester. Five gram samples were used every time.
The tests were carried out at room temperature with relative humidity of 65%.

Tensile Test
The tensile properties of PLA fibers were determined on an YG061-1500 yarn tensile tester (Laizhou Electron Instrument Co., Ltd., Laizhou, China) at room temperature. The cross-head speed and gauge length were 250 mm/min and 250 mm, respectively, and the pre-tension was 5 cN.  Figure 2c. The highly porous structure formed because of swelling and subsequent solvent-induced crystallization of PLA-POY fibers with low crystallinity [11].  The conductive properties of the treated PLA fibers with high resistivity were tested by Keithley 65167B high resistance meter (Cleveland, OH, USA). The conductive properties of the treated PLA fibers with low resistivity were tested using a TENMARS TM-87 digital multimeter (Taipei, Taiwan). The length of the tested fibers is 0.08m. The electrical resistivity of the untreated PLA fibers was characterized by a YG321 fiber-specific resistance tester. Five gram samples were used every time. The tests were carried out at room temperature with relative humidity of 65%.

Tensile Test
The tensile properties of PLA fibers were determined on an YG061-1500 yarn tensile tester (Laizhou Electron Instrument Co., Ltd., Laizhou, China) at room temperature. The cross-head speed and gauge length were 250 mm/min and 250 mm, respectively, and the pre-tension was 5 cN.  Figure 2c. The highly porous structure formed because of swelling and subsequent solvent-induced crystallization of PLA-POY fibers with low crystallinity [11].     However, the change of cross section of PLA-DTY fibers is difficult to observe. The effect of ethyl acetate on PLA-DTY fibers is small because PLA-DTY fibers own high crystallinity [11]. DTY is prepared by drawing and twisting/untwisting simultaneously POY so that PLA-DTY fibers own high crystallinity. PLA-DTY fibers. However, the change of cross section of PLA-DTY fibers is difficult to observe. The effect of ethyl acetate on PLA-DTY fibers is small because PLA-DTY fibers own high crystallinity [11]. DTY is prepared by drawing and twisting/untwisting simultaneously POY so that PLA-DTY fibers own high crystallinity. Figure

DSC Analysis
The original PLA-POY fibers, original PLA-DTY fibers, and the PLA fibers treated by MWCNTs and PVAc in ethyl acetate were analyzed by DSC. The DSC curves are shown in Figure 4. Figure 4a shows that in the DSC curve of PLA-POY fibers, the glass transition district, cold crystallization peak, and melting peak can be observed. In addition, the glass transition district and cold crystallization peak overlap partly in the range of 60 to 90 °C. However, in the DSC curves of the PLA-POY fibers treated by MWCNTs and PVAc in ethyl acetate, the glass transition temperature (Tg) and cold crystallization temperature (Tcc) disappear. This illustrates that compared with the original PLA-POY fibers, the crystallinity of the PLA-POY fibers treated by MWCNTs and PVAc in ethyl acetate increases. This is due to the ethyl acetate inducing the crystallization of PLA-POY fibers. However, Figure 4b shows that compared with the original PLA-DTY fibers, an obvious change in DSC curves of PLA-DTY fibers treated by MWCNTs and PVAc in ethyl acetate cannot be observed. This illustrates that the effect of ethyl acetate on the structure of PLA-DTY fibers is small because of their high crystallinity.

DSC Analysis
The original PLA-POY fibers, original PLA-DTY fibers, and the PLA fibers treated by MWCNTs and PVAc in ethyl acetate were analyzed by DSC. The DSC curves are shown in Figure 4. Figure 4a shows that in the DSC curve of PLA-POY fibers, the glass transition district, cold crystallization peak, and melting peak can be observed. In addition, the glass transition district and cold crystallization peak overlap partly in the range of 60 to 90 • C. However, in the DSC curves of the PLA-POY fibers treated by MWCNTs and PVAc in ethyl acetate, the glass transition temperature (T g ) and cold crystallization temperature (T cc ) disappear. This illustrates that compared with the original PLA-POY fibers, the crystallinity of the PLA-POY fibers treated by MWCNTs and PVAc in ethyl acetate increases. This is due to the ethyl acetate inducing the crystallization of PLA-POY fibers. However, Figure 4b shows that compared with the original PLA-DTY fibers, an obvious change in DSC curves of PLA-DTY fibers treated by MWCNTs and PVAc in ethyl acetate cannot be observed. This illustrates that the effect of ethyl acetate on the structure of PLA-DTY fibers is small because of their high crystallinity.

FTIR-ATR Analysis
The FTIR-ATR spectra of PLA-POY fibers treated by MWCNTs and PVAc in ethyl acetate with concentration of 8 mg/mL MWCNTs, original PLA-POY fibers, and PVAc are illustrated in Figure 5. In Figure 5, for PVAc, the peak at 1729 cm −1 corresponds to the amorphous C=O stretching. The

FTIR-ATR Analysis
The FTIR-ATR spectra of PLA-POY fibers treated by MWCNTs and PVAc in ethyl acetate with concentration of 8 mg/mL MWCNTs, original PLA-POY fibers, and PVAc are illustrated in Figure 5. In Figure 5, for PVAc, the peak at 1729 cm −1 corresponds to the amorphous C=O stretching. The vibration bands at 2970 cm −1 are ascribed to CH 3 asymmetric stretching. The band at 2926 cm −1 corresponds to CH 2 asymmetric stretching. The bands at 1433 and 1370 cm −1 correspond to asymmetic and symmetric bending vibrations of CH 3 , respectively. The peaks at 1225 and 1118 cm −1 are attributed to C-O-C asymmetric and symmetric vibrations, respectively. The peak at 946 cm −1 is assigned to CH bending vibration [15]. For PLA, the peak at 1749 cm −1 corresponds to C=O stretching. The bands at 2995 and 2945 cm −1 are attributed to CH 3 asymmetric and symmetric vibrating, respectively. The bands at 2881 cm −1 correspond to CH vibrating. The peaks at 1452 and 1382 cm −1 are assigned to CH 3 asymmetric deformation and CH 3 symmetric deformation, respectively. The peaks at 1359 or 1363 cm −1 are ascribed to CH deformation and crystalline CH 3 symmetric deformation. The peaks at 1181, 1128, 1083, and 1043 cm −1 correspond to C-O-C stretching, CH 3 rocking, C-O-C stretching, and C-CH 3 stretching, respectively [16]. Figure 5b shows that when the concentration of PVAc is 20 mg/mL, the FTIR-ATR spectra of the treated PLA-POY fibers are similar to those of the original PLA-POY fibers. However, when the concentration of PVAc is 40 mg/mL, the FTIR-ATR spectra of the treated PLA-POY fibers are similar to that of original PVAc. In addition, when the concentration of PVAc is 20 mg/mL, the C=O stretching band occurs at 1743 cm −1 , which is located at the middle district between the C=O stretching band of PLA and that of PVAc. Generally, FTIR-ATR is used to characterize the chemical structure of the surface of materials. This revealed that PLA-POY fibers are partly coated by PVAc or the PVAc layer on the surface of PLA-POY fibers is very thin. However, when the concentration of PVAc is 40 mg/mL, the C=O stretching band occurred at 1729 cm −1 , which is identical to the wavenumber of C=O in PVAc. This shows that the PLA-POY fibers have been coated completely by PVAc. The FTIR-ATR spectra of PLA-DTY fibers treated by MWCNTs and PVAc in ethyl acetate with the concentration of 8 mg/mL MWCNTs, original PLA-DTY, and PVAc are illustrated in Figure 6; similar results are found.

Conductive Properties
The conductive properties of PLA-POY and PLA-DTY fibers treated by MWCNTs and PVAc in ethyl acetate have been characterized by a Keithley 65167B high-resistance meter, TENMARS TM-87 digital multimeter, and YG321 fiber-specific resistance tester. The results of electrical conductivity are listed in Tables 1 and 2. It can be seen that the electrical conductivity of the treated PLA fibers is much higher than that of the untreated PLA fibers. The values of electrical conductivity of PLA fibers show that with the increase of the concentration of MWCNTs or PVAc, the electrical conductivity of PLA-DTY and PLA-POY fibers increases. However, when the concentration of MWCNTs is 2 mg/mL, with the increase of the concentration of PVAc from 10 to 20 mg/mL, the electrical conductivity of the treated PLA-POY and PLA-DTY fibers increased significantly from 1.2 × 10 −3 to 1.43 × 10 −2 μs/cm, 0.7 × 10 −3 to 8.3 × 10 −3 μs/cm, respectively, whereas with the increase in concentration of PVAc from 20 to 50 mg/mL, those of the PLA-POY and PLA-DTY fibers barely change from 1.43 × 10 −2 to 1.47 × 10 −2 μs/cm and 8.3 × 10 −3 to 8.9 × 10 −3 μs/cm, respectively. When the concentration of MWCNTs is more than 2 mg/mL, the effect of PVAc on with electrical conductivity of the treated PLA-POY and PLA-DTY fibers is obvious. However, when the concentration of PVAc reaches 40 mg/mL, with the further increase of the concentration of PVAc, the change of electrical conductivity of the treated PLA-POY and PLA-DTY fibers is small.

Conductive Properties
The conductive properties of PLA-POY and PLA-DTY fibers treated by MWCNTs and PVAc in ethyl acetate have been characterized by a Keithley 65167B high-resistance meter, TENMARS TM-87 digital multimeter, and YG321 fiber-specific resistance tester. The results of electrical conductivity are listed in Tables 1 and 2. It can be seen that the electrical conductivity of the treated PLA fibers is much higher than that of the untreated PLA fibers. The values of electrical conductivity of PLA fibers show that with the increase of the concentration of MWCNTs or PVAc, the electrical conductivity of PLA-DTY and PLA-POY fibers increases. However, when the concentration of MWCNTs is 2 mg/mL, with the increase of the concentration of PVAc from 10 to 20 mg/mL, the electrical conductivity of the treated PLA-POY and PLA-DTY fibers increased significantly from 1.2 × 10 −3 to 1.43 × 10 −2 µs/cm, 0.7 × 10 −3 to 8.3 × 10 −3 µs/cm, respectively, whereas with the increase in concentration of PVAc from 20 to 50 mg/mL, those of the PLA-POY and PLA-DTY fibers barely change from 1.43 × 10 −2 to 1.47 × 10 −2 µs/cm and 8.3 × 10 −3 to 8.9 × 10 −3 µs/cm, respectively. When the concentration of MWCNTs is more than 2 mg/mL, the effect of PVAc on with electrical conductivity of the treated PLA-POY and PLA-DTY fibers is obvious. However, when the concentration of PVAc reaches 40 mg/mL, with the further increase of the concentration of PVAc, the change of electrical conductivity of the treated PLA-POY and PLA-DTY fibers is small. When the concentration of PVAc is 10 mg/mL, with the increase of the concentration of MWCNTs from 2 to 4 mg/mL, the electrical conductivity of the treated PLA-POY and PLA-DTY fibers increases significantly from 1.2 × 10 −3 to 5.3 × 10 −3 µs/cm and 0.7 × 10 −3 to 2.7 × 10 −3 µs/cm, respectively; whereas, with the increase of the concentration of MWCNTs from 4 to 10 mg/mL, those of the PLA-POY and PLA-DTY fibers increase inapparently from 5.3 × 10 −3 to 7.7 × 10 −3 µs/cm, and 2.7 × 10 −3 to 4.8 × 10 −3 µs/cm, respectively. When the concentration of PVAc is 20 mg/mL, with the increase of the concentration of MWCNTs from 2 to 10 mg/mL, the electrical conductivity of the treated PLA-POY and PLA-DTY fibers almost does not change. However, when the concentration of MWCNTs is more than 30 mg/mL, the effect of MWCNTs on the electrical conductivity of the treated PLA-POY and PLA-DTY fibers is significant. However, when the concentration of MWCNTs is more than 8 mg/mL, with the further increase of the concentration of MWCNTs, the change of electrical conductivity of the treated PLA-POY and PLA-DTY fibers is not obvious.
Here, MWCNTs are used as the conductive additives. Therefore, with the increase in the concentration of MWCNTs, the conductive network can easily form so that the conductive properties increase. PVAc is used as a dispersing agent to make the MWCNTs disperse uniformly in ethyl acetate. Therefore, with the increase of PVAc, MWCNTs can be efficiently used by dispersing MWCNTs uniformly in ethyl acetate so that the conductive properties increase. When the concentration of MWCNTs is low (2 mg/mL), the PVAc concentration of 10 mg/mL is enough large to make MWCNTs disperse uniformly in ethyl acetate, so that further increasing the concentration of PVAc cannot improve the conductivity of the PLA fibers. In addition, when the concentration of PVAc is low (less than 20 mg/mL), it is difficult to make a large number of MWCNTs uniformly in ethyl acetate. Therefore, MWCNTs cannot be used efficiently, thus further increasing the concentration is meaningless.  Table 3. As can be seen in Figure 7, the original PLA-POY fibers and treated PLA-POY fibers present a typical tough fracture. It can be seen from Figure 7 and Table 3 that the tensile force of the treated PLA-POY fibers is much higher than that of the original PLA-POY fibers. The reason is as follows; the PLA-POY fibers have relatively low crystallinity when the PLA-POY fibers are treated by MWCNTs and PVAc in ethyl acetate. The ethyl acetate first will make amorphous district of the PLA-POY fibers swell. Then, when the PLA-POY fibers are taken out from the solution, ethyl acetate will evaporate to induce crystallization of PLA-POY fibers to form a highly porous structure, which makes the tensile force decrease obviously. the tensile force of the treated PLA-POY fibers is much higher than that of the original PLA-POY fibers. The reason is as follows; the PLA-POY fibers have relatively low crystallinity when the PLA-POY fibers are treated by MWCNTs and PVAc in ethyl acetate. The ethyl acetate first will make amorphous district of the PLA-POY fibers swell. Then, when the PLA-POY fibers are taken out from the solution, ethyl acetate will evaporate to induce crystallization of PLA-POY fibers to form a highly porous structure, which makes the tensile force decrease obviously.   Figure 7a and Table 3 illustrate that when the concentration of PVAc is 30 mg/mL, the effect of MWCNTs concentration on tensile properties of PLA-POY fibers is small. However, Figure 7b and Table 3 show that when the concentration of MWCNTs is 8 mg/mL, with the increase of PVAc concentration from 10 to 50 mg/mL, the tensile force, strain, and work of rupture of the PLA-POY fibers increase from 211 to 401 cN, 41% to 87%, and 0.2 to 0.6 J, respectively. The reason is as follows; PVAc and PLA are compatible completely when the PLA-POY fibers are treated by MWCNTs and PVAc in ethyl acetate. The PVAc will coat the PLA-POY fibers and fill the pores to improve the tensile property of PLA-POY.

Tensile Properties
In addition, the curve of the PLA-POY fibers treated by MWCNTs and PVAc in ethyl acetate with 8 mg/mL MWCNTs and 10 mg/mL (OC8P10) is different from those of the PLA-POY fibers treated by MWCNTs and PVAc in ethyl acetate with more than 20 mg/mL. The latter owns an obvious stress-hardening district, whereas the stress-hardening district cannot be observed in the   Figure 7a and Table 3 illustrate that when the concentration of PVAc is 30 mg/mL, the effect of MWCNTs concentration on tensile properties of PLA-POY fibers is small. However, Figure 7b and Table 3 show that when the concentration of MWCNTs is 8 mg/mL, with the increase of PVAc concentration from 10 to 50 mg/mL, the tensile force, strain, and work of rupture of the PLA-POY fibers increase from 211 to 401 cN, 41% to 87%, and 0.2 to 0.6 J, respectively. The reason is as follows; PVAc and PLA are compatible completely when the PLA-POY fibers are treated by MWCNTs and PVAc in ethyl acetate. The PVAc will coat the PLA-POY fibers and fill the pores to improve the tensile property of PLA-POY.
In addition, the curve of the PLA-POY fibers treated by MWCNTs and PVAc in ethyl acetate with 8 mg/mL MWCNTs and 10 mg/mL (OC8P10) is different from those of the PLA-POY fibers treated by MWCNTs and PVAc in ethyl acetate with more than 20 mg/mL. The latter owns an obvious stress-hardening district, whereas the stress-hardening district cannot be observed in the former, because the content of PVAc in the former is low. This further shows that the PVAc and PLA fibers have good adhesive force. PVAc can improve the tensile properties of highly porous PLA-POY fibers. Figure 8 illustrates the curves of load-strain relationship of PLA-DTY fibers treated by MWCNTs and PVAc in ethyl acetate. The values of tensile force (F), elongation at break (ε), and work of rupture (W) are listed in Table 4. Figure 8 shows that the curve of original PLA-DTY fibers has a similar shape to those of the treated PLA-DTY fibers; they present a typical tough fracture. It can be seen from Figure 8 and Table 4 that the tensile force of the treated PLA-DTY fibers is larger than that of original PLA-DTY fiber. The reason is as follows; the effect of ethyl acetate on PLA-DTY is small, and the PVAc on the surface of PLA-DTY fiber can improve the mechanical properties. However, Figure 8b shows that with the increase of PVAc, the tensile properties of the treated PLA-DTY fibers almost do not change. has a similar shape to those of the treated PLA-DTY fibers; they present a typical tough fracture. It can be seen from Figure 8 and Table 4 that the tensile force of the treated PLA-DTY fibers is larger than that of original PLA-DTY fiber. The reason is as follows; the effect of ethyl acetate on PLA-DTY is small, and the PVAc on the surface of PLA-DTY fiber can improve the mechanical properties. However, Figure 8b shows that with the increase of PVAc, the tensile properties of the treated PLA-DTY fibers almost do not change.  It can be seen from Table 3 that for PLA-POY, the tensile properties of the treated PLA fibers are much smaller than those of the untreated PLA fibers. However, it is exciting that OC8P40 and OC8P50, both with high electrical conductivity, own high tensile properties (Tables 1 and 3). For PLA-DTY, although the tensile properties of the treated PLA fibers are much larger than those of the untreated PLA fibers (Table 4), the TC8P50 with the highest electrical conductivity does not have the highest strength (Tables 2 and 4). However, the difference between the tensile strength of TC8P50 and the highest strength is small. Therefore, it can be concluded that PLA-POY and PLA-DTY, both with high electrical conductivity, own satisfactory tensile properties.  It can be seen from Table 3 that for PLA-POY, the tensile properties of the treated PLA fibers are much smaller than those of the untreated PLA fibers. However, it is exciting that OC8P40 and OC8P50, both with high electrical conductivity, own high tensile properties (Tables 1 and 3). For PLA-DTY, although the tensile properties of the treated PLA fibers are much larger than those of the untreated PLA fibers (Table 4), the TC8P50 with the highest electrical conductivity does not have the highest strength (Tables 2 and 4). However, the difference between the tensile strength of TC8P50 and the highest strength is small. Therefore, it can be concluded that PLA-POY and PLA-DTY, both with high electrical conductivity, own satisfactory tensile properties.

Conclusions
The conductive PLA-POY and PLA-DTY fibers are produced successfully by coating method using ethyl acetate as solvent, MWCNTs as conductive filler, and PVAc as dispersing agent and coating agent. The PLA fibers are characterized by SEM, FTIR, DSC, resistance meter, and tensile test. The larger the PVAc concentration is, the more uniformly the MWCNTs disperse in ethyl acetate. MWCNTs have successfully coated the surface of PLA-POY and PLA-DTY fibers. The highly porous structures form when PLA-POY fibers are treated by ethyl acetate, decreasing the tensile forces. The tensile force of original PLA-POY fibers is 566 cN, whereas that of the treated PLA-POY fibers ranges from 211 to 401 cN. However, the PVAc can improve the tensile force of the treated PLA-POY fibers. When the concentration of MWCNTs is 8 mg/mL, coupled with the increase of PVAc concentration from 10 to 50 mg/mL, the tensile force of the PLA-POY fibers increases from 211 to 401 cN. For PLA-DTY fibers, the effect of ethyl acetate on surface morphology is small. Therefore, the treated PLA-DTY fibers own higher tensile properties. With the increase of PVAc and MWCNTs, the conductive properties of the PLA fibers increase. The electrical conductivity of PLA-POY and PLA-DTY fibers can reach 0.53 and 0.13 µs/cm, respectively.