Accepted Manuscript

A flexible and transparent thin film heater based on a carbon fiber /heat-resistantcellulose composite

Pengbo Lu, Fan Cheng, Yanghao Ou, Meiyan Lin, Lingfeng Su, Size Chen, XilangYao, Detao Liu

PII: S0266-3538(17)31739-6

DOI: 10.1016/j.compscitech.2017.09.033

Reference: CSTE 6923

To appear in: Composites Science and Technology

Received Date: 18 July 2017

Revised Date: 5 September 2017

Accepted Date: 11 September 2017

Please cite this article as: Lu P, Cheng F, Ou Y, Lin M, Su L, Chen S, Yao X, Liu D, A flexible andtransparent thin film heater based on a carbon fiber /heat-resistant cellulose composite, CompositesScience and Technology (2017), doi: 10.1016/j.compscitech.2017.09.033.

This is a PDF file of an unedited manuscript that has been accepted for publication. As a service toour customers we are providing this early version of the manuscript. The manuscript will undergocopyediting, typesetting, and review of the resulting proof before it is published in its final form. Pleasenote that during the production process errors may be discovered which could affect the content, and alllegal disclaimers that apply to the journal pertain.

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

1

A Flexible and Transparent Thin Film Heater Based on a Carbon Fiber /Heat-resistant 1

Cellulose Composite 2

Pengbo Lu, Fan Cheng, Yanghao Ou, Meiyan Lin, Lingfeng Su, Size Chen, Xilang Yao, Detao 3

Liu* 4

State Key Laboratory of Pulp and Paper Engineering, South China University of Technology, 5

Guangzhou 510640, P. R. China 6

Abstract: The thin flexible film heater made of carbon fibers is widely considered to be an ideal 7

material for the use as self-heating devices because of its safe, low-cost, no noises, small size and 8

fast heating as well as energy saving. Presently thin flexible film heater is mostly fabricated by 9

mixing method using the long cellulose fibers as film-forming materials and carbon fibers as 10

self-heating materials, which mostly suffer from opaque or uneven heating field. In this work, we 11

firstly reported a flexible and transparent thin film heater (FTFH) composed of carbon fibers and 12

regenerated cellulose. The use of regenerated cellulose for membrane materials brings high 13

transmittance, strong adhesion, fast temperature response and high generated temperature. More 14

importantly, the FTFH using novel carbon fibers as self-heating materials and regenerated 15

cellulose as membrane materials show a rapid heating response (12 s), higher power density (2577 16

w/m2) and long-term stability of generated temperature (162.3 �). 17

Keywords: Carbon fibers; Flexible composites; Mechanical properties; Thermal properties 18

19

20

1. Introduction 21

*Corresponding author. Tel.: +86 182 0764 1980 Email: dtliu@scut.edu.cn(Dt.L)

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

2

In recent years, design and fabrication of FTFH have attracted significant attentions from 22

both academic and industrial interests [1]. Due to high efficiency in converting electric energy into 23

heat energy, FTFH is widely used in snow-cleaning device, thermal therapies or heating outdoor 24

displays [2-4]. Several emerging materials, including indium tin oxide (ITO), carbon nanotube, 25

metal grids, and grapheme have been studied as self-heating material in FTFH [5-8]. However, 26

their inferior performance and high-cost limit its further application in the next-generation devices. 27

Compared to the other self-heating material in FTFH, carbon fibers were widely considered to be 28

an ideal self-heating materials for use in FTFH because of its high generated temperature, low 29

density, high strength, easy processing and low-cost [9].In particular, much effort has been 30

focused on incorporating carbon fibers into membrane materials, such as cellulose and resin 31

[10,11]. Compared with the other thin flexible film heater, carbon fibers paper (CFP) has been 32

widely used as the thin flexible film heater due to its easy handling, low-cost and high heat 33

generation efficiency [12]. Whereas, research efforts at CFP have encountered numerous problems 34

because the long carbon fibers with high-surface-energy made the CFP opaque and uneven 35

temperature field [13]. Among known strategies for FTFH based on a carbon fiber as the 36

self-heating material, the main membrane materials for it are resin or plant fiber [14]. However, 37

there are several obstacles for these membrane materials to overcome before wide application in 38

thin flexible film heater. For example, the resin can be easily fabricated as a uniform film, but the 39

properties of resin made the thin flexible film heater inflexible [15]. The thin flexible film heater 40

using plant fiber as membrane materials have shown excellent heating performance. However, the 41

poor adhesion of carbon fiber network with the plant fibers made the thin flexible film heater poor 42

mechanical properties and the long fibers made it opaque [16]. Yet, the flexible and transparent 43

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

3

thin film heater with high transmittance (>90%), strong adhesion and fast temperature response 44

can be obtained by means of comprising Ag nanowires (NWs) in an ultrathin polyimide (PI) foil, 45

the process of this flexible and transparent thin film heater is complex and the cost is huge [17]. 46

Contrary to the other membrane materials, the regenerated cellulose is advantageous for practical 47

applications of the flexible and transparent thin film heater, since it will lead to much higher 48

transparency and tensile strength [18]. For this reason, the work presented herein is devoted to 49

obtaining a flexible and transparent thin film heater based on the carbon fiber /heat-resistant 50

cellulose composite by using a very simple and low-cost method. 51

In this paper, we reported a FTFH using regenerated cellulose as a membrane material and 52

carbon fibers as self-heating material. Our FTFH has the following advantages over previously 53

reported materials: (1) The FTFH exhibited uniform heating and rapid thermal response because 54

the regenerated cellulose with a large number of hydroxyl made the carbon fibers disperse evenly. 55

(2) Tensile property and optical transmission have been greatly improved owing to the regenerated 56

cellulose with small size. (3) The FTFH can reach to higher power density and generated 57

temperature. 58

59

60

2 Materials and methods 61

2.1 Materials 62

Commercial eucalyptus dissolving pulp was used as the raw cellulose source material was 63

purchased from Guangzhou Chenhui Paper Co., Ltd. (China). The 6 mm-length carbon fibers were 64

provided by Shanghai Lishuo Co., Ltd. (China); N, N-Dimethylacetamide (DMAC), lithium 65

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

4

chloride (LiCl), supplied by Aladdin-Reagent Co., Ltd. (Shanghai China). Commercial eucalyptus 66

dissolving pulp, DMAC, LiCl, acetone, were used to prepare regenerated cellulose. All the 67

reagents were used as received without further purification. 68

69

2.2 The dissolution of regenerated cellulose 70

The solvent of cellulose was synthesized by according previously reported literature [19]. A 71

specified amount of eucalyptus dissolving pulp was pre-treated by immersing it in acetone for 5 72

min at 25 � and subsequent dissolution of cellulose in 8% LiCl/DMAc (wt/v) solvent through 73

continuous stirring under the anhydrous condition. The process to fully dissolve the cellulose 74

fibers in the LiCl/DMAc took about 3 h at 40 �. Then the cellulose solution was added dropwise 75

into the stirring deionized water at a rate of 20 ml/min to produce the regenerated cellulose. The 76

deionized water was stirred at 5000 r/min to generate strong shear forces and prevent 77

agglomeration using an emulsification machine (Shanghai Yingdi Automation Inc., China). By 78

doing this, the solution of regenerated cellulose was obtained. 79

80

2.3 Fabrication of FTFH 81

The method of fabrication for FTFH is briefly described as below. The solution of regenerated 82

cellulose and carbon fibers were dispersed evenly in deionized water by agitating the mixture 83

using a mixer (Shanghai Yingdi Automation Inc., China). The FTFH was prepared by filtering 84

above mixture onto a glass filter with a nylon fabric membrane (pore size: 38 µm). The obtained 85

wet FTFH was repeatedly washed with deionized water to eliminate the residual LiCl or DMAc 86

and then was sandwiched between two stacks of regular filter paper to dry under o.4 MPa pressure 87

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

5

at 110 � for 5 min. The FTFH with base density of 37 g/m2 was obtained using the 88

above-mentioned method. 89

90

2.4 Characterizations 91

The structure of the FTFH was studied with a scanning electron microscope (SEM). 92

JEM-100CXII at an accelerating voltage of 10 kV. Prior to the examination, the surface of the 93

specimen was coated with a thin layer of gold, ~20 nm. 94

A KajaaniFS300 Fiber Analyzer was used to quantitatively analyze the dimensions of the 95

regenerated cellulose fibers in the DI water solution and the original cellulose fibers in DI water 96

solution. 97

The mechanical strength of samples was measured using a universal tensile tester (Instron5565, 98

Instron instruments Inc. USA). Samples were firstly cut to 15.0 mm×50.0 mm and placed in 99

constant temperature and humidity chamber at (50±1) % relative humidity (RH) and (23±1) � for 100

24 h to ensure the stabilization of their water content before characterization. 101

UV-Vis spectrometer with an integrating sphere (UV-9000 Shanghai Yuanyi Inc. China) with an 102

integrating sphere was used to measure the total transmittance of the FTFH in a wavelength range 103

of 400 nm to 900 nm. 104

The resistances of the FTFH were recorded by a multimeter (VC890D, China). Samples were 105

firstly cut to 80.0 mm×80.0 mm and placed in constant temperature and humidity chamber at 106

(50±1) % relative humidity (RH) and (23±1) � for 24 h to ensure the stabilization of their water 107

content before characterization. 108

The temperatures and heat distributions of the FTFH were measured using CEM infrared 109

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

6

thermal image (DT-980, China). Samples were firstly cut to 80.0 mm×80.0 mm and placed in 110

constant temperature and humidity chamber at (50±1) % relative humidity (RH) and (23±1) � for 111

24 h to ensure the stabilization of their water content before characterization. The applied DC 112

voltage was supplied by a power supply (HY3005ET, China) to the heater through two copper 113

conductive tapes pasted at the FTFH edges. 114

115

3. Results and discussion 116

3.1 Reaction Principle Analysis 117

118

119

120

Fig. 1. Schematic illustration of the procedure of FTFH. (a) The structure of original cellulose 121

fibers. (b) The structure of regenerated cellulose. (c) The dissolution of regenerated cellulose and 122

the carbon fibers. (d) The FTFH. 123

124

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

7

125

Cellulose is ideal membrane materials for FTFH due to its easy processing, low-cost, good 126

chemical and biodegrading properties [20]. However, since the original CFP is made of cellulose 127

fibers with diameters of ~20 mm, there are intrinsic disadvantages regarding original CFP. The 128

difference in refractive index between air in pores and the cellulose fibers results in the opaque of 129

the original CFP [21]. The long cellulose fibers also limit its overall mechanical properties due to 130

the tiny amounts of hydrogen bonds. Compared to the CFP made of long cellulose fibers, the 131

FTFH made of regenerated cellulose is recently attracting great attentions by providing excellent 132

mechanical properties, optical transparency [22]. A homogeneous cellulose solution was obtained 133

for preparing the FTFH [23-25]. Subsequently, the regenerated cellulose was obtained by a 134

debonding procedure. The obtained cellulose solution was slowly dropped into the stirring 135

deionized water under the action of high-speed shear force. The hydrogen bond network between 136

the cellulose chains broke again due to the attack from water molecules. The dissolution of 137

regenerated cellulose was prepared because of the interactions between the solvent 138

[26].Afterwards, the carbon fibers with an average length of 6 mm were homogeneously dispersed 139

in the solution of regenerated cellulose. The dispersing performance of carbon fibers is usually 140

unsatisfactory due to carbon fibers with less active groups [27]. In our work, the solution of 141

regenerated cellulose provides an excellent environment for dispersion of carbon fibers because 142

regenerated cellulose has many hydroxyl bonds. The solution with many hydroxyls made the 143

carbon fibers more difficult to flocculate. After that, the wet FTFH was obtained by random 144

deposition of the nylon fabric membrane through vacuum filtration. The FTFH have homogeneous 145

structures, glossy and excellent mechanical properties with acceptable elastic properties. The 146

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

8

reasons for that is the regenerated cellulose with many hydroxyl bonds is considered as the 147

adhesive to bond the neighboring carbon fibers. It was noted that the produced fines (fiber length 148

less than 200 µm) in the regenerate process increased the packing density and filled in the voids 149

between carbon fibers, which undoubtedly increased the packing area and caused the FTFH to 150

exhibit high mechanical strength, acceptable elastic properties and transparency. 151

152

3.2 Properties of transparent paper 153

154

155

156

Fig. 2. SEM images of the film samples. SEM micrographs of cross-sections: (a) Original 157

paper. (c) RCF. (e) FTFH; SEM micrographs of the fracture surface. (b) Original paper. (d) RCF. 158

(f) FTFH. 159

160

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

9

161

Table 1. Fiber dimension of regenerated cellulose and the original pulp fibers. 162

163

In order to investigate the properties of the samples, the structure of the samples was examined 164

with a scanning electron microscope (SEM). The differences from the ideal structure of original 165

paper to the FTFH samples were distinctly observed from SEM images by scanning cross-sections 166

and fracture surface. The original paper was loosely composed of large pores and long cellulose 167

fibers. The difference in refractive index between air in pores and the basic cellulose results in the 168

opaque of the original paper [28]. The images of original paper made by commercial eucalyptus 169

dissolving pulp through the traditional method were shown (Fig 2a-b). Compared with the images 170

of the film only made from regenerated cellulose (RCF), there is a significant difference between 171

two kinds of film. The film only made from regenerated cellulose (RCF) has no obvious pores on 172

the surface as shown in the SEM image (Fig. 2c). The flat smooth surface of the RCF indicated 173

that the regenerated cellulose is small in size. The regenerated cellulose with small size is highly 174

desirable for achieving good optical and mechanical properties of the resulting thin flexible heater. 175

This RCF also is denser than the original paper sample because the space between regenerated 176

cellulose is smaller than the long cellulose fibers. The images of FTFH were shown (Fig 2e-f). It 177

is clear that the carbon fibers and the regenerated cellulose are well combined with each other. The 178

regenerated cellulose in small size filled out the pores between the carbon fibers and glued on the 179

skeleton of the carbon fibers made the thin flexible film heater is more compact [29]. When the 180

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

10

dosage of carbon fibers increased, this made the crossed network in the film more intensive, which 181

led to the increase in the generated temperature while the transmittance declined for the FTFH. 182

The fiber dimensions for both regenerated cellulose fibers and original pulp fibers were 183

presented in table 1. The regenerated cellulose fibers have an average fiber length of 0.84 mm and 184

an average fiber width of 12.09 µm, which is slightly smaller than original pulp fibers. 185

Regenerated cellulose fibers have a higher curl index (24.56%) but a lower kink index (1063.58 186

1/m) compared to original pulp fibers, which explain the curvy and weavable nature of the 187

regenerated cellulose fibers. The fine content of the regenerated cellulose fibers (fiber length less 188

than 200 µm, 32.33%) is much than higher than that of original pulp fibers (8.31%). Therefore, the 189

basic hydroxyl groups on the surface of the regenerated cellulose fibers enable them to bond 190

tightly through hydrogen bonding pathways, which is similar to the original paper and nanopaper. 191

192

193

Fig. 3. The digital images of the RCF, the FTFH-4% and the optical transmittance plot for the 194

conductive nanopaper, RCF, the FTFH-4% and the FTFH -8%. 195

196

197

The optical properties of RCF, the FTFH-4% and the FTFH-8% were compared with a 198

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

11

conductive nanopaper [30] [Fig.3c]. The transmittance of the RCF made by regenerated cellulose 199

at 550 nm reaches up to 63%, which is lower than the conductive nanopaper (81%). The 200

conductive nanopaper is a transparent film made of network-forming nanocellulose fibers and Ag 201

nanowire. These materials are several micrometers long with a diameter of 4–50 nm [31]. As the 202

fiber diameter decreases, the optical transmittance of the film increases [32]. In comparison, 203

although the transmittance of the RCF is lower than the conductive nanopaper, the method of 204

fabrication RCF is greatly easier than the conductive nanopaper and the cost is lower. The 205

meaning of the FTFH-4% is that the sample contains 4% carbon fiber, and the same suits for 206

FTFH-8%. As the content of carbon fibers increases, the optical transmittance of the FTFH 207

decreases. When the content of the carbon fibers is 8%, the transmittance of the film decreases to 208

16%. The reason for the decrease in transparency of FTFH is that the light is hard to penetrate 209

through carbon fibers network. 210

211

212

213

Fig. 4. (a)Stress-strain curves of the Original paper, the RCF, the FTFH -4% and the FTFH 214

-8%. (b)X-ray diffraction profiles of original paper and the RCF. 215

216

The mechanical properties of FTFH play a significant role for the comprehensive device. To 217

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

12

examine the suitability of the samples for industrial applications, the mechanical properties of the 218

original paper, the RCF, the FTFH -4% and the FTFH -8% were determined (Fig.4a). It can be 219

seen that the RCF made from regenerated cellulose caused the most excellent tensile strength, 220

which was suggested by the highest tensile stress (34 MPa). As the content of carbon fibers 221

increases, the tensile stress of the FTFH decreases. The reason for the decrease in the tensile stress 222

of the FTFH is that the carbon fibers with less active groups are difficult to intertwine with 223

regenerated cellulose fibers. The XRD patterns from experiments for the sake of comparison 224

between the original paper and the RCF (Fig.4b). The XRD patterns of the original paper exhibit 225

obvious diffraction peaks at 14.86° and 22.75°, which correspond to the crystalline form of 226

cellulose-I. The RCF shows the diffraction peaks of cellulose II as indicated by the appearance of 227

a board peak at 2θ=20.2°. During regeneration, the dissolving of cellulose fibers in a solvent, 228

which is the main polymorphic modification of cellulose, causes a rearrangement of the crystal 229

packing of chains from native cellulose I to cellulose II. 230

231

232

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

13

233

234

Fig. 5. (a) A digital image of FTFH which illustrates its excellent optical and conductive 235

properties. (b)The power density of FTFH and the CFP; (c) the resistance of FTFH and the CFP 236

with the content of carbon fibers ranging from 4% to 12%; (d) the generated temperature of the 237

FTFH with the carbon fibers content of 12% at various voltages ranging from 5 V to 30 V. 238

239

240

The performance of the power density of FTFH was compared with CFP that composed of long 241

cellulose fibers and carbon fibers with the same length [Fig.5b] [33]. And the resistance of FTFH 242

and the CFP with the content of carbon fibers ranging from 4% to 12% were shown [Fig.5c]. As 243

the content of carbon fibers increases, the power density of FTFH increases and the resistance of 244

the FTFH decrease. It can be observed that the FTFT exhibited a higher power density compared 245

to the CFP. When the content of carbon fibers is 12%, the power density can reach to 2577 w/m2, 246

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

14

which is higher than the CFP. The improved power density of the FTFH could be mainly 247

attributed to the compact contact between carbon fibers and good adhesion of the carbon fibers to 248

the substrate. The generated temperature of the FTFH with the carbon fibers content of 12% at 249

various voltages were shown [Fig.5d]. When the voltages were set as 5, 10, 15, 20, 25 and 30 V, 250

the FTFH can reach to the temperature of 33.5, 41.9, 67.5, 90.6, 128.3 and 162.3�, respectively. 251

Therefore, the same FTFH could be used to meet different temperature requirements by simply 252

applying an appropriate voltage. Contrary to the long cellulose fibers, the network of carbon fibers 253

can be formed easily due to the regenerated cellulose with small size in FTFH. These results 254

indicate that the use of regenerated cellulose as membrane materials has enormous potential in the 255

fabrication of FTFH. 256

257

258

259

260

261

Fig. 6. (a) Digital image of the FTFH with carbon fibers content 2 %; The infrared thermal 262

images of the film samples, the CFP with carbon fibers content of (b) 4%, (c) 8% and (d) 12%, the 263

FTFH with carbon fibers content of (e) 4%, (f) 8% and (g) 12%. 264

265

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

15

The temperature evolution of the FTFH and the CFP with carbon content fibers of 4%, 8% and 266

12% were shown in Fig 6, respectively. All samples were driven at 20 V for 12 s. One of the 267

intriguing properties of the thin flexible film heater is their high heat generation efficiency. By 268

passing the current through the FTFH, they could be quickly heated from room temperature to a 269

steady temperature of 36.3 �, 59.9 � and 88.2 �, respectively. The presence of high generated 270

temperature will be desirable for self-heating heater devices. As the content of carbon fibers 271

increases, the generated temperature of the FTFH increases. The results indicated that the 272

generated temperature of the FTFH is tuned depending on the content of the carbon fibers. 273

Compared with the CFP with the same length and content of carbon fibers, the generated 274

temperature of FTFH is significantly higher than it. Its good heating performance was attributed to 275

its low resistance of the FTFH, which was improved by introducing regenerated cellulose with 276

small size enabling enhanced overlapping between the carbon fibers. Therefore, we propose that 277

the FTFH with industrially scalable could be fabricated, revealing a bright application prospect in 278

a large-areas heating production, such as heating in outdoors displays, defogging in vehicles, or 279

thermal therapies. 280

281

282

283

Fig. 7. (a) The generated temperature - response time of the FTFH and the CFP with the content 284

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

16

of 12% at 20 V; (b) the resistance - time of the FTFH with various carbon fibers content. 285

286

287

The response time is also an important part to evaluate the performance of the thin flexible film 288

heater. Both the FTFH and the CFP can reach to saturation temperature in 12 s. The results proved 289

that the carbon fibers are good self-heating material to use in the thin flexible film heater. The 290

stability of the resistance of the thin flexible film heater is essential for the sake of safety. To 291

examine the stability of the resistance of FTFH for safety, the change of the resistance of the 292

FTFH along the time was determined (Fig.7b). The resistance is no obvious change along the time. 293

Only when the first thirty minutes the resistance slightly increased due to the rise of the 294

temperature of the FTFH. Then the resistance maintains a steady value in about two hours. The 295

properties of the FTFH meet the requirement of the use of the thin flexible film heater due to 296

shorter response time, the stability of the resistance and higher generated temperature. 297

298

4. Conclusions 299

300

The FTFH with high optimal transmittance, excellent tensile strength, and higher generated 301

temperature has been successfully fabricated using novel carbon fibers as self-heating material and 302

regenerated cellulose as membrane materials. The FTFH based on carbon fibers-regenerated 303

cellulose composite generated hot temperature saturation up to 162 � at 30 V, exhibits shorter 304

response time and long-term stability of resistance. The performance attributes of FTFH are all 305

higher than the previously reported CFP. These results suggest that the use of regenerated 306

cellulose as membrane materials has enormous potential in the fabrication of FTFH. For device 307

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

17

applications, the FTFH should be a suitable material as outdoor display panels, defrosters in 308

vehicles, and other devices experiencing large temperature variations. This work is expected to be 309

helpful for the development of the flexible and transparent thin film heater for the fabrication of 310

large-scale, uniform film heaters. 311

312

313

314

315

316

317

318

319

320

321

322

323

324

325

326

327

Acknowledgments 328

This work was supported by funding received from State Key Laboratory of Pulp and Paper 329

Engineering (Grant No. 2016C08), Guangzhou Science and Technology Plan Project (Grant 330

No.201704030066), kindly supported by Guangdong Province Youth Science and Technology 331

Innovation Talents (Grant No. 2014TQ01C781) and the Fundamental Research Funds for the 332

Central Universities (Grant No.2017ZD087) South China University of Technology. 333

334

335

336

337

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

18

338

339

340

341

342

343

344

345

346

347

348

349

350

351

352

353

354

355

356

357

358

359

360

361

362

363

364

References: 365

[1]. Yuan, Q.; Fu, F. Application of Carbon Fiber Paper in Integrated Wooden Electric Heating 366

Composite. BIORESOURCES 2014, 9. 367

[2]. Liou, G.S.; Chou, C.Y.; Liu, H.S. Highly Transparent Silver Nanowires-Polyimide Electrode for 368

Snow-Cleaning Device. RSC ADV 2016, 6. 369

[3]. Jun, B.J.; Chu, L.S.; Han, G.H.; Woo, J.Y.; Loc, D.D.; Sung, K.E.; Jin, C.S.; Quang, H.T.; 370

Nguyen, V.L.; Hee, L.Y. Heat Dissipation of Transparent Graphene Defoggers. ADV FUNCT 371

MATER 2012, 22, 4819-4826. 372

[4]. Jun, B.J.; Chu, L.S.; Han, G.H.; Woo, J.Y.; Loc, D.D.; Sung, K.E.; Jin, C.S.; Quang, H.T.; 373

Nguyen, V.L.; Hee, L.Y. Heat Dissipation of Transparent Graphene Defoggers. ADV FUNCT 374

MATER 2012, 22, 4819-4826. 375

[5]. Camilli, L.; Pisani, C.; Passacantando, M.; Grossi, V.; Scarselli, M.; Castrucci, P.; De Crescenzi, 376

M. Pressure-dependent electrical conductivity of freestanding three-dimensional carbon nanotube 377

network. APPL PHYS LETT 2013, 102, 787. 378

[6]. Kang, T.J.; Kim, T.; Seo, S.M.; Park, Y.J.; Yong, H.K. Thickness-dependent thermal resistance of 379

a transparent glass heater with a single-walled carbon nanotube coating. CARBON 2011, 49, 380

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

19

1087-1093. 381

[7]. Sui, X.M.; Greenfeld, I.; Cohen, H.; Zhang, X.H.; Li, Q.W.; Wagner, H.D. Multilevel composite 382

using carbon nanotube fibers (CNTF). Composites Science & Technology 2016, 137, 35-43. 383

[8]. Li, G.; Tian, X.; Xu, X.; Zhou, C.; Wu, J.; Li, Q.; Zhang, L.; Yang, F.; Li, Y. Fabrication of robust 384

and highly thermally conductive nanofibrillated cellulose/graphite nanoplatelets composite papers. 385

Composites Science & Technology 2017, 138, 179-185. 386

[9]. Zhou, J.; Wu, L.; Lan, X.Z.; Zhang, Q.L.; Chen, X.Y.; Zhao, X.C. Research on Electrothermal 387

Properties of a Composite Carbon Fiber Paper. Materials Science Forum 2012, 724, 420-424. 388

[10]. Chung, D.D.L. Self-heating structural materials. Smart Materials & Structures 2004, 13, 562. 389

[11]. Zhang, H.; Ma, Y.; Tan, J.; Fan, X.; Liu, Y.; Gu, J.; Zhang, B.; Zhang, H.; Zhang, Q. Robust, 390

self-healing, superhydrophobic coatings highlighted by a novel branched thiol-ene fluorinated 391

siloxane nanocomposites. Composites Science & Technology 2016, 137, 78-86. 392

[12]. Yuan, C.J.; Wang, C.L.; Wu, T.Y.; Hwang, K.C.; Chao, W.C. Fabrication of a carbon fiber paper 393

as the electrode and its application toward developing a sensitive unmediated amperometric 394

biosensor. BIOSENS BIOELECTRON 2011, 26, 2858. 395

[13]. Huang, H.; Huang, K. Carbon fiber composite materials and carbon fiber paper technology. China 396

Pulp & Paper Industry 2014. 397

[14]. Park, S.J.; Kim, B.J. Carbon Fibers and Their Composites: Springer Netherlands; 2015. p. 398

275-317. 399

[15] Jiang, H.; Wang, S.; Qi, F.; Li, J.; Zhang, Q.; Zhang, J.; Gao, S. Comparison on Phenolic Resin 400

Ablative Composites Reinforced by Different Kinds of Carbon Fibers. Engineering Plastics 401

Application 2012. 402

[16]. Hu, Z.J. Research on Surface Treatment of Carbon Fiber and the Conductive Properties of Paper. 403

Advanced Materials Research 2012, 424-425, 1007-1010. 404

[17]. Ghosh, D.S.; Chen, T.L.; Mkhitaryan, V.; Pruneri, V. An ultrathin transparent conductive 405

polyimide foil embedding silver nanowires. ACS APPL MATER INTER 1944, 6, 20943-20948. 406

[18]. Chen, J.; Han, X.; Fang, Z.; Cheng, F.; Zhao, B.; Lu, P.; Li, J.; Dai, J.; Lacey, S.; Elspas, R. Rapid 407

Dissolving-Debonding Strategy for Optically Transparent Paper Production. SCI REP-UK 2015, 5, 408

17703. 409

[19]. Dupont, A.L. Cellulose in lithium chloride/ N,N -dimethylacetamide, optimisation of a dissolution 410

method using paper substrates and stability of the solutions. POLYMER 2003, 44, 4117-4126. 411

[20]. Hu, L.; Zheng, G.; Yao, J.; Liu, N.; Weil, B.; Eskilsson, M.; Karabulut, E.; Ruan, Z.; Fan, S.; 412

Bloking, J.T. Transparent and conductive paper from nanocellulose fibers. ENERG ENVIRON 413

SCI 2013, 6, 513-518. 414

[21]. Soykeabkaew, N.; Sian, C.; Gea, S.; Nishino, T.; Peijs, T. All-cellulose nanocomposites by 415

surface selective dissolution of bacterial cellulose. CELLULOSE 2009, 16, 435-444. 416

[22]. Fang, Z.; Zhu, H.; Yuan, Y.; Ha, D.; Zhu, S.; Preston, C.; Chen, Q.; Li, Y.; Han, X.; Lee, S. Novel 417

nanostructured paper with ultrahigh transparency and ultrahigh haze for solar cells. NANO LETT 418

2014, 14, 765. 419

[23]. Tamai, N.; Aono, H.; Tatsumi, D.; Matsumoto, T. Differences in Rheological Properties of 420

Solutions of Plant and Bacterial Cellulose in LiCl/N, N-Dimethylacetamide. NIHON REOROJI 421

GAKK 2003, 31, 119-130. 422

[24]. Dawsey, T.R.; Mccormick, C.L.J. The lithium chloride/dimethylacetamide solvent for cellulose: a 423

literature review. J Macromol Sci Rev Macromol Chem Phys C30:405-440. Journal of 424

MANUSCRIP

T

ACCEPTED

ACCEPTED MANUSCRIPT

20

Macromolecular Science Part C Polymer Reviews 1990, 30, 405-440. 425

[25]. Golova, L.K.; Kulichikhin, V.G.; Papkov, S.P. Mechanism of dissolution of cellulose in 426

non-aqueous dissolving systems. Review ☆. Polymer Science U.s.s.r 1986, 28, 1995-2011. 427

[26]. Chen, J.; Han, X.; Fang, Z.; Cheng, F.; Zhao, B.; Lu, P.; Li, J.; Dai, J.; Lacey, S.; Elspas, R. Rapid 428

Dissolving-Debonding Strategy for Optically Transparent Paper Production. SCI REP-UK 2015, 5, 429

17703. 430

[27]. Yue, X.U. Effect of Chitosan Coating on the Dispersion of Carbon Fibers in Water. China Pulp & 431

Paper 2010. 432

[28]. Soykeabkaew, N.; Sian, C.; Gea, S.; Nishino, T.; Peijs, T. All-cellulose nanocomposites by 433

surface selective dissolution of bacterial cellulose. CELLULOSE 2009, 16, 435-444. 434

[29]. Fliegener, S.; Hohe, J.; Gumbsch, P. The creep behavior of long fiber reinforced thermoplastics 435

examined by microstructural simulations. Composites Science & Technology 2016, 131, 1-11. 436

[30]. Guo, B.; Chen, W.; Yan, L. Preparation of Flexible, Highly Transparent, Cross-Linked Cellulose 437

Thin Film with High Mechanical Strength and Low Coefficient of Thermal Expansion. ACS 438

SUSTAIN CHEM ENG 2013, 1, 1474-1479. 439

[31]. Kulachenko, A.; Denoyelle, T.; Galland, S.; Lindström, S.B. Elastic properties of cellulose 440

nanopaper. CELLULOSE 2012, 19, 793-807. 441

[32]. Zhu, H.; Parvinian, S.; Preston, C.; Vaaland, O.; Ruan, Z.; Hu, L. Transparent nanopaper with 442

tailored optical properties. NANOSCALE 2013, 5, 3787. 443

[33]. Yang, X.P.; Rong, H.M.; Lu, Z.D. A study of the electrical properties of carbon fiber conductive 444

composite. Journal of Materials Engineering 2000, 30, 75-84. 445

446

447

本文献由“学霸图书馆-文献云下载”收集自网络，仅供学习交流使用。

学霸图书馆（www.xuebalib.com）是一个“整合众多图书馆数据库资源，

提供一站式文献检索和下载服务”的24 小时在线不限IP

图书馆。

图书馆致力于便利、促进学习与科研，提供最强文献下载服务。

图书馆导航：

图书馆首页 文献云下载 图书馆入口 外文数据库大全 疑难文献辅助工具