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Fabrication of self-assembly CNT flexible film and its piezoresistive sensing behaviors

  • Xiaoyang Zhou , Jianlin Luo EMAIL logo , Jigang Zhang , Xiaoping Wu , Xuejun Tao and Min Zhu
Published/Copyright: May 27, 2022
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Nanotechnology Reviews
From the journal Nanotechnology Reviews Volume 11 Issue 1

Abstract

Strain sensors are essential for health monitoring of complex-shaped structures. Here, carbon nanotube thin films (CNTFS) with different double-layers were fabricated on a flexible polyethylene terephthalate substrate using layer-by-layer self-assembly technique, and their resistance behaviors and piezoresistive sensing performances were comprehensively conducted. Results show that the assembled layers of CNTFS are evenly and compactly deposited with about 7–15 μm, and the resistance decreases with the increase in the assembly layer number. The piezoresistive sensing behavior increases first and then decreases with the increase in the number of assembly layers along with compression or tension cyclic loading; the nine-double-layer CNTFS shows the best linearity, sensitivity, hysterics, and repeatability of 3.22%, 0.12684/mm, 2.16%, and 3.06%, respectively.

Keywords: structural health monitoring; carbon nanotube; flexible film; layer-by-layer self-assembly method; piezoresistive sensing performance

1 Introduction

Structural health monitoring (SHM) is an effective means of non-destructive monitoring of the health of structures, as defined by Housner et al., to evaluate the internal damage and servicing status of the structure, to improve structural disaster prevention and mitigation and to guide the repair and maintenance of structures [1]. Sensors are the key elements to achieving SHM. There are various embedded sensor devices used for engineering, such as resistance strain gauges (wires), piezoelectric ceramics, fatigue life wires, shape memory alloys, and fiber optic gratings [2,3,4,5], and the embedded process is generally complex, with high cost, short life, poor interference resistance and corrosion resistance, the low survival rate, and poor compatibility with concrete further weakening the structure integrity [6,7,8]. With the development of functional materials, piezoresistive materials, piezoelectric ceramics, and other conductive/piezoelectric materials are mixed into cement concrete matrix to make intrinsic sensing blocks, but the preparation of sensing blocks requires complex operations such as mixing, pressing, and polarization and is not suitable for practical construction [9,10,11,12]. Zhang et al. studied the mechanical, electrical, and piezoresistive properties of the electrostatic self-assembled carbon nanotube/nano carbon black (CNT/NCB) cement-based sensor. It was shown that the higher content of filler led to a significant reduction in mobility and compressive strength, whereas at lower filler content, cement hydration severely affected the resistivity of the composite, and the piezoresistive sensitivity was negatively correlated with loading rate, resulting in loss of sensing information [13,14,15,16,17].

Compared to the intrinsically sensitive blocks mentioned above, the flexible strain sensor can be prepared in advance, eliminating the need for onsite fabrication, and can be adapting well to the requirements of various special sizes and shapes of structures, with minimal impact on the performance of the building material itself, and with high sensitivity. Among several common strain thin-film sensors (e.g., piezoresistive, piezoelectric, and capacitive-type) [18,19,20], the piezoresistive strain gauge thin-film sensor has the advantages of easy to fabricate, no polarization required, high accuracy, and good linearity, and is well suitable to the common needs of SHM.

With the continuous development of functional materials, more and more novel piezoresistive materials have emerged, such as metal nanomaterials, conductive polymers, and carbon-based conductive materials [21,22,23,24]. Since Iijima’s accidental discovery of CNTs by vacuum arc evaporation of graphite electrodes in 1991 [25,26], research around CNT has continued due to their unique mechanical [27,28], electrical [29], thermal [30,31], dielectric [32], and electromagnetic properties [33,34]. CNT has an excellent modulus of elasticity, with Young’s modulus of elasticity (0.27–0.95 TPa) reported for individual multi-wall CNT (MWNT) by Yu et al. [35], and for single-wall CNT (SWNT), the value is higher at 0.32–1.47 TPa [36]. This results in structural changes between the carbon elements of CNT when subjected to external forces, impeded electron movement, and changes in carrier mobility, which in turn affects macroscopic resistivity and exhibits excellent piezoresistive properties.

The piezoresistive effect of CNT-based composite is the key to their application in the field of sensors. CNT prepared by conventional methods is in the form of ultrafine powders, which can lead to agglomeration and uneven distribution during application due to side effects, high surface energy, and strong van der Waals forces between them, resulting in the material’s excellent properties not being effectively exploited. Young’s modulus of flexible piezoresistive nanocomposites made from a certain amount of MWNT dispersed in polydimethylsiloxane (PDMS) was investigated by Pardis et al. The results show that at a small amount of MWNT (w f = 0.25%), the inclusion of MWNT in the PDMS matrix resulted in a significant increase in Young’s modulus of the nanocomposites; however, exceeding content of this nanofiller did not increase Young’s modulus due to the agglomeration of MWNT inside the nanocomposite [37]. Therefore, nanomaterials should be made into macroscopic filaments, membranes, or blocks to enlarge the internal reaction surface and expand the range of molecular transfer [38], improving the mechanical and electrical properties of the nanomaterials without affecting the original properties [39,40,41]. There are various methods for the preparation of CNT macrobodies, such as solution spinning [42,43], array spinning [44,45,46], chemical vapor deposition [47], coating [48], layer-by-layer self-assembly (LBL) [49], electrophoretic deposition [50], Langmuir–Blodgett method [51,52], and blown bubble method [53]. The LBL does not require complex and expensive equipment, is used to obtain uniform and complete films at room temperature, simple to operate, does not require an excessive investment of resources, can be in-scale produced [54], and can finely control the composition and structure by adjusting the assembly conditions (e.g., salt concentration, pH, and dipping times [55]) and the components incorporated into the film [56]. It has become the simplest and most practical of the many CNT film preparation methods. Olek et al. reported a method for the assembly of homogeneous polyelectrolyte/MWNT films on glass substrates by the LBL technique, showing that homogeneous CNT films could be produced by this method and that the structural components of the assembled layers showed strong adhesion to each other [57]. Mamedov et al. assembled uniform polyelectrolyte/MWNT films on glass substrates using the LBL technique. MWNT uniformly covered the entire surface of the glass substrate and the resulting poly(acrylic acid) (PAA)/MWNT films exhibited extremely high mechanical strength with an ultimate tensile strength of 220 ± 40 MPa, and the LBL film strength could meet the requirements of the sensor [58].

Yang et al. assembled seven layers of Pt-CNT-CHIT (polyelectrolyte chitosan)/polystyrene sulfonate films on gold substrates, placed them in a 7% phosphate solution, and stirred for 30 min, with no significant change in peak current in cyclic voltammograms (CV). The relative standard deviation of the assembled films in ten consecutive CV tests was 4.5%. This indicates that the LBL film has sufficient stability against ionic attacks [59]. The stability of LBL films was also confirmed by Hong et al. through bending tests, where 25 layers of MWNT/reduced graphene oxide (rGO) films on a polyethylene terephthalate (PET) substrate maintained their initial resistivity values after 100 times 90° bends [60]. The relationship between the number of assembled layers and the electrical properties of the films was investigated by Park et al. using the LBL method where 2–20 layers of SWNT and poly diallyl dimethylammonium chloride (PDDA) were deposited alternately on a fused silica substrate. The electrical conductivity increased continuously with the increase in the number of assembled layers, while the change in conductivity was no longer significant when the number of assembled layers exceeded 9 [61]. Zhu et al. assembled a resistive vapor-sensing device using the LBL technique, which showed excellent sensitivity, linearity, and durability in humidity-sensing tests [62].

Most LBL CNT films are prepared on rigid substrates such as silicon, glass, and metal, making them difficult to use in flexible strain gauge thin-film sensors. Ma et al. investigated the piezoresistive sensing characteristics of LBL MWNT/rGO-polyurethane sponges under different pressures, showing that the rate of change of resistance gradually increased with increasing pressure and that the strain showed the same relationship with the rate of change of resistance [63]. Zhang and his team prepared LBL MWNT/PDDA human body thin films based on PDMS with tensile properties and low modulus of elasticity. It was found that the sensitivity of the LBL sensor depends on the number of layers of the MWNT assembly. By adjusting the number of layers of the assembly, sensors with different sensitivity requirements can be obtained. However, they used the two-electrode method to directly measure the resistance of the sensor through a multimeter, which could not avoid the influence of the contact resistance between the sensor film and the electrode. On the other hand, the influence of the number of LBL layers assembled on other sensor characteristics was not thoroughly studied [64,65,66].

In this article, a flexible CNT strain transducer was prepared based on the LBL technique. Positively charged PDDA and negatively charged carboxylated CNT were alternately deposited on a PET sheet to investigate the effect of the number of assembled layers on the resistance behaviors of the strain transducer as well as the piezoresistive sensing performance such as sensitivity, linearity, hysteresis, and repeatability.

2 Materials and test methods

2.1 Raw materials

The MWNT used in this experiment was >90% in purity, 10–20 nm in diameter, and 2–15 μm in average length. MWNT was treated with a 3:1 volume ratio of mixed concentrated sulfuric acid and concentrated nitric acid, and the mixture was diluted by cooling in a water bath at 80°C for 4 h. After cooling, the mixture was vacuum filtered through a 0.22 μm mixed fiber membrane and diluted several times until it reached a neutral filtrate; the mixture was dried at 50°C for 4 h to obtain carboxylated MWNT. The carboxylated MWNT dispersion was prepared at a concentration of 0.5 mg/mL and sonicated for 1 h.

PDDA was purchased from Aldrich, a 20% aqueous solution, prepared at a concentration of 15 mg/mL, with the addition of 0.5 mol/L of NaCl. NaCl increases the conductivity of the solution, increases the ionic strength, increases the ionic adsorption capacity, and helps to improve the self-assembly efficiency [67,68].

PET was selected as the assembly base, which had weak polarity, low surface energy, and weak adsorption capacity at room temperature. Therefore, the surface of PET was oxidized by ozone, and the macromolecular structure on the surface of PET was broken and wound, and the molecular chain structure and side groups were changed, forming −COOH/COOR group. The surface of PET became rough, and the adsorption capacity was enhanced [69].

2.2 Film fabrication

As shown in Figure 1, at room temperature, PET treated with ozone had a negative charge on its surface and is immersed in PDDA solution. The positively charged PDDA was adsorbed on PET, and the excess PDDA was removed with deionizing water. After drying in the air for 15 min, it was immersed in CNT solution for 20 min, washed, dried to complete the first layer assembly, and repeated the above steps to proceed to the next assembly round. According to the above steps, we assembled carbon nanotube thin films (CNTFS) with 3, 6, 9, and 12 different double layers. Figure 2 shows the composition of the assembled CNTFS structure.

Figure 1 Assembly flowchart of self-assembly CNT film.
Figure 1

Assembly flowchart of self-assembly CNT film.

Figure 2 Schematic section structure of CNTFS.
Figure 2

Schematic section structure of CNTFS.

2.3 Test methods

The four-electrode method is used to test the resistance change of different layers of CNTFS. CNTFS, DC power supply, and standard resistance box were in-series connected, by measuring the voltage at both ends of the CNTFS and standard resistance to obtain the resistance value of CNTFS. The four-electrode method effectively avoids the contact resistance between the electrode and CNTFS caused by the electrode acting as both voltage electrode and current electrode in the two-electrode method, which brings out more accurate resistances.

Scanning electron microscopy (SEM, S-5100 type) was used to observe the morphological characteristics of the strain gauge thin-film sensor, and the sample was broken up to observe the cross-sectional morphology.

A universal tensile testing machine (MTS (China) Ltd. Co.) was used to carry out the three-point bending test of the simply supported beam, as shown in Figure 3. The mid-span displacement of the film was controlled from 0 to 5 mm, and the loading rate was 2 mm/min. The resistance changes of the film with different assembly layers were studied under tensile and compressive stress states of the strain sensing film under five cyclic loads. And the sensor parameters involving piezoresistive linearity, sensitivity, repeatability, and hysteresis of the flexible film were comprehensively characterized.

Figure 3 Piezoresistive testing of CNTFS under cyclic loading with four-electrode method by a universal testing machine.
Figure 3

Piezoresistive testing of CNTFS under cyclic loading with four-electrode method by a universal testing machine.

3 Results and discussion

3.1 Morphology of CNTFS

Figure 4(a) shows SEM images of the surface of the CNTFS. Figure 4(b) and (c) shows the film cross-section, where the boundaries between the assembled layers are clear and the CNT is tightly connected to the PDDA, which is conducive to the connection between different layers of CNT and the improvement of electrical conductivity [70]. These pictures show that the CNT is uniformly deposited on the PET sheet, forming a dense, well-bonded, high-purity random CNT structure in the polymeric material, as shown in Figure 4(d), with a homogeneous mixture of CNT and PDDA and a stable ratio distribution, indicating a well-dispersed CNT solution.

Figure 4 SEM images of self-assembled nine-double-layer CNTFS: (a) ×70, (b) ×2.0 k, (c) ×15 k, and (d) × 30 k (yellow line – assembled layer interface; dashed red circle – CNT distribution network).
Figure 4

SEM images of self-assembled nine-double-layer CNTFS: (a) ×70, (b) ×2.0 k, (c) ×15 k, and (d) × 30 k (yellow line – assembled layer interface; dashed red circle – CNT distribution network).

3.2 Effect of the number of layers of CNTFS assembly on resistance properties

The trend of the film resistance properties with the number of assembled layers is shown in Figure 5. As the number of layers increases, the film resistance properties tends to decrease. It decreases rapidly at the beginning and then decreases slowly, and after the ninth layer, the trend of decreasing resistance properties is not obvious. The resistivities of 3, 6, 9, and 12 double-layer CNTFS are 127, 103, 18.3, and 7.98 kΩ cm, respectively, and the resistivity of the three-double-layer films is accordingly 15.9 times higher than that of the 12 double-layer film.

Figure 5 Relationship between the number of layers and resistance properties of CNTFS flexible film.
Figure 5

Relationship between the number of layers and resistance properties of CNTFS flexible film.

Figures 6 and 7 show that the relative rate of change in resistance is approximately linear with respect to displacement over the displacement range of 0–5 mm. When the film is compressed, the resistance decreases (ΔR < 0), and conversely when the film is stretched, the resistance increases (ΔR > 0). As the number of double layers increases, the relative change in resistance is the first to show an upward trend, and the relative change in resistance of the film is the largest at nine layers, reaching 80%; the relative change in resistance decreases as the number of double layers continues to increase, and the relative change in resistance of the 12-double-layer film is the smallest at about 50%.

Figure 6 Relationship between change rate of resistance and mid-span displacement of varied double-layer CNTFS in compression side.
Figure 6

Relationship between change rate of resistance and mid-span displacement of varied double-layer CNTFS in compression side.

Figure 7 Relationship between change rate of resistance and mid-span displacement of varied double-layer CNTFS in tension side.
Figure 7

Relationship between change rate of resistance and mid-span displacement of varied double-layer CNTFS in tension side.

This variation in resistance and strain can be attributed to the relationship between the change in cross-sectional area and resistance from a macroscopic point of view. We know that the resistance is inversely proportional to the cross-sectional area when all other conditions are equal. Assume that the volume of the CNTFS remains constant during compression and stretching. When the film is in compression, the cross-sectional area of the film increases and the total film resistance decreases; when the film is stretched, the cross-sectional area decreases, and the total film resistance increases in response.

From the microscopic point of view, it can be understood as the change of CNT resistance. The resistance of the CNT film consists of two parts: the CNT’s own resistance (R 1) and the contact resistance (R 2) between the CNT tubes. The inter-tube contact resistance also includes the resistance R contact generated by direct contact of CNT and the resistance R tunnel generated by the tunneling effect. The piezoresistive effect of CNT is mainly the change in the forbidden bandwidth (E g ) and the inter-tube contact resistance R 2 due to deformation [71,72]. When the film is subjected to external forces, the internal lattice structure of the CNT changes, leading to changes in the tube diameter and helix angle, causing changes in the forbidden bandwidth E g and eventually leading to changes in the CNT’s own resistance R 1. The effect of CNT deformation on E g was noted in the study by Jamal et al. The E g of the original CNT was 0.879 eV, and the E g of the CNT was 0.135 and 1.147 eV for 10% compression and tensile deformation, respectively [73]. Deformation also leads to changes in R 2. Bao et al. argued that the contact between CNT and CNT occurs at the nanoscale, and the contact region consists of only a few atoms, which has a limited impact on the enhancement of conductivity [74]. Thus, film deformation mainly affects R tunnel, and when the film is deformed, the tunneling chance changes subsequently, and the resistance transfer between CNTs is affected, leading to the change of R 2. The change in film resistance is therefore the sum of the changes in R 1 and R 2.

The influence of the tunneling effect on resistance can also explain the trend of resistance varies with the increase in assembly layers. It also confirms the interlayer connection of the CNTs in the SEM image. The PDDA only glues the CNTs to each other and does not wrap the CNTs, and the layers of CNTs are not only simply connected in parallel. When the number of assembled layers increases from 3 to 9, the CNT spacing decreases, and the tunneling probability increases. Under the condition of high CNT, the chance of direct contact between CNT is greatly increased, but CNT may appear agglomerated, which is not conducive to the formation of the conductive pathway. Moreover, mutually close, single-root CNTs that can produce tunneling effects are rarely found. It is easy to know from the circuit knowledge that when two CNTS are effectively overlapped, the current will flow through the path with low resistance formed by overlap. The formed conductive network is not easy to change under the action of external forces [75]. Therefore, when the number of assembled layers continues to increase from 9 to 12, the resistance steadily decreases (Figure 5), but the relative rate of change in resistance becomes worse (Figures 6 and 7).

3.3 Effect of the number of layers of CNTFS assembly on sensing performance

The linearity δ is defined as the percentage of the maximum deviation Δmax between the curve of the relative rate of change of resistance–displacement relationship and its fitted straight line at standard conditions (20 ± 5°C) and the full-scale output value of the relative rate of change of resistance (ΔR/R)F.S.

The ideal sensor should have a strict one-to-one correspondence between input and output, and the smaller the linearity value, the better. The vast majority of current flexible sensors do not have the same characteristic linearity as rigid sensors [76,77], Table 1 shows that the average linearity of the 9-double-layer film is 3.22% minimum and the average linearity of the 12-double-layer film is 6.21% maximum, with a difference of 2.89%. Yasuoka et al. assume that the direct contact resistance is equal to the tunneling resistance and point out that the nonlinear variation of resistance is mainly caused by the tunneling resistance [78]. It is obvious that the linearity of the 12-double-layer CNT/PDDA-PET film cannot be explained.

Table 1

Linearity of resistivity–displacement curves for different double layers of films

Number of double layers
Linearity Number of load cycles 3 6 9 12
1 Tension 3.09% 6.07% 2.58% 6.54%
Compression 2.80% 3.33% 3.76% 3.51%
2 Tension 3.69% 3.23% 3.11% 6.31%
Compression 4.15% 3.91% 3.99% 6.52%
3 Tension 3.74% 2.25% 2.50% 6.58%
Compression 4.31% 3.77% 2.75% 5.89%
4 Tension 3.50% 4.46% 3.39% 6.97%
Compression 4.26% 3.41% 3.72% 6.72%
5 Tension 3.82% 4.67% 3.11% 6.57%
Compression 4.80% 4.40% 3.29% 6.51%
Average linearity 3.82% 3.95% 3.22% 6.21%

Figure (8b) gives the sensitivity GF of CNTFS with different assembled layers under five cycles of loading and the same variation pattern as in Table 1. Nine-double-layer films have the largest GF with the average GF value of 0.12684/mm, and 12-double-layer films have the smallest GF of 0.03774/mm. Nine-double-layer films have 3.36 times the GF value of 12-double-layer. Figure 8(c) shows the hysteresis curve, where hysteresis is defined as the percentage of the maximum deviation Δ max ′ between the forward and reverse travels of the resistance relative rate of change–displacement relationship curve and the full-scale output of the change rate of resistance ( Δ R / R ) F .S , which reflects the degree of non-coincidence between the forward and reverse travels of the resistance relative rate of the change–displacement curve and can be expressed as follows [79]:

(2) e z = ± Δ max ′ ( Δ R / R ) F .S × 100 % .

Figure 8 Effect of the number of layers of CNTFS assembly on sensing performance: (a) linearity, (b) sensitivity, (c) hysteresis, and (d) repeatability.
Figure 8

Effect of the number of layers of CNTFS assembly on sensing performance: (a) linearity, (b) sensitivity, (c) hysteresis, and (d) repeatability.

The smaller the hysteresis, the better the performance of the sensor. The hysteresis decreases and then increases with the increase in the number of film layers, reaching a minimum hysteresis average of 2.16% at nine layers.

Repeatability is also an important indicator to describe the sensing performance. When the displacement is changed multiple times for the full range according to the agreed direction, the degree of inconsistency in the relative rate of change of each resistance for each change–displacement, which also reflects the stability of the sensor. The repeatability error,

(3) e f = ± 1 2 Δ max ″ ( Δ R / R ) F .S × 100 % .

The e f is described by the maximum deviation in the forward and reverse travels, as shown in Figure 8(d). The maximum repeatability error is 6.35% for the six-double-layer film, and the minimum is 3.06% for the nine-double-layer film, and the nine-double-layer CNTFS has the best sensing repeatability.

Actually, the resistance of the film decreases linearly with increasing compression displacement and increases linearly with increasing tensile displacement. Microscopically, this is because when the CNT is subjected to loading, resulting in changes in diameter and helicity, causing changes in E g , which affects the resistance of the CNT itself. Moreover, the inter-tube distance of CNT also changes, which affects the electron transport and thus causes the inter-tube resistance of CNT to change. Macroscopic analysis suggests that under tensile displacement, the entire length of the film increases, the cross-sectional area decreases, and the overall total resistance of the film increases. In compression, the cross-sectional area decreases and the total resistance decreases.

The change rate of resistance increases with the increase in the number of assembled layers, but when the number of assembled layers exceeds 9, the connection between CNT layers increases, and more conductive networks are formed by direct contact between CNTs, yet the chance of tunneling decreases and the change rate of resistance decreases.

4 Conclusion

  1. The assembled layers of CNTFS are evenly and compactly deposited with about 7–15 μm.

  2. The resistance decreases gradually with the increase in the number of layers of film assembly, and the decreasing trend becomes flat when the number of assembled layers exceeds nine layers.

  3. The CNTFS with varied double layers all show superior piezoresistive performance in terms of linearity, repeatability, and recoverability under five cyclic loadings. The nine-double-layer CNT film shows the most outstanding strain-sensitive performance in terms of linearity, sensitivity, hysteresis, and repeatability whose values are 3.22%, 0.12684/mm, 2.16%, and 3.06%, respectively.

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Acknowledgments

The authors are obliged to the conducting mechanism discussion with Prof. Huarong Nie (Qingdao University of Science and Technology).

  1. Funding information: This study was financially supported by the NSFC-Shandong Province Joint Key Project (Grant No. U2106222), the National Natural Science Foundation of China (No. 51878364), the project from The Fourth Construction Co., Ltd, China Construction Eighth Engineering Division, and the National “111” project, and Gaofeng discipline project funded by Shandong Province.

  2. Author contributions: Conceptualization, supervision, and resources: Jianlin Luo, Jigang Zhang. Data curation, formal analysis, and methodology: Xiaoyang Zhou, Jianlin Luo, and Xiaoping Wu. Funding acquisition, investigation and project administration: Jianlin Luo, Jigang Zhang, and Min Zhu. Validation, visualization, and writing – original draft: Xiaoyang Zhou and Jianlin Luo. Writing – review and editing: Xiaoyang Zhou, Jianlin Luo and Xuejun Tao. All authors have accepted responsibility for the entire content of this manuscript and approved its submission.

  3. Conflict of interest: The authors state no conflict of interest.

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Received: 2021-12-31
Revised: 2022-03-24
Accepted: 2022-05-06
Published Online: 2022-05-27

© 2022 Xiaoyang Zhou et al., published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 International License.

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  147. Framework materials for supercapacitors
  148. An overview on the reproductive toxicity of graphene derivatives: Highlighting the importance
  149. Antibacterial nanomaterials: Upcoming hope to overcome antibiotic resistance crisis
  150. Research progress of carbon materials in the field of three-dimensional printing polymer nanocomposites
  151. A review of atomic layer deposition modelling and simulation methodologies: Density functional theory and molecular dynamics
  152. Recent advances in the preparation of PVDF-based piezoelectric materials
  153. Recent developments in tensile properties of friction welding of carbon fiber-reinforced composite: A review
  154. Comprehensive review of the properties of fly ash-based geopolymer with additive of nano-SiO2
  155. Perspectives in biopolymer/graphene-based composite application: Advances, challenges, and recommendations
  156. Graphene-based nanocomposite using new modeling molecular dynamic simulations for proposed neutralizing mechanism and real-time sensing of COVID-19
  157. Nanotechnology application on bamboo materials: A review
  158. Recent developments and future perspectives of biorenewable nanocomposites for advanced applications
  159. Nanostructured lipid carrier system: A compendium of their formulation development approaches, optimization strategies by quality by design, and recent applications in drug delivery
  160. 3D printing customized design of human bone tissue implant and its application
  161. Design, preparation, and functionalization of nanobiomaterials for enhanced efficacy in current and future biomedical applications
  162. A brief review of nanoparticles-doped PEDOT:PSS nanocomposite for OLED and OPV
  163. Nanotechnology interventions as a putative tool for the treatment of dental afflictions
  164. Recent advancements in metal–organic frameworks integrating quantum dots (QDs@MOF) and their potential applications
  165. A focused review of short electrospun nanofiber preparation techniques for composite reinforcement
  166. Microstructural characteristics and nano-modification of interfacial transition zone in concrete: A review
  167. Latest developments in the upconversion nanotechnology for the rapid detection of food safety: A review
  168. Strategic applications of nano-fertilizers for sustainable agriculture: Benefits and bottlenecks
  169. Molecular dynamics application of cocrystal energetic materials: A review
  170. Synthesis and application of nanometer hydroxyapatite in biomedicine
  171. Cutting-edge development in waste-recycled nanomaterials for energy storage and conversion applications
  172. Biological applications of ternary quantum dots: A review
  173. Nanotherapeutics for hydrogen sulfide-involved treatment: An emerging approach for cancer therapy
  174. Application of antibacterial nanoparticles in orthodontic materials
  175. Effect of natural-based biological hydrogels combined with growth factors on skin wound healing
  176. Nanozymes – A route to overcome microbial resistance: A viewpoint
  177. Recent developments and applications of smart nanoparticles in biomedicine
  178. Contemporary review on carbon nanotube (CNT) composites and their impact on multifarious applications
  179. Interfacial interactions and reinforcing mechanisms of cellulose and chitin nanomaterials and starch derivatives for cement and concrete strength and durability enhancement: A review
  180. Diamond-like carbon films for tribological modification of rubber
  181. Layered double hydroxides (LDHs) modified cement-based materials: A systematic review
  182. Recent research progress and advanced applications of silica/polymer nanocomposites
  183. Modeling of supramolecular biopolymers: Leading the in silico revolution of tissue engineering and nanomedicine
  184. Recent advances in perovskites-based optoelectronics
  185. Biogenic synthesis of palladium nanoparticles: New production methods and applications
  186. A comprehensive review of nanofluids with fractional derivatives: Modeling and application
  187. Electrospinning of marine polysaccharides: Processing and chemical aspects, challenges, and future prospects
  188. Electrohydrodynamic printing for demanding devices: A review of processing and applications
  189. Rapid Communications
  190. Structural material with designed thermal twist for a simple actuation
  191. Recent advances in photothermal materials for solar-driven crude oil adsorption
https://doi.org/10.1515/ntrev-2022-0121
Keywords for this article
structural health monitoring; carbon nanotube; flexible film; layer-by-layer self-assembly method; piezoresistive sensing performance
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  158. Recent developments and future perspectives of biorenewable nanocomposites for advanced applications
  159. Nanostructured lipid carrier system: A compendium of their formulation development approaches, optimization strategies by quality by design, and recent applications in drug delivery
  160. 3D printing customized design of human bone tissue implant and its application
  161. Design, preparation, and functionalization of nanobiomaterials for enhanced efficacy in current and future biomedical applications
  162. A brief review of nanoparticles-doped PEDOT:PSS nanocomposite for OLED and OPV
  163. Nanotechnology interventions as a putative tool for the treatment of dental afflictions
  164. Recent advancements in metal–organic frameworks integrating quantum dots (QDs@MOF) and their potential applications
  165. A focused review of short electrospun nanofiber preparation techniques for composite reinforcement
  166. Microstructural characteristics and nano-modification of interfacial transition zone in concrete: A review
  167. Latest developments in the upconversion nanotechnology for the rapid detection of food safety: A review
  168. Strategic applications of nano-fertilizers for sustainable agriculture: Benefits and bottlenecks
  169. Molecular dynamics application of cocrystal energetic materials: A review
  170. Synthesis and application of nanometer hydroxyapatite in biomedicine
  171. Cutting-edge development in waste-recycled nanomaterials for energy storage and conversion applications
  172. Biological applications of ternary quantum dots: A review
  173. Nanotherapeutics for hydrogen sulfide-involved treatment: An emerging approach for cancer therapy
  174. Application of antibacterial nanoparticles in orthodontic materials
  175. Effect of natural-based biological hydrogels combined with growth factors on skin wound healing
  176. Nanozymes – A route to overcome microbial resistance: A viewpoint
  177. Recent developments and applications of smart nanoparticles in biomedicine
  178. Contemporary review on carbon nanotube (CNT) composites and their impact on multifarious applications
  179. Interfacial interactions and reinforcing mechanisms of cellulose and chitin nanomaterials and starch derivatives for cement and concrete strength and durability enhancement: A review
  180. Diamond-like carbon films for tribological modification of rubber
  181. Layered double hydroxides (LDHs) modified cement-based materials: A systematic review
  182. Recent research progress and advanced applications of silica/polymer nanocomposites
  183. Modeling of supramolecular biopolymers: Leading the in silico revolution of tissue engineering and nanomedicine
  184. Recent advances in perovskites-based optoelectronics
  185. Biogenic synthesis of palladium nanoparticles: New production methods and applications
  186. A comprehensive review of nanofluids with fractional derivatives: Modeling and application
  187. Electrospinning of marine polysaccharides: Processing and chemical aspects, challenges, and future prospects
  188. Electrohydrodynamic printing for demanding devices: A review of processing and applications
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  191. Recent advances in photothermal materials for solar-driven crude oil adsorption
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