Home Mechanical, morphological, and fracture-deformation behavior of MWCNTs-reinforced (Al–Cu–Mg–T351) alloy cast nanocomposites fabricated by optimized mechanical milling and powder metallurgy techniques
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Mechanical, morphological, and fracture-deformation behavior of MWCNTs-reinforced (Al–Cu–Mg–T351) alloy cast nanocomposites fabricated by optimized mechanical milling and powder metallurgy techniques

  • Shubham Sharma EMAIL logo , Vikas Patyal EMAIL logo , P. Sudhakara , Jujhar Singh , Michal Petru EMAIL logo and R. A. Ilyas
Published/Copyright: December 7, 2021
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Abstract

The carbon nanotube (CNT) is becoming more popular due to their low-density, high-strength etc. Among CNTs, multi-walled carbon nanotubes (MWCNTs) are gaining more importance due to their enhanced thermal and electrical conductivity. The present research is exploring the applicability of MWCNTs reinforced with AA2024-T351 alloys for electromechanical applications. This study is currently undertaken for using MWCNTs as a reinforcing particulate for the purpose to enhance the characteristics including low density, high strength, and hardness together with excellent thermal and electrical conductivity of the aluminum alloy matrices. Therefore, this article provides a state-of-the-art experimental approach to fabricate and furthermore, to evaluate the mechanical characteristics, microstructural analysis, and fatigue behavior of Al–Cu–Mg–T351/MWCNT composites under both the mechanical and thermal loading by utilizing powder technology processing route. The uniform dispersion of CNTs has been exposed using ball milling process. Results revealed that the MWCNTs provide extraordinary synergistic strength, enhances fatigue resistance, creep resistance, ductility, and other mechanical characteristics of the aluminum-based composites. The mechanical loading of the composite exhibited increased properties as compared to thermal-loaded aluminum-MWCNT composites. Findings conclude that the maximum hardness of 35Hv obtained for sintered AA2024-T351 and 45Hv for 0.5% MWCNT heat-treated samples indicate that the addition of MWCNT enhances the hardness which may be because CNT is evenly dispersed at the interfacial space. Maximum UTS of 105.21 MPa was obtained with 0.5% MWCNT for sintered composites. Microstructural analysis of the Al–Cu–Mg–T351/MWCNTs composite exhibits reasonably uniform distribution, void formation, and good interfacial bonding. X-ray Diffraction method patterns of fabricated composite shows that the CNT is present at 2β = 23.6 and 44.6°, whereas high peaks of aluminum are present at uniform dispersed positions. Transmission electron magnifying instrument study further substantiates the above research. Fracture micrographs of the Al–Cu–Mg–T351/MWCNTs composite portray the resistant nature of the nanotubes due to the presence of CNTs, Al–Cu, and aluminum carbide elements in the alloy and the reactions that happened during heat treatment. This significant improvement was attributed to the shear interactions among the constituents and high load carrying capacity of the CNT, uniform dispersion, and interface bond strength among the matrix and constituents. The findings in the study will undoubtedly be beneficial for the development of high-strength, MWCNTs/Al–Cu–Mg–T351, matrix composites in future for multifunctional applications on broader spectrum.

1 Introduction

In metal matrix nanoparticle composites (MNCs), the nanoscaled reinforcement is mixed with the matrix material to attain excellent mechanical, corrosion, and dynamic properties at room temperature. It also has various advantageous properties like excellent wear resistance, fatigue, and creep resistance [1,2]. There are various methods to fabricate MNCs such as solid-state, liquid-state, in situ processes, and deposition methods which are the most promising techniques to fabricate MNCs for structural applications. MNCs have the most efficient properties, which vary from bulk materials. The nanoscaled reinforcement-based composite material has attracted much interest in industries, while very minimum interest for domestic purposes. Generally, inorganic nanoparticles are dispersed in polymer or metal or ceramic. In comparison with the macro and micro- reinforced particulate sizes, nanoparticle have an influence on the material characteristics like, chemical, mechanical, and physicochemical properties [3]. Due to its surface to volume ratio characteristics, a minimum amount of reinforcement will improve the MNCs property significantly. Recently, carbon nanotubes (CNTs) have been considered as ideal reinforcements because of their higher aspect ratio, strength, and thermomechanical property. To overcome the limitations of micro/macro-reinforced composites, nanoparticle-reinforced composite is a good alternative solution [4,5,6]. Though it provides a solution, the dispersion of nanoparticle into the matrix material is the major challenge faced by the researchers [7,8].

Aluminum matrix composites (AMCs) show better mechanical and corrosion resistance properties than pure aluminum (Al) and Al alloys. AMCs have an extensive variety of applications like sporting goods, electronic packaging, armors, nuclear, bio-technology, aerospace, marine, automotive, and transportation industries due to its high Young’s modulus, specific strength, wear resistance, and lightweight. Besides, Al and its alloys have more advantages than other composite matrixes, such as good damping capacities, high stiffness and specific strength, good machinability, and dimensional stability. Compared to all other Al alloys, AA2024-T351 is used in various applications because of its mechanical and corrosion resistance property, and only limited researchers have selected AA2024-T351 as matrix material [9,10]. Moreover, Al is also a low density with good stiffness metal that can be processed either by a liquid/powder metallurgy technique to make a composite. Extensive work has been carried out by several researchers using SiC, Al2O3, TiB2, etc., as reinforcing material in processing Al composite. To strengthen the matrix material nano-sized ceramic particles are the latest interest of the researchers as it has good ductility, better fatigue, and better resistance to creep at high temperature. In the past few years, metal MNCs have attracted various applications because of their mechanical properties compared to microparticle reinforcement. The purity of the CNT also serves a crucial purpose in the property [11]. The purity of the multi-walled CNT (MWCNT) can be evaluated for defects based on Raman spectroscopy [11,12], as shown in Figure 1.

Figure 1 
               General Raman spectra patterns of MWCNTs [11,12].
Figure 1

General Raman spectra patterns of MWCNTs [11,12].

The ratio of the G-band to the D-band clearly shows that the intensity will be 1,300–1,680/cm, and the G-band intensity represents the amount of amorphous content present in the CNT. The diminution in the intensity of G-band represents the high purity of the CNT [11,12].

Different kinds of matrix/particulate reinforcing constituent materials used and the conclusions drawn from past research studies are given in Table 1.

Table 1

Investigations on AMCs by researchers

Investigators Matrix Reinforcement Remarks References
Liao and Tan. (2011) Al CNT of 0.5 wt% Increase in tensile strength by 66% with minor decrease in ductility [13]
Choi et al. (2010) Al MWCNT of 0, 1.5, 3, 4.5, and 6 vol% CNT increases strength and wear resistance. Grain size also plays a significant role [14]
Stein et al. (2012) AA5083 MWCNT of 1.5 wt% Tensile, Young’s modulus, and yield strength increased by 18%, 3%, and 27%, respectively. The load transfer mechanism plays a dominant role in CNT/matrix [15]
Stein et al. (2014) AA5083 MWCNT of 0, 0.5, 1, 1.5, and 2 wt% With the concentration of CNTs, mechanical properties significantly increase persistently up to 1.5 wt%. The mechanical property is decreased by increasing the concentration of CNT [11]
MWCNT of 0, 0.74, 1.47, 2.20, and 2.93 vol%
Kim et al. (2013) A356 Al2O3 of 10, 15, and 20 vol% Al2O3 helps to disperse the CNT into the matrix material. Excess amount of Al2O3 or CNT influenced the material because of cluster formation and, indeed, very low wettability [12]
CNTs of 1, 2, and 3 vol%
Fukuda et al. (2010) AZ31B (Mg alloy) CNT of 0.89 and 2.66 vol% Mg alloy composite material’s corrosion resistance is increased due to the addition of CNT [16]
Tak et al. (2011) Al Al2O3 of 5 vol% and CNT of 1–10 vol% The electrical conductivity of the material is increased by adding CNT. Machining accuracy was achieved using EDM [17]
Kim and Kim (2014) Al Al2O3 of 10, 15, and 20 vol% Al2O3 helps to disperse the CNT into the matrix material. The hardness value is increased significantly. At the surface, the reinforcement was aligned in a longitudinal direction [18]
CNTs of 1, 2, and 3 vol%
Wu et al. (2011) AA6061 CNT of 1 wt% Increased hardness value was obtained at 620°C. Relatively weaker bonding and lower density was obtained at 600°C (lower temperature). To achieve an optimal microstructure, carbide formation at the interfaces of the reinforcement and matrix material must be controlled [19]
Bakshi et al. (2011) Al CNT of 1–10 vol% The interface between matrix and CNT is important; improper bonding could lead to failure in load transfer to the CNT [20]
Li et al. (2010) Mg CNT of 0.1, 0.5, and 1 wt% On addition of a minimum amount of CNT, the mechanical property was improved. No carbide formation was observed through X-ray diffraction method (XRD) results. CNT was well dispersed into the Mg matrix [21]
Kondoh et al. (2014) AA6063 CNT of 0.56 and 1.22 vol% Yield strength value decreases gradually on addition of CNT due to the inadequate effect of hardening of by Mg2Si precipitates [22]
Kang et al. (2012) Al CNT of 1 wt% Aluminum carbide (Al4C3) was created at the MWCNT surface. The mechanical property of the composite material was enhanced [23]
Gupta et al. (2012) UHMWPE Al2O3 of 2–5 wt% UHMWPE-reinforced CNT shows enhanced protein density. The wettability of the material is also increased, and a significant role was played by surface energy [24]
CNT of 2–4 wt%
Thakur et al. (2007) Mg CNT of 0.3, 0.5, 0.7, and 1 wt% and vol% The coefficient of thermal expansion value of Mg is reduced because of nanosized SiC-CNT addition. By adding SiC and nanosized CNT, the micro-hardness value of the developed composite material was increased. When nanosized CNT, as well as SiC, were incorporated into the matrix material, 0.2% enhancement in tensile and yield strength, and reduced failure strain were obtained [25]
SiC of 0.7, 0.5, and 0.3 wt% and 0.4, 0.3, and 0.2 vol%
Goh et al. (2008) Mg CNT of 0.3, 1.3, 1.6, and 2 wt% During tensile deformation of Mg alloy and Mg-1.3 wt% CNT nanocomposites, there are some instigations of both basal slidings as well as a nonbasal slip. The ductility of the material is improved in Mg-CNT nanocomposites due to prismatic slip. Compared to Mg alloy, the developed composite shows increased hardness value [26]
Esawi AMK (2010) Al MWCNT of 0.5, 1, 2, and 5 wt% Mechanical property values were enhanced as a result of the addition of MWCNT, and the predicted values also close to the tested values. The predicted value varied at 5 wt% of CNT addition [27]
The cluster formation of CNT affected the mechanical property at 5 wt% CNT
Kwon et al. (2014) AA6061 CNT of 6 wt% and SiC of 1 vol% The Vickers hardness value was enhanced by adding SiC and CNT because of the increase in the milling time. The hardness value is five times higher than that of AA6061 [28]

Bradbury et al. [6] studied the microstructure of Al and MWCNT using transmission electron magnifying instrument (TEM) images. The MWCNT was on the Al particle superficial substrate, and during the mechanical alloying process, the length of the MWCNT was broken; however, no crack was found in the interface with the matrix. The microstructure characterization of the tensile specimen and scanning electron microscope (SEM) images revealed the occurrence of the fracture surface on the tensile specimens and some CNT particles were observed in the cracks [6]. Nam (2012) observed from the SEM image that the CNT is attached along with the Cu particle. The CNT was uniformly dispersed in the Al–Cu alloy matrix material. From the XRD, it is clearly shown that there is no sign of Al4C3 between Al–Cu and CNT [29]. Akbarpour et al. [30] observed that along with the uniformly distributed CNT nanoparticles in the matrices of the composite some cluster formation was also visible in the SEM image because of the inclusion of CNT. The grain size of the matrix material showed some deviation from the standard size [30]. Q. Li (2009) investigated the microstructure using the SEM image of Mg alloy-MWCNT composite and found a big bundle of cluster formation. The presence of MWCNT without any damage is confirmed using Raman spectroscopy [21]. Kwon et al. (2010) observed the microstructure of the Al-CNT composite using the FE-SEM image. There is no change in the diameter of the CNT particle, but the length was reduced during the de-binding process. The CNT was uniformly and omnidirectionally distributed on the surface of each Al particle [31]. Kuzumaki et al. used the powder metallurgy process for the first time to fabricate CNT/Al composite. They used carbon powder containing approximately 60 vol% of CNT. They mixed 5–10% of carbon powder with Al powder with a size of 40 μm and having a purity of 99.99%. The mix was then agitated in the ethanol solution at 300 rpm for 30 mins. Then, the composite powder was removed from the solution and prepared by the vacuum drying method. Due to the impurity of the CNT, non-uniform dispersion is observed in the Al powder [32]. Xu et al. mixed the pure CNT produced by catalytic decomposition of propylene, with 99.5% purity, with powdered Al having an average particle size of 70 μm. Different wt% of CNTs were mixed with 35 g Al powder by hand grinding for 30 min. They observed some agglomeration of CNT at the grain boundary of Al; this agglomeration was probably due to the hand grinding process [33]. However, unlike Kuzumaki, Xu et al. could see some interfacial reactions in the form of carbide between Al and CNT. Esawi et al. reported that the strength was enhanced as the CNT content increased within a specific range. The best result was obtained when the content of CNT was 2 wt%, while further addition of CNT caused a deterioration in strength [34]. Zhang et al. investigated the CNT/SiC/Al 6061 hybrid composite processed by squeeze casting and found that the heat treatment improved the bond strength among CNT, SiC, and Al, which enhanced the strength of the composite [35]. However, Zhao et al. investigated the CNT/Al 6061 composite made by FSP and found that the T6 heat treatment strengthening effect was insignificant [36].

Hence, in the recent few years, CNTs are gaining importance in processing Al composite. MWCNT is a material having low density, high strength, and hardness together with excellent thermal and electrical conductivity. This research work uses the MWCNT as a reinforcing constituent to improve the characteristics of the Al alloy matrix. The popularity of MWCNT is due to its specific characteristics such as mechanical strength (15–20 times more than steel), density (5 times lighter than steel), thermal conductivity nearly equal to that of diamond and almost 5 times that of copper, and electrical conductivity same as that of copper [37]. These new type of composites promise application in the lightweight components, nonlinear optics, batteries, nanowires, sensors, and high strength devices. A study on the thermal and mechanical properties of CNT has revealed that it has Young’s modulus of 800 GPa with a yield strength of 20 GPa [38]. Work on the mechanical behavior of CNT composite has been conducted using TEM to investigate the interfacial structure and mechanical properties [39]. The hardness of Al + 5% SWCNT was 78% higher than that of Al. An addition of 1% MWCNT to Al shows enormous enhancement in yield strength (almost 500%), which promises this material for several industrial applications [40]. Further, nano-mechanics of CNT composite indicates that SWCNTs have elastic modulus around 1TPa and can withstand 5–10% axial strength corresponding to the stress of about 50 GPa [41].

Thermo-mechanical characteristics of CNT bring them to cover a larger sector of industrial applications [42]. Due to its enhanced thermal and electrical conductivity, CNTs excel in wide industrial applications where the conventional material fails [43]. The work on the hot pressing technique of Al-CNT composites reveals a moderate increase in electrical conductivity at room temperature when compared with an increased volume fraction of the CNTs [33]. The controlled mechanical milling process of Al-CNT exhibited a strong surface interface bonding among matrix and reinforcement [44]. Al-CNT composite of 4.5 vol% MWCNT reveals elastic yield/proof strength of 620 MPa and fractural toughness of 61 MPa mm1/2, which is almost 15 and 7 times higher, respectively, as compared to the matrix [45]. The dispersion quality of CNT governs the homogeneity and hence ultimate mechanical property of the composite. Studies have shown that CNT affects the mechanical properties of the base Al, and the composite can be produced by the powder metallurgy technique, as observed in other studies [46,47].

Since Al–Cu–Mg–T351 is utterly a novel matrix material with high physicomechanical characteristics and as far as the existing studies/sources are concerned, the outcomes have inferred that, in the current decade, Al–Cu–Mg–T351-based metallic composites with MWCNTs as a reinforcing particulate have been characterized by limited researchers to investigate their suitable potential in high-strength structural applications. The processing fabrication method has been optimized by using combined effect of ball-milling and powder-metallurgy. Such novel composites provide significant characteristics and offers promising application in the industrial automotive, aircraft, electromechanical, lightweight component, nonlinear optics, batteries, nanowires, sensors, and high-strength devices. Additionally, MWCNT is a material having low density, high strength, and hardness together with excellent thermal and electrical conductivity. This research work uses the MWCNT as a reinforcing constituent to improve the characteristics of the Al alloy matrix by using optimized mechanical milling and powder metallurgy techniques. As the load transfer mechanism plays a dominant role in MWCNTs/Al–Cu–Mg–T351 matrix, the primary objective of this novel study is to escalate the physciomechanical, wear resistance, corrosion resistant, and thermal conductivity characteristics of the fabricated composites by ameliorating the surface interface bonding adherence among matrix and reinforcement and refining the grain size. The current work is focused on the study of MWCNT reinforced with AA2024-T351 alloy and its suitability for electromechanical applications as exhibited in Figure 2.

Figure 2 
               Systematic mapping summary of scientific advancements regarding an implication of MWCNTs on a physicomechanical, interface adhesion strength, and morphological characteristics of MWCNTs/Al–Cu–Mg–T351 alloy cast nanocomposites.
Figure 2

Systematic mapping summary of scientific advancements regarding an implication of MWCNTs on a physicomechanical, interface adhesion strength, and morphological characteristics of MWCNTs/Al–Cu–Mg–T351 alloy cast nanocomposites.

2 Experimental details

2.1 Materials

Al (AA2024-T351) powder with mechanical properties and chemical composition are presented in Tables 2 and 3, respectively. AA2024-T351 with physical/mechanical properties of density of 2.78 g/cm3, melting point of 660°C, hardness of 120 BHN, ultimate tensile strength of 469 MPa, and ductility/elongation of 19% has been used for matrix material. The SEM image of AA2024-T351 is shown in Figure 3(a). The properties of the AA2024-T351 alloy are presented in Table 3.

Table 2

Chemical composition of AA2024-T351 alloy

Elements Mg Si Fe Cu Zn Ti Mn Cr Al
Amount of wt% 1.5 0.5 0.5 4.5 0.25 0.15 0.5 0.1 Balance
Table 3

Properties of AA2024-T351 alloy

Parameters Average particle size (µm) Melting point (°C) Density (g/cm3) Brinell hardness (BHN) Ultimate tensile strength (MPa) Ductility/elongation (%)
Values 75 660 2.78 120 469 19
Figure 3 
                  (a) SEM of Al–Cu–Mg–T351 Al powder and (b) SEM image of CNT powder (MWCNT).
Figure 3

(a) SEM of Al–Cu–Mg–T351 Al powder and (b) SEM image of CNT powder (MWCNT).

Pristine MWCNT powder of 98% purity (Figure 3b) having 80–98 vol%, as assessed through SEM analysis, with no residual catalyst impurities was procured from Nanoshel USA. The MWCNT of 10–20 nm × 2–6 nm × 10–20 µm size, melting point of 3,652–3,697°C, and having a density of 1–2 g/cm3 has been used in the present work.

The Raman spectroscopy (LabRAM HR-HORIBA, France-SAS, micro-spectrometer), as revealed in Figure 4, indicates the prevalence of defect in MWCNT samples around two sharp curves 1,339 and 1,573/cm. The Raman-order peak at 1,573/cm was attributed by the molecular vibrational frequency mode of the graphite plane in the carbon–carbon atoms termed as first-order spectra G-band, and the frequency at 1,339/cm was named as the D-band mode because of the vibrational movement of non-bridging carbon–carbon dangling bonds in the structural disorder/defect in the plane-mode.

Figure 4 
                  Raman spectra pattern of MWCNTs.
Figure 4

Raman spectra pattern of MWCNTs.

The previous outcomes reported by Papageorgiou et al. [48] presented a review article on the literature related to graphene and CNT-reinforced PMCs. The article focused on parameters affecting the mechanical behavior of such composites. The article described the use of Raman spectroscopy to evaluate the stress transfer efficiency among the constituents. This article also described the challenges and future scope of these composites.

2.2 Methods

2.2.1 Fabrication of MWCNTs/AA2024-T351 alloy nanocomposite

MWCNT powder was treated subsequently by blending it with concentrated nitric acid (HNO3), filtered and washed with deionized water, and dried at 120°C. The process was carried out to eradicate the impurities like amorphous carbon, graphitic particles, or any other contaminants observed in MWCNTs. The Al (AA2024-T351) powder was mixed with MWCNTs powder in the weight percentage of 0.1, 0.2, 0.3, 0.4, and 0.5% using ball mill continuously for the duration of 10 h at 200 rpm to get homogeneous mixing as shown in Figure 5 [49,50]. Further, the mixture of each proportion is compacted in a hydraulic press of 1,000 kN capacity [51]. The mixed powder is pressed by a load of 180 kN to get billets of size 20 mm diameter and 55 mm length. Compacted specimens were sintered in a vacuum tube furnace at 580°C for 2 h in a nitrogen atmosphere followed by air cooling [52]. The related findings reported by Ali and Rubel [53] presented a comparative review article on the CNT-reinforced Mg and Al-based metal matrix composites. Authors reported that more attention on the fabrication is required to obtain uniform distribution of the CNTs in the base matrices. Also, the need of reduction in CNT fibers breakage during processing is necessary during fabrication. Further, the relationship among the processing factors, macro and micro structure, modeling, and simulation of such composite is still required to increase their scope in many industrial applications.

Figure 5 
                     Fabrication of MWCNTs/Al nanocomposite using powder metallurgy processing route.
Figure 5

Fabrication of MWCNTs/Al nanocomposite using powder metallurgy processing route.

A recently reported comparable outcomes were shown by Hussain et al. [54] who developed MWCNT fiber-reinforced nano-Al matrix composites using powder metallurgy process and evaluated the effect of reinforcement contents on the hardness value of the base matrix. Authors reported that mass density varied proportionally with respect to the reinforcement contents, structure of composites, and milling time. Also, by increasing milling time, a fine structure was obtained.

2.3 Mechanical loading

The split die was indigenously designed and fabricated using the P20 tool steel of grade 40CrMnNiMo8-6-4, German (1.2738): EN 4957:2000 tool steel, having a die-angle of 60° and extrusion ratio of 2. In order to evade the disruption or failure liable to happen during extrusion, the billets were tapered at the entry for smooth extrusion. Sintered billets of size 20 mm diameter and 50 mm length were cold extruded in a hydraulic press at an average load of 300 kN and an average speed of 0.5 mm/min.

2.4 Thermal loading

Sintered samples of both matrix and its composites were heat treated in a muffle furnace (Thermolyne-scientific, PID-controller) at a temperature range from 20 to 1,000°C. Samples were initially solutionized by heating them to 560°C and maintained at this temperature for 8 h, followed by water quenching and artificial aging by heating for 4 h at 180°C.

2.5 Preparation of samples for density, hardness, and tensile tests

The density test was carried out according to Archimedes’ principle. Theoretical densities of all the sintered, sintered-heat treated, and sintered-extruded samples of both the matrix and composites were determined using the rule of mixtures. Hardness tests were performed according to the ASTM E92 standard [55], and the tensile test was done according to the ASTM E8 standard for all the samples [56].

2.6 Morphological study using XRD, SEM, and TEM

The morphological study of the AA2024-T351 + MWCNT composites was done using a SEM (Tescan vega-3 LMU, Czech Republic). Crystal structures of the composite were analyzed by an X-ray diffractometer (Panalytical, Netherlands) with Cu-Ka radiation. Nanoshel USA supplied TEM images of MWCNT, and TEM images of AA2024-T351 + MWCNT were taken from JEOL JEM-2100 LaB6, (JEOL, Akishima-Japan), TEM operates at an accelerating voltage of 200 kV and a lattice resolution of 0.14 nm and magnification of 2,000×–1,500,000×.

3 Results and discussions

3.1 Measurement of density and porosity

Theoretical and experimental density measurements were studied using the rule of the mixture and using the Archimedes principle [57]. Figure 6 shows that the density of the composites with varying weight percentage of reinforcements of 0, 0.1, 0.2, 0.3, 0.4, and 0.5 wt% MWCNTs decreases with an increase in MWCNTs addition. This fact may be due to the displacement of atoms by the lightweight carbon atom, which usually occupies the interstitial position of the Al crystal structure [58].

Figure 6 
                  Density of the composites with varying weight percentages of MWCNTs.
Figure 6

Density of the composites with varying weight percentages of MWCNTs.

Further, the decrease in the density was attributed to increasing pores observed in sintered nanocomposite because MWCNT was processed in an HNO3 environment in which carboxyl (−COOH) or hydroxyl (−OH) functional group exist. At sintering temperatures and heat-treated composites of different percentages of reinforcing MWCNT, the impurities in the composite material were pushed out completely [56]. This leads to the shrinking of the particles and reduction in the volume, thereby enhancing the density of a given volume of Al2024-T351 + MWCNT.

Second, porosity which predominantly occurs in most of the sintered metallic compositions decreases the density even though dislocations take place, as shown in Figure 6. Initially, the density of the sintered-heat treated samples increases by 4.48% and sintered-extruded samples increases by 5.23% compared to sintered composites.

As the percentage addition of MWCNT increases, the density individually decreases by 2.3, 3.8, and 4.04% in sintered, sintered-heat treated, and sintered-extruded AA2024-T351 + 0.5% MWCNT composites, respectively. Similarly, porosity usually exists in sintered AA2024-T351 + MWCNT composites. It increases with an increasing percentage of MWCNT from 0 to 0.5% [59]. This can be reduced by heat treating and extruding the composite.

It is observed from Figure 7 that the percentage of porosity in a sintered composite ranges from 6.88–8.24% for various percentages of MWCNT. Porosity is 2.47–5.31% in case of sintered-heat treated composites after the addition of MWCNT. This reduction in porosity is due to the intergranular motion of matrix and dislocations due to higher temperature during heat treatment [60,61]. The decrease in porosity, as observed in the sintered-heat treated composite, maybe due to the dislocation movement of atoms and extension of grain boundaries by the addition of CNT at high temperatures during heat treatment [60].

Figure 7 
                  Porosity of the composites with varying weight percentages of MWCNTs.
Figure 7

Porosity of the composites with varying weight percentages of MWCNTs.

The related findings have been unveiled by Sharma et al. [62] who developed MWCNTs-reinforced alumina matrix composites using powder metallurgy processing route. Conventional and field-assisted sintering processes were followed during the fabrication of composites. Mechanical, tribological, and microstructural behaviors were analyzed. The effect of sintering time and temperature were evaluated. Authors observed reduction in hardness and density of base matrix with the addition of CNT up to 0.2 wt% and then increased continuously with further increase in CNT contents. Composites, which were sintered conventionally, possessed better wear resistance with respect to sintering time. However, the spark plasma sintered composites exhibited better density and mechanical and wear properties than other ones.

Further reinforcement of MWCNT decreases the porosity marginally because its interfacial bonding hinders the movement during heat treatment of the nanocomposite. The addition of MWCNT increases the porosity, which may be because its hardness will not allow the pores to slide across each other during the application of pressure during either sintering or heat treatment. Further reduction in porosity of sintered-extruded by 12% compared to sintered-heat treated is because of the refining of grains.

Comparable outcomes have been described by Suk [63] who prepared lightweight CNT-reinforced AMCs with significant reduction in the weight of Al and the mechanical behavior was analyzed using simulation. Authors also observed an enhancement of about 106% in tensile strength, 247% in toughness, and 244% in modulus of elasticity with an addition of CNT in the base Al matrix. This improvement was attributed to the shear interactions among the constituents and high load carrying capacity of the CNT.

3.2 Mechanical properties

3.2.1 Hardness

Hardness tests have been conducted using a Vickers micro-hardness tester (HXD:1000-TM). Test results of the study are shown in Figure 8(a–d), for sintered, sintered-heat treated, and sintered-extruded samples of the AA2024-T351 + MWCNT composites. Maximum hardness of 35Hv was obtained for sintered AA2024-T351, and 45Hv for 0.5% MWCNT heat-treated samples was obtained indicating that the addition of MWCNT enhances the hardness which may be because CNTs are evenly dispersed at the interfacial space [64].

Figure 8 
                     Microhardness of sintered, sintered-heat treated, and sintered-extruded samples plotted against wt% of AA2024-T351 + MWCNT composites.
Figure 8

Microhardness of sintered, sintered-heat treated, and sintered-extruded samples plotted against wt% of AA2024-T351 + MWCNT composites.

Further, sintered and sintered-extruded composites exhibited hardness of 50Hv which is an overall increase of 42.8%. The enhancement in the hardness incurred as a result of the formation of Al4C3 during heat treatment [6567]. The proper surface interface bonding among matrix and reinforcing constituents may be considered as the other prime factor for the increase in the hardness [60,68,69].

Similar empirical evidences are reported by Soni et al. [70] who evaluated titanium dioxide and MWCNT-reinforced Al (Al6061) metal matrix composites. Authors followed ultrasonic-based squeeze casting to fabricate AMCs. The reinforcement contents were pre-processed using different methods before mixing to achieve regular dispersion within the base matrix. Advanced techniques such as SEM, TEM, XRD, optical microscopy (OM), and X-ray microscopy (XRM) were used to evaluate the morphology of newly developed AMCs. Hardness test and tensile test were also conducted to evaluate mechanical behavior of the composites. Authors observed significant improvement in the strength and hardness values with the addition of MWCNTs together with TiO2. Also 20 min of sonication was best to attain uniform microstructure. The fabrication using ultrasonic-assisted stir casting and pre-processing of reinforcements before mixing produced AMCs with best composite properties. Moreover, squeeze casting composites possessed better properties than stir casting ones.

3.2.2 Tensile strength

Further, the tensile test has been conducted on the universal testing machine (ZwickRoell Z100:Z250) (IS: 1608-2005). Ultimate tensile strength (UTS) of the composites exhibited a substantial improvement, as shown in Figure 9, for sintered-heat treated composites when compared to sintered-extruded composites [57]. Maximum UTS of 105.21 MPa was obtained with 0.5% MWCNT for sintered composites. Further increase in UTS to 140.02 MPa was observed in sintered-heat treated composites, while sintered-extruded composites exhibited 150.93 MPa, indicating an increase of 33.1 and 43.46% increase in strength, respectively.

Figure 9 
                     Ultimate tensile strength of sintered, heat-treated, and extruded samples plotted against wt% of CNT.
Figure 9

Ultimate tensile strength of sintered, heat-treated, and extruded samples plotted against wt% of CNT.

Sintered-extruded specimens showed better capability, which may be due to the intergranular refinement [60,71]. This is evident from the various research studies that report effective uniform dispersion and better interfacial bonding between the matrix and bent MWCNTs leading to enhanced properties [60].

Heat treating of sintered nanocomposite enhances the UTS due to the mobility of large mass of atoms resulting in smaller grain sizes [60,71] due to applied tensile force. An increase in temperature during heat treatment fills the pores and reduces the imperfection, which was observed during the sintering process. This is evident from the earlier research studies; the tensile load exerted on the composite transferred to the CNT, thereby pulling the CNT which leads to bending of the nanotubes and break in the form of telescopic sheath [60,71]. Thermal treatment is also a factor for enhancing the strength of AA2024-T351 + MWCNT composites [72,73].

Comparable outcomes have been revealed by Yuan et al. [74] who developed CNTs-reinforced AMCs using milling- and rolling-based powder metallurgy process to evaluate the influence of reinforcement’s contents on the microstructure and mechanical behavior of the base matrix. Authors reported that tensile strength of 382 MPa and fracture ductility of 9.8% were obtained with the addition of 1.5% CNT contents in the base matrix. Authors also reported that the used process is the best route to produce CNTs-reinforced AMCs with better mechanical properties.

3.3 Morphological analysis

Figure 10 illustrates the SEM micrographs of Al alloy powder obtained at a frequent time intervals from 0 to 30 h during ball milling operation. During the preliminary initial stage, the Al particulates were equiaxial or unrecrystallized grain structure with uneven or distorted morphology. Because of the ductility characteristic of Al, the pellets distorted and transformed into a flake-like segment after 5 h of the mechanical alloying process.

Figure 10 
                  SEM micrographs of Al powder at, (a) 5 h; (b) 15 h, (c) 25 h, and (d) 30 h, ballmilling time-periods.
Figure 10

SEM micrographs of Al powder at, (a) 5 h; (b) 15 h, (c) 25 h, and (d) 30 h, ballmilling time-periods.

The pulverized Al powder with uneven, erratic, and non-spherical grain size had a diverse wide-range dispersion. After 5 h of attrition, the alloying elements provided a stratified uniform homogenous mixture. After 10 h of the ball milling process, the grain particulates first formed a smooth, flattened plate-like surface. Furthermore, after 15 h of milling-processing continuance, the particulate segments with plate-like texture experience strain-hardening, culminating in the continued persistence of solid-phase re-welding and brittle micro-cracks based fractured-mechanics morphological shape/structure.

The flakes-like fragments with lamellar morphology continuously persist with significantly reduced particulate grain size, even after 15 h of the ball milling process. A lower size distribution-defined aspect ratio of the powdery particulates was observed for 20 h, and afterward, there was a restricted narrow distribution that appears in the particulate matter. Continuous attrition processing up to 30 h reveals a significant shift in the size of the uniformly dispersed particulate.

Similar empirical evidences are reported by Billah and Chen [75] who prepared Ni-coated CNT-reinforced AMCs using powder metallurgy route. Prior to mixing, CNT contents were coated with Ni using electroless deposition technique. Authors observed increasing trends of tensile strength and hardness. An improvement in tensile strength around 129% and yield strength of about 157% were obtained with the addition of 7% Ni-coated CNTs in the base matrix. Also, the coating of Ni on CNT improved the interfacial bonding significantly among the constituents with even dispersion of the reinforcements.

SEM analysis was used to describe the morphology of the extruded Al/MWCNT nanocomposites and also to examine the influence of concentrations of MWCNTs reinforcement on the distribution of Al matrix thereof.

Figure 11 indicates that while all samples were mechanical alloyed/milled at different time intervals, the particle size reduced as the percentage content of MWCNTs increased. This consequence can be ascribed to the way that the MWCNTs serve as a processing control organic surfactant, mitigating the influence of cold-pressure contact welding and facilitating the process of fracturing mechanics of the particulate grains. This diminution in particulate grain matter was owing to the raised propinquity of CNTs, which serve as a refiner by generating a tougher particle surface after each influence from planetary ball milling medium, thereby raising their brittleness.

Figure 11 
                  SEM micrographs of Al–Cu–Mg–T351/MWCNT nanocomposite pulverized powder mechanical alloyed for specific time period according to the percentage weight content of MWCNT.
Figure 11

SEM micrographs of Al–Cu–Mg–T351/MWCNT nanocomposite pulverized powder mechanical alloyed for specific time period according to the percentage weight content of MWCNT.

Therefore, during the attrition process, where each particulate endures continual, persistent fatigue fracture welding cycles, external secondary stages regarding CNTs intervene with this phased process at the same time that they have been integrated into the Al pellets by making them tougher at each time period. This influence was substantially increased with increasing CNTs’ content, thus acquiring a preponderance of the fracturing process and hard/tough as well as tiny minute fragments.

A related research finding was observed by Kundalwal and Rathi [76] who prepared nano MWCNT particulates-reinforced epoxy polymer matrix composites using ultrasonically processed dual mixing method to evaluate various characteristics of the newly developed PMCs. Authors reported that there was an improvement of 21% in tensile strength, 46% in toughness, 22% in shear strength, and 26% in storage modulus with the addition of 0.5% MWCNTs in the epoxy resins. Results of TEM analysis revealed uniform distribution of reinforcements without clustering at any location.

The surface characteristic of AA2024-T351 + MWCNT was studied by XRD analysis as shown in Figure 12(a). Figure 12(b) is the enlarged image (circled portion) of Figure 12(a) of AA2024-T351 + 0.5% MWCNT and reveals that the bulk material comprises of AA2024-T351 and CNTs which indicate that the remaining phases were minor constituents of the composites. XRD scans of Al2024-T351 + MWCNT shows that the CNT is present at 2β = 23.6 and 44.6°, whereas high peaks of aluminum are present at uniform dispersed positions.

Figure 12 
                  (a) XRD image of Al–Cu–Mg–T351 + 0.5% MWCNT composite. (b) Enlarged XRD image of Al–Cu–Mg–T351 + 0.5% MWCNT composite.
Figure 12

(a) XRD image of Al–Cu–Mg–T351 + 0.5% MWCNT composite. (b) Enlarged XRD image of Al–Cu–Mg–T351 + 0.5% MWCNT composite.

Similar outcomes have been observed by Fathi [77] who presented a review article on mechanical behavior of nano composites that describes the difficulties arising during fabrication and enhancement of mechanical properties of the nano composites like MMCs, PMCs etc. Authors presented that these properties of the nanocomposites were highly dependent on their composition, particle size, level of distribution etc.

SEM micrograph images of AA2024-T351 + MWCNT composites of varying percentages processed through ball milling, as shown in Figure 13(a–f), reveals the uniform distribution of CNT. Al particles of 200 mesh size were chosen for better compactness during sintering. Sintered-heat treated and sintered-extruded composites have a favorable effect on tensile strength and hardness.

Figure 13 
                  SEM of heat-treated (a) 0%, (b) 0.1%, (c) 0.2%, (d) 0.3%, (e) 0.4%, and (f) 0.5% MWCNT-reinforced Al–Cu–Mg–T351 alloy.
Figure 13

SEM of heat-treated (a) 0%, (b) 0.1%, (c) 0.2%, (d) 0.3%, (e) 0.4%, and (f) 0.5% MWCNT-reinforced Al–Cu–Mg–T351 alloy.

SEM of sintered-heat treated composites showed the formation of Al4C3 as a result of high temperature after heat treatment. The considerable effect of MWCNT along with carbide formed due to heat treatment resulted in enhanced properties of the tensile strength of the composite. The presence of CNTs, Al–Cu, and Al4C3 are observed after aging heat treatment.

The related research has been reported by Shivaramu et al. [78] who presented an experimental study on MMC’s of Al-Si alloy, which was strengthened with MWCNTs utilizing powder metallurgy processing technique. During production, the concentration of MWCNTs was varied as 0, 0.25, 0.5, 0.75, and 1.0 wt%. The composites were analyzed employing TEM, XRD, and energy-dispersive spectra techniques. Tensile test was conducted according to ASTM G99-95a standard. Wear test was conducted under variable loads and sliding distances (disk/wheel rotational speed ranging from 250 to 750 rpm), and load suddenly dropped with the increment in sliding distance. For certain nanocomposites, though, the ratio of volume loss per unit distance escalated on linear basis with sliding distance. The reinforcing constituents for varied concentrations of MWCNTs exhibited reduced wear resistance, the incorporation of aforesaid caused moderately superior wear rate. Due to the obvious superior characteristics of the reinforcing particulates, the abrasion resistance had strengthened to fervent extent. The type of mechanism operation with volumetric-wear-loss was discovered employing an SEM. The accompanying research revealed by Carneiro and Simoes [79] evaluated the influence of morphology and structure of MWCNTs on the properties of metal matrix composites. The simulation was performed and the results were validated experimentally. Authors reported that morphology and microstructure were the most predominant factors affecting the particle distribution. The related findings have been described by Feijoo et al. [80] who fabricated Al alloy (AA7075)-based composites, which were reinforced with 0.5 and 1 wt% MWCNTs. Composites were fabricated using powder metallurgical process using ball mills for better reinforcement distribution within the matrix. The powders of Al and MWCNT were analyzed using XRD and SEM techniques. The Scherrer formula was adopted to analyze the change in crystal size and micro level deformations of crystal lattice. Authors observed regular dispersion of reinforcements within the matrix without porosity. Also, Al-0.5%MWCNTs composite possessed better hardness and tensile strength together with improved ductility than others.

SEM profile of sintered-heat treated and sintered-extruded composites exhibits the Al2024-T351 + MWCNT fractured nature of nanocomposites, which is similar to the base Al fracture as shown in Figure 14(a–d). The presence of CNTs, Al–Cu, and Al4C3 are observed after aging [71] may be due to the presence of elements present in the alloy, and the reactions that happened during the heat treatment. Fracture micrographs of the Al2024-T351 + MWCNT composite displayed the resistance nature of nanotubes, as illustrated in Figure 14(c) by way of deformation. The breaking of the material for the applied force due to which matrix pulls out and nanotubes breaks in telescopic sheath form are reported by few investigators [7183]. Bent nanotubes increase Young’s modulus during applied tensile load and are rigid in nature [71].

Figure 14 
                  SEM image of Al–Cu–Mg–T351 + MWCNT, (a) tensile fracture with cup-cone failure, (b) sintered-heat treated surface with MWCNT fracture, (c) enlarged image of the X, and (d) sintered-heat treated surface with the distribution of nanotubes at the grain boundary.
Figure 14

SEM image of Al–Cu–Mg–T351 + MWCNT, (a) tensile fracture with cup-cone failure, (b) sintered-heat treated surface with MWCNT fracture, (c) enlarged image of the X, and (d) sintered-heat treated surface with the distribution of nanotubes at the grain boundary.

The related research has been exhibited by Uriza-Vega et al. [84] who prepared MWCNT-reinforced AMCs. Al alloy (Al-7075) was used as base matrix and MWCNTs were synthesized prior to blending in the base matrix and then mixed in the base matrix. The reinforcements were dispersed evenly within the matrix using ultrasonic process, which was followed by milling. The influence of CNTs on the microstructure and mechanical behavior was then analyzed using advance testing techniques. Authors observed uniform distribution of the reinforcements without much clustering as seen in the SEM images. The mechanical behavior was significantly improved with the addition of CNT up to 2 wt% in the base matrix.

Figure 15(a–d) shows the TEM image of MWCNT and Figure 16 illustrates the TEM image of AA2024-T351 + 0.5% MWCNT powder showing the distribution of MWCNT in the composite. MWCNTs are dispersed uniformly and agglomerated evenly at various places in all the reinforced fractions in the composite after a higher rate of the ball milling process. This agglomerated MWCNT has been reduced by controlled ball milling time, not crossing 20 h [82].

Figure 15 
                  (a–d) TEM images of MWCNT powder (courtesy: Nanoshel, USA).
Figure 15

(a–d) TEM images of MWCNT powder (courtesy: Nanoshel, USA).

Figure 16 
                  TEM image of Al–Cu–Mg–T351 + 0.5% MWCNT nanocomposites.
Figure 16

TEM image of Al–Cu–Mg–T351 + 0.5% MWCNT nanocomposites.

TEM image reveals the presence of entangled networks of CNT, and the formation of nanoscale particles of Al4C3 due to heat treatment can be observed [83].

The results of a study of relevant studies have now been unveiled by Tserpes et al. [85] who performed testing of tension and nano-indentation of nanocomposite to find mechanical and nano-mechanical properties of the MWCNT-reinforced polypropylene PMCs. The SEM and scanning probe microscopy analysis for structural properties and topography were also performed. The outcomes of this research work indicated an enhancement in the modulus of elasticity and yield stress. A good dispersion of MWCNTs was observed by the authors and material was divided in three regions namely polymer, interface, and CNTs cluster/conglomeration region. Resistance varied substantially across numerous different regions, ranging from minimal to 130 MPa. The incorporation of CNTs to polypropylene contributed to increased modulus, flexibility, resilience, and elasticity; however, the surface portion seemed to be relatively plastic, according to the ([hardness]3/[modulus-of-elasticity2]) proportion relationship.

The assertions of an existing literature have indeed been disclosed by Devadiga and Fernandes [86] who studied the wear behavior of the CNT and fly ash (FA)-reinforced nano AMCs. During fabrication, the composition of CNT was varied from 0.25 to 0.75 wt % in steps of 0.25 and FA was varied from 4 to 16 wt% in steps of 4 and composites were prepared using powder metallurgy route. The wear behavior was analyzed according to L9 OA. Authors observed that the composition of reinforcements was the most influencing parameter affecting the wear behavior. Authors reported that composition of MWCNTs as 0.25%, FA as 8%, milling time of 2 h, sintering time of 6 h, normal load of 10 N, speed of 200 rpm, and track-distance of 500 m employed better wear resistance among others.

The scientometric analysis has been performed to chalk out potential applications based upon current research trends in the area of MWCNTs-reinforced Al–Cu–Mg–T351 metallic composites. Figure 17 shows the key work overlay chart of last 10 years in the domain of prospective applications of Al–Cu–Mg–T351/MWCNT nanocomposites [87115]. It has been inferred that, in the current decade, metallic composites with MWCNTs as a reinforcing particulates have been characterized by limited researchers to investigate their suitable potential in structural applications [103108]. Such novel composites provide significant characteristics and offer promising application in the industrial automotive, aircraft, electromechanical, lightweight component, nonlinear optics, batteries, nanowires, sensors, and high-strength devices.

Figure 17 
                  Bibliometric analysis on the applications of MWCNTs/Al–Cu–Mg–T351 nanocomposites for structural loadbearing applications.
Figure 17

Bibliometric analysis on the applications of MWCNTs/Al–Cu–Mg–T351 nanocomposites for structural loadbearing applications.

Based upon the aforementioned outcomes from the current novel study, it is concluded that the MWCNTs/Al-Cu-Mg-T351-based nanocomposites have considerable promising applications in automobiles, aviation, and other advanced cutting edge industries, due to its ability to obtain maximum physicomechanical and thermal conductivity characteristics of the composites even at lower reinforcing phase composition owing to the reinforcement’s elongated specific surface area, and the consequences that come with nano-structuring. The advancement of progressive scientific works and innovations in the domain of MWCNTs/Al–Cu–Mg–T351-based nanocomposites have been significantly aided by rise in global industrialized synthesis of MWCNTs as well as advance breakthroughs in the perspective of its commercialized, real-world applications in myriads of sectors.

4 Conclusion and future outlook

Reinforcement of MWCNT with the AA2024-T351 matrix has shown this composite as a potential lightweight material suitable for industrial applications. The development of AA2024-T351 + MWCNT composite by the powder technology route has shown the uniform dispersion of CNT using the ball milling process. Sintered and sintered-heat treated composites have shown the formation of Al4C3 with traces of “Cu” with good interfacial bonding between matrix and reinforcement. The microstructure of SEM and TEM reveals a uniform distribution of CNT and direction of the nanotube in the matrix for both extruded and heat-treated samples. SEM and TEM images revealed that CNT decomposes at a relatively low temperature of 450°C and forms fine Al4C3 precipitates. The inter-granular refinement due to reaction and internal stress relieved during increased heat at the time of sintering and heat treatment enhances the properties. The dispersion strengthening effect by unbundled or bent CNT particles enabled the improvement in the tensile property. Extruded and heat-treated specimens showed enhanced hardness and tensile strength. Tensile-fractured surface exhibited the ductile fracture with a telescopic sheath like pulling of the nanotubes in the composite. It is apparent that milling-time does indeed have a substantial influence on the improvement of physicomechanical characteristics, specifically, elastic modulus. The influence of MWCNT’s concentration, process regulating/governing reagents, CNT dimension, and inert gas environmental conditions on MWCNTs/Al composite is indeed explored. Considering findings from present experimental tests performed with the combined effect of ball milling and powder metallurgy techniques, it is concluded that MWCNT distribution is significantly vital in producing novel composites of high-strength. As a result, the ball milling parameters must be optimized in order to produce the optimal combination of MWCNTs distribution, superior MWCNTs/metallic matrix interfacial contact, relatively low cold working of the metal matrix, and minimal MWCNT damages. Numerous futuristic challenges include accomplishing relatively homogenous distribution of MWCNT's at higher-concentrations, diffusion of MWCNTs at a microlevel if bulk-processing and production processes are used. Furthermore, the adverse-affect of MWCNT orientation/configuration, efforts to bridge the gap between nanoscale and bulk-characteristics, and thus continuing to develop advanced creative modernistic approaches with all of these factors or considerations are keeping in mind.



Acknowledgement

The author Shubham Sharma wishes to acknowledge the Department of RIC, IKGPTU, Kapurthala, Punjab, India for providing the opportunity to conduct this research task.

  1. Funding information: The result was obtained through the financial support of the Ministry of Education, Youth and Sports of the Czech Republic and the European Union (European Structural and Investment Funds – Operational Programme Research, Development and Education) in the frames of the project “Modular platform for autonomous chassis of specialized electric vehicles for freight and equipment transportation,” Reg. No. CZ.02.1.01/0.0/0.0/16_025/0007293. Author Shubham Sharma wishes to acknowledge the Department of RIC, IKGPTU, Kapurthala, Punjab, India for providing opportunity to conduct this research task. Author P. Sudhakara gratefully acknowledges the support from Science and Engineering Research Board (SERB-YSS/2015/001294)), New Delhi, India.

  2. Author contributions: S.S.: conceptualization, methodology, supervision, and writing – original draft preparation; S.S. and V.P.: formal analysis and investigation; S.S., V.P., P.S., J.S., M.P., and R.A.I.: resources; S.S., V.P., P.S., and J.S.: writing – review and editing; S.S., V.P., M.P., and R.A.I.: project administration; S.S. and M.P.: funding acquisition. All authors have read and agreed to the published version of the manuscript.

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

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Received: 2021-07-12
Revised: 2021-09-14
Accepted: 2021-11-01
Published Online: 2021-12-07

© 2022 Shubham Sharma et al., published by De Gruyter

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

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  82. Fabrication of self-assembly CNT flexible film and its piezoresistive sensing behaviors
  83. Thermal valuation and entropy inspection of second-grade nanoscale fluid flow over a stretching surface by applying Koo–Kleinstreuer–Li relation
  84. Mechanical properties and microstructure of nano-SiO2 and basalt-fiber-reinforced recycled aggregate concrete
  85. Characterization and tribology performance of polyaniline-coated nanodiamond lubricant additives
  86. Combined impact of Marangoni convection and thermophoretic particle deposition on chemically reactive transport of nanofluid flow over a stretching surface
  87. Spark plasma extrusion of binder free hydroxyapatite powder
  88. An investigation on thermo-mechanical performance of graphene-oxide-reinforced shape memory polymer
  89. Effect of nanoadditives on the novel leather fiber/recycled poly(ethylene-vinyl-acetate) polymer composites for multifunctional applications: Fabrication, characterizations, and multiobjective optimization using central composite design
  90. Design selection for a hemispherical dimple core sandwich panel using hybrid multi-criteria decision-making methods
  91. Improving tensile strength and impact toughness of plasticized poly(lactic acid) biocomposites by incorporating nanofibrillated cellulose
  92. Green synthesis of spinel copper ferrite (CuFe2O4) nanoparticles and their toxicity
  93. The effect of TaC and NbC hybrid and mono-nanoparticles on AA2024 nanocomposites: Microstructure, strengthening, and artificial aging
  94. Excited-state geometry relaxation of pyrene-modified cellulose nanocrystals under UV-light excitation for detecting Fe3+
  95. Effect of CNTs and MEA on the creep of face-slab concrete at an early age
  96. Effect of deformation conditions on compression phase transformation of AZ31
  97. Application of MXene as a new generation of highly conductive coating materials for electromembrane-surrounded solid-phase microextraction
  98. A comparative study of the elasto-plastic properties for ceramic nanocomposites filled by graphene or graphene oxide nanoplates
  99. Encapsulation strategies for improving the biological behavior of CdS@ZIF-8 nanocomposites
  100. Biosynthesis of ZnO NPs from pumpkin seeds’ extract and elucidation of its anticancer potential against breast cancer
  101. Preliminary trials of the gold nanoparticles conjugated chrysin: An assessment of anti-oxidant, anti-microbial, and in vitro cytotoxic activities of a nanoformulated flavonoid
  102. Effect of micron-scale pores increased by nano-SiO2 sol modification on the strength of cement mortar
  103. Fractional simulations for thermal flow of hybrid nanofluid with aluminum oxide and titanium oxide nanoparticles with water and blood base fluids
  104. The effect of graphene nano-powder on the viscosity of water: An experimental study and artificial neural network modeling
  105. Development of a novel heat- and shear-resistant nano-silica gelling agent
  106. Characterization, biocompatibility and in vivo of nominal MnO2-containing wollastonite glass-ceramic
  107. Entropy production simulation of second-grade magnetic nanomaterials flowing across an expanding surface with viscidness dissipative flux
  108. Enhancement in structural, morphological, and optical properties of copper oxide for optoelectronic device applications
  109. Aptamer-functionalized chitosan-coated gold nanoparticle complex as a suitable targeted drug carrier for improved breast cancer treatment
  110. Performance and overall evaluation of nano-alumina-modified asphalt mixture
  111. Analysis of pure nanofluid (GO/engine oil) and hybrid nanofluid (GO–Fe3O4/engine oil): Novel thermal and magnetic features
  112. Synthesis of Ag@AgCl modified anatase/rutile/brookite mixed phase TiO2 and their photocatalytic property
  113. Mechanisms and influential variables on the abrasion resistance hydraulic concrete
  114. Synergistic reinforcement mechanism of basalt fiber/cellulose nanocrystals/polypropylene composites
  115. Achieving excellent oxidation resistance and mechanical properties of TiB2–B4C/carbon aerogel composites by quick-gelation and mechanical mixing
  116. Microwave-assisted sol–gel template-free synthesis and characterization of silica nanoparticles obtained from South African coal fly ash
  117. Pulsed laser-assisted synthesis of nano nickel(ii) oxide-anchored graphitic carbon nitride: Characterizations and their potential antibacterial/anti-biofilm applications
  118. Effects of nano-ZrSi2 on thermal stability of phenolic resin and thermal reusability of quartz–phenolic composites
  119. Benzaldehyde derivatives on tin electroplating as corrosion resistance for fabricating copper circuit
  120. Mechanical and heat transfer properties of 4D-printed shape memory graphene oxide/epoxy acrylate composites
  121. Coupling the vanadium-induced amorphous/crystalline NiFe2O4 with phosphide heterojunction toward active oxygen evolution reaction catalysts
  122. Graphene-oxide-reinforced cement composites mechanical and microstructural characteristics at elevated temperatures
  123. Gray correlation analysis of factors influencing compressive strength and durability of nano-SiO2 and PVA fiber reinforced geopolymer mortar
  124. Preparation of layered gradient Cu–Cr–Ti alloy with excellent mechanical properties, thermal stability, and electrical conductivity
  125. Recovery of Cr from chrome-containing leather wastes to develop aluminum-based composite material along with Al2O3 ceramic particles: An ingenious approach
  126. Mechanisms of the improved stiffness of flexible polymers under impact loading
  127. Anticancer potential of gold nanoparticles (AuNPs) using a battery of in vitro tests
  128. Review Articles
  129. Proposed approaches for coronaviruses elimination from wastewater: Membrane techniques and nanotechnology solutions
  130. Application of Pickering emulsion in oil drilling and production
  131. The contribution of microfluidics to the fight against tuberculosis
  132. Graphene-based biosensors for disease theranostics: Development, applications, and recent advancements
  133. Synthesis and encapsulation of iron oxide nanorods for application in magnetic hyperthermia and photothermal therapy
  134. Contemporary nano-architectured drugs and leads for ανβ3 integrin-based chemotherapy: Rationale and retrospect
  135. State-of-the-art review of fabrication, application, and mechanical properties of functionally graded porous nanocomposite materials
  136. Insights on magnetic spinel ferrites for targeted drug delivery and hyperthermia applications
  137. A review on heterogeneous oxidation of acetaminophen based on micro and nanoparticles catalyzed by different activators
  138. Early diagnosis of lung cancer using magnetic nanoparticles-integrated systems
  139. Advances in ZnO: Manipulation of defects for enhancing their technological potentials
  140. Efficacious nanomedicine track toward combating COVID-19
  141. A review of the design, processes, and properties of Mg-based composites
  142. Green synthesis of nanoparticles for varied applications: Green renewable resources and energy-efficient synthetic routes
  143. Two-dimensional nanomaterial-based polymer composites: Fundamentals and applications
  144. Recent progress and challenges in plasmonic nanomaterials
  145. Apoptotic cell-derived micro/nanosized extracellular vesicles in tissue regeneration
  146. Electronic noses based on metal oxide nanowires: A review
  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
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