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Microstructural evolution and properties of Cu–20 wt% Ag alloy wire by multi-pass continuous drawing

  • Chu Cheng , Kexing Song EMAIL logo , Xujun Mi , Baoan Wu , Zhu Xiao , Haofeng Xie , Yanjun Zhou , Xiuhua Guo , Haitao Liu , Dingbiao Chen , Xiaoyu Shen and Yong Ding
Published/Copyright: December 31, 2020
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Nanotechnology Reviews
From the journal Nanotechnology Reviews Volume 9 Issue 1

Abstract

The Cu–20 wt% Ag alloy wire rod was prepared using three-chamber vacuum cold mold vertical continuous up-casting followed by multi-pass continuous drawing. The evolution of microstructure, mechanical property, and electrical property of the Cu–20 wt% Ag alloy wire during multi-pass continuous drawing was studied. After multi-pass continuous drawing, the continuous network eutectic structure in the longitudinal section of the as-casted rod was gradually drawn into long fibers that approximately parallel to the axial direction, while the space of the continuous network eutectic structure in the transverse section is getting smaller and smaller. Both the preferred orientation of copper and silver grains are (1,1,1). With the increase of drawing strain (η), the tensile strength of Cu–20 wt% Ag alloy wire gradually increases while the elongation gradually decreases. When the diameter is drawn to 0.02 mm (η = 11.94), the tensile strength of the alloy is 1,682 MPa and elongation is 2.0%. The relationship between tensile strength, elongation, and diameter conforms to Allometric and Boltzmann functions, respectively.

Keywords: Cu–Ag alloy; multi-pass continuous drawing; microstructure evolution; mechanical property; electrical property

1 Introduction

Copper alloy and copper matrix composite materials have many advantages of good arc erosion corrosion resistance [1], wear resistance [2], high strength [3], and other special properties [4]. Due to the excellent strength and high conductivity of Cu–Ag alloy, they are widely used as bonding wire in high-end fields such as integrated circuit packaging, connector [5], electronic communication [6], and audio and video transmission [7]. At present, the Cu–Ag alloy mainly contains low-silver and high-silver alloy wire according to the silver content [8]. Cu–Ag alloy wire with silver content of 0.06–0.3 wt% is widely used as contact wire and data wire [9]. It can replace pure copper as data wire because it has a higher strength, and at the same time, its processing characteristics are the same as those of pure copper wire [10]. The Cu–Ag alloy wire with silver content of 1–20 wt% mainly includes Cu–1 wt% Ag, Cu–2 wt% Ag, Cu–3 wt% Ag, Cu–4 wt% Ag, Cu–6 wt% Ag, Cu–10 wt% Ag, and Cu–20 wt% Ag. Cu–Ag alloy wire with silver content of 1–6 wt% is widely used as voice coil, flexible cables, and bending resistance cable in the field of automotive, medical, and smart devices [11]. When the silver content is more than 10.0 wt%, the Cu–Ag alloy wire is often used as conductive material in splice pieces and precise resistance [12].

The traditional method to prepare Cu–Ag alloy wire is cold mold continuous casting, followed by multi-pass drawing and intermediate annealing [13]. The obtained materials by this mature method usually present good stability [14]. However, segregation and defects always can be observed when we prepared Cu–Ag alloy with high Ag content because of wide solidification range, which leads to breaking during the subsequent drawing process [15]. As a result, super long and slim Cu–Ag alloy wire with high Ag content is difficult to be prepared [16,17]. At present, many researchers in the world are working on the preparation technology of Cu–Ag alloy wire [18]. Feng et al. [19] have studied the influence of drawing process on the performance of directional solidified Cu–Ag alloy wire. The result shows that Cu–Ag alloy wire with the diameter of 0.12 mm can be prepared through the horizontal continuous solidification, followed by multiple cold drawing. The electrical conductivity of the material is up to 58.0 MS/m, with a tensile strength of 300 MPa and elongation of 23%. Ning et al. [20] have researched the preparation of Cu–10Ag in situ nanofiber composite by large deformation, and the results show that the tensile strength of the Cu–Ag alloy wire is up to 1,190 MPa and the conductivity is 68.7% IACS. Zhang et al. [21,22] and Konakov et al. [23] have studied the effects of fiber phase and alloying elements on the microstructure, mechanical properties, and electrical properties of Cu–Ag alloy wire. The result shows that when the eutectic fiber bundle space is more than 150 nm, the relationship between tensile strength and the eutectic fiber bundle space is consistent with Hall–Pecth, and the strengthening effect is considered to be the dislocation plug mechanism [24]. For the as-casted Cu–Ag alloy with low Ag content, few second phases were draw into loosely arranged fibers after cold drawing, which loosely distributed in the copper dendrite gap [25]. However, for the alloy with high Ag content, second phases in the microstructure exist in the form of reticular continuous eutectic layer, and the fibers were arranged in a straight and dense manner after cold drawing. Zuo et al. [26] and Zhao et al. [27] have studied the microstructure and properties of nanostructured Cu–28 wt% Ag microcomposite deformed after solidifying under a high magnetic field. The result shows that the strength of Cu–Ag alloy composites solidified under a high magnetic field is significantly improved due to the smaller space of silver eutectic tissue. Previous research work reported by Liu et al. [28] evaluated the evolution of microstructure and properties of Cu–Ag microcomposites with different Ag content. They found that the increased deformation may lead to the improved tensile strength and decreased electrical conductivity of Cu–Ag alloy. The morphology of eutectic microstructure of Cu–24 wt% Ag alloy has a greater influence on the strength and conductivity than its volume fraction.

In this paper, Cu–20 wt% Ag alloy wire was prepared through three-chamber vacuum and cold mold vertical continuous up-casting followed by multi-pass continuous drawing [29]. The effect of drawing process on the microstructure, texture, mechanical properties, and electrical performance of Cu–20 wt% Ag alloy wire was systematically studied. This study will provide theoretical basis for the superfine, continuous, and accurate drawing control of Cu–Ag alloy with high Ag content.

2 Experiment

2.1 Experimental process

The as-cast Cu–20Ag rod was prepared by self-developed three-chamber vacuum and cold mold vertical continuous up-casting equipment, as shown in Figure 1. Electrolytic copper (99.95%) and high-purity silver particles (99.99%) were used as raw materials. They were placed with a mass proportion of 4:1 in vacuum chamber I. After that, the vacuum chamber I was vacuumed. Secondly, they were smelted in an intermediate frequency induction furnace (≤2,000 Hz) in vacuum chamber II [30]. Thirdly, the as-cast Cu–20Ag rod with a diameter (Φ) of 7.83 mm was prepared from casting mold with a speed of 150 mm/min by cooling after they were fully mixed [31]. Finally, the as-cast Cu–20Ag rod was continuously cold drawn from Φ 7.83 mm to Φ 0.02 mm. Then the materials were heated at 550°C for 1 s. The drawing strain is calculated by η = ln(A 0/A), where A 0 and A are initial and final cross-sectional areas, respectively. The total drawing strain ƞ is 11.94.

Figure 1 Three-chamber vacuum cold mold vertical drawing continuous casting device (a) and its schematic diagram (b).
Figure 1

Three-chamber vacuum cold mold vertical drawing continuous casting device (a) and its schematic diagram (b).

2.2 Analysis methods

The longitudinal and transverse samples were taken from as-cast rod and as-drawn wire with different diameters during multi-pass continuous drawing. After the surface is polished and corroded, the samples were etched using the mixture solution containing 30% NH3·H2O and 20%H2O2 (vol% 1:1). The microstructure was analyzed using a Zeiss AxioVert A1 optical microscope and a field-emission scanning electron microscope (FE-SEM, JSM-7800F, JEOL, Japan). The texture was analyzed using a X-Ray Diffraction (Model D8 Bruker, Germany) with a Cu Kα1 source at 40 kV and 40 mA. Tensile mechanical tests were carried out using a AG-I250KN electronic universal materials testing machine at room temperature. The electrical conductivity were measured using ZY9987 electrical conductivity gauge.

3 Results and discussion

3.1 Microstructure and texture

Figure 2 shows the longitudinal macrophotograph, longitudinal and transverse microstructure of as-cast rod, and as-drawn wire during multi-pass continuous drawing.

Figure 2 The longitudinal macrophotograph, longitudinal, and transverse microstructure of as-cast rod and as-drawn wire with different diameters (a–c – 7.83 mm, η = 0; d–f – 2.13 mm, η = 2.6; g–i – 1.00 mm, η = 4.1; j–l – 0.45 mm, η = 5.7).
Figure 2

The longitudinal macrophotograph, longitudinal, and transverse microstructure of as-cast rod and as-drawn wire with different diameters (a–c – 7.83 mm, η = 0; d–f – 2.13 mm, η = 2.6; g–i – 1.00 mm, η = 4.1; j–l – 0.45 mm, η = 5.7).

As shown in Figure 2b, the longitudinal microstructure of as-cast rod prepared using three-chamber vacuum cold mold vertical continuous up-casting consists of two components: Cu-rich proeutectic matrix (dark contrasts) and Ag-rich eutectic dendrite (light contrasts), which form a rhombic network along the axial direction [32]. Compared with Figure 2e, h, and k, the continuous network eutectic structure in the longitudinal section of the as-cast rod is gradually drawn into long fibers during multi-pass continuous drawing. Those fibers are approximately completely parallel to the axial direction as a function of drawing strain and its space is getting smaller and smaller [33]. In addition, longitudinal macrophotographs in Figure 2a, d, g, and j show that the space of the peripheral fibers is much smaller than that of the core, indicating that the deformation of the periphery in the wire is significantly greater than that of the core during multi-pass continuous drawing [34]. What is more, the deformation gradually weakens from the circumference to the core along the diameter direction. This is mainly due to the deformation process during the drawing: the metal of the periphery in the wire first deforms as a result of shear force when the wire goes across the obconical mould, and then grains in the center slip being motivated by the deformation of the periphery. As a result, the deformation of the periphery in the wire is significantly greater than that of the core during multi-pass continuous drawing [35]. Figure 2c shows that the transverse microstructure of as-cast rod is composed of Cu-rich proeutectic matrix and Ag-rich eutectic dendrite, which form a ruleless network. Compared with Figure 2f, i, and l, after multi-pass continuous drawing, they are still ruleless network in the transverse microstructure, but the space is getting smaller and smaller and the microstructure is getting more dense [36]. In conclusion, after multi-pass continuous drawing, the continuous network eutectic structure in the longitudinal section of the as-cast rod is gradually drawn into long fibers which are approximately parallel to the axial direction, while the cross section is gradually drawn into ruleless network with a smaller space.

Figure 3 shows XRD patterns of as-casted rod and as-drawn wire with different diameters after multi-pass continuous drawing. Three diffraction peaks of Cu(111), Cu(220), and Cu(311) and two diffraction peaks of Ag(111) and Ag(311) can be observed in the as-casted rod prepared using three-chamber vacuum cold mold vertical continuous up-casting. The intensity of Cu(111) and Cu(311) diffraction peaks is stronger than that of Cu(220), and Ag(311) is stronger than that of Ag(111). This is mainly determined by in-house crystal structure and the parameters of vertical continuous up-casting. During multi-pass continuous drawing, the intensity of diffraction peak Cu(111) increases. At the same time, the diffraction peak of Cu(200) can be observed, the intensity of which weakened with the decrease of diameter. The diffraction peak of Cu(220) was weak in the as-cast rod and the wire with a diameter of 5.34 mm, but it increases when the diameter of the wire is drawn to 2.95 mm, indicating that the process is conducive to the growth of Cu(220) and the volume fraction of Cu(220) increases in its structure. Then, its intensity weakens with the decreasing diameter. However, the intensity of Cu(311) peak changed a little during multi-pass continuous drawing. The intensity of Ag(111) peak increases after drawing, and the intensity without obvious difference with the decreased diameter. At the same time, the diffraction peak of Ag(200) arises, and its intensity decreases with the decreased diameter. In addition, the diffraction peaks of Ag(311) gradually disappear, indicating that the volume fraction of Cu(311) gradually decreases. It can be concluded that, after multi-pass continuous drawing, the slip plane and the slip direction of each grain in the Cu–20 wt% Ag wire turn toward the direction of drawing as a function of drawing strain, resulting in the formation of organized grain orientation. The strongest peak is Cu(111) and the preferred orientation of copper grains is (1,1,1) [37]. The intensity of Ag(111) peak is the highest and the preferred orientation of silver grains is (1,1,1).

Figure 3 XRD patterns of as-cast rod and as-drawn wire with different diameters during multi-pass continuous drawing (a – as-cast; b–f – as-drawn).
Figure 3

XRD patterns of as-cast rod and as-drawn wire with different diameters during multi-pass continuous drawing (a – as-cast; b–f – as-drawn).

3.2 Mechanical properties

Figure 4 shows the tensile strength and elongation of alloy wires with different diameters during multi-pass continuous drawing.

Figure 4 Mechanical properties of as-drawn wires with different diameters during multi-pass continuous drawing.
Figure 4

Mechanical properties of as-drawn wires with different diameters during multi-pass continuous drawing.

Figure 4 shows the tensile strength and elongation of alloy wires with different diameters during multi-pass continuous drawing. The rod prepared using three-chamber vacuum cold moertical continuous up-casting presents excellent plasticity, with a tensile strength of 284 MPa and elongation of 48.0%. During the multi-pass continuous drawing, its tensile strength increases gradually with the decrease of diameter [38]. The tensile strength continuously increases when the diameter of alloy wires is drawn from 7.83 to 1.00 mm (η = 4.12). When the diameter is drawn from 1.00 to 0.02 mm (η = 11.94), the tensile strength of alloy wires gradually increases to 1,682 MPa. This is mainly attributed to the fact that the continuous network eutectic structure in the longitudinal section is gradually drawn into long fibers through multi-pass continuous drawing, which are approximately parallel to the axial direction. Meanwhile, work-hardening occurs as the function of drawing strain, which leads to a gradual increase of the tensile strength[39]. However, the elongation of the Cu–20 wt% Ag alloy wire is closely related to the diameter, which decreases rapidly from 48% to 3.68% when the diameter of alloy wires is drawn from 7.83 to 2.95 mm (η = 1.95) due to the sharp increase of the dislocation density inside the grains after drawing deformation [40]. When the diameter is gradually drawn from 2.13 mm (η = 2.60) to 0.02 mm, the elongation of Cu–20 wt% Ag alloy wire tends to be stable at a range of 1.8–3.3%. This is mainly attributed to the fact that the silver fibers have been approximately parallel to the axial direction with a diameter less than 2.13 mm [41].

In order to further research the relationship between the diameter and mechanical properties of Cu–20 wt% Ag alloy wires during multi-pass continuous drawing, Allometric and Boltzmann functions were used to fit the data of the tensile strength and elongation of the alloy wires, respectively. The fitting results were shown in Figure 4. The relationship for tensile strength (δ), elongation (e), and diameter (x) is shown as the following equation:

(1) δ = 178285.85 − 177468.84 × x 0.00118

(2) e = ( 5437.56257 − 5435.11958 ) / ( 1 + exp ( x − 12.71763 / d x ) )

The correlation coefficients between tensile strength (δ), elongation (e), and diameter (x) are calculated as 0.98656 and 0.99763, respectively, indicating that the fitting results are highly reliable.

Figure 5 shows the fracture morphology of the as-casted rod and as-drawn wire with different diameters during multi-pass continuous drawing. Significant differences can be found for the fracture dimples with different diameters. Numerous dimples with large size and deep depth can be observed on the as-casted rod fracture, presenting apparent necking phenomenon, which belongs to a typical ductile fracture. With the increase of the drawing strain, the necking phenomenon of the fracture becomes weaker, especially when the diameter is less than 2.13 mm (η = 2.6), the fracture almost tends to be flat. In addition, the number, depth, and size of the fracture dimples gradually become smaller and more uniform, which indicates that the microstructure of the alloy wire has been refined and its structure is more and more uniform through the deformation in the process of multi-pass continuous drawing. In addition, the tensile strength of the material is significantly improved, and the plasticity is greatly reduced, which is in accordance with the change rule of tensile strength and elongation in Figure 4.

Figure 5 Fracture morphology of as-cast rod and as-drawn wire with different diameters (a and b – 7.83 mm, η = 0; c and d – 5.34 mm, η = 0.77; e and f – 2.95 mm, η = 1.95; g and h – 2.13 mm, η = 2.6; k and l – 1.49 mm, η = 3.31).
Figure 5

Fracture morphology of as-cast rod and as-drawn wire with different diameters (a and b – 7.83 mm, η = 0; c and d – 5.34 mm, η = 0.77; e and f – 2.95 mm, η = 1.95; g and h – 2.13 mm, η = 2.6; k and l – 1.49 mm, η = 3.31).

3.3 Electrical properties

Figure 6 shows the conductivity, DC resistance, and electrical resistivity of Cu–20 wt% Ag alloy wires with different diameters during multi-pass continuous drawing.

Figure 6 Electrical properties of as-drawn wires with different diameters during multi-pass continuous drawing.
Figure 6

Electrical properties of as-drawn wires with different diameters during multi-pass continuous drawing.

It can be seen that the conductivity, resistivity, and DC resistance for the as-casted rod obtained by vacuum cold mold vertical continuous up-casting are 79.30% IACS, 2.17 × 10−2 Ω/M, and 4.51 × 10−4 Ω, respectively. During multi-pass continuous drawing, with the decrease of the diameter (the drawing strain increases, namely), the conductivity of alloy wires gradually decreases, while the electrical resistivity and DC resistance gradually increase [42]. When the diameter of the alloy wire is drawn from 7.83 mm (η = 0) to 0.452 mm (η = 5.70), its conductivity gradually decreases, while electrical resistivity gradually increases and the DC resistance slightly increases. When the diameter of the alloy wire is drawn from 0.452 to 0.0435 mm (η = 10.39), the conductivity rapidly decreases, while the electrical resistivity and DC resistance both rapidly increase. When the diameter of the alloy wire is gradually drawn from 0.0435 to 0.02 mm (η = 11.94), the conductivity rapidly decreases, while the electrical resistivity and DC resistivity sharply increase. Meanwhile, when the diameter of the alloy wire is gradually drawn from 0.435 to 0.02 mm, its conductivity drops sharply from 58.5% IACS to 54.4% IACS, electrical resistivity increases greatly from 2.95 × 10−2 to 3.17 × 10−2 Ω/M, and the DC resistance increases sharply from 19.82 to 100.88 Ω. This is mainly attributed to that, as the drawing proceeds, crystal defects such as microscopic cracks, inter-space, lattice defects, and dislocations are generated in the intragranular [43]. These defects will accumulate as the amount of deformation increases, resulting in the increase of the electrical resistance and decrease of the conductivity [44]. On the other hand, compared to the microstructure in Figure 2, it can be noticed that the average distance of the fibrous structure gradually becomes smaller, and the interface scattering increases with the decrease of distance of the fibers, which will cause the increase of the electrical resistivity and the decrease of the conductivity simultaneously [45].

In order to further research the relationship between the diameter and electrical properties of Cu–20 wt% Ag alloy wires during multi-pass continuous drawing, ExpAssoc and Allometric functions were used to fit the data of conductivity, DC resistance, and electrical resistivity of the alloy wires, respectively. The curves in Figure 6 are the fitting results. The conductivity (σ), electrical resistivity (ρ), and DC resistance (R), respectively, satisfy the following equation:

(3) σ = 54.14533 + 13.22378 × ( 1 − exp ( − x / 0.16254 ) ) + 25.25106 × ( 1 − exp ( − x / 12.39722 ) )

(4) ρ = 0.03204 − 0.00499 × ( 1 − exp ( − x / 4.49466 ) ) − 0.00603 × ( 1 − exp ( − x / 0.11232 ) )

(5) R = 0.02852 × x − 2.08785

The correlation coefficients between conductivity (σ), electrical resistivity (ρ), and DC resistance (R) and diameter (x) are, respectively, calculated as 0.9907, 0.9857, and 0.9997, indicating that the fitting results are highly reliable.

4 Conclusions

During the multi-pass continuous drawing process, the continuous network eutectic structure in the longitudinal section of the as-casted Cu–20 wt% Ag rod is gradually drawn into long fibers that approximately parallel to the axial direction. However, the space of the continuous network eutectic structure in the transverse section became much more smaller. The obtained wire present typical (1,1,1) face-centered cubic structure. With the increase of drawing strain, the tensile strength of Cu–20 wt% Ag alloy wire appeared an increasing trend, while the elongation showed an opposite character. The relationship between tensile strength, elongation, and its diameter conforms to Allometric and Boltzmann functions, respectively. The conductivity decreases while the resistivity and DC resistance gradually increase, and the relationship between conductivity, resistivity, DC resistance, and its diameter conforms to the ExpAssoc. ExpAssoc, and Allometric function relation, respectively.

Acknowledgments

This work was supported by the National Natural Science Foundation of China (Grant No. 52071133), National Key Research and Development Program (Grant No. 2016YFB0301400), Key Technologies R & D Program of He’nan Province (Grant No. 202102210207), Chinese Postdoctoral Science Foundation (Grant No. 2020M672222), Henan Innovation Leading Project (Grant No. 191110210400), Innovation Fund for Outstanding Talents of Henan Province (Grant No. 182101510003), and Luoyang Science and Technology Major Project (Grant No. 1901006A).

  1. Conflict of interest: The authors declare no conflict of interest regarding the publication of this paper.

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Received: 2020-11-26
Accepted: 2020-12-09
Published Online: 2020-12-31

© 2020 Chu Cheng et al., published by De Gruyter

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

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https://doi.org/10.1515/ntrev-2020-0108
Keywords for this article
Cu–Ag alloy; multi-pass continuous drawing; microstructure evolution; mechanical property; electrical property
Creative Commons
BY 4.0

Articles in the same Issue

  1. Research Articles
  2. Generalized locally-exact homogenization theory for evaluation of electric conductivity and resistance of multiphase materials
  3. Enhancing ultra-early strength of sulphoaluminate cement-based materials by incorporating graphene oxide
  4. Characterization of mechanical properties of epoxy/nanohybrid composites by nanoindentation
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  6. A facile and simple approach to synthesis and characterization of methacrylated graphene oxide nanostructured polyaniline nanocomposites
  7. Ultrasmall Fe3O4 nanoparticles induce S-phase arrest and inhibit cancer cells proliferation
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  9. Effect of nano-strengthening on the properties and microstructure of recycled concrete
  10. Stabilizing effect of methylcellulose on the dispersion of multi-walled carbon nanotubes in cementitious composites
  11. Preparation and electromagnetic properties characterization of reduced graphene oxide/strontium hexaferrite nanocomposites
  12. Interfacial characteristics of a carbon nanotube-polyimide nanocomposite by molecular dynamics simulation
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  16. Experimental study on photocatalytic degradation efficiency of mixed crystal nano-TiO2 concrete
  17. Halloysite nanotubes in polymer science: purification, characterization, modification and applications
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  23. Printability of photo-sensitive nanocomposites using two-photon polymerization
  24. In situ synthesis of expanded graphite embedded with amorphous carbon-coated aluminum particles as anode materials for lithium-ion batteries
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  27. Supramolecular ionic polymer/carbon nanotube composite hydrogels with enhanced electromechanical performance
  28. Genetic mechanisms of deep-water massive sandstones in continental lake basins and their significance in micro–nano reservoir storage systems: A case study of the Yanchang formation in the Ordos Basin
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  51. Exact solutions of bending deflection for single-walled BNNTs based on the classical Euler–Bernoulli beam theory
  52. Effects of substrate properties and sputtering methods on self-formation of Ag particles on the Ag–Mo(Zr) alloy films
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  66. Combining Zn0.76Co0.24S with S-doped graphene as high-performance anode materials for lithium- and sodium-ion batteries
  67. Synthesis of functionalized carbon nanotubes for fluorescent biosensors
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  69. Incorporation of redox-active polyimide binder into LiFePO4 cathode for high-rate electrochemical energy storage
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  72. Microfluidic-assisted synthesis and modelling of monodispersed magnetic nanocomposites for biomedical applications
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  77. Mechanical reinforcement with enhanced electrical and heat conduction of epoxy resin by polyaniline and graphene nanoplatelets
  78. High-efficiency method for recycling lithium from spent LiFePO4 cathode
  79. Degradable tough chitosan dressing for skin wound recovery
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  81. Review articles
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  83. Review on the research progress of cement-based and geopolymer materials modified by graphene and graphene oxide
  84. Review on modeling and application of chemical mechanical polishing
  85. Research on the interface properties and strengthening–toughening mechanism of nanocarbon-toughened ceramic matrix composites
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  104. Recent advance in surface modification for regulating cell adhesion and behaviors
  105. Hyaluronic acid as a bioactive component for bone tissue regeneration: Fabrication, modification, properties, and biological functions
  106. Theoretical calculation of a TiO2-based photocatalyst in the field of water splitting: A review
  107. Two-photon polymerization nanolithography technology for fabrication of stimulus-responsive micro/nano-structures for biomedical applications
  108. A review of passive methods in microchannel heat sink application through advanced geometric structure and nanofluids: Current advancements and challenges
  109. Stress effect on 3D culturing of MC3T3-E1 cells on microporous bovine bone slices
  110. Progress in magnetic Fe3O4 nanomaterials in magnetic resonance imaging
  111. Synthesis of graphene: Potential carbon precursors and approaches
  112. A comprehensive review of the influences of nanoparticles as a fuel additive in an internal combustion engine (ICE)
  113. Advances in layered double hydroxide-based ternary nanocomposites for photocatalysis of contaminants in water
  114. Analysis of functionally graded carbon nanotube-reinforced composite structures: A review
  115. Application of nanomaterials in ultra-high performance concrete: A review
  116. Therapeutic strategies and potential implications of silver nanoparticles in the management of skin cancer
  117. Advanced nickel nanoparticles technology: From synthesis to applications
  118. Cobalt magnetic nanoparticles as theranostics: Conceivable or forgettable?
  119. Progress in construction of bio-inspired physico-antimicrobial surfaces
  120. From materials to devices using fused deposition modeling: A state-of-art review
  121. A review for modified Li composite anode: Principle, preparation and challenge
  122. Naturally or artificially constructed nanocellulose architectures for epoxy composites: A review
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