Microstructure and Properties of Cu-ZrO₂ Nanocomposites Synthesized by in Situ Processing

Abstract

In situ chemical reaction method was used to synthesize Cu-ZrO₂ nanocomposite powders. The process was carried out by addition of NH₄(OH) to certain amount of dispersed Cu(NO₃)₂·3H₂O and ZrOCl₂·8H₂O solution. Afterwards, a thermal treatment at 650 °C for 1 h was conducted to get the powders of CuO and ZrO₂ and remove the remaining liquid. The CuO was then reduced in preferential hydrogen atmosphere into copper. The powders were cold pressed at a pressure of 600 MPa and sintered in a hydrogen atmosphere at 950 °C for 2 h. The structure and characteristics were examined by X-ray diffraction (XRD), field emission scanning electron microscopy (FESEM) and transmission electron microscopy (TEM). The results showed that the nanosized ZrO₂ particles (with a diameter of about 30-50 nm) was successfully formed and dispersed within the copper matrix. The density, electrical conductivity, mechanical strength measurements (compression strength and Vickers microhardness) and wear properties of Cu-ZrO₂ nanocomposite were investigated. Increment in the weight % of ZrO₂ nano-particles up to 10 wt.% in the samples, caused the reduction in the densification (7.2%) and electrical conductivity (53.8%) of the nanocomposites. The highest microhardness (146.5 HV) and compressive strength (474.5 MPa) of the nanocomposites is related to the Cu-10 wt.% ZrO₂. Owing to the good interfacial bonding between uniformly dispersed ZrO₂ nanoparticles and the copper matrix. The abrasive wear rate of the Cu-ZrO₂ nanocomposite increased with the increasing load or sliding velocity and is always lower than that of copper at any load or any velocity.

Keywords:
Cu-ZrO₂ nanocomposite; In Situ chemical synthesis; Microhardness; Compressive strength; Electrical conductivity; Abrasive wear

1. Introduction

Nano-sized ceramic particles in a nanocrystalline metal matrix prepared by the in situ chemical reaction can improve the mechanical, tribological, and anti-corrosion properties of the metal^1-5. In recent years nanocomposite materials have attracted much attention owing to their improved physical and mechanical properties. The properties of such materials strongly depend on the particle size and distribution of nanoparticles in the matrix^6-9.

Copper based materials are widely used where high electrical and thermal conductivities are required. Rotating source neutron targets, combustion chamber liners, the electrode of resistance welding, integrated circuit sealing materials, high voltage switches and heat exchangers are examples of copper based materials' applications. These applications require a suitable performance, e.g. high conductivity and excellent mechanical properties, at elevated temperatures and in electronic industries^10-14. Pure copper, on the other hand, suffers from low tensile strength, low hardness and poor wear resistance^10,12,15. Therefore, one of the potential solutions for these drawbacks is the incorporation of a reinforcement element, which results in copper matrix composite as a by-product^16-18.

Oxide dispersion strengthening (ODS) is a suitable method to improve the mechanical properties of the copper matrix composites¹⁹. Due to high interfacial energy between the molten metal and oxide particles melting and casting techniques are not used to fabricate such composites; therefore these composites should be produced by the powder metallurgy methods. The main steps of these methods are the production of composite powder, followed by consolidation to get a bulk material.

The oxide dispersoids can be added into the copper matrix by ex-situ method or in-situ method. The shortcoming of ex-situ method is that nano-sized oxide dispersoids can be homogeneously dispersed in the copper matrix²⁰. Meanwhile, the bonding between the particles and the copper matrix is poor. In contrast, dispersion strengthened copper alloys can be produced by various in-situ processing methods with a homogeneous structure, such as internal oxidation, reactive spray deposition and reaction synthesis, etc^20-22.

Nowadays, it is well known that by proper reinforcement selection, better properties for MMCs could be produced. Considering this comment, a variety of particulate ceramic materials like Al₂O₃^{2,6,8,14-16,19-22}, SiC^12,13, and TiB₂¹⁸ have been utilized to reinforce the copper matrix. The usage of above reinforcements has led to the enhancement of mechanical properties, which have been reported by researchers cited above. Among these, however, fine stabilized ZrO₂ ceramic particles could be a proper reinforcing material due to their high strength and stiffness, high melting temperature, and relatively good electrical property²³.

Few studies have been published about strengthening copper using zirconia particles by the method of the in-situ chemical reaction. A Cu-ZrO₂ nanocomposite has been prepared by Ding Jian²⁴ by the in-situ chemical method, and another by Gao Jing²⁵ using the powder metallurgy techniques, respectively. They studied the effect of the process parameters including the initial pressure, the sintering temperature and sintering time, content of ZrO₂ particles on the properties of the composite.

Based on the above research work, the present study aims at producing homogeneous Cu-ZrO₂ composites from chemically prepared CuO-ZrO₂ mixtures and investigate the effect of ZrO₂ on the crystallite size, particle size and morphology of the obtained powder. Furthermore, their effect on microstructure, and relative density of sintered compacted samples were studied. Electrical conductivity, mechanical and abrasive wear properties of resulting nanocomposites were also studied.

2. Experimental Work

Soluble nitrates of copper (II) nitrate Cu(NO₃)₂·3H₂O, zirconium oxychloride ZrOCl₂·8H₂O and ammonium hydroxide NH₄(OH), could be used as transient components for the in situ chemical synthesis of nanocomposite Cu-ZrO₂ powders. The accomplished in situ chemical processes were adopted to prepare Cu-ZrO₂ nanocomposite, as summarized in Figure 1. This process consists of four main stages:

Figure 1
Flowchart of preparation of Cu-ZrO₂ nanocomposite powder using in situ chemical process.

• Making an aqueous solution of Cu(NO₃)₂·3H₂O and ZrOCl₂·8H₂O; the quantities of salts were taken such that the resulting composition of the Cu-ZrO₂ nanocomposite system with 2.5, 5 &10 wt. % of zirconia would be attained;

• NH₄(OH), dissolved in water (28%), was added dropwise while stirring the mixture with a magnetic stirrer for 20 min and then washed with water repeatedly and filtered Eqn. (1);

(1) $\begin{array}{c}\mathit{Cu}{\left({\mathit{NO}}_{\mathit{3}}\right)}_{\mathit{2}}\mathit{+}{\mathit{ZrOCl}}_{\mathit{2}}\mathit{+}\mathit{3}{\mathit{NH}}_{\mathit{4}}\left(\mathit{OH}\right)\mathit{+}{\mathit{H}}_{\mathit{2}}\mathit{O}\mathit{\to }\hfill \\ \mathit{Cu}{\left(\mathit{OH}\right)}_{\mathit{2}}\mathit{+}\mathit{Zr}{\left(\mathit{OH}\right)}_{\mathit{3}}\mathit{+}\mathit{2}{\mathit{NH}}_{\mathit{4}}{\mathit{NO}}_{\mathit{3}}\mathit{+}{\mathit{NH}}_{\mathit{4}}{\mathit{Cl}}_{\mathit{2}}\hfill \end{array}$

• The filtered mixture was dried at 120 °C overnight, and then annealed in an air atmosphere at 650 ◦C for 1 h to obtain the composite powder of the Cu and Zr oxides Eqn. (2);

(2) $\begin{array}{c}\mathit{Cu}{\left(\mathit{OH}\right)}_2+\mathit{Zr}{\left(\mathit{OH}\right)}_3\stackrel{650°\mathit{C},1\mathit{h}}{\to }\mathit{CuO}+\hfill \\ {\mathit{ZrO}}_2+2{\mathit{H}}_2\mathit{O}+\frac{1}{2}{\mathit{O}}_2\hfill \end{array}$

• Reduction of thermally treated powders in a hydrogen atmosphere at a temperature of 500 °C for one hour, whereby the copper oxide was transformed into elementary copper and the ZrO₂ remained unchanged Eqn. (3).

(3) $\mathit{CuO}+{\mathit{ZrO}}_2\stackrel{500°\mathit{C},30\min }{\to }\mathit{Cu}+{\mathit{ZrO}}_2+{\mathit{H}}_2\mathit{O}$

After reduction, the powders were characterized by X-ray diffraction (XRD) with CuKα radiation, λ= 1.5418 Å and at 36 kV and 26 mA. The X-ray data were collected in steps of 0.02^◦ (2θ) with the scanning scope of 20-80^◦. Evaluation of effective sizes of coherent scattering area was carried out in compliance with the Scherrer formula with the strongest peaks of phases analyzed. And the zirconia extracted from the Cu-ZrO₂ composite powder was characterized using transmission electron microscopy (TEM; Model JEOL JEM-2010).

Prior to sintering, the produced Cu-ZrO₂ nanocomposite powders were compacted in a hydraulic press at a pressure of 600 MPa. in a steel mold to obtain cylindrical shaped specimens having 12 mm diameter and 12 mm height. The powders were mixed with 0.5% paraffin wax as a lubricant to reduce friction during compaction. Sintering of all the green compacts were carried out using a ceramic tubular furnace in a hydrogen atmosphere at 950 °C for 2 h and a heating rate of 10 °C /min²¹.

The microstructure of the prepared nanocomposites was examined by optical microscope model Olympus PMG 3−F3, while microstructural analyses were performed using field emission scanning electron microscopy (FESEM Hitachi S4160) and SEM fitted with EDS. True densities of the nanocomposites were measured by using the Archimedes' method (ASTM-C20) and compared with the theoretical densities to obtain varying degree of densification. The theoretical densities of compacts were calculated from the simple rule of mixtures, taking the fully dense values for copper (8.96 g/cm³) and zirconia (5.68 g/cm³). The electrical resistivity of the composite samples was measured using the two-probe using Omega micro-ohmmeter, and electrical conductivity of composite was calculated from these measurements. Vickers microhardness was performed on the polished samples under a test load of 50 g_f and a dwell time of 10 s in accordance with the ASTM standard E 92. In order to obtain optimum results, microhardness values were determined by taking the average of six different measurements randomly on each sample. The Compression tests were performed over an initial strain rate of 10^-4 s^-1 at room temperature using a universal testing machine model HU−F500KN. Cylindrical specimens with a height of 12 mm and a diameter of 12 mm were used in compliance with ASTM E9-89a standard for measuring the compressive response of the matrix and composite materials²⁶. Special graphite based grease is placed between the tested specimen and the platen of the compression machine to minimize friction. The percentage reduction was maintained at 60 %. The end surfaces of the specimen were maintained as normal to the axis of specimen.

Abrasive wear tests were carried out with a pin-on-disc tester. Rectangular specimens having contact area of 44 mm² are loaded against a rotating disc, which carried a bonded abrasive SiC paper of 600 grit. The applied normal loads used were 3, 5, 7 and 9 N. The sliding velocities employed were 0.5, 0.75 and 1 m/s. The sliding distance was kept constant at 120 m for each sample. In these tests, each specimen was ground up to grade 2000 abrasive paper to ensure that the wear surface is in complete contact with the abrasive counterface. The weight loss of the pin was measured at various intervals in an analytical balance of 0.0001g precision. The pins were cleaned in acetone and dried prior to each weight measurement. The abrasive wear rate of the pins was defined as the weight loss suffered per unit sliding distance.

3. Results and Discussions

3.1 Characterization of the prepared powders

Figure 2 shows X-ray diffraction (XRD) pattern of nanocomposite (Cu-2.5, 5 and 10 wt.% ZrO₂) powders after reduction by hydrogen. The sharp XRD peaks on the pattern correspond to Cu phase and the low intensity ones could be attributed to tetragonal ZrO₂ phase. The ZrO₂ peaks showed lower intensity values than that of copper. It was noticed that the intensity of the ZrO₂ peaks are not clear up to 10% ZrO₂. This may be attributed to the fact that ZrO₂ particles are extremely small that they were embedded in the copper matrix. However, XRD peak intensities of the ZrO₂ phase are noticeably increased with increasing weight percentage of ZrO₂. The particle size of zirconia was calculated from X-ray line broadening using Scherer's formula (D = 0.9λ/β cosθ), where, D is the crystallite size, λ is the wavelength of the radiation, θ is the Bragg's angle and β is the full width at half maximum²⁷. The crystallite size of zirconia nanoparticles showed a value of 50 nm whilst size of copper crystallites were 270 nm.

Figure 2
XRD pattern of the Cu-ZrO₂ nanocomposite after reduction.

The obtained Cu-ZrO₂ nanocomposite powders were characterized by FESEM as presented in Figure 3. Particles with a size of 20-60 nm are clearly visible, as well as the presence of few agglomerates >100 nm. The particles are irregularly shaped, with the presence of individual nodular particles with a rough surface morphology.

Figure 3
FE-SEM micrograph of the nanocomposite powder; (a) Cu-2.5 wt% ZrO₂, (b) Cu-5 wt% ZrO₂ and (c) Cu-10 wt% ZrO₂.

The structure of ZrO₂ is formed during the heat treatment of nanocomposite powder in air (650 °C, 1 h). In order to identify the ZrO₂ dispersoids embedded in Cu-ZrO₂ powders, mixed powder was flushed with 10% nitric acid to selectively pickle Cu matrix, the remaining ZrO₂ dispersions were collected by filtering. Figure 4 shows the particle sizes and shapes of ZrO₂ powder. This was observed clearly in the high resolution of TEM. TEM observations confirmed that the ZrO₂ particle size ranged from 40 to 60 nm. All extracted particles showed regular shape appearance.

Figure 4
TEM images of ZrO₂ extracted from the Cu-ZrO₂ nanocomposite powder.

3.2 Characterization of the sintered nanocomposites

Microstructural studies conducted on the composites revealed homogeneous distribution of the ZrO₂ particles in the Cu matrix. To achieve optimized mechanical and electrical properties of the composite materials, it is significant to obtain uniform distribution of reinforcement in the matrix. If reinforcement particles in the composites do not disperse uniformly, this affects mechanical and electrical properties of composites negatively²³. Microstructural morphology and distribution of the components in the Cu ZrO₂ composites sintered at 950 °C for 2 h, as a function of ZrO₂ content, are shown in Figure 5. Brighter regions imply Cu matrix and darker and cornered particles imply the reinforcement component of ZrO₂. It can be seen that ZrO₂ particles are homogeneously dispersed in the Cu matrix.

Figure 5
Optical images of the nanocomposite metallographic structure; (a) Cu-2.5 wt% ZrO₂, (b) Cu-5 wt% ZrO₂ and (c) Cu-10 wt% ZrO₂.

Figure 6 shows the FE-SEM images of Cu-2.5, 5 and 10 wt.% ZrO₂ composites sintered at 950 ^o C for 2 h. The FE-SEM micrographs give abundant information about the ZrO₂ distribution, status of physical intimacy between Cu and ZrO₂ and mechanical phenomena. With the increase in weight percentage of ZrO₂ in Cu matrix the efficiency of distribution becomes remarkably better. The density difference between the matrix and reinforcement also leads to the formation of clusters sometimes at high wt.% of the reinforcement²⁸. The physical contact of the ZrO₂ nanoparticles with the Cu matrix can be attributed to the high atomic diffusivity of the nanoparticles. The stabilization of the surface energy of nanoparticles is a thermodynamic driven phenomenon; hence it is quite obvious that the physical adherence of Cu with ZrO₂ is proper in the nanocomposites.

Figure 6
FE-SEM micrographs of nanocomposites; (a) Cu-2.5 wt% ZrO₂, (b) Cu-5 wt% ZrO₂ and (c) Cu-10 wt% ZrO₂.

In order to determine the distribution of elements in the structure, surface analysis of the sample was performed by FE-SEM and the composition scanning (EDS) images shown in Figure 7. From the microstructure analysis, it can be concluded that the samples are well densified and sintered. Peaks of elementary Cu, O and Zr were detected, which are related to the composition of ZrO₂ particles and Cu matrix, respectively. The ZrO₂ particles with the high melting point, high hardness and excellent thermal stability and chemical inertness do not melt or coarsen when the annealing temperature approaches the melting point of copper, which effectively pins down the grain and sub-grain boundaries of the copper matrix and impedes the movement of dislocation and improves strength of the composite at elevated temperature.

Figure 7
FE-SEM micrograph (a) and EDS (b) of Cu-10 wt.% ZrO₂ nanocomposite.

The powder compaction is an important step in the preparation of bulk materials by powder technology. This step controls the porosity and the shape of the final product that can be sintered. Bar graph illustrating the densification measured after compaction and sintering of the Cu-ZrO₂ composites as a function of ZrO₂ content is shown in Figure 8. Relative density is the ratio of experimental and theoretical densities of sample. Experimental density was determined by the Archimedes method and the theoretical density was calculated from the simple rule of mixtures. It was clear that, the densification of Cu-ZrO₂ composites was decreased from 95.6 % to 88.7 % by increasing ZrO₂ weight fraction from 0 % up to 10% under the same processing conditions. This is due to the density of ZrO₂ nanoparticles being much smaller than that of copper and high porosity content which accompanies the high fraction of reinforcement ZrO₂²⁴. Moreover, decreasing of relative density with increasing zirconia content in the metal matrix probably could be due to the presence of zirconia nanoparticles on the surface of copper micrometric particles produces a remarkable increase of porosity in the microstructure of the samples. The creation of voids in the Cu matrix hinders the densification and impedes the continuity in intimacy contact of Cu and zirconia. In addition, the decline in the pressing capacity of samples with increasing in the amount of ZrO₂ is due to the high hardness of ZrO₂. Therefore, these composites have lower compressibility that results in lower densification^29,30.

Figure 8
Bar graph of densification of Cu−ZrO₂ composites as function of ZrO₂ content.

Electrical conductivity of each sample was measured and compared to the value of standard electrical conductivity, which is given by copper compact of industrial grade and reported as percentage of standard conductivity as shown in Eq. (4);

(4) $\mathrm{Electrical}\mathrm{conductivity}\mathrm{(\%}\mathrm{std})=\frac{{\mathit{\sigma }}_{\mathit{s}}}{{\mathit{\sigma }}_{\mathit{std}}}x100$

where σ_s is the electrical conductivity of the tested sample and σ_std is the electrical conductivity of the standard copper. Bar graph illustrating the electrical conductivity after compaction and sintering of the Cu-ZrO₂ composites as a function of ZrO₂ content is shown in Figure 9. Electrical conductivity of composites decreased with increasing content of ZrO₂. This can be attributed to the lower electrical conductivity of ZrO₂ compared to that of Cu. The second reason is the agglomeration of some ZrO₂ particles at the grain boundaries which can form a kind of grain boundary phase that increases the scattering of the charge carrier, hence reducing the electrical conductivity. Electrical conductivity of the metal is mainly dependent on the movement of the internal electron. ZrO₂ particles can increase the scattering surfaces for the conduction electrons in the matrix and reduce the electrical conductivity of the Cu matrix composites³¹. Overall, increment in the weight % of ZrO₂ nano-particles up to 10 wt.% in the samples, caused the reduction in the electrical conductivity (53.8%) of the nanocomposites, while using Al₂O₃ decreased the electrical conductivity to18.5%²².

Figure 9
Bar graph of electrical conductivity of Cu−ZrO₂ composites as function of ZrO₂ content.

Bar graph illustrating the microhardness after compaction and sintering of the Cu ZrO₂ composites as a function of ZrO₂ content is shown in Figure 10. It was observed from the present study that by increasing the amount of ZrO₂ from 0% to 10%, microhardness increased from 63.2 to 146.5 HV. The microhardness of Cu is improved considerably with the addition of ZrO₂ nanoparticles at the expense of its ductility, this can be attributed to the high hardness of ZrO₂. The increase in hardness of the composite can also be attributed to the gradual decrease in grain size of the Cu matrix as a result of the presence of nano-ZrO₂ particles. Also, the nano-ZrO₂ particles embedded in the Cu matrix would prevent the slip of the grain boundary of Cu matrix, thereby, improving the hardness of the composite³². The hardness of material is a physical parameter indicating the ability of resisting local plastic deformation. Reinforcing nano-ZrO₂ particles with high hardness, are dispersed in the copper matrix and act as obstacles to the movement of dislocation when plastic deformation occurs. Also the hardness enhancement is an indication of high interfacial strength at Cu-ZrO₂ interface and homogeneous distribution of ZrO₂ within Cu matrix²⁵.

Figure 10
Bar graph of microhardness of Cu−ZrO₂ composites as function of ZrO₂ content.

Bar graph illustrating the compressive strength after compaction and sintering of the Cu-ZrO₂ composites as a function of ZrO₂ content is shown in Figure 11. Obviously, the compressive strength value of Cu-ZrO₂ composite is significantly higher than that of the Cu matrix, suggesting that the ZrO₂ nanoparticles can strongly enhance the mechanical strength of the Cu matrix. The highest value of the compressive strength of the sintered samples, 474.5 MPa, were obtained after addition of up to 10 wt.% ZrO₂. Although tensile testing can determine if a proper bonding has been produced yet, compression test can also be helpful to studying the barreling and upsetting behavior of the compacts. Stronger bonds among particles delay the crack initiation during deformation especially at the time of barreling^33,34.

Figure 11
Bar graph of compressive strength of Cu−ZrO₂ composites as function of ZrO₂ content.

Also, it can be observed that by increasing the amount of ZrO₂ from 0 to 10 wt.%, the compressive strength increased from 318.7 to 474.5 MPa. This increase can be explained by the presence of incoherent zirconia nanoparticles that act like barriers to the motion of dislocations. Also the compressive strength enhancement is an indication of stronger bonding at Cu-ZrO₂ interface and homogeneous distribution of ZrO₂ within Cu matrix³⁵. Additionally, increasing the amount of ZrO₂ lead to a decrease in the distance between the ZrO₂ particles. Decreasing the distance between the ZrO₂ particles will increase the required tension for dislocation motion between the ZrO₂ particles leading to an increase in the material strength³¹.

The fractographs of different deformed composites at room temperature are shown in Figure 12. It was observed that the shape of compression specimens gradually changed their original shapes from cylinder to barrel-like shape during the deformation due to friction between the surfaces of the specimens and graphite plates. It was observed during the compression tests that, all tested nanocomposite specimens were cracked before reaching 60% reduction in height whilst monolithic copper specimen showed no cracks up to 60% reduction. It was observed that increasing ZrO₂ content composites are more prone to circumferential cracks.

Figure 12
Fractography of different deformed composites: (a) Cu, (b) Cu-2.5 wt.% ZrO₂, (c) Cu-5 wt.% ZrO₂, (d) Cu-10 wt.% ZrO₂.

Figures 13(a-c) show the effect of the applied load on abrasive wear rate of Cu ZrO₂ nanocomposite at sliding distance of 120 m and various velocities from 0.5 to 1 m/s. It can be observed from Figs. 13(a-c), that with increasing the applied normal load during wear tests, the abrasive wear rate of pure copper and Cu-ZrO₂ nanocomposite increases^20,21. Applied load affects the wear rate of compacts significantly and is the most dominating factor controlling the wear behavior. By increasing the applied load, plastic deformation on the subsurface due to increased penetration depth of counterface can occur.

Figure 13
Abrasive wear rate of Cu−ZrO₂ nanocomposites with various ZrO₂ content at the sliding distance of 120 m; (a) V = 0.5 m/s, (b) V = 0.75m/s, (c) V = 1 m/s, (d) load = 9 N.

It can also be seen that the increase in amount of incorporated ZrO₂ particles in the pure copper matrix decreased the abrasive wear rate and increased the wear resistance. The significant reduction in the abrasive wear rate of Cu-ZrO₂ nanocomposite is due to the incorporation of inert ZrO₂ nanoparticles in the pure copper matrix which led to reduction in the size of copper crystals and an improvement in microhardness of the nanocomposites. This latter is due to the combined effect of both grain-refinement and dispersion-strengthening, which results in considerable improvement in abrasion wear resistance of the Cu-ZrO₂ nanocomposites^36,37. It can also be clearly seen in Figure 13d that the abrasive wear rate increases with the increase of sliding velocity. This is associated with the increase of surface temperature under high sliding velocity, which promotes softening of the surface, leading to more surface and subsurface damage, eventually resulting in higher abrasive wear rate.

The worn surfaces of unreinforced Cu and Cu−10% ZrO₂ nanocomposite specimens under 9 N load and sliding velocity of 1 m/s were revealed in Figure 14. As shown in Figure 10a, the continuous furrow and deeper furrow can be found on the surface, which was paralleled to sliding direction. Some finer copper grains had peeled off during the wear process. The worn surface of the Cu-10% ZrO₂ nanocomposites was shown in Figure 10b. Compared with Cu matrix materials, the shallower and narrower furrow was found on the wear surface, and grain stripping was slight. The figure shows distinct grooves and ridges running parallel to each other's in the sliding direction. It can be seen from the micrographs that the grooves are wider and debris in Cu matrix as compared within the Cu-ZrO₂ one under the sample conditions indicating the higher wear resistance of Cu-ZrO₂ sample. This can be explained by the formation of a thick transfer lager which protects the underlying Cu matrix from any contact with the sliding SiC abrasive counterpart so reduction of wear rate takes place.

Figure 14
The worn surface; (a) Cu matrix, (b) Cu-10 wt. % ZrO₂ nanocomposites.

4. Conclusions

The following conclusions can be drawn based on the present study:

1. Cu matrix reinforced with different weight fraction of the zirconia (2.5, 5 and 10 wt.%), were successfully prepared by in situ chemical route followed by pressing and sintering.

2. In situ chemical route gave nanoparticles of zirconia of 50 nm size that are uniformly dispersed within Cu-matrix.

3. Increasing the weight fraction of ZrO₂ nano-particles up to 10 wt.% in the samples, caused reduction in the densification (7.2%) and electrical conductivity (53.8%) of the nano-composites.

4. The Cu-10 wt.% ZrO₂, achieved the highest micro-hardness (146.5 HV) and compressive strength (474.5 MPa) of the nanocomposites.

5. The abrasive wear rate of the Cu-ZrO₂ nanocomposite increased with the increasing load or sliding velocity and is always lower than that of unreinforced copper at any load or any velocity. The wear resistance of the Cu-ZrO₂ nanocomposite reinforced with 10% ZrO₂ is obviously improved.

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Publication Dates

• Publication in this collection
  23 Oct 2017
• Date of issue
  2018

History

• Received
  19 Apr 2017
• Reviewed
  20 Aug 2017
• Accepted
  17 Sept 2017