Open Journal of Applied Sciences
 Vol.3 No.1(2013), Article ID:29381,13 pages DOI:10.4236/ojapps.2013.31003

Fabrication and Characterization of Tungsten Heavy Alloys Using Chemical Reduction and Mechanical Alloying Methods

Zeinab Abdel Hamid1*, Sayed Farag Moustafa2, Walid Mohamed Daoush2,3, Fatema Abdel Mouez1, Mona Hassan1

1Corrosion Control and Surface Protection Department, Central Metallurgical R&D Institute, Helwan, Cairo, Egypt

2Powder Technology Department, Central Metallurgical R&D Institute, Helwan, Cairo, Egypt

3Department of Production Technology, Faculty of Industrial Education, Helwan University, Cairo, Egypt

Email: *forzeinab@yahoo.com

Received September 27, 2012; revised November 5, 2012; accepted November 14, 2012

Keywords: Tungsten Heavy Alloys; Mechanical Alloying; Chemical Reduction; Powder Metallurgy; Hardness; Transverse Rupture Strength; Conductivity

ABSTRACT

A novel reduction technique has been developed to synthesize nano-sized tungsten heavy alloys powders and compared with the same powders processed by mechanical alloying technique. In the first method, nano-sized tungsten heavy alloys powders have been obtained by reduction of precursors obtained by spray drying of several appropriate aqueous solutions, which were made from salts containing tungsten, cobalt, and nickel. By adjusting the stoichiometry of the component of the solutions, it is possible to obtain the desired chemical composition of the tungsten heavy alloys powders. In the second method, highly pure elemental powders of tungsten heavy alloys have been mechanically alloyed in a tumbler ball mill for different milling time. The investigated tungsten heavy alloy powders with the composition (95%W-3.5%Ni-1.5%Fe), (93%W-4.5%Ni-1.0%Fe-1.5%Co), and (90%W-6%Ni-4%Cu) have been prepared using both methods. The prepared powders have been compacted at 70 bar (200 MPa) and sintered in vacuum furnace at 1400˚C. Vacuum sintering was carried out to achieve full densification of the produced tungsten heavy alloys. The investigated materials were going to be evaluated the physical and mechanical properties of the sintered parts such as density; electrical conductivity, hardness, and transverse rupture strength. The results reveal that, the grain size of alloys fabricated by chemical reduction technique (53.1 - 63.8 nm) is smaller than that fabricated by mechanical alloying technique (56.4 - 71.4 nm).

1. Introduction

Tungsten heavy alloys (WHA’s) illustrate the advantages of microencapsulated powders. WHA’s are a kind of composite materials, consisting of two-phase microstructure of spherical tungsten particles embedded uniformly in a metallic matrix, such as W-Ni-Fe or W-NiCu or even W-Ni-Cu-Fe solid solution [1,2]. Some elements are added to WHA’s such as Co, Mo, Cr, etc. The addition of cobalt to a W-Ni-Fe alloy is a common approach for slight enhancement of both strength and ductility. The presence of cobalt within the alloy provides solid-solution strengthening of the binder and slightly enhanced tungsten-matrix interfacial strength. Nickel, iron and copper serve as a binder matrix, which holds the brittle tungsten grains together and makes the alloys ductile and easy to machine. These alloys provide a unique combination of properties, such as high density, excellent mechanical properties and good corrosion resistance, making them increasingly attractive in many practical applications, such as radiation shielding, mass balance for aerospace, vibrating masses for cell phones and kinetic energy penetrators [3-8]. Tungsten content in conventional heavy alloys varies from 90 to 98 weight percent and is the reason for their high density (between 16.5 and 18.75 g/cc).

There are several conventional methods for fabrication of tungsten heavy alloys, including mechanical alloying [9-11], electro-deposition technique [12,13], metal injection molding [10] and spray drying [14-16]. L. DongWon et al. [16] studied a novel reduction method to fabricate ultrafine tungsten heavy alloy powders, using cost effective source materials. The advantages of mechanical alloying method have the simple equipment and process and easy operation that make it suitable for mass production.

Using fine powder raw materials and/or novel techniques to prepare fine-or ultrafine-grained WHA’s are the current trends. Fine-or ultrafine grained WHA’s are usually prepared via sintering ultrafine/nano tungsten composite powders and controlling the growth of the tungsten grains [10,15-21]. By refining the microstructure of the tungsten heavy alloys, the mechanical properties can be improved.

The conventional processing route includes mixing the desired amount of elemental powders, followed by cold pressing and sintering. There are two essential phases during the sintering process: solid state phase, and liquid state phase. At melting, the liquid phase of the matrix, wet and infiltrate the solid grain structure by a combination of reaction and capillary forces, followed by a dissolving and growth of the solid particles by coalescence and Ostwald-ripening. The driving force for liquid phase sintering is not only the reduction of surface energy by capillary forces but also the reduction of chemical potential by dissolving of original and growth of equilibrium solid phase [22].

Liquid phase sintering is generally easier and more cost-effective than solid state. However, a certain degradation of the raw material will occur that is not the case with the solid state process. The sintering process occurs by mass transport at high temperature and sometimes a high pressure is also required as a driving force. The driving force for solid-state sintering is the reduction of surface free energy of the particles, which is achieved either by atomic diffusion transporting matter from inside the grains to fill the pores (densification) or rearrangement of the matter between different parts of the pore surfaces (without reducing pore volume) coarsens the microstructure.

In this study, a novel process was developed to synthesize nano-sized tungsten heavy alloys (WHA’s) composite powders by chemical reduction method. For comparison, the same compositions of the investigated powders were also processed by mechanical alloying method. The prepared powders from both methods were cold compacted and sintered under vacuum. The fabricated composites have been evaluated in terms of density, microstructure, hardness, transverse rupture strength, thermal and electrical conductivities.

2. Materials and Methods

Heavy tungsten alloy powders with composition of 95W- 3.5Ni-1.5Fe, 93W-4.5Ni-1.0Fe-1.5Co, and 90W-6Ni-4Cu in wt% were prepared by chemical reduction and mechanical alloying (MA) techniques. Tungsten, iron, cobalt and nickel have been characterized in terms of flow rate, average grain sizes and apparent density. Table 1 summarizes these characterizations. A scanning electron microscope (SEM) equipped model JEOL, JSM-5410 was used to study surface morphologies of the powders. A JEOL (JEM 2010) transmission electron microscope was used to analyze the powder size. The phase structure was analyzed by X-ray diffractometer (XRD) model PAN analytical X’pert PRO with Cu Kα1 target with wavelength 1.5046 A and operated at 45 kV and 40 mA. The step size, rate and range were 0.02˚, 0.05˚ s−1 and 10˚ - 100˚, respectively.

2.1. Tungsten Heavy Alloys Fabrication

2.1.1. Chemical Reduction Method

In the chemical reduction method, a novel process was developed to synthesize tungsten heavy alloys nanocomposite powders by controlled reduction of precursors obtained by spray drying of several appropriate aqueous solutions, which was made from salts containing tungsten, cobalt, nickel, and iron. Tungsten powder was obtained from solution of ammonium metatungstate

, whereas Co-powders was made from cobalt nitrate solution, and the Ni powder was made from nickel acetate

solution, Fe and Cu were formed from their oxides Fe2O3 and CuO respectively. Hydrogen gas was used as the reductant gas. By adjusting the stoichiometry of the component of the solutions and iron or copper oxide, it is possible to obtain the desired chemical composition of the tungsten heavy alloys powders.

Table 1. Characteristics of starting powders.

2.1.2. Mechanical Alloying Method

In the mechanical alloying method, highly pure elemental powders of tungsten of 1 - 3 µm particle sizes, nickel of 2.5 µm, cobalt of 2 µm, iron of 0.3 - 0.5 µm and copper of 0.2 - 0.4 µm in average diameter particles of the investigated chemical compositions of WHA’s have been mechanically alloyed by rod milling for different milling time. The elemental powders of W, Ni, Fe and Co weighed to the target compositions and milled in a milling machine. The diameter of the mill was 255 mm, and Cr-steel balls of 8 mm in diameter were used as the milling media. The milling speed was 120 rpm, milling time varied up to 72 h, rod-to-powder ratio was 20:1 by weight, and the ball filling ratio was 15% by volume.

The prepared powders from both methods were blended with 0.5 wt% paraffin wax and cold compacted using Hydraulic press at compaction pressure of 70 bar. The green compacts were sintered using solid-state sintering at a temperature 1400˚C for 1 h under vacuum as illustrates in the schematic diagram of the sintering cycle in Figure 1.

2.2. Characterization of Alloys

The evaluation testing of the powder and consolidated materials includes: density, hardness, transverse rupture strength as well as electrical and thermal conductivities. Moreover, extensive metallographic studies were performed using both optical and SEM microscopy for the sintered materials in order to measure the contiguity and structure homogeneity.

2.2.1. Densities Measurements

The densities of the sintered powders were measured according to MPIF Standards 42, 1998, using Archimedes rule. The density of the samples was calculated according to the following formula [22]:

(1)

Figure 1. The heating cycle for the vacuum sintering process at 1400˚C for the investigated tungsten heavy alloys.

where Wa and Ww are the weights in air and water respectively.

The compact sinterability was also expressed in the terms of densification parameter which is calculated as follows:

(2)

where δs is the sintered density, δg is the green density and δth is the theoretical density.

2.2.2. The Electrical Resistivity Measurements

The electrical resistivity of the sintered materials was measured using the four-probe method by using Omega CL 8400 micrometer device. The resistivity was calculated according to the following equation by using High Precision Micro-ohmmeter.

(3)

where, R is the resistance in micro ohm, L is the measured length in cm, A is the cross section area in cm2, and ρ is the resistivity in µW cm.

2.2.3. The Microhardness Measurements

The Vickers microhardness of the alloys was determined by an indentation technique at 500 gf load with a diamond pyramid indenter technique, Tukon Series B200 microhardness tester.

2.2.4. Transverse Rupture Strength (TRS) Measurements

The rupture test was performed using compression testing machine and a test fixture, according to MPIF Standard 41. All the samples of the powders were compacted into rectangular compacts of dimension of (30 × 10 × 6) mm3. In the transverse rupture fixture, the test bar was placed centrally located and perpendicular to the supporting rods with the top up. The fixture with the test bar was placed between the plates of the compression testing machine and the load was applied at constant rate of 2.5 mm/min, until the test bar fractured. The transverse rupture strength for sintered samples was calculated according to the following expression [22]:

(4)

where: TRS is Transverse rupture strength in

P is the fracturing (rupture) load (N).

L is the distance between the supporting rods (25.4 mm).

t is the thickness of the sample in (mm).

W is the width of the sample in (mm).

2.2.5. Thermal Conductivity

The thermal conductivity was calculated from electrical resistivity measurement using Wiedemann and Franz equation which derived a relation equation between the thermal and electrical conductivities [23]. The Wiedemann-Franz equation is as follows:

(5)

where, l is thermal conductivity, s is electrical conductivity, T is absolute temperature in degree Kelvin, KB is Boltzmann constant, and L is Lorentz number.

3. Results and Discussion

3.1. Fabrication of Tungsten Heavy Alloys Using Chemical Reduction Method

Firstly, Salts of cobalt nitrate, ammonium metatungstate, and nickel acetate were used to prepare cobalt, tungsten and nickel powders by chemical method. The salt solution of each one was spray dries using the centrifugal atomization which was adjusted at rotating velocity of 11,000 rpm, and feeding rate of 30 CC/min. The spray dried powder of each composition was collected and heated up in air at 800˚C to form oxide powders. XRD spectra of each salt after heated are shown in Figure 2. XRD patterns illustrate the peaks of W oxide at different 2θ angles 24˚, 33˚, 42˚, 48˚, 55.5˚, 61˚ (Figure 2(a)), cobalt oxide at 18.98˚, 31.28˚, 36.86˚, 38.54˚, 44.82˚, 59.35˚ and 65.25˚ (Figure 2(b)) and nickel oxide at 26.6˚, 37.25˚, and 43.29˚, 62.88˚ and 75.40˚ (Figure 2(c)). The oxide powders were reduced in hydrogen atmosphere for 30 min at 750˚C to obtain pure metal powder.

Similarly, synthesis of tungsten-base nanocomposite alloy powders have been prepared by chemical reduction of precursors obtained by spray drying of several appropriate aqueous solutions, which were made from salts containing tungsten, cobalt and nickel, whereas iron and copper were added as oxides. Three tungsten-base alloy powders were obtained, namely, (95%W-3.5%Ni- 1.5%Fe), (93%W-4.5%Ni-1%Fe-1.5%Co), and (90%W- 6%Ni-4%Cu) alloys. Dried solution salts were further heated up in open air at 800˚C for 2 hrs in order to obtain corresponding alloy oxides. Figure 3 illustrates the XRD of the three investigated oxide alloys. The apparent crystallite size of the oxides of WHA’s prepared by chemical reduction technique reaches to the nanoscaled dimension as shown in TEM images (Figure 4).

The resulted oxide alloy powders were reduced in tube furnace using hydrogen gas as reductant. According to the analysis of the X-ray diffraction pattern (Figure 5) it can be concluded that the complete reduction was achieved at that condition. The apparent crystallite size of the WHA’s powders prepared by chemical reduction technique after reduction using TEM is shown in Figure 6. The images reveal that the crystal size reaches to the nano-scaled dimension.

The reduction of WO3 by H2 gas is a complex process, while Lassner and Schubert proved that, the reduction of WO3 can be divided into two steps: firstly, oxygen transport by solid state diffusion, secondly, tungsten transport by chemical vapor transport as shown in the following chemical reactions [24]:

(6)

(7)

(8)

(9)

Figure 2. XRD of the oxide powders; where (a) tungsten oxide, (b) cobalt oxide, and (c) nickel oxide.

(a)(b)(c)

Figure 3. XRD of the three investigated oxide alloys.

Additionally, during the synthesis process, it can be assumed that nickel, cobalt and iron components are reduced before the tungsten due to the low reduction temperatures of their oxides.

3.2. Fabrication of Tungsten Heavy Alloys Using Mechanical Alloying Method

Figure 7 shows scanning electron microscopy images of the tungsten, nickel, iron and cobalt powder used in this study. The grain sizes of elemental powders were ranged from 2 up to 10 μm. In this investigation, three alloys composite powders were prepared from these highly pure elemental powders, namely; (95%W-3.5%Ni-1.5%Fe),

(a)(b)

Figure 4. TEM images of different WHA’s oxides compositions prepared by chemical reduction method, where: (a) (93%W-4.5%Ni-1%Fe-1.5%Co) oxide and (b) (90%W, 6%Ni, and 4%Cu) oxide.

(93%W-4.5%Ni-1%Fe-1.5%Co), and (90%W, 6%Ni, and 4%Cu).

The sequences of structural sizes, phase transformation and the behavior of mechanically alloyed powders have been assessed using XRD and TEM microscopy. The XRD analysis of different MA’s milled for 72 hrs are shown in Figure 8. Due to the percents of other elements in the powders are too small to be detected; only diffraction peaks of W phase are observed in the XRD patterns. The intensity of diffraction peaks becomes gradually low with the increase of milling time, indicating a continuous decrease in the W grain size. After milling for about 72 hrs, the average particle size approaches the minimum, owing to the role of colliding and rolling of milling balls. The crystallite size of the three different MA’s powder which calculated by the Scherer formula (d = 0.9λ/βcosθ) as a function of milling time is shown as Table 2. The results reveal that the grain size decreases with increasing milling time in all three groups. The apparent crystallite size of these MA’s reaches to the nano-scaled dimension. This agrees closely with measuring by TEM observation. It is clearly seen that morphology appears threadlike and flocculencelike. TEM morphologies show that

(a)(b)(c)

Figure 5. XRD of the three investigated WHA’s powder after reduction where: (a) (95W-3.5Ni-1.5Fe), (b) (93%W- 4.5%Ni-1%Fe-1.5%Co), and (c) (90%W, 6%Ni, 4%Cu).

there is a significant reduction in grain sizes elemental powders of each alloy, as can be seen in Figure 9. It can be noted that all ingredients are in the nanosize grains. The average grain size of the MA’s after 72 hrs milling is in the range of 63 - 72 nm.

3.3. Compaction and Solid-State Sintering

The prepared powders made by either chemical reduction or mechanical methods were cold compacted at 70 MPa in cylindrical shape of 10 mm diameter and 10 mm length and rectangular of 30 × 12 × 6 mm. The Cylin-

Figure 6. TEM image of the three investigated WHA’s powder after reduction where: (a) (95W-3.5Ni-1.5Fe), (b) (93%W-4.5%Ni-1%Fe-1.5%Co), and (c) (90%W, 6%Ni, and 4%Cu).

drical shape samples were used for measuring density, hardness and microstructure investigation, whereas the rectangular ones were used for measuring transverse rupture strength, electrical resistivity, and thermal conductivity.

Figure 7. SEM micrographs of the as received powders: (a) tungsten, (b) nickel, (c) iron and (d) cobalt powders.

Figure 8. XRD of different MA’s before and after milling for 72 h, where: (a) MA (W-3.5Ni-1.5Fe) before milling, (b) MA (95W-3.5Ni-1.5Fe) after milling, (c) MA (93%W-4.5%Ni-1%Fe-1.5%Co) before milling, (d) MA (93%W-4.5%Ni-1%Fe- 1.5%Co) after milling, (e) MA (90%W, 6%Ni, and 4%Cu) before milling, and f) MA (90%W, 6%Ni, and 4%Cu) after milling.

Figure 9. TEM images of different MA’s before and after milling for 72 h, where: (a) MA (95W-3.5Ni-1.5Fe) before milling, (b) MA (95W-3.5Ni-1.5Fe) after milling, (c) MA (93%W-4.5%Ni-1%Fe-1.5%Co) before milling, (d) MA (93%W-4.5%Ni- 1%Fe-1.5%Co) after milling, (e) MA (90%W, 6%Ni, and 4%Cu) before milling, and f) MA (90%W, 6%Ni, and 4%Cu) after milling.

Table 2. Effect of milling time on the grain size of the WHA’s powder fabricated by mechanical method.

The compacts were solid state sintered in vacuum furnace at temperature 1400˚C. Many studies proved that sintering temperature is related to the powder size, when the size is in nano-scale, the sintering temperature can be decreased up to several hundreds of degrees [25-27]. So solid state sintered in vacuum furnace at temperature 1400˚C used in the present study.

3.4. Characterization of WHA’s

3.4.1. The Density of WHA’s

Table 3 compares the effect of fabrication method on the sintered density and densification parameter of the three investigated tungsten powder groups. It is worth noticing that irrespective of the fabrication method the compacts undergo significant densification during sintering. This can be attributed to the ultra-fine particle size of the powder used in this investigation. The data reveals that, the sintered density and densification parameter of the WHA powder compacts made by either chemical or mechanical method is high. The density ranged from 16.5 to 17.27 gm/cm–3, and the maximum density was reached at 17.0 and 17.28 gm/cm–3 for (95%W-3.5%Ni-1.5%Fe) WHA’s fabricated by chemical reduction and mechanical method respectively, and the densification ranged from 94.2% to 99.1%.

3.4.2. The Microstructure of WHA’s

The experimental results reveal that the best sintering temperature for WHA’s fabricated by either chemical or mechanical method was 1400˚C for 1 h. Figure 10 shows the microstructures of the sintered WHA’s using optical microscopy. In WHA’s, the tungsten particle generally present as polyhedral shape with regular microstructure of grain boundaries, that the diffusion in these polyhedral particles exhibit higher activation energy than the non-polyhedral particles as described by Hwany et al. [28]. Additionally, Figure 10 shows the porous-free metallograph for each (95%W-3.5%Ni-1.5%Fe), (93%W- 4.5%Ni-1.0%Fe-1.5%Co) and (90%W-6%Ni-4%Cu) alloy as-sintered at 1400˚C fabricated by mechanical or chemical reduction methods. These images illustrate two different phases area, the randomly distributed dark area phase surrounding the matrix phase (W) (white area).

The X-ray diffractions of the three groups of WHA’s sintered at 1400˚C for 1 hr and fabricated by two techniques are shown in Figure 11. The patterns of the X-ray

Table 3. Comparison between density for both chemical and mechanical alloys sintered at 1400˚C.

Figure 10. Optical microstructures of WHA’s prepared by chemical and mechanical process, (a) mechanical alloy (95%W-3.5%Ni-1.5%Fe), (b) mechanical alloy (93%W-4.5%Ni-1%Fe-1.5%Co), (c) mechanical alloy (90%W-6%Ni-4%Cu), (d) chemical alloy (95%W-3.5%Ni-1.5%Fe), (e) chemical alloy (93%W-4.5%Ni-1%Fe-1.5%Co), (f) chemical alloy (90%W- 6%Ni-4%Cu).

Figure 11. XRD of the three investigated alloys by chemical and mechanical technique after sintering at 1400˚C where: (a) (95W-3.5Ni-1.5Fe), (b) (93%W-4.5%Ni-1%Fe-1.5%Co), and (c) (90%W, 6%Ni, and 4%Cu).

for the alloys which fabricated by mechanical method illustrated the main peaks for bcc-structured tungsten phase (which is in very good agreement with the data of JCPDS file No. 04-0806). While the patterns of the X-ray diffraction for the alloys fabricated by chemical method revealed the main peaks for tungsten and two relatively weak peaks which corresponding to Ni-Fe solid solution phase for (95%W-3.5%Ni-1.5%Fe) and (93%W-4.5%Ni- 1%Fe-1.5%Co) alloys.

The grain size of the three different WHA’s and fabricated by two techniques is shown in Table 4. The data illustrated that the grain size of these alloys reach to the nano-scaled dimension. Additionally, the results reveal that the grain size of the alloy fabricated by chemical technique is less slightly than that fabricated by mechanical technique. This indicates that the chemical

Table 4. The grain size of sintered WHA’s fabricated by mechanical and chemical techniques.

method produce alloys with fine grain size.

3.4.3. Hardness Measurement

The microhardness for the three investigated alloys fabricated by chemical and mechanical methods is shown in Table 5. The data reveals that the micro hardness of the all alloys fabricated by chemical or mechanical methods ranged from 430 to 475 Hv. The increase of hardness for the samples sintered is suggested contributing by the formation of fine nano tungsten solid solution phase.

3.4.4. Electrical Resistivity and Thermal Conductivity Measurement

Table 6 illustrates the electrical resistivity and thermal conductivity values of the all fabricated alloys. It is clear that the electrical resistivity (µΩ·cm) for all WHA’s fabricated by chemical methods is lower than that fabricated by mechanical method. This can be rationalized by the fine grains of the alloy fabricated by chemical method which led to increase the mobility of the free electron causing low resistivity. Additionally, the data reveals that the thermal conductivity of the WHAs fabricated by chemical method is higher than that fabricated by mechanical method.

3.4.5. Transverse Rupture Strength (TRS)

The variations of transverse rupture strength of the different sintered alloys fabricated by chemical or mechanical methods are shown in Table 7. According to the data obtained, the TRS of the alloyed fabricated by mechaniccal method is higher than that fabricated by chemical method. The maximum TRS of 977 ± 40 N/mm2 was obtained for the 90%W-6%Ni-4%Cu alloy sintered at 1400˚C fabricated by mechanical method and 700 N/mm2 was obtained for the same alloy fabricated by chemical method.

4. Conclusions

The solid phase sintered of (95W-3.5%Ni-1.5%Fe), (93W-4.5%Ni-1.0%Fe-1.5%Co), and (90W-6%NiTable 5. Comparison between microhardness for both chemical and mechanical WHA’s sintered at 1400˚C.

Table 6. Comparison between electrical resistivity and thermal conductivity for both chemical and mechanical WHA’s sintered at 1400˚C.

Table 7. Comparison between TRS for both chemical and mechanical WHA’s sintered at 1400˚C.

4%Cu) WHA’s has been prepared using chemical and mechanical techniques. The WHA’s fabricated by chemical reduction or mechanical techniques were characterized by X-ray diffraction, SEM, and TEM techniques. The results of this study can be summarized as follow:

1) Milling prior to fabricating WHA’s by mechanical technique is helpful to preparing fine grain and good property. The sequences of structural sizes and/or phase transformation and the behavior of mechanically alloyed powders have been assessed using XRD and TEM microscopy. The results reveal that the grain size decreases with increasing milling time in all three groups. The apparent crystallite size of these mechanical alloys reaches to the nano-scaled dimension. This agrees closely with measuring by TEM observation. Additionally, X-ray patterns of WHA’s powders after mechanical milling 72 hrs proved that the crystal size ranged from 63.5 to 71.5 nm.

2) X-ray diffraction of the sintered alloys revealed that the bcc (body centered cubic) solid solution tungsten phase formed with WHA’s fabricated by mechanical and chemical reduction techniques after sintering at 1400˚C while, the fcc (face centered cubic) Fe-Ni solid solution phase formed only with the chemical reduction technique, indicating that composite powders are well synthesized by chemical reduction process.

3) TEM observation revealed the formation of nano tungsten solid solution phase.

4) The grain size of the matrix phase after sintering is arranged from 53.1 to 63.8 nm for the alloys fabricated by chemical reduction technique and from 56.4 to 71.4 nm for the alloys fabricated by mechanical technique.

5) The microhardness of WHA’s sintered at 1400˚C for 1 h fabricated by either chemical reduction or mechanical technique is ranged from 430 to 475 Hv. The increasing of hardness for the WHA’s is due to the formation of nano tungsten solid solution phase.

The TRS of the alloyed fabricated by chemical method is higher than that fabricated by mechanical method.

5. Acknowledgements

The authors gratefully acknowledged the financial support from Science & Technology Development Fund (STDF) (Grant No. ID 55). Additionally, I would like to thank Prof. Sayed Farag Moustafa, Prof. of Powder Technology, and asking Allah to rest his soul in Heaven, where he was suggesting the line of project investigated. He was as a godfather for us in the work.

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NOTES

*Corresponding author.

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