1. Introduction
Cobalt-tungsten (Co-W) alloy is a promising material that can be used for among others coatings and corrosion resistance applications. The alloy is often manufactured as thin films produced by deposition [1-4] or magnetron sputtering spanning [5]. Due to rapid cooling involved during deposition and sputtering, formation of novel metastable and amorphous phases is attained. Electrodeposited Co-W is a potential candidate to replace Co-Cr due to better mechanical properties such as high surface sliding hardness, wear resistance and good ductility [6]. In addition, the processing of Co-W system is environmentally friendly compared to Co-Cr. Some studies reveal that a deposited film of Co-W consists of a bi-phasic structure, mainly metastable hexagonal close-packed (HCP) and amorphous phases [6,7]. In some cases, only the existence of amorphous structure is observed [1,3,8]. To the best of our knowledge, the study on the influence of ball milling (BM) on Co-W powder mixture is still lacking. BM is a versatile solid-state powder synthesizing technique used to produce alloying of powders with reduced crystalline size [9,10]. The objective of the current study is to investigate the crystal structure of unmilled and milled Co 50 at% W powder mixtures after annealing.
2. Experimental Procedure
Commercial W and Co powders of 99.5% purity were used during ball milling and cold pressing experiments. The measured particle sizes has percentage particle distribution D50 = 32.40 and 5.42 µm for Co and W, respectively. Milling was conducted in a high-energy ball mill at 650 rpm and 20:1 ball to powder ratio for time intervals of 10 and 20 hours (h). In order to minimize contamination, milling was performed under inert atmosphere with no process control agent (PCA) added. The changes in powder particle morphology were analysed using the LEO 1525 field-emission scanning electron microscope (FE-SEM) coupled with a Robinson Backscatter Electron Detector (RBSD). Phase evolution was traced with a Panalytical X’pert PRO PW 3040/60 x-ray diffractometer (XRD) equipped with a Cu Ka monochromated radiation source, scanning from 20˚ to 90˚ (2θ) in 0.02˚ step size. The crystalline sizes (D) of unpressed and cold-pressed powders were estimated by Williamson-Hall (W-H) equation as follows:
(1)
where θ is the Bragg diffraction angle, D is the average crystalline size, ɛ is the average internal strain, k is a constant with a value of 0.9, λ = 0.154056 nm is the wavelength for Cu Kα radiation and β is the diffraction peak width at half maximum intensity. The average internal strain (ɛ) is estimated from the slope of βcosθ versus 4sinθ linear plot, while the average crystalline (D) is estimated from the y-intercept. Annealing of powder compacts was carried out in a Carbolite tube furnace under flowing argon gas at 800˚C and1200˚C.
3. Results and Discussions
3.1. Unmilled Co-W Powders
Shown in Figures 1(a)-(d) is the SEM images of unmilled Co, W and milled Co-W powder mixture for 10 and 20 h, respectively. The Co particles appear coarse compared to those of W. The mixture of fine and large, flat-round particles is evident on both 10 and 20 h milled powders. This large particles could be due to agglomeration as a result of cold-welding during milling.
The XRD patterns of the Co-W compact after coldpressing, 800˚C and 1200˚C annealing are presented in Figures 2(a)-(c). It is evident from Figures 2(a) and (b) that the diffraction peaks belonging to body centered cubic (BCC) W are more intense compared to those representing HCP and FCC (face centered cubic) Co phases. In addition, these peaks indicate broadening.
XRD peak widening is well known to be caused by the refinement of particles and sometimes also associated with amorphous phases. However, the lattice parameter of the cold-pressed compact is 3.143 Å, smaller than that of pure W (3.165 Å). It is likely that thereduction of the lattice parameter is due to surface deformation during coldpressing. Moreover, it has been reported that cold pressing can promote structural change on Co [11,12]. Although low melting temperature elements such as tin (Sn) and tellurium (Te) mixture were alloyed by repeated coldpressing process [13], it is not logical to expect high melting temperature metals such as Co and W to be alloyed by cold-pressing, but their surfaces might be coldwelded. From the XRD analyses of Co-W compacts annealed at 800˚C and 1200˚C shown in Figures 2(b) and (c), respectively, it is apparent that the peak broadening observed after cold-pressing was reversed by annealing as shown by sharp peaks. This behaviour is could be attributed to the beginning of sintering effect. In addition to the retained BCC phase with lattice parameter of 3.143 Å after annealing at 800˚C, FCC Co with lattice parameter of 3.554 Å was detected, as presented in Table 1.
Figure 2. XRD patterns of (a) cold-pressed Co-W powder (b) sintered at 800˚C and (c) 1200˚C.
Table 1. Experimental XRD data of cold pressed, ball milled and annealed Co-W powders.
A similar FCC phase of about 3.506 Å was obtained in milled Co annealed at 800˚C in previous study [14]. Upon annealing Co-W compacts at 1200˚C, formation of tetragonal (TET) and FCC superstructure called eta (ƞ) phase with space group Fd-3m # 227 were detected, as indicated in Figure 2(c). Similar phases were obtained and reported as follows: 1) TET phase formed from ball milled W powder compacts annealed at 1200˚C [15], 2) eta phase obtained from milled and 800˚C annealed W [14], W milled and annealed at 730˚C [16], milled W-Ni powder mixture annealed at 730˚C and 1400˚C [16] as well as from mixture of separately milled elemental Co and W powders compacted and annealed at 800˚C [14]. The corresponding formation mechanisms were also provided. Although ƞ-phase has been detected in pure W [14,16], pre-milled Co-W mixture [14], Ni-W [17] and Ni-Mo materials [18], it does not exist under equilibrium conditionsin any of the above systems including the Co-W, Ni-W and Ni-Mo systems in the absence of carbon. Furthermore, it is well known that this phase is unstable and dissociates at high temperatures [14,19]. The obtained lattice parameter (11.090 Å) of ƞ-phase is larger than that found after reduction of cobalt-tungsten oxide (10.846 Å) [20]. The phases obtained in the current study are not found in Co-W equilibrium phase diagram shown in Figure 1 in [14]. They are therefore regarded as metastable or rather intermediate.
3.2. Ball milled Co-W Powders
The XRD patterns of 0, 10 and 20 h ball milled Co-W powders are shown in Figures 3(a)-(c). In comparison with the unmilled, the peaks of 10 h sample are slightly broader and their intensity significantly reduced. Almost similar to the compaction effect, the lattice parameter of BCC W was decreased from 3.165 to 3.147 Å with the estimated crystallite size of about 60 nm, while lattice parameters of HCP Co remained unchanged. Upon 20 h of BM, the peaks were further broadened and reduced in height. Surprisingly, the undeformed lattice of pure BCC W (3.165 Å) was recovered. This could imply that BM just reversed the deformation on the surface of W particles observed on the 10 h ball-milled powder. Similarly, crystallite size of ~60 nm was calculated. Since the crystal structure of Co did not change either, it thus follows that no alloying was induced by BM. For alloying to be achieved, high energy is required considering the melting temperatures of both Co and W. Physical properties such as thermal expansion coefficient, melting temperature, activation energy, elastic modulus and yield strength which are 13.4 × 10−6 C−1, 1495˚C, QB = 117 KJ/mol, 211 GPa and 345 MPa for Co, and 4.5 × 10−6 C−1, 3410˚C, QB = 385 KJ/mol, 411 GPa, and 550 MPa in the case of W, respectively [21], also play an important role in order for alloying to occur at approximately room temperature.
Figure 3. XRD patterns of (a) 0, (b) 10, and (c) 20 h ball milled Co-W powders.
Other than quicker grain refinement, the above properties imply that W is expected to have higher resistance to deformation during BM compared to Co.
Figure 4 presents the XRD patterns of 1200˚C compacts, though the results for unmilled powder was only shown for comparison since it has been discussed in Figure 2(c). The XRD patterns of annealed 10 and 20 h ball milled compacts show similar phases as shown in Figures 4(b) and (c), though the peak intensities remains slightly higher for the 10 h milled compacts. Furthermore, the detected phases were alike in crystal structure, HCP and RHL (rhombohedral), though their corresponding lattice parameters varied as indicated in Table 1. This variation from the reported lattice parameters of equilibrium phases such as RHL Co7W6 (a = 4.751, c = 25.670 Å) is attributed to deviation from stoichiometric composition