The role of the binder phase in the WC-Co sintering

The Role of the Binder Phase in the WC-Co Sintering

A.G.P. da Silva^a*, W.D. Schubert^b, B. Lux^b

^aDepartamento de Física, Universidade Federal do Rio Grande do Norte,

59072-970 Natal - RN, Brasil

^bInstitut für chemische Technologie anorganischer Stoffe, Technische Universität Wien, Getreidemarkt, 9/161, A-1060, Vienna, Austria

*e-mail: [e-mail]

Received: November 16, 2000; Revised: April 27, 2001

The sintering of hardmetal in the solid state is studied. The influence of the WC particle size on the sintering kinetics, the role of the binder phase in the densification process and how sintering depends on the heating conditions are investigated. It is observed that alloys with different WC particle size show quite different structural evolution during sintering, although the densification mechanisms are the same. This is explained by the formation of agglomerates of WC and Co. Hardmetal alloys can sinter very rapidly when high heating rates are used, since rapid heating accelerates the binder spreading and the formation of WC-Co agglomerates. The binder phase (Co) spreads on the WC particles initially as a thin layer. Subsequently, more Co spreads on this layer and WC-Co agglomerates are formed.

Keywords: sintering, hardmetal, cobalt

1. Introduction

Hardmetal alloys are a typical example of a composite material. Their most simple constitution is a hard phase, tungsten carbide, together with a metal which plays the role of binder. Cobalt is the most frequently used metal, but nickel can also be used. This material exhibits high hardness, maintaining an elevated strength level. Furthermore, hardness and strength can be easily adjusted by varying the alloy’s composition. For instance, the higher the WC content the harder is the alloy. The final alloy’s properties are a combination of the properties of the individual constituents. In some cases, small amounts of other refractory carbides are added to inhibit the WC grain coarsening during sintering, but they do not directly affect the alloy’s properties.

Tungsten carbide is not the hardest carbide nor is Co the toughest metal, but WC-Co is the best system for hardmetals. The reason for this is the outstanding coupling between WC and Co, represented by: (1) the low dihedral angle of the system WC-Co, which is reported to be zero¹; (2) Co dissolves a significant amount of WC, but WC does not dissolve Co²; (3) this system has an ternary eutectic reaction at 1275 °C. Characteristics (1) and (2) contribute to the good sinterability of the WC-Co, compared to other systems. They also help to increase the adherence between the WC and Co phases, improving the mechanical properties. The third characteristic allows this system to be sintered at temperatures significantly lower than the melting point of Co and the sintering temperature of other similar systems.

Hardmetal alloys are sintered in a “liquid phase environment” but significant shrinkage takes place in the solid state. As early as 1944, Dawihl and Schroeter³ reported that full density could be reached by sintering a piece at 1250 °C for 80 h. Later on, Exner⁴ and Bock⁵ reported that around 90% of the alloy’s relative density could be obtained during the heating stage. Milner and co-workers^6-9 have proposed a model for the solid phase sintering of WC-Co hardmetal, which was extended by da Silva¹⁰. According to Milner et al., solid state sintering proceeds in three stages: (1) Co spreads over the WC particles and covers the surface of the particles; (2) the spreading Co agglomerates neighboring WC particles, acting like a cement and; (3) the resulting agglomerates form a network and sinter together as large particles.

In the sintering of hardmetal, the binder phase plays the most significant role. It is responsible for densification through wetting, spreading and formation of agglomerates. The hard phase has a passive role, since the WC particles do not sinter together but are moved by the binder.

This work focus on the role of the binder phase in hardmetal sintering. It investigates how the binder contributes to sintering and how this contribution depends on several parameters of the material, such as the mean WC particle size and the heating conditions.

2. Materials and Methods

The characteristics of the starting powders used in the work are shown in Table 1. The WC powders were supplied by the Company Wolfram Bergbau und Hütten Gesellschaft (Austria). The Co powder was supplied by H.C. Starck (Germany).

Two alloy grades were prepared with these powders through the powder metallurgical route for hardmetal production, that is, ball milling, granulation, presintering-dewaxing and sintering. Table 2 gives details of the alloys. Alloy G2 was milled for short time to avoid the size reduction of the WC particles.

All samples were sintered in a furnace coupled to a dilatometer under a vacuum of about 10^-3 mbar. Some samples were sintered by using a temperature program consisting of two heating stages of 10 °C/min from room temperature up to 800 °C and 3 °C/min up to 1400 °C/min., with a soaking time of 1 h at 1400 °C. After sintering, the samples are cut, embedded, ground, polished and etched for observation of their structures. This kind of sintering shows the shrinkage behavior and the shrinkage rate through dilatometry. All samples sintered in this way showed only two phases (WC and Co), indicating the right carbon balance of the alloys.

Other samples were sintered at intermediate temperatures, between 700 °C and 1400 °C (without isotherm), to follow the structure development step by step during sintering. The samples are then fractured and observed by SEM.

Special experiments were planned to determine how the binder phase spreads over the carbide surface. Co particles were poured on a mirror polished flat surface of a pure hot pressed WC plate and quickly heated up to 1250 °C by pushing the sample in a boat up to the hot zone of a furnace pre-set at that temperature. The experiment was carried out under a H₂ flow. A thermocouple installed in the boat measured the actual temperature that was never above 1250 °C. In less than one minute the final temperature is reached. The samples were kept for 3 minutes in the hot zone and then quenched by withdrawing to the cooling zone. The particles and plate are then observed under a scanning electron microscope. Powder compacts were also sintered under these heating conditions.

3. Results

Figures 1 and 2 show SEM images of fracture surfaces of alloys G1 and G2, sintered at intermediate temperatures (interrupted sintering).

In order to compare the shrinkage behaviour of the two alloys, the percent shrinkage was employed, since the absolute shrinkage depends on the sample dimensions. The percent shrinkage varies from zero, at the beginning of the sintering cycle, to 100% at the end of the cycle. Figures 3 and 4 show dilatometric curves of alloys G1 and G2 for percent shrinkage and percent shrinkage rate respectively.

Figure 5 shows the result of the Co spreading on the flat WC surface after fast heating up to 1250 °C. Around the actual particles, it is possible to see a spot, like a shadow. It is a cobalt layer spreading over the WC surface.

4. Discussion

The binder plays an active role in hardmetal sintering. It is in fact responsible for the densification since it is more sensitive to temperature than the carbide in both solid and liquid phase sintering. For instance, it can diffuse faster. The initial structure of the sample (the green body structure) consists of a porous body in which particles of WC and Co are mixed and in contact with each other. The final sintered structure is dense, consisting of faceted WC grains embedded in a Co matrix. The matrix phase surrounds most of the WC grains, separating them from each other. During sintering, the pores are closed, the WC particles change their shape and the binder phase spreads throughout the structure. According to Milner et al.^6-9, Co initially wets and spreads over the surface of the WC particles. Next, it forms agglomerates when it pulls the WC particles close to each other. This stage of sintering is accompanied by shrinkage.

Figures 1 and 2 show these two stages of sintering. Figure 1 is an early stage of solid state sintering of alloy G2 (coarse WC). It shows Co wetting and spreading over the large WC particles at 1120 °C. For alloy G1 (fine WC), shown in Fig. 2, at 1200 °C, the agglomerates can be clearly seen. At this stage, the microstructure of alloy G1 consists of a network of WC-Co agglomerates.

The microstructures of alloys G1 and G2 look quite different, although the sintering mechanism for both alloys is the same. This difference can also be seen in the dilatometric curves for shrinkage and shrinkage rate (Figs. 3 and 4). Alloy G1 sinters much faster than alloy G2. Alloy G1 begins to shrink at around 800 °C. At 1300 °C, this alloy reaches almost 80% of the whole densification whilst alloy G2 reaches a bit less than 20% at the same temperature. At 1300 °C, sintering can still be considered to proceed in solid state. Alloy G2 sinters rapidly only above 1320 °C, when a liquid phase is formed in large amount.

Experiments specially designed for studying the Co spreading on WC under conditions of fast heating show how Co actually spreads and how fast Co can respond to the temperature increase. Figure 5 is a SEM image of some Co particles on a WC flat surface after fast heating up to 1250 °C. Three regions are clearly seen: the Co particles in the center, a darker region surrounding the particles and a bright region, which is the WC surface. The dark spot surrounding the Co particles is a thin Co layer as shown by EDS measurements. This result shows how Co spreads on WC. Initially, a thin Co film spreads on the WC surface and covers it. Then the Co particles spread on this film. The spreading velocity of the film increases as the heating rate increases. A powder compact sintered under the same fast heating conditions exhibited a microstructure comparable to that of a sample sintered at 1250 °C, under the slow heating condition. This shows that this spreading mechanism is also able to promote rapid densification. The Co spreading begins as early as 800 °C because at this temperature alloy G1 begins to shrink.

Although the sintering mechanism is the same for both alloys, the sintered microstructures of the alloys develop differently. Parameters such as the WC mean particle size influence the sintering kinetics, as shown by the dilatometric curves. The WC particle size influences the mixture dispersion, the pore size and the coordination number of each Co particle. The number of WC particles surrounding each Co particle decreases and the pore size increases as the mean WC particle size increases. In a green structure, consisting of small Co particles and large WC particles, the Co particles would preferentially occupy the pores between the WC particles, forming Co agglomerates. As a consequence of this, the number of contacts between WC and Co particles decreases as the WC mean size increases. Under such conditions, Co has to travel long distances to wet and cover different WC particles, forming a WC-Co agglomerate. Furthermore, the formation of WC-Co agglomerates depends on the movement (including rotation and sliding) of the WC particles closer to each other due to the action of capillary forces, caused by the Co links between the WC particles. Large WC particles are more difficult to move than small ones. If the WC particles are small, Co can wet and cover several WC particles, moving along relatively short distances and the capillary forces can move the small particles more easily. Thus the WC-Co agglomerates with fine WC particles are more easily formed than in the case of coarse WC particles.

In every site where a Co particle lies, a WC-Co agglomerate is formed. The movement of WC particles to the center of the agglomerate forms a large peripheral porosity around each agglomerate. As the agglomerates grow in size, Co necks link them together and a network is formed. The larger the agglomerates the larger is the peripheral porosity. The size of the agglomerates is co-determined by the WC particle size. The closure of the peripheral porosity depends on the deformation of the agglomerates and on the enlargement of the contact area between them. The larger the peripheral porosity the slower this stage proceeds. Figure 6 shows schematically how solid state sintering proceeds.

In general, the structure is porous when the liquid phase is formed, at the eutectic temperature, and the porosity volume and mean size depend on the WC mean particle size. The liquid phase is then responsible for closing the remaining porosity. Liquid can penetrate more easily into the pores. The overall viscosity of the system (viscosity of the mixture WC and binder) decreases and the agglomerates can deform more easily under the action of the capillary forces. However, if the pores are very large, even the liquid phase cannot completely close the pores and the structure will consist of large, round and isolated pores after sintering.

5. Conclusions

The experiments reveal details about hardmetal solid state sintering, such as the mechanism of sintering, how it depends on the WC particle size and how the binder phase spreads on the WC surfaces.

The model proposed by Milner and co-workers is quite suitable to describe hardmetal solid state sintering, but depending on certain parameters the evolution of the structure can differ significantly. The WC particle size changes the kinetics of the agglomerate formation and determine the size of the peripheral porosity. The larger the WC particles the more difficult is the agglomeration and the larger is the porosity around the agglomerates.

The agglomerates are formed basically due to the binder mobility. The binder initially spreads on the WC particles as a thin layer. The bulk of the binder then spreads on this layer and forms the WC-Co agglomerates. The binder can spread very rapidly and the spreading velocity depends on the heating rate. The structure can densify even if very high heating rates are used.

Most of the densification can occur before liquid formation, depending on certain parameters such as the WC particle size, but frequently pores remain in the structure, which are closed when the liquid phase is formed. For hardmetal alloys prepared with very large WC particles, most of the densification occurs only after liquid formation and it is likely that some large pores remain in the structure.

Acknowledgements

We thank to CNPq and OeAD for the partial financial support and to the Company Wolfram Bergbau & Hütten GmbH for supplying the WC powders.

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Publication Dates

• Publication in this collection
  11 July 2001
• Date of issue
  2001

History

• Reviewed
  27 Apr 2001
• Received
  16 Nov 2000