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The Use of Protective Weld Overlays in Oil Sands Mining
Gary Fisher1, Tonya Wolfe
1, Matthew Yarmuch
1, Adrian Gerlich
2 & Patricio Mendez
2
1 Alberta Innovates – Technology Futures, Edmonton, AB
2 University of Alberta, Edmonton, AB
Alberta’s oil sands are the second largest reserve of oil in the world, after Saudi Arabia
[1], with an estimated 170 billion barrels recoverable using current technologies [2]. The
oil sands are processed primarily by surface mining; a schematic of the open pit process
is shown in Figure 1. Oil sand deposits are removed via truck-and-shovel operations and
transported to a crusher/conveyor system where the sands are sized. The processed sands
are mixed with water and other additives to form slurry, which is piped to the extraction
plant for subsequent processing to extract the bitumen. Approximately two tonnes of oil
sands ore has to be processed to produce one barrel of synthetic crude. The sands in the
ore are mainly composed of quartz sand, silt, clay, water and bitumen [3]. Quartz
particles typically comprise of between 80 to 95% of the total solids, and are generally
less than 150 µm in size with a semi-angular shape. This scale of processing has
produced unique challenges as the hard particles within the oil sands are responsible for
severe wear of equipment and components.
In the Fort McMurray, Alberta region, the four commercial oil sands mining and
processing operations encounter high maintenance costs and significant production losses
due to material degradation through wear and corrosion. These costs include both the
replacement of the equipment and the associated labour and lost production. In 2011, the
annual operating budget for Syncrude Canada Ltd. was estimated at $1.3 billion [4].
Operating costs across the four commercial mine sites can be estimated at approximately
$5 billion. A major portion of this budget is due to wear damage to machinery and
equipment [5].
The main wear mechanisms encountered when extracting the oil sands are abrasion,
impact and erosive wear. Low stress abrasion is prominent where sands are sliding over
a surface with a relatively low contact force (e.g. a hopper wall) [6]. High stress
abrasion (and gouging) tends to result in higher levels of material loss as abrasives are
driven under high load into the contacting surfaces of equipment (e.g. bucket teeth) [7].
Rocks and boulders present in deposits cause impact-related damage to equipment; the
degree of which is somewhat governed by climatic conditions. During winter months the
sand and bitumen can consolidate into larger lumps, increasing the level of impact
damage [8]. The addition of water in the hydrotransport operations has introduced wear-
corrosion issues. The main corrosive species present are chloride-containing compounds
in the sands and dissolved oxygen in the water [9]. Increased wear rates of separating
screens, slurry pumps and tailings lines have been observed and attributed to the
synergistic effects of wear and corrosion producing an amplified rate of material removal
[10].
There has been a wide adoption of wear resistant weld overlays in an effort to combat
these repair and maintenance issues. By employing weld overlays it is possible to retain
the desired properties of the bulk material used to produce a component while vastly
improving the protective qualities of surfaces in contact with the wear- and corrosive-
media. The two main categories of weld overlays used for wear protection are chromium
carbide-based alloys and tungsten carbide metal matrix composites.
The compositions of chromium carbide-based hardfacing alloys are essentially based on
high chromium cast irons. Typically, the grades of alloy will contain in the range of 25
to 32 w% chromium and up to 5% of carbon. Their microstructures tend to contain large
amounts of M7C3 carbides, where M can represent metals such as chromium, iron or
manganese (Figure 2) [11]. The carbides are contained within an iron-based austenitic or
martensitic matrix, and have the microstructure of acicular, hollow rods. These are
aligned parallel to the heat flow direction of the weld deposition, i.e. roughly
perpendicular to the surface of the substrate material [12]. The M7C3 carbides have a
reported hardness of approximately 1700 Hv, whilst the matrix of the alloys tends to be
softer (approximately 350 Hv) [13].
Chromium carbide-based overlays (CCOs) are usually applied using arc welding
processes [14]. These can be either manual, or for larger components automated
processes are used. Compared to other wear-resistant materials (tungsten carbide-based
overlays and certain polymer liners), CCOs are relatively inexpensive. As such, they are
utilised for larger scale, high volume applications such as wear-plate for truck beds and
piping in hydrotransport applications [15]. The overlays are generally deposited in two
passes, with the second pass having a larger thickness. This is to compensate for the
dilution of the hardfacing alloy with the base material, and allows the second pass to
nucleate and grow the large, acicular carbides necessary for wear resistance. The
overlays tend to contain transverse cracking resulting from the contraction of the weld
pool upon cooling (i.e., often called ‘relief’ or ‘check’ cracking).
CCOs are commonly employed to protect against abrasive wear in wet or dry
environments. There is a general consensus that having a high proportion of M7C3
carbides in the overlay is beneficial to protect against abrasion. However, there is a lack
of available information correlating the effects of carbide size or populations with the
performance in specific, abrasive oil sands mining applications. CCOs are generally less
suitable for protection from impact wear. If the impact loading is high enough to produce
plastic deformation, the brittle nature of the carbide-rich alloy can act in tandem with the
pre-existing transverse cracks in the hardfacing, resulting in the spallation of the overlay.
To extend the service life of production-critical components it has been found necessary
to use tungsten carbide-based metal matrix composites (MMCs) [16]. These tend to be
deposited by plasma transferred arc welding (PTAW); however for specific components
or in-field repairs gas metal arc welding (GMAW) techniques are employed.
The MMCs contain distributions of hard tungsten carbide particles suspended in a tough,
ductile metal matrix alloy (Figure 3). PTAW is the most common method for depositing
MMC overlays. The PTAW process involves an arc being established between a non-
consumable tungsten electrode and the work piece, typically with argon gas shielding and
powder feeding through the welding torch (Figure 4). This process can produce
relatively thick deposits (between 3 to 6 mm in a single pass), with low dilution rates
while maintaining the integrity of the composite materials [17].
Commercial MMCs usually combine tungsten carbide particles with a Ni-based matrix
alloy. The carbide particles can be either angular or spherical, with the angular particles
being sub-divided between monocrystalline tungsten carbide (WC) and eutectic
(WC/W2C) (Figure 5). The heat produced by the PTAW deposition can promote the
dissolution of the tungsten carbide particles into the metal matrix. This dissolution effect
can embrittle and reduce the overall corrosion and wear resistance performance of the
MMC. WC is more chemically stable than W2C and less prone to this effect [18]. WC-
bearing MMCs are more widely used in the oil sands industry as they allow for a wider
window of production welding parameters and improved material consistency compared
to WC/W2C particles, since Spherical carbides generally have a eutectic WC/W2C
composition, making them more prone to dissolution. However, due to the fine lamellar
structure of WC/W2C, these tend to be harder than WC carbides, with measured hardness
in excess of 2,200 Hv (while WC has a range of hardness from approximately 1,100 to
2,100 Hv [19]).
Commercial MMC overlay powders tend to contain a blend of between 60 to 65 w%
tungsten carbide combined with a Ni-based matrix alloy. The Ni-alloys are based on
NiBSi or NiCrBSi, and contain typically 2 to 5w% B and Si to suppress the melting point
of the alloy to around 1050ºC, and act as self-fluxing agents. The matrix microstructure
typically consists of primary nickel dendrites, with interdendritic eutectics composed of
Ni+Ni3B or Ni+Ni3Si. These boride and silicide phases are harder than the Ni phase,
however the hardness of the tungsten carbide is far superior [20].
The addition of up to 15wt% Cr to the alloy can augment the hard precipitate phases in
the matrix due to the formation of Cr-borides and Cr-carbides, however this may not
necessarily improve the wear or corrosion resistance of the MMC overlay. The issue is
that the presence of Cr will accelerate the dissolution of tungsten carbide particles [21].
This not only reduces the volume fraction of primary tungsten carbide, but may also
promote other secondary carbides to precipitate in the matrix during cooling. These
secondary carbides are often very fine in size/shape, and may be too brittle to provide
significant improvements in wear resistance.
The PTAW process is generally limited to shop production environments, and is
impractical for most field welding applications since the gravity fed powder requires
deposition in the flat position. In-field repair welding tends to be conducted using
techniques such as GMAW using tungsten carbide-based wire consumables. However,
due to the increased WC dissolution caused by the high droplet temperatures during
deposition and limitations in the composition of the consumables, the performance of
overlays deposited by GMAW are currently significantly lower than those deposited by
PTAW [22].
The extreme wear-conditions in oil sands processing has led to a wide adoption of
tungsten carbide-MMC overlays deposited by PTAW, especially for production-critical
components. To be economically feasible, PTAW overlays should at least double the
service life of a component. Field experience of overlays used to protect equipment such
as bucket teeth, hydrotransport screens and crushers report improved service lives of up
to 600%, with the associated economic savings [23].
Research and development is on-going in an effort to build on the performance exhibited
by current, commercial composite weld overlays. Key areas of work include the design
of MMCs with improved corrosion resistance and the tailoring of overlay compositions to
combat specific types of wear. Research is also being conducted on developing processes
(such as advanced complex-waveform modes of GMAW and GTAW welding) for the
effective deposition of MMC materials for the demanding wear and corrosions
application encountered in Oil Sands operations.
References
1. J. F. Flores & A Neville, Materials selection in the oil sands industry based on
materials degradation mechanisms, Exploration & Production, 7, (1), 2009, 42-45.
2. DOE/EIA – 0484 (2010) International Energy Outlook 2010, U. S. Energy Information
Administration, Office of Integrated Analysis and Forecasting, U.S. Department of
Energy, Washington, DC 20585.
3. P. Bayliss & A. A. Levinson, Mineralogical review of the Alberta oil sand deposits
(lower cretaceous, Mannville Group), Bulletin of Canadian Petroleum Geology, v24, (2),
1976, 211-224.
4. http://www.gumberg.org/canadian-oil-sands-announced-provides-2011-budget
5. M. Anderson, S. Chiovelli & S. Hoskins, Improving reliability and productivity at
Syncrude Canada Ltd through materials research: past, present and future, CIM
Bulletin, October 2004, 1-6.
6. G. Fisher, Development of wear- and corrosion-resistant coatings in oil sands mining,
Canadian Chemical News, June 2006, 12-13.
7. R. Llewellyn, Resisting wear attack in oil sands mining and processing, CIM Bulletin,
July 1997, 75-81.
8. G. Fisher, J. Wolodko & D. Crick, Impact testing of materials for oil sands processing
applications, Corrosion 2007, March 11 – 15 2007, NACE International, paper #07682.
9. J. Been, G. Fisher, J. Wolodko, K. Alemaskin, B. Lu, M. Danysh & D. Kiel, Erosion-
corrosion testing of materials in the prediction of wear of hydrotransport pipelines in oil
sands slurries, 17th
International Corrosion Congress, October 2008, paper #4844.
10. J. F. Flores, A. Neville, N. Kapur & A. Gnanavel, Erosion-corrosion degradation
mechanisms of Fe-Cr and WC-Fe-Cr-C PTA overlays in concentrated slurries, Wear
v267, 2009, 213-222.
11. M. F. Buchely, J. C Gutierrez, L. M. Leon & A. Toro, The effect of microstructure on
abrasive wear of hardfacing alloys, Wear v259, 2005, 52 – 61.
12. G. L. F. Powell, The microstructure of hypereutectic Cr-C hard surfacing deposits
and its dependence on welding variables, Australian Welding Research, January 1979, 16
– 23.
13. H. S. Avery & H. J. Chapin, Hard-facing alloys of the chromium carbide type, The
Welding Journal, October 1952, 917 – 930.
14. T. B Jefferson & G. Woods, Metals and how to weld them, James Lincoln Arc
Welding Foundation, 1954.
15. R Llewellyn & C. Tuite, Hardfacing fights wear in oil sands operation, Welding
Journal, March 1995, 55 – 60.
16. M. Anderson, S. Chiovelli & R. Llewellyn, The use of tungsten carbide materials for
oilsand wear applications, Thermal Spray 2003, ASM International, 2003, 509 – 518.
17. M. Yarmuch, B. M. Patchett, D. G. Ivey & M. Anderson, Effect of welding
parameters and gas composition on PTAW behaviour, Trends in Welding Research, 8th
International Conference, June 1-8, 2008, AWS, ASM.
18. L. Choi, T. Wolfe, M. Yarmuch & A. Gerlich, Effect of welding parameters on
tungsten carbide-metal matrix composites (WC-MMC) produced by GMAW, Canadian
Welding Association, 1st Annual Conference, Collingwood, Ont., 2010
19. T. Takahashi & E. J. Freise, Determination of the slip system in single crystals of
tungsten monocarbide, Philosophical Magazine, v12, 1964, 1 – 8.
20. T. Liyanage, G. Fisher & A. P. Gerlich, The influence of alloy chemistry on
microstructure and properties in NiCrBSi overlay coatings deposited by plasma
transferred arc welding (PTAW), Surface Coatings Technology, v205, 2010, 759-765.
21. T. Liyanage, Microstructure and properties of Ni-alloy and Ni-WC composite
overlays, MSc Thesis, University of Alberta, 2010.
22. M. Anderson, S. Chiovelli & D. Reid, Wear resistant materials for use in the oil
sands hydraulic transportation process, materials for Resource Recovery &
Transportation, Ed. L. Collins, CIM, 1998, 451 – 465.
23. D. Harper, M. Gill, K. W. D. Hart & M. Anderson, International Thermal Spray 2002,
Proceedings, 2002, 278-283.
Figure 1: Schematic diagram of the open pit process used for oil sands mining.
Figure 2: Micrograph of a chromium carbide-based overlay, etched, showing the acicular
carbides in an iron-based matrix. Magnification x50.
Figure 3: Micrograph of a tungsten carbide-based MMC overlay, showing the tungsten
carbide particles distributed in a nickel-based matrix alloy. Magnification x50.
Figure 4: Photograph showing PTA welding apparatus
Figure 5: SEM Micrograph of a typical angular tungsten carbide powder. Magnification
x100.