Patent Application
20070099014
Not Applicable
Not Applicable
Not Applicable
1. Field of the Invention
The present invention relates to a composite thermal spray coating and method of making the coating, and more particularly to a coating that is produced by using a thermal spray process to apply a powder containing both a hard phase material, such as a carbide or oxide, and a self lubricating phase material, such as graphite.
2. Description of the Related Art
In various machines and machinery with parts that require lubrication, there are occasions where the lubricated parts are starved of lubrication, or high exertion forces render the lubrication ineffective. For machines like pumps, motors, and turbines, there are two basic types of lubrication systems. One type of lubricant is pressure based, typically found in combustion engines and turbines, wherein a lubricant is forced into the bearing or seal under pressure. The other type of lubricant is hydrodynamic, typically used on small motors and pumps, wherein the lubrication is drawn into the seal or bearing as a result of the rotation of the mating surface. In both lubrication systems, the principle is to establish a layer of lubricant under pressure between mating parts. Insufficient pressure, either as a result of low sliding speeds (hydrodynamic) or low supply pressure (pressure based) results in increased friction and wear as expressed in the Stribeck Curve, the characteristic curve of the coefficient of friction versus sliding speed.
During startup, the seals, bearing surfaces, and rings lack liquid lubrication until the lubrication system either comes up to pressure or the rotating parts achieve sufficient rotation velocity to draw the lubricant into the gap between the parts. This condition is worsened the longer the machine is idle between startups as the residual lubrication on the surfaces drains. The loss of lubrication while components are stationary is especially a problem with hydrodynamic seals, and the lubrication may be nothing more than water, as is the case with boiler pumps. Thus, for some machines, it is not only the number of hours in operation but the number of startup cycles that determines component life. One solution for pressure based lubricating systems is to pre-start the lubrication system prior to machine startup; but this has limited advantage as some seals and bearings will still have surfaces that are devoid of lubricant until the rotational parts of the machine reach operating speed (hydrodynamic component). For hydrodynamic lubrication there is no easy or viable solution in terms of pre-starting the lubrication; the parts simply must have a sufficient sliding speed to exceed boundary lubrication conditions.
Some pumps and motors are exposed to high exertion forces due to their nature of changing power output rapidly. These forces, when translated to seals and bearings, can momentarily overcome the lubrication pressure separating the mating parts, causing the surfaces to make contact. As a result, the lifetimes of these components are shortened and friction and additional heat are introduced into the machine.
Developments in thermal spray technology over the years have introduced a number of coatings that can extend the life of bearing surfaces. The most simple and basic is a wear or erosion resistant coating consisting of a hard metal, such as molybdenum (Mo). This coating does not solve the root lubrication problem but does extend the life of the lubricated surfaces. For more extreme applications, coatings that not only resist wear but afford some protection from corrosion, heat, and oxidation have been created, such as tungsten carbide and chrome carbide. With the use of these coatings, the underlying problem—lack of lubrication—remains, but the components survive longer in their intended operating environment. It has been previously known to add a solid lubricant to the coating matrix in that a graphite solid lubricant clad in nickel was introduced as part of a coating. This addition substantially improved the performance of the coating in use. The addition of a solid lubricant provided reduced wear rates and lower friction at lower speeds but there is room for improvement. There remains a need in the art for a coating that provides not only lubrication in addition to the protection of traditional coatings at low operating speeds, but also a method of improving the performance of the lubrication itself at those lower speeds.
As an example of the state of conventional coating systems, thermal shock testing was conducted on a boiler pump wear ring made with a tungsten carbide and cobalt chrome matrix coating applied by conventional methods (e.g., without micro-pore inclusions and other techniques disclosed in the present invention). Thermal shock is common when components are heated and subsequently purged or otherwise quickly cooled for installation. When clearances are especially tight, components may require shrink fitting onto other components. This involves using a heating mechanism, such as an oxygen-acetylene flame to expand and fit the component. Once the components are fitted they are often shrunk using an accelerant such as immersing them in cold water or using liquid carbon dioxide, nitrogen or argon. In the tested wear ring sample, cracking was clearly evident at the bottom edge of the component. The cause of the cracks is from two properties inherent to the coating. The first property is the pre-existing tensile stress when the coating was produced. Coupled with the second property of the coating to be brittle results in the coating cracking when subjected to thermal shock. There remains a need for lubricated coatings that exhibit good thermal shock resistance properties.
In addition to the protection the coatings offer, the porosity inherent in thermal spray coatings has been observed to trap some liquid lubrication. This trapped lubrication results in reduced friction and heat when there is no lubricating layer. Typically the creation of pores in thermal spray coatings is haphazard and unpredictable, and is normally considered a flaw in the coating process. Thus, there remains a need in the art for a coating and application method that can include consistent porosity to retain liquid lubricant while still providing maximum protective functionality.
To address the aforementioned deficiencies in conventional systems, the present invention provides a composite coating and method for forming and applying a composite coating that is resistant to galling, fretting, and sliding wear. The coating is applied to a substrate and includes a mixture of hard carbide particles with an aggregate size range of less than about 2 μm in an alloy matrix or oxides with an aggregate size range of less than about 0.5 μm and solid lubricant particles captured in a binder. The coating is produced by using a thermal spray process to apply a powder with a hard face (or oxide) phase and a self lubricating phase such that the resulting coating exhibits neutral or compressive residual stress. Thus, the applied coating of the present invention combines the benefits achieved with previous thermal spray coatings in terms of wear, abrasion, heat and corrosion with those afforded by solid lubricants as an optimal coating using the latest techniques in thermal spray to produce the feedstock and apply the coating. In addition, the coating of the present invention provides consistently distributed surface porosity to retain liquid lubricant on the coating surface.
According to one embodiment of the present invention, a method of forming a coating is provided. The coating has a low coefficient of friction that is wear resistant, corrosion resistant, and heat resistant. The method includes the steps of providing particles that include a hard face material, providing particles that include a solid lubricant material, applying both of the particle types to a substrate to form the coating, wherein the coating includes a blend of the hard face material and the solid lubricant material. The hard face material particles may be made of one or more of chromium carbide, tungsten carbide, titanium carbide, molybdenum carbide, and vanadium carbide. The solid lubricant material particles may be one or more of graphite, boron nitride, silicone, polyester, and PTFE.
According to another embodiment, the fine particles of carbide hard phase material that are less than about 2 μm are agglomerated into larger particles using a binder material before they are combined in order to better facilitate passing through the thermal spray process. The binder material is made of one or more of cobalt, nickel and iron alloyed with one or more of chrome, molybdenum, vanadium and copper.
Additional objects and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. The objects and advantages of the invention may be realized and obtained by means of the instrumentalities and combinations particularly pointed out hereinafter.
The accompanying drawings are included to provide further understanding of the invention and are incorporated in and constitute a part of this specification. The accompanying drawings illustrate embodiments of the invention and together with the description serve to explain the principles of the invention. In the figures:
Reference will now be made in detail to the preferred embodiments of the present invention, examples of which are illustrated in the accompanying drawings.
The invention as defined herein uses two separate thermal spray materials, blended together to achieve a thermal spray coating that combines the benefits achieved with previous thermal spray coatings in terms of wear, abrasion, heat and corrosion with those afforded by solid lubricants. When applied using a thermal spray process in accordance with the invention, the resulting coatings exhibit the properties necessary to provide superior galling, fretting and sliding wear resistance in applications where components requiring lubrication are operated in conditions where the components are at least temporarily void of lubrication or where the lubrication pressure is temporarily compromised. As used herein, thermal spray processes refer to, but are not limited to, high velocity oxygen fuel (HVOF), high velocity liquid fuel (HVLF), high velocity air fuel (HVAF), plasma, cold spray, detonation processes, and similar processes.
The hard face materials produced in step S102 provide the necessary wear resistance as well as resistance to heat, corrosion, and oxidation. Typical carbides include tungsten carbide, chromium carbide, titanium carbide and vanadium carbide, all of which are commonly used thermal spray materials. Carbides provide excellent erosion, corrosion, and heat resistance. However, carbides do not perform well in environments that are starved of lubrication as they possess poor coefficients of friction. In addition, materials such as agglomerated nano titanium oxide (TiO2), chrome oxide (Cr2O3), aluminum oxide (Al2O3), or mixtures thereof also offer similar benefits as a hard face material in that the nano particles have higher ductility and are considerably less brittle than coatings produced using larger particles. For example, chromium carbide is a good material choice, as the corrosion and oxidation resistance is the highest and the use of this material creates a coating that has a high resistance to thermal shock gradients when applied using the appropriate thermal spray process.
The particle size of the carbides formed as a raw powder in step S102 needs to be small, for example about than 2 microns (μm) or smaller, to produce a coating with good ductility. One method to prepare the carbide particles is to use an attrition mill to grind the particles and then use an inert gas atomizing process to produce particles less than 0.5 μm. An alternate method after grinding in an attrition mill is to spray dry and sinter which will produce larger particles of about 2 μm. The process then moves to step S104. In step S104, the small particle raw powder is agglomerated into larger particles using a binder material. The agglomeration may be accomplished using an inert gas atomizer or by a spray drying and sintering process.
The binder materials used in step S104 are selected based on a number of factors to additionally benefit the resulting coating. First, the base material of the binder may be selected from the group of iron (Fe), cobalt (Co), or nickel (Ni). For corrosion resistance, nickel exhibits the best properties, followed by cobalt, and then iron. The alloying of chromium (Cr) (for example, less than 30% by weight) to the base material adds corrosion resistance. The alloying of vanadium (V) (for example, less than 10% by weight) to the base material aids in forming vanadium carbide over the formation of chrome carbide during the thermal spraying process in the presence of free carbon atoms residual from the process of forming carbides, leaving the chromium in the alloy matrix free for added corrosion resistance. The alloying of molybdenum (Mo) (for example, less than 10% by weight) adds wear and corrosion resistance. The alloying of copper (Cu) in low concentrations (less than 5% by weight) adds corrosion resistance.
Preparation of the agglomerated hard face particles in step S104 is preferably performed using an inert gas oven to melt the binder, followed by introduction of the carbide particles and then inert gas atomizing to produce acceptable particle sizing for thermal spray application. This results in carbide particles about 0.5 μm or smaller in the alloy matrix. The final agglomerated particles are preferred to be in the size range of about 11 μm to about 60 μm.
As described above, as an alternate form of the hard face material, nano titania (TiO2), nano chromia (Cr2O3), and/or nano alumina (Al2O3) may be used. These oxides are formed first as nano crystals less than about 0.1 μm in step S102 and then agglomerated in a spray drying process followed by plasma reprocessing to form congealed particles of suitable size for thermal spray application in step S104. Variations in processing will result in variations in the properties of the resulting coating that can be tailored to alter properties such as wear resistance, hardness, ductility, resistance to cracking, etc. The processing of the material uses a binder in the initial steps that does not remain in the final product. The use of additives similar to those used with the carbides (such as chromium or vanadium to aid in corrosion, heat, and wear resistance) is not required for the aforementioned nano oxides. Furthermore, the use of metal alloys as a binder will not add additional corrosion or wear protection, and are not required.
In step S106, the second thermal spray material is produced. This material is a solid lubricant to provide a low coefficient of friction for purposes of lubrication of the component. Typical solid lubricants that can be thermal sprayed include graphite, boron nitride, silicone, polyester, and polytetrafluoroethylene (PTFE). Because these materials possess release agent characteristics, their spray-ability can be poor and in the case of graphite could result in the formation of undesirable carbides with the metal alloy binder of the hard phase material. To improve spray-ability and prevent reactive formations with the hard phase material, they can be clad in nickel, cobalt, copper, molybdenum or gold or alloys thereof. Alternatively, the solid lubricants can be spray-dried with a suitable binder such as, for example, polyvinyl alcohol (PVA) or carboxymethylcellulose (CMC). The preferred use of the metallic clad materials have other key benefits in the resulting coating as well when applied using a thermal spray process as described previously in the preparation of the hard phase material. The preferred material choice is graphite clad in nickel. The use of cladding is required for use of some materials, such as polyester, that cannot otherwise withstand some thermal spray processes. Materials like polyester could vaporize or decompose in the plume of the plasma gun if the plasma spray process is used to apply the coating or could oxidize in either the cold spray or HVOF processes. The resulting agglomerated solid lubricant particles should be larger than those for the agglomerated hard phase particles and preferably in the range of about 20 μm to 150 μm.
The process then moves to step S110, where the two above-described thermal spray materials are combined. The particles can be pre-blended prior to feeding into the thermal spray process or they can be fed into the thermal spray process as two separate materials. Feeding the materials separately provides the advantage of permitting the tailoring of the individual coating layers to suit specific applications such as to produce gradients within the coating to concentrate the solid lubricant at or near the exposed surface. In step S112, the coating is applied to the component to be coated using a suitable thermal spray process that includes, but is not limited to, high velocity oxygen fuel (HVOF), high velocity liquid fuel (HVLF), high velocity air fuel (HVAF), plasma, cold spray, and detonation processes.
The application of the coating in step S112 is performed such that the resulting internal stresses are either neutral or compressive. This can be achieved by minimizing particle temperature and maximizing particle velocity through proper selection of process parameters specific to each thermal spray process. The control of stresses is further enhanced by spraying the coating at high surface speeds to minimize the amount of material that is applied per pass, as well as the efficient use of cooling procedures to maintain an even temperature during the coating process. Maintaining the component temperature consistently is important in maintaining the suitable amount of lubricating constituents within the protective coating as well as controlling the buildup of internal stress.
In step S114, the coating is finished with suitable equipment necessary to attain the optimal surface finish and dimensions. For example, diamond grinding is typically used to remove material and achieve these final dimensional and finish requirements. The importance of retaining a suitable amount of solid lubricant within the coating during spraying then comes into effect as the inherent nature of the diamond grinding process will “pull out” some, but not all, exposed solid lubricant particles. As discussed below with respect to
The dynamics of the finished coating of the present invention are illustrated in
The micro-pores also allow for expansion and contraction of the substrate and protective coating layer due to temperature fluctuations in operation. Each pore on the surface serves as a stress relief point; and the entrapped solid lubricant internal to the coating, being softer and less dense than the hard phase material serves also in the same fashion. Any tendencies for the coating to crack from stress are relieved when the crack encounters either a pore for a surface crack or a solid lubricant region in the interior of the coating. These micro-pores are also beneficial in certain components when being installed into machinery. Very often the clearances are tight, sometimes less than 1/1000 of an inch, and these components require shrink fitting onto other components. This involves using a heating mechanism, typically an oxygen-acetylene flame to expand and fit the component. Once the components are fitted they are often shrunk using an accelerant such as immersing them in cold water or using liquid carbon dioxide, nitrogen or argon. These coatings exhibit good thermal shock resistance properties in that any stress cracks that develop do not propagate and remain as short micro-cracks that do not propagate farther than the average distance between solid lubricant particles.
Suitable applications for a coating with low coefficient of friction according to the present invention are in turbo-machinery, pumps and engines with typical components being seals, bearings and piston rings. The coating is, for example, usable as a protective layer for wear rings, balance drum, impeller wear rings and various components in boiler feed pumps, where these components operate in conditions void of lubrication at startup and pump fresh and/or saline, medium to high pH water, and particulate matter of various size and volume. The small (smaller than 2 μm and preferably small than 0.5 μm) carbide phases of the coating act to reduce abrasive, corrosive and erosive wear whilst offering oxidation resistance. The inclusion of solid lubricants allows these carbides to perform at maximum capability by reducing the amount of rubbing, galling, fretting and pickup, particularly in conditions void of any lubrication. The presence of micro-pores aids in hydrodynamic lubrication, especially at lower speeds.
Experimental testing of the present invention was performed in two sets of tests. First, initial test work was completed to optimize a coating for a specific application by spraying a variety of different material and blend compositions. Test coupons for pin-on-disc, corrosion, erosion, and metallographic analysis were sprayed to determine the material compositions with the most potential for a particular application that being boiler feed pump components. Next, subsequent testing included spray testing of actual boiler feed pump wear rings and measuring the thermal shock and direct flame impingement characteristics.
Pin-on-disc tests generally are performed to determine the wear resistance and friction co-efficient of the coating with water added to the interface to simulate the actual lubricating medium. In tests of coatings of the present invention, a stainless-steel pin was pressed with a pre-determined load against the finished coating which rotated at staged speeds. The coating to be tested thus formed the contact surface with the pin and its resultant wear rate was measured. In the tests, the critical load for the onset of “scuff tracks” is determined. Erosion testing was performed to determine the coatings' ability to resist abrasion against water jet impingement containing abrasive particulate. Corrosion testing was performed by measuring the breakthrough potential of each coating at pH values of 6.5 and 9.0 respectively.
Superior corrosion and erosion results were obtained using a Sulzer Metco SM5241 CrC Ni C hard face material (approximately chrome carbide 54% weight, nickel 39% weight, and carbon 7% weight), with a small size distribution (less than 2 μm) proportion of carbide particles. This material displayed its best erosion resistance at low impact angles (e.g., 15 degrees) and higher erosion resistance relative to other materials such as tungsten carbide, hasetlloy C, and nano titanium oxide at high impact angles (e.g., 90 degrees), due in part to the small chrome carbide particles. This material also displayed high corrosion resistance at medium to high pH values. In comparison to the other materials this was a preferred, but not the only, choice for use as the hard face material in the present invention. It must be noted the carbon indicated in the CrC Ni C material is a residual, present in small amounts of less than 1%, residual in the process of forming the carbide.
Further initial experimental tests, including pin-on-disc tests (ASTM G99), were performed with the original CrC Ni C hard face material blended with a 25 weight percentage of Ni 25CGraphite (25 weight percentage of graphite particles clad in a nickel sheath) to serve as the solid lubricant. The HVOF spray process, where the powder is applied onto the substrate at velocities exceeding 500 m/sec, produced coating results with compressive residual stress, a relatively smooth coating finish, and even distribution of solid lubricant particles in the hard phase material.
Wear and friction measurements using the pin-on-disc test in water at 20 degrees C, showed the onset of adhesive wear at 175 N/mm2 at 0.5 m/sec (approximately 175% higher than coatings of the CrC Ni C hard face material alone) and 25 N/mm2 at 1 m/sec (approximately 25% higher than coatings of the CrC Ni C hard face material alone). Thus, the presence of the solid lubricant and pores increased the resistance to adhesive wear most at lower speeds when hydrodynamic forces are the lowest. ASTM G99 test results on 314 stainless steel and similar alloys indicate the onset of adhesive wear at less than 25 N/mm2 under both test velocity conditions.
Thermal shock experimental testing was performed by spraying the coating onto a boiler feed pump wear ring 300, shown in
While exemplary embodiments of the invention have been shown and described herein, it will be obvious to those skilled in the art that such embodiments are provided by way of example only. Numerous insubstantial variations, changes, and substitutions will now be apparent to those skilled in the art without departing from the scope of the invention disclosed herein by the Applicants. Accordingly, it is intended that the invention be limited only by the spirit and scope of the claims, as they will be allowed.
