Patent Grant
9388482
This application relates to functionally graded cemented tungsten carbide materials that contain a metal binder gradient. The metal binder can be cobalt, nickel, iron or alloy thereof. Such materials may be used for metal cutting tools, rock drilling tools for oil exploration, mining, construction and road working tools and many other metal-working tools, metal-forming tools, metal-shaping tools, and other applications. For background information, the reader should consult U.S. Patent Application Publication No. 2005/0276717, which patent application is expressly incorporated herein by reference.
As explained in the prior patent publication noted above, it is desirable to construct a cemented tungsten carbide material (“WC” material) that includes an amount of metal binder. It is desirable to construct a cemented tungsten carbide material that has a combination of toughness and wear-resistance.
Cemented tungsten carbide, consisting of large volume fractions of WC particles in a metal binder matrix, is one of the most widely used industrial tool materials for metal machining, metal forming, mining, oil and gas drilling and all other applications. Compared with conventional cemented tungsten carbide, functionally graded cemented tungsten carbide (FGM cemented tungsten carbide) with a metal binder gradient spreading from the surface to the interior of a sintered piece offers a superior combination of mechanical properties. For example, FGM cemented tungsten carbide with a lower metal binder content in the surface region demonstrates better wear-resistance performance, resulting from the combination of a harder surface and a tougher core. Though the potential advantages of FGM cemented tungsten carbide are easily understood, manufacturing of FGM cemented tungsten carbide is however a difficult challenge. Cemented tungsten carbide is typically sintered via liquid phase sintering (LPS) process in vacuum. Unfortunately, when cemented tungsten carbide with an initial metal binder gradient is subjected to liquid phase sintering, migration of the liquid metal binder phase occurs and the gradient of metal binder is easily eliminated.
Briefly, and in general terms, a method of preparing a functionally graded cemented tungsten carbide material is described. In one embodiment, the method can comprise obtaining sintered cemented tungsten carbide of tungsten carbide and a metal binder. The sintered material can be heat treated via a process comprising a step that heats the sintered material in a first temperature range of a multi-phase state, in which temperature range at least solid tungsten carbide, liquid metal binder, and solid metal binder coexist. Additionally, the material, after the heat treating process, comprises a surface layer with lower content of metal binder than that of the nominal value of the metal binder content in the bulk of the material. Optionally, the heat treating process can be a two-step process which includes heating the sintered material in a carburizing atmosphere and at a temperature above the multi-phase state so that liquid metal binder, but no solid metal binder, coexists with tungsten carbide and then heating in the temperature range of multi-phase-region. In still another optional embodiment, the heat treating process can be a three-step process which includes heating the sintered material subsequent to the multi-phase state, in a decarburizing atmosphere and at a temperature below the multi-phase-region so that solid metal binder, but no liquid metal binder, coexists with tungsten carbide.
Additional features and advantages of the invention will be apparent from the detailed description which follows, taken in conjunction with the accompanying drawings, which together illustrate, by way of example, features of the invention; and, wherein:
Reference will now be made to the exemplary embodiments illustrated, and specific language will be used herein to describe the same. It will nevertheless be understood that no limitation of the scope of the invention is thereby intended.
Before the present invention is disclosed and described, it is to be understood that this disclosure is not limited to the particular process steps and materials disclosed herein because such process steps and materials may vary somewhat. It is also to be understood that the terminology used herein is used for the purpose of describing particular embodiments only. The terms are not intended to be limiting because the scope of the present disclosure is intended to be limited only by the appended claims and equivalents thereof.
It must be noted that, as used in this specification and the appended claims, the singular forms “a,” “an,” and “the” include plural referents unless the context clearly dictates otherwise.
As used herein, “surface layer” refers to the thickness from the surface to the depth at which the metal binder content rises up to equal that of the nominal composition.
As used herein, “bulk of material” or “bulk of the material” refers to the portion of the material that is not the surface layer.
As used herein, “heat treating” normally refers to a single continuous heating process which may have one or more steps. Typically, the multi-step processes are part of a single heating run where the temperature is adjusted stepwise to obtain a new region and no cooling in between steps is required or even typically desirable.
As used herein, “nominal” refers to the average composition of the material regardless whether it is homogeneous or graded.
As used herein, when referring to a range, “within” includes the endpoints of the range. For example, a temperature within the multi-phase-region, would include the endpoints of the multi-phase-region; i.e., if the multi-phase-region was a temperature range between 1275° C. and 1325° C., the endpoints of 1275 and 1325 would be considered included in the recited range.
Functionally graded cemented tungsten carbide materials can be obtained from sintered cemented tungsten carbide materials using a uniquely designed heat treating process. The methods to obtain sintered cemented tungsten carbide materials generally include preparing a powder mixture of tungsten carbide and metal binder, and compacting the powder mixture together. In some embodiments, the powders can be compacted using known techniques, such as using uniaxial cold dies pressing methods although other compacting techniques can be suitable.
After compaction, the powder can then be sintered according to standard sintering procedures, e.g., at 1400° C. under a vacuum. The sintered tungsten carbide is fully densified. Porosity in the sintered cemented tungsten carbide is less than A04B04C04 per ASTM B276-91 standard. The sintered cemented tungsten carbide can also be produced by sinter-HIP, which is a vacuum sintering plus a low pressure (<10 MPa) hot isostatic pressing step in the same furnace as a part of the sintering cycle. As is known in the art, such sintering processes can produce a homogeneous cemented tungsten carbide material, with the amount of metal binder in the WC matrix being equal (homogenous or substantially homogenous) throughout the entire sample.
In the present embodiments, however, an additional process is performed to produce desired functionally graded (FGM) cemented tungsten carbide having improved properties. Specifically, this step is a “heat treating” process. The heat treating process itself includes at least one step of heat treatment in the temperature range of multi-phase-region, in which temperature range at least solid tungsten carbide, liquid metal binder, and solid metal binder coexist. Other solid additives such as carbides of other transition metals including VC, Cr2C3, NbC, TiC, TaC can also be present. The heat treating process can also include one or more additional steps in a temperature range above or below the multi-phase-region. Notably, it has been found that the 2-step and 3-step heat treatments provide more desirable results over even the 1-step heat treating process. The heat treating process as a whole, or its constituent steps, can be conducted either in the same sintering furnace run without removing the sample from the furnace, or in separate furnaces in separate thermal cycles. For example, if the sintering and heat treating are performed in a common furnace run, the heat treating process described herein becomes an extension of the sintering cycle. The desired FGM cemented tungsten carbide can have a harder and more wear-resistant surface layer and a tougher core compared to conventional cemented tungsten carbide.
The hard and wear-resistant surface layer can be comprised of the cemented tungsten carbide with graded metal binder content. The metal binder content at the surface can be significantly lower than that of the nominal composition of the bulk. The metal binder content usually increases as a function of the depth from the surface and can reach and even surpass the nominal composition of the composite at a certain depth. The metal binder content at the surface can be less than 95% of the nominal composition, and in some cases 30 to 90 percent of the nominal composition. The depth of the surface layer can be greater than 10 microns, such as from 30 to 5000 microns and in many cases is from 50 μm to 3 mm. These materials can also exhibit a more uniform gradient within a graded region of the surface layer than previous methods. For example, within the surface layer, the metal binder content can exhibit a substantially continuous gradient across the surface layer.
To manufacture the above described functionally graded cemented tungsten carbide product, the following method is described.
Sintered cemented tungsten carbide materials can be prepared according to standard manufacturing procedures as used in the industry. The sintered cemented tungsten carbide material can be prepared or obtained from a suitable commercial source. In one aspect, the metal binder can be cobalt, nickel, iron or their alloys. In another aspect, the sintered material can further include at least one of titanium, tantalum, chromium, molybdenum, niobium, vanadium, and carbides, nitrides and carbonitrides thereof. Most often these additives can be present in amounts less than about 20 wt %, although variations can be made for specific applications. These additives are often added for either grain size refinement or improvement of high temperature deformation and chemical wear resistance.
Sintered cemented tungsten carbide materials may have a carbon content of either sub-stoichiometry (or carbon deficient relative to stoichiometry), stoichiometry, or super-stoichiometry (or carbon excess relative to stoichiometry). In one aspect, the carbon content can be sub-stoichiometric. Stoichiometric carbon content of WC by its formula is 6.125% by weight. After metal binder is added, total carbon content will decrease proportionally depending on the metal binder content.
Prior to the heat treating process, a pre-treatment can optionally be applied where the sintered material is decarburized. The pre-treatment can be conducted in the same furnace run with the heat treating process or in separate furnace runs or separate furnace. Such a decarburizing step can be performed by subjecting the sintered material to a decarburizing atmosphere. For example, the atmosphere can be vacuum, hydrogen, nitrogen, or the like.
Another aspect regarding the carbon content of the material is that, prior to the heat treating process, the carbon content of the material can be high enough such that there are no complex carbides in the material. The complex carbides, that have lower carbon contents than that of tungsten carbide, are undesired brittle carbides of tungsten and metal binder, which form when the total carbon content is excessively low. When the metal binder is cobalt, the complex carbide is η-phase with a typical formula of Co3W3C.
If there are above-mentioned complex carbides in the sintered material, a carburizing pre-treatment may be applied to remove the complex carbides, prior to the heat treating process. The pre-treatment may be conducted in the same furnace run with the heat treating process or in a separate furnace run. Such a carburizing step can be performed by subjecting the sintered material to a carburizing atmosphere. For example, the atmosphere can include carbon dioxide, carbon monoxide, methane, and the like, and may include optional carrier gases such as nitrogen, oxygen, or the like.
Another aspect of the invention is that the heat treatment can include a multi-phase-region treatment step, carried out within a multi-phase-region temperature range, in which temperature range at least solid tungsten carbide, liquid metal binder, and solid metal binder coexist. This step is referred to as a multi-phase-region step herein. This step can influence whether a significant metal binder gradient can be obtained in the case where substantially no complex carbide exists in the material. In one aspect, for straight WC—Co (i.e., the binder is cobalt and there is no other additives), the multi-phase-region temperature range is 1275° C. to 1325° C. When carbides of other transitional elements such as V, Cr, Ta, Ti, and Mo, are added, the temperature the multi-phase-region temperature range will vary depending on exact content. When the metal binder of cobalt is substituted by nickel, iron or alloy, the temperature the multi-phase-region temperature range will be changed as well. If the heat treating process includes only this step, this step can be carried out in a carburizing atmosphere, and is referred to as a one-step heat treatment. Regardless, the sintered material can be free of complex carbides during any step of the heat treatment.
Another aspect of the invention is that the heat treating process can also include other one or two steps in the temperature range outside the multi-phase-region, so that the heat treatment becomes 2-step or 3-step heat treatment. The step above the multi-phase-region is referred to as liquid-binder-region step, since liquid metal binder, but no solid metal binder, coexists with WC in this step; while the treatment step below the multi-phase-region is referred to as solid-binder-region step, since solid metal binder, but no liquid metal binder, coexists with WC in this step. The specific temperature limits for these respective regions will vary with the choice of materials and relative proportions.
Another aspect of the invention is that the 2-step heat treatment can include a liquid-binder-region step followed by a multi-phase-region step. The first step can be carried out in a carburizing atmosphere. The second step can be carried out in either a) a vacuum, b) an inert gas, c) a non-carburizing and non-decarburizing atmosphere, d) a decarburizing atmosphere, or e) a carburizing atmosphere. In one aspect, the second step is carried out under a carburizing atmosphere.
In another aspect, the multi-step heat treating process can comprise a third step in solid-binder-region. In one aspect, the 3-step heat treatment can include a liquid-binder-region step, then a multi-phase-region step, followed by a solid-binder-region step. The first step can be carried out in a carburizing atmosphere. The second step can be carried out in either a) a vacuum, b) an inert gas, c) a non-carburizing and non-decarburizing atmosphere, d) a decarburizing atmosphere, or e) a carburizing atmosphere. In one aspect, the second step can be carried out in a carburizing atmosphere. The third step can be carried out in either a) a non-carburizing atmosphere including vacuum, neutral and inert or b) a decarburizing atmosphere. In one aspect, the third step can be carried out under a decarburizing atmosphere.
Optionally, the heat treating is a two step process which includes a first step of heat treating by the multi-phase-region step followed by the second step of heat treating by the solid-binder-region step. For example, heating the sintered material within a temperature range which is below the multi-phase region temperature such that solid metal binder, but no liquid metal binder, coexists with solid tungsten carbide, after heating the sintered material to the multi-phase state but without heating to form all liquid binder.
Oversaturation of carbon can result in free carbon at the surface of the material. Depending on the intended application, such free carbon may not be commercially acceptable. Therefore, an optional decarburizing step can be performed if free carbon is not desired. This can be removed by any suitable process and in one example can include maintaining the material in a heated state but which is at a temperature region of all solid. A vacuum or decarburizing atmosphere can be applied such that carbon diffuses into the material and/or is removed from the surface.
A method of preparing a functionally graded cemented tungsten carbide material can comprise obtaining sintered cemented tungsten carbide of tungsten carbide, a metal binder and optional additives and heat treating the sintered material via a one- or multi-step heat treating process. As described herein, the heat treating process include at least a step that heats the sintered material in the temperature range of multi-phase-region, in which temperature range at least solid tungsten carbide, liquid metal binder, and solid metal binder coexist. Additionally, the material, after the heat treating step, comprises a surface layer with lower content of metal binder than that of the nominal value of the metal binder content in the bulk of the material.
In one embodiment, a functionally graded cemented tungsten carbide material can be manufactured by any of the heat treating processes described herein. In one aspect, the functionally graded cemented tungsten carbide material can be manufactured by a 1-step heat treating process. In another aspect, the functionally graded cemented tungsten carbide material can be manufactured by a 2-step heat treating process. In still another aspect, the functionally graded cemented tungsten carbide material can be manufactured by a 3-step heat treating process.
As discussed herein, the present materials can have superior properties compared to materials not formed by the present methods. In one aspect, the functionally graded cemented tungsten carbide can comprise a hard surface layer and a tough core, in which the hardness of the surface is higher than that of the center of the interior by at least 30 Vickers hardness number using standard Vickers hardness testing method under 1 to 50 kilogram load. Furthermore, in some cases, the functionally graded cemented tungsten carbide can be substantially free of graphite (i.e. free carbon), and in many cases completely free of graphite. In other alternative, free-carbon can be left in the microstructure in order to reach deeper into the material. Also, using the methods described herein, the functionally graded cemented tungsten carbide material can have an interior (deeper than the surface layer gradient) metal binder content which is near nominal (e.g. within 5-10% of nominal). Herein, “nominal” refers to the average bulk content (i.e. total binder per total material).
Another aspect is that the heat treatment can be carried out at a pressure ranging from near-vacuum to above the atmospheric pressure, preferably between 10 torr and 100 MPa.
Yet another aspect is that the heat treating process can be carried out as an added step to the standard sintering cycle without removing the specimens from the furnace. In other words, the desired FGM cemented tungsten carbide material can be produced in one thermal cycle from powder. This is possible because of the kinetic rate of the binder metal gradient formation is sufficiently fast. A separate treatment procedure may also be used if so desired due to other non-technical reasons.
Generally, a metal binder gradient is considered to be formed in the multi-phase-region step in heat treatment. Although all details of this mechanism are not fully understood and without being bound to the following observations, it appears that the mechanism of metal binder gradient formation is based on the following two principles:
The ternary phase diagram of W—Co—C system, as shown in
Without intending to be bound by any particular theory, the following observations regarding the mechanism of a Co gradient in the multi-phase-region step of heat treatment can be summarized as follows:
Surface carburization=>
Solid Co in surface region partially or totally transforms to liquid=>
Liquid Co in surface region increase=>
Balance of liquid Co distribution between surface and core regions breaks=>
Liquid Co migrates from surface region to core region=>
Co gradient forms.
Given the above mechanism, the general expected process is as follows. For example, for a WC-10 wt % Co specimen with a stoichiometric C content (5.53 wt % C), to be carburized at 1300° C., the C and Co contents are uniform throughout the specimen before carburization begins. Thus, the volume fraction of liquid Co phase in the surface region is equal to that in the core region. In other words, the distribution of liquid Co phase within the specimen is balanced between the surface and the core. During the carburization process, the C content in the surface region increases, leading to the increase of the volume fraction of liquid Co phase in the surface region. The higher volume fraction of liquid Co phase in the surface region breaks the balance of the distribution of liquid Co phase between the surface region and the core region, giving rise to the migration of the liquid Co phase from the surface region towards the core region and thus resulting in the formation of Co gradient with reduced Co content in the surface region.
It can be noted, however, the above descriptions of the metal binder migration addresses the thermodynamic direction of the change. The final gradient in a product also depends on the control of the kinetics of the processes including carbon diffusion and liquid migration.
The experiments using 1-step heat treating process showed that the thickness of obtained Co gradients is usually less than 200 μm. This limited thickness of Co gradient is attributed to the limited depth of carbon diffusion into the product by 1-step heat treatment. In the 1-step heat treatment, the carbon diffusion process and the cobalt gradient formation process are coupled with each other. In other words, Co gradient frontier matches along with the carbon diffusion frontier. As carbon diffusion proceeds, the volume fraction of liquid Co content near the surface layer decreases which in turn dramatically reduces the diffusion flux of carbon and the advance of graded layer. Thus, the heat treatment can involve diffusion, phase transformation and liquid migration and other unit processes.
However, for many applications, especially for rock drilling, thicker gradients may be needed for significant gains in performance. Therefore, a 2-step heat treatment is devised to make thicker gradients, via decoupling the carbon diffusion and cobalt gradient formation so as to overcome the limitation of carbon diffusion depth in 1-step heat treatment.
In one aspect, the first step can be a liquid-binder-region step, of the 2-step heat treatment and can be carried out in a carburizing atmosphere at a temperature above the temperature range of multi-phase-region. At this temperature, all metal binder exists in liquid state, so carbon content increase in the surface region will not significantly increase the amount of liquid metal binder phase and drive liquid metal binder to migrate inwards resulting in the decrease of metal binder content at the surface. Thus, the depth of carbon diffusion in this step can be very large.
In one aspect, the second step can be a multi-phase-region step, of the 2-step heat treatment. As soon as the temperature is lowered down to the multi-phase-region temperature range, part of the liquid metal binder in both the surface region and the core region will transform to solid. More liquid metal binder will be in the surface region because the surface region has higher carbon content. This breaks the balance of liquid metal binder distribution between the surface region and the core region, causing the migration of liquid metal binder from the surface towards the core, thus forming a metal binder gradient between the surface and the core. In this way, the final depth of metal binder gradient is equal to the very large depth of carbon diffusion obtained in the first step.
The experiments using 2-step heat treatment showed that the thickness of obtained metal binder gradients is usually less than 3000 μm. Further increase in gradients' thickness often results in the occurrence of a surface layer with free graphite, which limits the thickness of gradient layer without free graphite to be 200 to 3000 μm.
In order to further increase the thickness of gradient without free graphite, a 3-step heat treatment is devised, via adding a third step to the 2-step heat treating process to remove free graphite.
The third step can be a solid-binder-region step in the 3-step heat treatment, which can be carried out at a temperature below the temperature range of multi-phase-region. At this temperature, all binder exists in solid state. After holding the sintered material in a decarburizing atmosphere for a sufficient period of time, the free graphite is found to disappear. Since there is no liquid metal binder at this step, the metal binder gradient formed before this step is found to be preserved. Therefore, very thick Co gradients without free graphite can be made using 3-step heat treating process. In one aspect, the resultant thickness can be over 2000 μm. In fact, there is no limit to the maximum thickness of the gradient. Depending on the application of the material and the actual dimension of a component, thickness of the gradient may vary from 50 to 5000 microns or even greater.
It is worth pointing out that the mechanism of the well-known DP carbide process to make similar FGM WC—Co with cobalt-depleted surface is different from this invention. In DP carbide process, η phase existed before and after carbonization heat treatment in the core region, while the η phase in the surface region was totally consumed by the carbonization reaction
The release of liquid Co at surface region via the above reaction drives the liquid Co to migrate inwards and results in a Co-depleted surface.
For the samples used in the present process, no η phase existed before and after heat treatment, indicating a different mechanism of forming Co gradient in this process as discussed in the previous part.
The functionally graded cemented tungsten carbide material can be particularly suitable for a variety of applications including abrasive tools, wear parts, consumer products and the like. For example, the functionally graded cemented tungsten carbide material can be especially useful for compacts often used in rock drilling. Rock drilling including drilling wells for crude oil and/or natural gas, drilling for mining of metallic minerals, coal, or other natural deposits, and drilling or digging or crushing tools for construction of buildings or road working. Tungsten carbide tipped saw blades, stone working tools, and other home improvement tools are examples of these tools. Compacts can be used to form a variety of configurations such as, but not limited to, dome, chisel, tile, and other types of drilling or cutting or crushing tools of various geometric shapes, extraction bits, roof bits, and the like.
The functionally graded cemented tungsten carbide material can also be integrated into a high performance metal machining tool such as, but not limited to, twist drills, turning bits (lath), indexable turning inserts (lath), end mills, reamers, burrs and the like. Such tools can be suitable for machining and working metal alloys such as, but not limited to, steel, nickel, aluminum, titanium, copper, refractory metals and their alloys, etc, ceramics, and other soft or hard materials. Such tools can also be suitable for machining and working non-metallic materials including but not limited to composite materials such as, but not limited to carbon fiber reinforced polymer (CFRP), glass fiber reinforced composite, metal matrix composites, ceramic matrix composites, and other such materials.
The functionally graded cemented tungsten carbide material can also be advantageously incorporated into various engineered wear parts. Non-limiting examples of such wear parts can include mechanical seals, punches, dies, drawing tools, stamping tools, forging tools, bearings, water jet cutting nozzles, automotive parts, turbine blades, high speed mixers, and the like. The functionally graded cemented tungsten carbide material can be brazed, welded, mechanically secured (e.g. via latches, pins, detents, etc), or otherwise attached to a corresponding tool substrate. However, in some cases, the functionally graded cemented tungsten carbide material can be formed integrally with the tool substrate.
Another application for these functionally graded WC—Co materials is as metal machining milling inserts with or without ceramic coatings. One of the common issues of milling inserts is the formation of thermal fatigue cracks, or heat checking cracks, which tend to form along the edge of cutting tools in an equal distance periodic pattern, i.e. one crack for each interval of a specific distance. Heat checking problems can be lessened by using the functionally graded WC—Co as the substrate, because less cobalt content on the surface would enhance the thermal conductivity of the material and reduce thermal stresses.
Although industrial applications can benefit from the unique wear resistance and toughness of these materials, the functionally graded cemented tungsten carbide material can also be incorporated into a variety of consumer products. Non-limiting examples of such consumer products include jewelry (e.g. rings, wedding bands, watch band links, necklaces, earrings, etc), household goods (e.g. cookware surfacing, etc.), and decorative items.
The functionally graded cemented tungsten carbide material can also serve as a substrate for additional coatings. For example, cemented tungsten carbide tools for metal machining tools are mostly coated with ceramic materials such as TiN, TiC, Al2O3, CrN, TiCN, and other suitable hard ceramic materials and combinations of them in alternating layers. The coating materials also include synthetic diamond or cubic boron nitride. The thickness of individual coating layers could range from a few nanometers to tens of micrometers. Such coatings can be deposited by any suitable technique such as, but not limited to, chemical vapor deposition, physical vapor deposition, atomic layer deposition, and the like. Corresponding coating materials are not particularly limited, although inorganic and hard materials such as nitrides, carbides, metal oxides, and diamond can be of particular interest. Non-limiting examples of coating materials can include TiN, TiC, TiCN, TiAlN, Al2O3, diamond (including amorphous diamond, polycrystalline diamond and monocrystalline diamond).
The functionally graded cemented tungsten carbide provides a superior substrate than conventional cemented tungsten carbide to these coatings because of increased adhesion between the substrate and coatings. A higher cobalt content of the substrate, corresponds to a lower adhesion between the substrate and the coating because there is a larger thermal mismatch between the cobalt and the ceramic coating. The cobalt can also react with coating material such as diamond. The functionally graded cemented tungsten carbide provide a substrate with less cobalt on the surface without reducing the cobalt content of the bulk of the substrate which is important for maintaining impact resistance of the cutting tools.
The following examples illustrate a number of embodiments of the present compositions, systems, and methods. However, it is to be understood that the following are only exemplary or illustrative of the application of the principles of the present compositions, systems, and methods. Numerous modifications and alternative compositions, methods, and systems may be devised by those skilled in the art without departing from the spirit and scope of the present systems and methods. The appended claims are intended to cover such modifications and arrangements. Thus, while the present compositions, systems, and methods have been described above with particularity, the following examples provide further detail in connection with what are presently deemed to be the acceptable embodiments.
The conventionally liquid-phase-sintered homogenous WC—Co was used for 1-step heat treatment test. The nominal Co content was 13 wt %. The C content was sub-stoichiometric.
The multi-phase-region step of the 1-step heat treatment was conducted in a carburizing atmosphere of mixed methane (CH4) and hydrogen (H2), holding at 1300° C. for 3 hours. The (PH2)2/PCH4 in the gas mixture was 50 and the total pressure was 1 bar.
After treatment, the cross-sections of specimen was polished and etched with Murakami's reagent for 10 s to determine if there were any Co3W3C (η) phase or free graphite present. Cobalt concentration profile perpendicular to the surface was measured using the Energy Dispersive Spectroscopy (EDS) technique. Each data point of the cobalt content is an averaged value obtained by scanning a 10 μm by 140 μm rectangular area on the polished surface. The standard variation of the data is less than 10% of the measured cobalt content.
The obtained Co content profile, as shown in
The same material as in Example 1 was used for 2-step heat treatment test.
The first step of a 2-step heat treatment was a liquid-Co-region step and was conducted in a carburizing atmosphere of mixed methane (CH4) and hydrogen (H2), holding at 1370° C. for 0.5 hours. The (PH2)2/PCH4 in the gas mixture was 900 and the total pressure was 1 bar.
The second step was a 3-phase-region step and was conducted in a carburizing atmosphere of mixed methane (CH4) and hydrogen (H2), holding at 1300° C. for 1 hours. The (PH2)2/PCH4 in the gas mixture was 50 and the total pressure was 1 bar.
The analysis method was the same as in Example 1. The obtained Co content profile, as shown in
The same material as in Example 1 was used for 3-step heat treatment test.
The first step was a liquid-Co-region step and was conducted in a carburizing atmosphere of mixed methane (CH4) and hydrogen (H2), holding at 1370° C. for 25 minutes. The (PH2)2/PCH4 in the gas mixture was 50 and the total pressure was 1 bar.
The second step was a 3-phase-region step and was conducted in a carburizing atmosphere of mixed methane (CH4) and hydrogen (H2), holding at 1290° C. for 1 hour. The (PH2)2/PCH4 in the gas mixture was 50 and the total pressure was 1 bar.
The third step was a solid-Co-region step and was conducted in a de-carburizing atmosphere of mixed methane (CH4) and hydrogen (H2), holding at 1230° C. for 12 hour. The (PH2)2/PCH4 in the gas mixture was 1300 and the total pressure was 1 bar.
The analysis method was the same as in Example 1. The obtained Co content profile, as shown in
The same material as in Example 1 was used for 2-step heat treatment test.
The first step of a 2-step heat treatment was a liquid-Co-region step and was conducted in a carburizing atmosphere of mixed methane (CH4) and hydrogen (H2), holding at 1370° C. for 0.5 hours. The (PH2)2/PCH4 in the gas mixture was 900 and the total pressure was 1 bar.
The second step was a 3-phase-region step and was conducted in a carburizing atmosphere of mixed methane (CH4) and hydrogen (H2), holding at 1300° C. for 1 hour. The (PH2)2/PCH4 in the gas mixture was 50 and the total pressure was 1 bar or slightly higher than 1 bar.
The analysis method was the same as in Example 1. The obtained Co content profile, as shown in
The same material as in Example 1 was used with a 2-step heat treatment test.
The first step of a 2-step heat treatment was a liquid-Co-region step and was conducted in a carburizing atmosphere of mixed methane (CH4) and hydrogen (H2), holding at 1370° C. for a total of 1 hour. The (PH2)2/PCH4 was varied at different values and held at the different values for varying amount of time, ranging from one minute to several tens of minutes. Pulsed techniques can be used to control and manipulate the atmosphere conditions in order to control the total amount of carbon input as well as the depth of diffusion of carbon. The total pressure was maintained at 1 bar or slightly higher than 1 bar.
The second step was a 3-phase-region step and was conducted in a carburizing atmosphere of mixed methane (CH4) and hydrogen (H2), holding at 1300° C. for 1 hour. The total pressure of the atmosphere was 1 bar or moderately higher than 1 bar.
The analysis method was the same as in Example 1. The obtained Co content profile, as shown in
While the disclosure has been described with reference to certain preferred embodiments, those skilled in the art will appreciate that various modifications, changes, omissions, and substitutions can be made without departing from the spirit of the disclosure. It is intended, therefore, that the invention be limited only by the scope of the following claims.
This application is a continuation-in-part of U.S. application Ser. No. 12/621,629, filed Nov. 19, 2009 and which is incorporated herein by reference.
| Number | Name | Date | Kind |
|---|---|---|---|
| 3660050 | Iler et al. | May 1972 | A |
| 4610931 | Nemeth et al. | Sep 1986 | A |
| 4743515 | Fischer et al. | May 1988 | A |
| 4820482 | Fischer et al. | Apr 1989 | A |
| 4830930 | Taniguchi et al. | May 1989 | A |
| 5181953 | Nakano et al. | Jan 1993 | A |
| 5279901 | Akerman et al. | Jan 1994 | A |
| 5283030 | Nakano et al. | Feb 1994 | A |
| 5286549 | Hartzell et al. | Feb 1994 | A |
| 5401461 | Hartzell et al. | Mar 1995 | A |
| 5413869 | Hartzell et al. | May 1995 | A |
| 5418049 | Drougge | May 1995 | A |
| 5453241 | Akerman et al. | Sep 1995 | A |
| 5541006 | Conley | Jul 1996 | A |
| 5549980 | Ostlund et al. | Aug 1996 | A |
| RE35538 | Akesson et al. | Jun 1997 | E |
| 5856626 | Fischer et al. | Jan 1999 | A |
| 5880382 | Fang et al. | Mar 1999 | A |
| 6063502 | Sue et al. | May 2000 | A |
| 6214079 | Kear et al. | Apr 2001 | B1 |
| 6638474 | Liu et al. | Oct 2003 | B2 |
| 6641918 | Sherman et al. | Nov 2003 | B1 |
| 6869460 | Bennett et al. | Mar 2005 | B1 |
| 7157148 | Takai et al. | Jan 2007 | B2 |
| 20020194955 | Fang et al. | Dec 2002 | A1 |
| 20050126335 | Norgren et al. | Jun 2005 | A1 |
| 20050276717 | Fang | Dec 2005 | A1 |
| 20060040104 | Wort et al. | Feb 2006 | A1 |
| 20060266559 | Keshavan et al. | Nov 2006 | A1 |
| 20070214913 | Fang | Sep 2007 | A1 |
| 20080010905 | Eyre | Jan 2008 | A1 |
| 20100101368 | Fang | Apr 2010 | A1 |
| Number | Date | Country |
|---|---|---|
| 0500514 | Aug 1992 | EP |
| 02-221353 | Sep 1990 | JP |
| 03-115571 | May 1991 | JP |
| 2004183075 | Jul 2004 | JP |
| WO 2010062649 | Jun 2010 | WO |
| Entry |
|---|
| American Society for Testing and Materials; “Standard Test Method for Apparent Porosity in Cemented Carbides”; Annual Book of ASTM Standards, B276-91;1996. |
| Miyamoto et al.; “Functionally Graded Materials: Design, Processing and Applications”; Book, Kluwer Academic Publishers, 1999. |
| Put et al.; “Functionally Graded WC-Co materials Produced by Electrophoretic Deposition”; Scipta Materialia 45 (2001) 1139-1145. |
| Eso et al.; University of Utah Department of Metallurgical Engineering: A New Method for Making Functionally Graded WC-Co Composites via Liquid Phase Sintering: paper presented at PM Tec2 Conference in Chicago, IL, Jun. 2004. |
| Eso, Oladapo O.; University of Utah Department of Metallurgical Engineering: Sintering Studies of Functionally Graded WC-Co Composites, handout distributed at PM Tec 2 Conference in Chicago, IL, Jun. 2004. |
| Eso et al.,; University of Utah Department of Metallurgical Engineering: Liquid Phase Sintering of Functionally Graded WC-Co Composites: to appear in Int. J. Refractory Metals and Hard Materials, 2005. |
| U.S. Appl. No. 12/621,629, filed Nov. 19, 2009; Zhigang Z. Fang; office action dated May 3, 2012. |
| U.S. Appl. No. 12/621,629, filed Nov. 19, 2009; Zhigang Z. Fang; office action dated Sep. 25, 2012. |
| Xiao Yi-feng, et al.; “Effects of carburizing process on gradient structure and hardness of WC-Co gradient cemented carbides” The Chinese Journal of Nonferrous Metals, vol. 18, No. 3, Mar. 31, 2008, pp. 465-470. |
| PCT application 09829616.3; Filing date Oct. 28, 2009; University of Utah Research Foundation; European search report mailed Nov. 29, 2013. |
| Number | Date | Country | |
|---|---|---|---|
| 20130118308 A1 | May 2013 | US |
| Number | Date | Country | |
|---|---|---|---|
| Parent | 12621629 | Nov 2009 | US |
| Child | 13449062 | US |
