Patent Application
20190203541
Embodiments of the present disclosure relate generally to polycrystalline hard materials, cutting elements comprising such hard materials, earth-boring tools incorporating such cutting elements, and method of forming such materials, cutting elements, and tools.
Earth-boring tools for forming wellbores in subterranean earth formations may include a plurality of cutting elements secured to a body. For example, fixed-cutter earth-boring rotary drill bits (also referred to as “drag bits”) include a plurality of cutting elements that are fixedly attached to a bit body of the drill bit. Similarly, roller-cone earth-boring rotary drill bits include cones that are mounted on bearing pins extending from legs of a bit body such that each cone is capable of rotating about the bearing pin on which the cone is mounted. A plurality of cutting elements may be mounted to each cone of the drill bit.
The cutting elements used in earth-boring tools often include polycrystalline diamond compact (often referred to as “PDC”) cutters, which are cutting elements that include a polycrystalline diamond (PCD) material. Such polycrystalline diamond cutting elements are formed by sintering and bonding together relatively small diamond grains or crystals under conditions of high pressure and high temperature, conventionally in the presence of a catalyst (such as cobalt, iron, nickel, or alloys and mixtures thereof), to form a layer of polycrystalline diamond material on a cutting element substrate. These processes are often referred to as high pressure/high temperature (or “HPHT”) processes. Catalyst material is mixed with the diamond grains to reduce the amount of oxidation of diamond by oxygen and carbon dioxide during an HPHT process and to promote diamond-to-diamond bonding.
The cutting element substrate may include a cermet material (i.e., a ceramic-metal composite material) such as cobalt-cemented tungsten carbide. In such instances, the cobalt (or other catalyst material) in the cutting element substrate may be drawn into the diamond grains or crystals during sintering and serve as a catalyst material for forming a diamond table from the diamond grains or crystals. In other methods, powdered catalyst material may be mixed with the diamond grains or crystals prior to sintering the grains or crystals together in an HPHT process.
Upon formation of a diamond table using an HPHT process, catalyst material may remain in interstitial spaces between the grains or crystals of diamond in the resulting polycrystalline diamond table. The presence of the catalyst material in the diamond table may contribute to thermal damage in the diamond table when the cutting element is heated during use, due to friction at the contact point between the cutting element and the formation.
Conventional PDC formation relies on the catalyst alloy, which sweeps through the compacted diamond feed during HPHT synthesis. Traditional catalyst alloys are cobalt-based with varying amounts of nickel, tungsten, and chromium to facilitate diamond intergrowth between the compacted diamond material. However, in addition to facilitating the formation of diamond-to-diamond bonds during HPHT sintering, these alloys also facilitate the formation of graphite from diamond during drilling. Formation of graphite can rupture diamond necking regions (i.e., grain boundaries) due to an approximate 57% volumetric expansion during the transformation. This phase transformation is known as “back-conversion” or “graphitization,” and typically occurs at temperatures approaching 600° C. to 1,000° C., which temperatures may be experienced at the portions of the PDC contacting a subterranean formation during drilling applications. This mechanism, coupled with mismatch of the coefficients of thermal expansion of the metallic phase and diamond, is believed to account for a significant part of the failure of conventional PDC cutters to meet general performance criteria known as “thermal stability.”
To reduce problems associated with different rates of thermal expansion and with back-conversion in polycrystalline diamond cutting elements, so-called “thermally stable” polycrystalline diamond (TSD) cutting elements have been developed. A TSD cutting element may be formed by leaching the catalyst material (e.g., cobalt) out from interstitial spaces between the diamond grains in the diamond table using, for example, an acid. Substantially all of the catalyst material may be removed from the diamond table, or only a portion may be removed. TSD cutting elements in which substantially all catalyst material has been leached from the diamond table have been reported to be thermally stable up to temperatures of about 1,200° C. It has also been reported, however, that fully leached diamond tables are relatively more brittle and substantially more vulnerable to failure under shear, compressive, and tensile stresses and impact than are non-leached diamond tables. In an effort to provide cutting elements having PDC diamond tables that are more thermally stable relative to non-leached diamond tables, but that are also relatively less brittle and vulnerable to shear, compressive, and tensile stresses relative to fully leached diamond tables, cutting elements have been provided that include a PDC diamond table in which the catalyst material has been leached from only a portion of the diamond table, for example, to a depth within the diamond table from the cutting face and a part of the side of the diamond table.
In some embodiments, a polycrystalline diamond compact includes a polycrystalline diamond material having a plurality of grains of diamond bonded to one another by inter-granular bonds and an ordered intermetallic gamma prime (γ′) or κ-carbide phase disposed within interstitial spaces between the inter-bonded diamond grains. The ordered intermetallic gamma prime (γ′) or κ-carbide phase includes a Group VIII metal, aluminum, and a stabilizer.
A method of forming polycrystalline diamond includes subjecting diamond particles in the presence of a metal material comprising a Group VIII metal and aluminum to a pressure of at least 4.5 GPa and a temperature of at least 1,000° C. to form inter-granular bonds between adjacent diamond particles, cooling the diamond particles and the metal material to a temperature below 500° C., and forming an ordered intermetallic gamma prime (γ′) or κ-carbide phase adjacent the diamond particles. The ordered intermetallic gamma prime (γ′) or κ-carbide phase includes a Group VIII metal, aluminum, and a stabilizer.
An earth-boring tool includes a bit body and a polycrystalline diamond compact secured to the bit body. The polycrystalline diamond compact includes a polycrystalline diamond material having a plurality of grains of diamond bonded to one another by inter-granular bonds and an ordered intermetallic gamma prime (γ′) or κ-carbide phase disposed within interstitial spaces between the inter-bonded diamond grains. The ordered intermetallic gamma prime (γ′) or κ-carbide phase includes a Group VIII metal, aluminum, and a stabilizer.
While the specification concludes with claims particularly pointing out and distinctly claiming what are regarded as embodiments of the present disclosure, various features and advantages of embodiments of the disclosure may be more readily ascertained from the following description of example embodiments of the disclosure when read in conjunction with the accompanying drawings, in which:
The illustrations presented herein are not meant to be actual views of any particular material, apparatus, system, or method, but are merely idealized representations employed to describe certain embodiments. For clarity in description, various features and elements common among the embodiments may be referenced with the same or similar reference numerals.
As used herein, the term “substantially” in reference to a given parameter, property, or condition means and includes to a degree that one skilled in the art would understand that the given parameter, property, or condition is met with a small degree of variance, such as within acceptable manufacturing tolerances. For example, a parameter that is substantially met may be at least about 90% met, at least about 95% met, or even at least about 99% met.
As used herein, any relational term, such as “first,” “second,” “over,” “top,” “bottom,” “underlying,” etc., is used for clarity and convenience in understanding the disclosure and accompanying drawings and does not connote or depend on any specific preference, orientation, or order, except where the context clearly indicates otherwise.
As used herein, the term “particle” means and includes any coherent volume of solid matter having an average dimension of about 500 μm or less. Grains (i.e., crystals) and coated grains are types of particles. As used herein, the term “nanoparticle” means and includes any particle having an average particle diameter of about 500 nm or less. Nanoparticles include grains in a polycrystalline hard material having an average grain size of about 500 nm or less.
As used herein, the term “hard material” means and includes any material having a Knoop hardness value of about 3,000 Kgf/mm2 (29,420 MPa) or more. Hard materials include, for example, diamond and cubic boron nitride.
As used herein, the term “inter-granular bond” means and includes any direct atomic bond (e.g., covalent, metallic, etc.) between atoms in adjacent grains of material.
As used herein, the terms “nanodiamond” and “diamond nanoparticles” mean and include any single or polycrystalline or agglomeration of nanocrystalline carbon material comprising a mixture of sp-3 and sp-2 bonded carbon wherein the individual particle or crystal whether singular or part of an agglomerate is primarily made up of sp-3 bonds. Commercial nanodiamonds are typically derived from detonation sources (UDD) and crushed sources and can be naturally occurring or manufactured synthetically. Naturally occurring nanodiamond includes the natural lonsdaleite phase identified with meteoric deposits.
As used herein, the term “polycrystalline hard material” means and includes any material comprising a plurality of grains or crystals of the material that are bonded directly together by inter-granular bonds. The crystal structures of the individual grains of polycrystalline hard material may be randomly oriented in space within the polycrystalline hard material.
As used herein, the term “polycrystalline compact” means and includes any structure comprising a polycrystalline hard material comprising inter-granular bonds formed by a process that involves application of pressure (e.g., compaction) to the precursor material or materials used to form the polycrystalline hard material.
As used herein, the term “earth-boring tool” means and includes any type of bit or tool used for drilling during the formation or enlargement of a wellbore and includes, for example, rotary drill bits, percussion bits, core bits, eccentric bits, bi-center bits, reamers, mills, drag bits, roller-cone bits, hybrid bits, and other drilling bits and tools known in the art.
As shown in
For example, in some embodiments, the polycrystalline hard material 102 may include larger grains 106 and smaller grains 108. The larger grains 106 and/or the smaller grains 108 may have average particle dimensions (e.g., mean diameters) of less than 0.5 mm (500 μm), less than 0.1 mm (100 μm), less than 0.01 mm (10 μm), less than 1 μm, less than 0.1 μm, or even less than 0.01 μm. That is, the larger grains 106 and smaller grains 108 may each include micron-sized particles (grains having an average particle diameter in a range from about 1 μm to about 500 μm (0.5 mm)), submicron-sized particles (grains having an average particle diameter in a range from about 500 nm (0.5 μm) to about 1 μm), and/or nanoparticles (particles having an average particle diameter of about 500 nm or less). In some embodiments, the larger grains 106 may be micron-sized diamond particles, and the smaller grains 108 may be submicron diamond particles or diamond nanoparticles. In some embodiments, the larger grains 106 may be submicron diamond particles, and the smaller grains 108 may be diamond nanoparticles. In other embodiments, the grains of the polycrystalline hard material 102 may have a monomodal grain size distribution. The polycrystalline hard material 102 may include direct inter-granular bonds 110 between the grains 106, 108, represented in
As used herein, the term “grain size” means and includes a geometric mean diameter measured from a two-dimensional section through a bulk material. The geometric mean diameter for a group of particles may be determined using techniques known in the art, such as those set forth in Ervin E. Underwood, QUANTITATIVE STEREOLOGY, 103-105 (Addison-Wesley Publishing Company, Inc., 1970), the disclosure of which is incorporated herein in its entirety by this reference. As known in the art, the average grain size of grains within a microstructure may be determined by measuring grains of the microstructure under magnification. For example, a scanning electron microscope (SEM), a field emission scanning electron microscope (FESEM), or a transmission electron microscope (TEM) may be used to view or image a surface of a polycrystalline hard material 102 (e.g., a polished and etched surface of the polycrystalline hard material 102). Commercially available vision systems are often used with such microscopy systems, and these vision systems are capable of measuring the average grain size of grains within a microstructure.
Referring again to
The stabilizer in the intermetallic or carbide material 112 may be any material formulated to cause the intermetallic or carbide material 112 to form a gamma prime or κ-carbide phase. For example, the stabilizer may include titanium (Ti), nickel (Ni), tungsten (W), or carbon (C). A gamma prime Co3Al phase within a binary Co—Al system is a metastable ordered metallic phase. Under ambient temperature and pressure conditions, the Co3Al structure is not stable and typically requires another element such as Ti, Ni, W, or C to stabilize the structure. That is, the intermetallic or carbide material 112 may form a solution at Co sites of the Co3Al structure, resulting in a (Co3-n,Wn)Al phase, a (Co3-n,Nin)Al phase, a (Co3-n,Wn)Al phase, or a Co3Al Cm phase, where n and m are any positive numbers between 0 and 3, and 0 and 1, respectively.
In some embodiments, the intermetallic or carbide material 112 may be substantially free of elemental forms of Group VIII metals, such as iron, cobalt, and nickel. These metals in elemental form are known to be catalytic to the reactions that form and decompose diamond. Therefore, if the intermetallic or carbide material 112 does not contain an appreciable amount of these metals in elemental form, the polycrystalline hard material 102 may be relatively more stable than polycrystalline hard materials that contain greater quantities of these metals in elemental form.
At least a portion of the intermetallic or carbide material 112 may exhibit a face-centered cubic (FCC) structure of space group Pm-3m (221) that remains stable even at room temperature. The stabilizer (e.g., Ti, Ni, W, or C) may occupy the (0,0,0), (0,½,½), or the (½,½,1/2) lattice positions of the FCC structure. The stabilizer may render the gamma prime or κ-carbide phase stable at ambient pressure and temperature conditions. Without the stabilizer, the gamma prime and κ-carbide phases may not be stable at ambient pressure and temperature conditions.
In a volume of polycrystalline hard material, the hard material typically occupies less than 100% of the total volume due to the inclusion of interstitial spaces. The polycrystalline hard material 102 may include at least about 90% hard material by volume, such as at least about 94% hard material by volume, at least about 95% hard material by volume, at least about 96% hard material by volume, or even at least about 97% hard material by volume. In general, higher volume fractions of hard materials may exhibit better cutting performance.
Embodiments of cutting elements 100 (
Referring to
The disk 312, if present, or other metallic material may include one or more elements of the intermetallic or carbide material 112 (
The disk 312 or other metallic material may be formulated to include an approximately 3:1 molar ratio of cobalt to aluminum, such that a majority of the cobalt and aluminum will form a Co3Al phase during sintering. For example, the disk 312 or other metallic material may include from about 0.1 mol % to about 24 mol % aluminum, and from about 0.3 mol % to about 50 mol % aluminum. In some embodiments, the disk 312 or other metallic material may include from about 1.0 mol % to about 15 mol % aluminum, and from about 3.0 mol % to about 45 mol % aluminum. The disk 312 or other metallic material may include other elements, such as the stabilizer or an inert element (i.e., an element that does not form a part of the crystal structure of the gamma prime or κ-carbide phase of the intermetallic or carbide material 112 and that is non-catalytic toward the grains 106, 108). The disk 312 or other metallic material may exhibit a melting point of less than about 1,100° C. at atmospheric pressure, less than about 1,300° C. at atmospheric pressure, or less than about 1,500° C. at atmospheric pressure.
The container 304 with the hard particles 302 therein may be subjected to an HPHT sintering process to form a polycrystalline hard material (e.g., the polycrystalline hard material 102 shown in
The HPHT sintering process may cause the formation of inter-granular (e.g., diamond-to-diamond) bonds between the hard particles 302 so as to form a polycrystalline compact from the hard particles 302. If a substrate 104 is within the container 304, catalyst material (e.g., cobalt) may sweep through the hard particles 302 from the substrate 104 and catalyze the formation of inter-granular bonds. In some embodiments, the hard particles 302 may be admixed or coated with the catalyst material, such that the catalyst material need not sweep through the volume of hard particles 302.
The HPHT sintering process may also cause elements within the container 304 to transform into an ordered intermetallic gamma prime (γ′) or κ-carbide phase adjacent the diamond particles. For example, the intermetallic or carbide material 112 may form from cobalt sweeping or diffusing through the hard particles 302 in combination with aluminum and a stabilizer. The aluminum and/or the stabilizer may also sweep through the hard particles 302 from the disk 312 (if present). Alternatively, the aluminum and/or the stabilizer may be placed into contact with the hard particles 302 before sintering. For example, particles of the aluminum and/or the stabilizer may be dispersed throughout the hard particles 302 before the HPHT sintering begins, or the hard particles 302 may be coated with the aluminum and/or the stabilizer. The material in the γ′ or κ-carbide phase may at least partially encapsulate or coat surfaces of the hard particles 302 during the HPHT sintering process, such that when the material cools, surfaces of the grains 106, 108 are at least partially covered with the intermetallic or carbide material 112 (see
The stabilizer may be dissolved in a mixture of cobalt and aluminum during the HPHT sintering process or during a processing step prior to HPHT. The material may form a stabilized Co3Al phase structure having an FCC L12 (space group Pm-3m) ordered/disordered structure, such as a (Co3-nTin)3Al phase, a (Co3-nNin)Al phase, or a Co3-nWn)3Al phase. For the case of carbon acting as a stabilizer, the Co and Al may occupy similar sites as the FCC L12 order/disorder structure, mentioned above, with the carbon occupying the octahedral lattice position having a stoichiometry of Co3Al Cm. This structure is an E21 (space group Pm-3m) ordered/disorder carbide structure differing from the traditional γ′ having the order/disorder FCC L12 structure.
During liquid-phase sintering of diamond, the alloy material may dissolve an appreciable amount of carbon from the diamond or other carbon phase. For the FCC L12 structure, atoms of Ti, Ni, or W may stabilize the Co3Al ordered/disorder structure on the corner or face centered lattice sites. Additionally, a carbon atom may occupy the octahedral site of an FCC-E21 structure, which may remain stable even at room temperature.
The container 304 and the material therein may be cooled to a temperature below 500° C., such as to a temperature below 250° C. or to room temperature, while maintaining at least a portion of the alloy material in the γ′ or κ-carbide phase. The stabilizer may keep the γ′ or κ-carbide phase thermodynamically stable as the material cools, such that the γ′ or κ-carbide phase may continue to prevent conversion of the grains 106, 108 and degradation of the polycrystalline hard material 102.
The presence of the intermetallic or carbide material 112 in the γ′ or κ-carbide phase may render the resulting polycrystalline hard material 102 thermally stable without the need for leaching or otherwise removing the catalyst material 114 from the monolithic polycrystalline hard material 102. For example, all or substantially all the cobalt or other catalyst material adjacent the hard particles 302 during HPHT sintering may be converted into the intermetallic or carbide material 112 in the γ′ or κ-carbide phase. In certain embodiments, the catalyst material 114 may not be present after the HPHT sintering process, because the catalyst material used in the sintering process may be entirely or substantially incorporated into the intermetallic or carbide material 112.
Use of an intermetallic or carbide material 112 as described herein may impart certain benefits to polycrystalline hard materials 102. For example, the intermetallic or carbide material 112, stabilized in a γ′ or κ-carbide phase, may exhibit inert (i.e., non-catalytic) behavior toward the polycrystalline hard material 102, even at elevated temperatures, such as above about 400° C. For example, the intermetallic or carbide material 112 may not promote carbon transformations (e.g., graphite-to-diamond or vice versa), and it may displace catalytic materials from the cutting element 100. Thus, after the polycrystalline hard material 102 has been sintered and cooled with the intermetallic or carbide material 112, further changes to the crystalline structure of the polycrystalline hard material 102 may occur at negligible rates. The cutting element 100 may exhibit significantly increased abrasion resistance and thermal stability in a range between the temperature at which back-conversion typically occurs (e.g., between 600° C. and 1,000° C. for catalysts based on Fe, Co, or Ni) and the melting temperature of the intermetallic or carbide material 112. For example, if the melting temperature of the intermetallic or carbide material 112 is 1,200° C., the cutting element 100 may be thermally and physically stable even at temperatures of 1,100° C. or higher. Thus, a drill bit with such a cutting element 100 may operate in relatively harsher conditions than conventional drill bits with lower rates of failure and costs of repair. Alternatively, a drill bit with such cutting elements 100 may exhibit lower wear of the cutting elements 100, allowing for reduced weight-on-bit for subterranean material removal of the drill bit.
Though this disclosure has generally discussed the use of alloy materials including a complex of cobalt and aluminum, other metals may be substituted for all or a portion of the cobalt or aluminum to form a stabilized non-catalytic phase.
For example, in a container 304 in which the disk 312 is a pre-alloyed binary (Co—Al) or ternary (Co—Al-M, wherein M represents a metal) foil and the substrate 104 is a W—Co substrate, tungsten from the substrate may alloy with the binary (Co—Al) or ternary (Co—Al-M) to form a Co—Al—W or Co—Al—W-M alloy, respectively. Additionally, pre-alloying with carbon in each of the above scenarios is possible prior to HPHT cell loading. In the presence of diamond, the alloy swept into the diamond grains would include Co—Al—W—C or Co—Al—W-M-C. Also, other materials may be included in the substrate, such as Cr. In such embodiments, the alloy would include Co—Al—W—Cr—C, or, in the presence of diamond, Co—Al—W—Cr-M-C. The M may be replaced with a suitable element for stabilizing the γ′ or κ-carbide ordered phase. For instance, the presence of Ni promotes the segregation of Al to the diamond interface and stabilizes the γ′ or κ-carbide phase as (Co,Ni)3Al. W and Cr appear to remain in solution, without gross carbide precipitation. Moreover, though WC may still be present at the diamond interface, W and Cr appear to remain largely in solution.
Without being bound by theory, the ordered γ′ or κ-carbide phase appears to form when atoms in the lattice of the more-plentiful element are replaced by atoms of the less-plentiful element in the intermetallic, and when the replacement atom is positioned in a regular position throughout the lattice. In contrast, a disordered γ′ or κ-carbide phase would occur when the replacement atom is substituted into the lattice, but in irregular positions. Detection of whether a lattice exhibits an ordered or a disordered configuration can be demonstrated using X-ray diffraction techniques or in detection of magnetic phases.
The ordered γ′ or κ-carbide phase can be manufactured by subjecting the intermetallic to thermodynamic conditions in which the γ′ or κ-carbide phase is stable in the ordered configuration. In a conventionally-known HPHT cycles, the temperature of the polycrystalline diamond body is typically decreased as rapidly as possible to minimize manufacturing times while avoiding cracking in the diamond layer. In some embodiments of the present disclosure, the HPHT cycle is controlled to hold the temperature of the polycrystalline diamond body, and by extension, the intermetallic phase present in the interstices between diamond grains, below an ordered-disordered transition temperature at the working pressure for a time sufficient to convert at least a portion of the intermetallic into the ordered γ′ or κ-carbide phase. In some embodiments, the intermetallic may be quenched to maintain the disordered γ′ or κ-carbide phase during the HPHT cycle.
The ordered intermetallic γ′ or κ-carbide phase may be a thermodynamically stable phase at ambient pressure and temperate, as well as at temperatures and pressures of use, for example, at temperatures and pressures experienced during downhole drilling. Without being bound by theory, it is believed that the presence of the thermodynamically stable ordered phase is beneficial to the thermal stability of the cutting tool. As the ordered γ′ or κ-carbide phase is the thermodynamically stable phase, phase transition from the disordered to the ordered phase is not expected when the cutting element is subject to the temperatures and pressures associated with use. Additionally, it is believed that the ordered γ′ or κ-carbide phase is less likely to catalyze graphitization of the diamond during usage than that of the disordered, metastable γ′ or κ-carbide phase.
The metallic materials disclosed herein, in the liquid state, may promote diamond nucleation and growth. Upon cooling, the metallic material may nucleate and grow to form the intermetallic or carbide material 112 in the γ′ or κ-carbide phase at the interface of diamond grains. The intermetallic or carbide material 112 may suppress back-conversion better than leaching of conventional PDC cutting elements because the intermetallic or carbide material 112 may be evenly distributed through the cutting element 100. In comparison, leaching typically occurs from a face of a cutting element, and therefore residual cobalt remains in portions of polycrystalline hard materials. Further, certain interstitial spaces of polycrystalline hard materials may be blocked following the HPHT sintering process, and may be inaccessible by a leaching medium. Accordingly, residual cobalt may remain within the blocked interstitial spaces of otherwise fully leached polycrystalline hard materials.
Additionally, the composition of the intermetallic or carbide material 112 may be varied to adjust its melting point. Without a significant increase in the melting point of the intermetallic or carbide material 112, an alloy of approximately 13.5% Al by weight may completely consume any residual cobalt solid solution. Thus, a cutting element 100 having such an intermetallic or carbide material 112 may be an inherently thermally stable product without leaching.
Diamond grains were placed in a container as shown in
Energy-dispersive spectroscopy (EDS) and scanning electron microscopy (SEM) were used to determine the distribution of phases in the diamond table.
Further evidence of possible growth of the Co3AlC phase from the diamond interface is the large Co3AlC crystalline peak observed in
A vertical boring mill experiment was conducted on the PDC cutting element formed in Example 1 and with a conventional unleached cutting element (i.e., a cutting element formed in the same manner, but without the cobalt-aluminum disk).
Each cutting element was held in a vertical turret lathe (“VTL”) to machine granite. Parameters of the VTL test may be varied to replicate desired test conditions. In this Example, the cutting elements were configured to remove material from a Barre white granite workpiece. The cutting elements were positioned with a 15° back-rake angle relative to the workpiece surface, at a nominal depth of cut of 0.25 mm. The infeed of the cutting elements was set to a constant rate of 7.6 mm/revolution with the workpiece rotating at 60 RPM. The cutting elements were water cooled.
The VTL test introduces a wear scar into the cutting elements along the position of contact between the cutting elements and the granite. The size of the wear scar is compared to the material removed from the granite workpiece to evaluate the abrasion resistance of the cutting elements. The respective performance of multiple cutting elements may be evaluated by comparing the rate of wear scar growth and the material removal from the granite workpiece.
Additional non-limiting example embodiments of the disclosure are described below.
A polycrystalline diamond compact comprising a polycrystalline diamond material comprising a plurality of grains of diamond bonded to one another by inter-granular bonds; and an intermetallic gamma prime (γ′) or κ-carbide phase disposed within interstitial spaces between the inter-bonded diamond grains. The gamma prime (γ′) or κ-carbide phase comprises a Group VIII metal, aluminum, and a stabilizer.
The polycrystalline diamond compact of Embodiment 1, wherein the grains of diamond comprise nanodiamond grains.
The polycrystalline diamond compact of Embodiment 1 or Embodiment 2, wherein the stabilizer comprises a material selected from the group consisting of titanium, nickel, tungsten, and carbon.
The polycrystalline diamond compact of any of Embodiments 1 through 3, wherein the gamma prime (γ′) or κ-carbide phase comprises a metastable Co3Al phase stabilized by the stabilizer.
The polycrystalline diamond compact of any of Embodiments 1 through 4, wherein the gamma prime (γ′) or κ-carbide phase comprises a metastable (CoxNi3-x)Al phase stabilized by the stabilizer.
The polycrystalline diamond compact of any of Embodiments 1 through 5, wherein the stabilizer comprises carbon.
The polycrystalline diamond compact of any of Embodiments 1 through 6, wherein the gamma prime (γ′) or κ-carbide phase exhibits an ordered face-centered cubic structure.
The polycrystalline diamond compact of any of Embodiments 1 through 7, wherein the polycrystalline diamond material is disposed over a substrate comprising the Group VIII metal.
The polycrystalline diamond compact of any of Embodiments 1 through 8, wherein the polycrystalline diamond material is substantially free of elemental iron, cobalt, and nickel.
The polycrystalline diamond compact of any of Embodiments 1 through 9, wherein the polycrystalline diamond compact comprises at least 94% diamond by volume.
The polycrystalline diamond compact of any of Embodiments 1 through 10, wherein the alloy exhibits a melting point of less than about 1,500° C. at atmospheric pressure.
The polycrystalline diamond compact of any of Embodiments 1 through 11, further comprising a catalyst material disposed in interstitial spaces between the grains of diamond, the catalyst material substantially separated from the polycrystalline diamond material by the intermetallic gamma prime (γ′) or κ-carbide phase.
The polycrystalline diamond compact of any of Embodiments 1 through 12, wherein the gamma prime (γ′) or κ-carbide phase comprises a metastable CoxAly phase having less than about 13% Co by weight.
The polycrystalline diamond compact of any of Embodiments 1 through 14, wherein the gamma prime (γ′) or κ-carbide phase comprises a metastable CoxAly phase having less than about 50 mol % Al.
The polycrystalline diamond compact of any of Embodiments 1 through 14, wherein the intermetallic gamma prime (γ′) or κ-carbide phase is structurally ordered.
The polycrystalline diamond compact of any of Embodiments 1 through 14, wherein the intermetallic gamma prime (γ′) or κ-carbide phase is structurally disordered.
A method of forming polycrystalline diamond comprising subjecting diamond particles in the presence of a metal material comprising a Group VIII metal and aluminum to a pressure of at least 4.5 GPa and a temperature of at least 1,000° C. to form inter-granular bonds between adjacent diamond particles, cooling the diamond particles and the metal material to a temperature below an ordered-disordered transition temperature, and forming an ordered intermetallic gamma prime (γ′) or κ-carbide phase adjacent the diamond particles. The ordered intermetallic gamma prime (γ′) or κ-carbide phase comprises the Group VIII metal, aluminum, and a stabilizer.
The method of Embodiment 17, further comprising selecting the stabilizer to comprise at least one element selected from the group consisting of titanium, nickel, tungsten, and carbon.
The method of Embodiment 17 or Embodiment 18, wherein subjecting diamond particles to a pressure of at least 4.5 GPa and a temperature of at least 1,000° C. comprises dissolving the stabilizer in a mixture of the Group VIII metal and the aluminum.
The method of any of Embodiments 17 through 19, wherein dissolving the stabilizer in a mixture of the Group VIII metal and the aluminum comprises dissolving carbon originating from the diamond particles into a molten alloy comprising the Group VIII metal and the aluminum.
The method of any of Embodiments 17 through 20, wherein forming an ordered intermetallic gamma prime (γ′) or κ-carbide phase comprises forming a metastable Co3Al phase stabilized by the stabilizer.
The method of any of Embodiments 17 through 21, wherein forming an ordered intermetallic gamma prime (γ′) or κ-carbide phase comprises forming a metastable (CoxNi3-x)Al phase stabilized by the stabilizer.
The method of any of Embodiments 17 through 22, further comprising admixing the diamond particles with particles comprising at least one material selected from the group consisting of the Group VIII metal, the aluminum, and the stabilizer.
The method of any of Embodiments 17 through 23, further comprising disposing the diamond particles in a container with a metal foil comprising at least one material selected from the group consisting of the Group VIII metal, the aluminum, and the stabilizer.
The method of any of Embodiments 17 through 24, further comprising forming a thermally stable polycrystalline diamond compact comprising the diamond particles without leaching.
The method of any of Embodiments 17 through 25, further comprising forming the polycrystalline diamond in the form of a finished cutting element comprising a diamond table including the ordered intermetallic gamma prime (γ′) or κ-carbide phase comprising the Group VIII metal, aluminum, and the stabilizer.
The method of any of Embodiments 17 through 26, further comprising at least substantially entirely filling interstitial spaces between the diamond particles with the gamma prime (γ′) or κ-carbide phase.
The method of any of Embodiments 17 through 27, further comprising coating the diamond particles with at least one material selected from the group consisting of the Group VIII metal, the aluminum, and the stabilizer.
An earth-boring tool comprising a bit body and a polycrystalline diamond compact secured to the bit body. The polycrystalline diamond compact comprises any of Embodiments 1 through 16.
While the present invention has been described herein with respect to certain illustrated embodiments, those of ordinary skill in the art will recognize and appreciate that it is not so limited. Rather, many additions, deletions, and modifications to the illustrated embodiments may be made without departing from the scope of the invention as hereinafter claimed, including legal equivalents thereof. In addition, features from one embodiment may be combined with features of another embodiment while still being encompassed within the scope of the invention as contemplated by the inventors. Further, embodiments of the disclosure have utility with different and various tool types and configurations.
This application is a divisional of U.S. patent application Ser. No. 15/060,911, filed Mar. 4, 2016, pending, the disclosure of which is hereby incorporated herein in its entirety by this reference. The subject matter of this application is related to the subject matter of U.S. patent application Ser. No. 15/594,174, filed May 12, 2017, for “Methods of Forming Supporting Substrates for Cutting Elements, and Related Cutting Elements, Methods of Forming Cutting Elements, and Earth-Boring Tools,” to U.S. patent application Ser. No. 15/842,530, filed Dec. 14, 2017, for “Methods of Forming Supporting Substrates for Cutting Elements, and Related Cutting Elements, Methods of Forming Cutting Elements, and Earth-Boring Tools,” and to U.S. patent application Ser. No. 15/993,362, filed May 30, 2018, for “Cutting Elements, and Related Earth-Boring Tools, Supporting Substrates, and Methods.”
| Number | Date | Country | |
|---|---|---|---|
| Parent | 15060911 | Mar 2016 | US |
| Child | 16292982 | US |
