Patent Grant
11939646
Embodiments of this disclosure generally relate to nickel-based alloys that can serve as effective feedstock for hardfacing processes, such as for plasma transferred arc (PTA), laser cladding hardfacing processes including high speed laser cladding, and thermal spray processes such as high velocity oxygen fuel (HVOF) thermal spray.
Abrasive and erosive wear is a major concern for operators in applications that involve sand, rock, or other hard media wearing away against a surface. Applications which see severe wear typically utilize materials of high hardness to resist material failure due to the severe wear. These materials typically contain carbides and/or borides as hard precipitates which resist abrasion and increase the bulk hardness of the material. These materials are often applied as a coating, known as hardfacing, through various welding processes or cast directly into a part.
Another major concern for operators is corrosion. Applications that see severe corrosion typically utilize soft nickel based or stainless steel type materials with high chromium. In these types of applications, no cracks can be present in the overlay as this will result in corrosion of the underlying base material.
Currently, it is common to use either the wear resistant material, or the corrosion resistant material, as there are few alloys that satisfy both requirements. Often the current materials do not provide the necessary lifetime or require the addition of carbides for the increase in wear resistance, which may cause cracking.
Disclosed herein are embodiments of a feedstock material comprising, in wt. %, Ni, C: 0.5-2, Cr: 10-30, Mo: 5.81-18.2, Nb+Ti: 2.38-10.
In some embodiments, the feedstock material may further comprise, in wt. %, C: about 0.8-about 1.6, Cr: about 14-about 26, and Mo: about 8-about 16. In some embodiments, the feedstock material may further comprise, in wt. %, C: about 0.84-about 1.56, Cr: about 14-about 26, Mo: about 8.4-about 15.6, and Nb+Ti: about 4.2-about 8.5. In some embodiments, the feedstock material may further comprise, in wt. %, C: about 8.4-about 1.56, Cr: about 14-about 26, Mo: about 8.4-about 15.6, Nb: about 4.2-about 7.8, and Ti: about 0.35-about 0.65. In some embodiments, the feedstock material may further comprise, in wt. %, C: about 1.08-about 1.32, Cr: about 13-about 22, Mo: about 10.8-about 13.2, and Nb: about 5.4-about 6.6. In some embodiments, the feedstock material may further comprise, in wt. %, C: about 1.2, Cr: about 20, Mo: about 12, Nb: about 6, and Ti: about 0.5.
In some embodiments, the feedstock material is a powder. In some embodiments, the feedstock material is a wire. In some embodiments, the feedstock material is a combination of a wire and a powder.
Also disclosed herein are embodiments of a hardfacing layer formed from the feedstock material as disclosed herein.
In some embodiments, the hardfacing layer can comprise a nickel matrix comprising hard phases of 1,000 Vickers hardness or greater totaling 5 mol. % or greater, 20 wt. % or greater of a combined total of chromium and molybdenum, isolated hypereutectic hard phases totaling to 50 mol. % or more of a total hard phase fraction, a WC/Cr3C2 ratio of 0.33 to 3, an ASTM G65A abrasion loss of less than 250 mm3, and a hardness of 650 Vickers or greater.
In some embodiments, the hardfacing layer can have a hardness of 750 Vickers or greater. In some embodiments, the hardfacing layer can exhibit two cracks or fewer per square inch, have an adhesion of 9,000 psi or greater, and have a porosity of 2 volume % or less. In some embodiments, the hardfacing layer can have a porosity of 0.5 volume % or less. In some embodiments, the hardfacing layer can have a corrosion rate of 1 mpy or less in a 28% CaCl2) electrolyte, pH=9.5 environment. In some embodiments, the hardfacing layer can have a corrosion rate of 0.4 mpy or less in a 28% CaCl2) electrolyte, pH=9.5 environment. In some embodiments, the hardfacing layer can have a corrosion rate of below 0.1 mpy in a 3.5% sodium chloride solution for 16 hours according to G-59/G-61. In some embodiments, the hardfacing layer can have a corrosion rate of below 0.08 mpy in a 3.5% sodium chloride solution for 16 hours according to G-59/G-61.
In some embodiments, the nickel matrix can have a matrix proximity of 80% or greater as compared to a corrosion resistant alloy defined by Ni: BAL, X >20 wt. %, wherein X represents at least one of Cu, Cr, or Mo. In some embodiments, the corrosion resistant alloy is selected from the group consisting of Inconel 625, Inconel 622, Hastelloy C276, Hastelloy X, and Monel 400.
In some embodiments, the hardfacing layer can be applied onto a hydraulic cylinder, tension riser, mud motor rotor, or oilfield component application.
Further disclosed herein are embodiments of a feedstock material comprising nickel; wherein the feedstock material is configured to form a corrosion resistant matrix which is characterized by having, under thermodynamic equilibrium conditions hard phases of 1,000 Vickers hardness or greater totaling 5 mol. % or greater, and a matrix proximity of 80% or greater when compared to a known corrosion resistant nickel alloy.
In some embodiments, the known corrosion resistant nickel alloy can be represented by the formula Ni: BAL X >20 wt. %, wherein X represents at least one of Cu, Cr, or Mo.
In some embodiments, the feedstock material can be a powder. In some embodiments, the powder can be made via an atomization process. In some embodiments, the powder can be made via an agglomerated and sintered process.
In some embodiments, the corrosion resistant matrix can be a nickel matrix comprising 20 wt. % or greater of a combined total of chromium and molybdenum. In some embodiments, under thermodynamic equilibrium conditions, the corrosion resistant matrix can be characterized by having isolated hypereutectic hard phases totaling to 50 mol. % or more of a total hard phase fraction.
In some embodiments, the known corrosion resistant nickel alloy can be selected from the group consisting of Inconel 625, Inconel 622, Hastelloy C276, Hastelloy X, and Monel 400.
In some embodiments, the feedstock material can comprise C: 0.84-1.56, Cr: 14-26, Mo: 8.4-15.6, Nb: 4.2-7.8, and Ti: 0.35-0.65. In some embodiments, the feedstock material can further comprise B: about 2.5 to about 5.7, and Cu: about 9.8 to about 23. In some embodiments, the feedstock material can further comprise Cr: about 7 to about 14.5.
In some embodiments, under thermodynamic equilibrium conditions, the corrosion resistant matrix can be characterized by having hard phases totaling 50 mol. % or greater, and a liquidus temperature of 1550 K or lower.
In some embodiments, the feedstock material can comprise a blend of Monel and at least one of WC or Cr3C2.
In some embodiments, the feedstock material is selected from the group consisting of, by wt. 75-85% WC+15-25% Monel, 65-75% WC+25-35% Monel, 60-75% WC+25-40% Monel, 75-85% Cr3C2+15-25% Monel, 65-75% Cr3C2+25-35% Monel, 60-75% Cr3C2+25-40% Monel, 75-85% WC/Cr3C2+15-25% Monel, 65-75% WC/Cr3C2+25-35% Monel, and 60-75% WC/Cr3C2+25-40% Monel.
In some embodiments, a WC/Cr3C2 ratio of the corrosion resistant matrix can be 0.25 to 5 by volume. In some embodiments, the thermal spray feedstock material can comprise a wire. In some embodiments, the thermal spray feedstock material can comprise a combination of a wire and powder.
Also disclosed herein are embodiments of a hardfacing layer formed from the feedstock material as disclosed herein.
In some embodiments, the hardfacing layer can comprise an ASTM G65A abrasion loss of less than 250 mm3, and two cracks or fewer per square inch when forming the hardfacing layer from a PTA or laser cladding process. In some embodiments, the hardfacing layer can comprise an impermeable HVOF coating which exhibits a corrosion rate of 1 mpy or less in a 28% CaCl2) electrolyte, pH=9.5 environment.
In some embodiments, the hardfacing layer can further comprise a hardness of 650 Vickers or greater, and an adhesion of 9,000 psi or greater when forming the hardfacing layer from a HVOF thermal spray process.
In some embodiments, the hardfacing layer can be applied onto a hydraulic cylinder, tension riser, mud motor rotor, or oilfield component application.
In some embodiments, the hardfacing layer can comprise a hardness of 750 Vickers or greater, and a porosity of 2 volume % or less, preferably 0.5% or less when forming the hardfacing layer from a HVOF thermal spray process.
Embodiments of the present disclosure include but are not limited to hardfacing/hardbanding materials, alloys or powder compositions used to make such hardfacing/hardbanding materials, methods of forming the hardfacing/hardbanding materials, and the components or substrates incorporating or protected by these hardfacing/hardbanding materials.
In certain applications it can be advantageous to form a metal layer with high resistance to abrasive and erosive wear, and to resist corrosion. Disclosed herein are embodiments of nickel-based alloys that have been developed to provide abrasive and corrosion resistance. Industries which would benefit from combined corrosion and wear resistance include marine applications, power industry coatings, oil & gas applications, and coatings for glass manufacturing.
In some embodiments, alloys disclosed herein can be engineered to form a microstructure which possesses both a matrix chemistry similar to some known alloys, such as Inconel and Hastelloys, while also including additional elements to improve performance. For example, carbides can be added into the matrix of the material. In particular, improved corrosion resistance and improved abrasion resistance can be formed.
It should be understood that in the complex alloy space, it is not possible to simply remove an element or substitute one for the other and yield equivalent results.
In some embodiments, nickel-based alloys as described herein may serve as effective feedstock for the plasma transferred arc (PTA), laser cladding hardfacing processes including high speed laser cladding, and thermal spray processing including high velocity oxygen fuel (HVOF) thermal spray, though the disclosure is not so limited. Some embodiments include the manufacture of nickel-based alloys into cored wires for hardfacing processes, and the welding methods of nickel-based wires and powders using wire fed laser and short wave lasers.
The term alloy can refer to the chemical composition of a powder used to form a metal component, the powder itself, the chemical composition of a melt used to form a casting component, the melt itself, and the composition of the metal component formed by the heating, sintering, and/or deposition of the powder, including the composition of the metal component after cooling. In some embodiments, the term alloy can refer to the chemical composition forming the powder disclosed within, the powder itself, the feedstock itself, the wire, the wire including a powder, the combined composition of a combination of wires, the composition of the metal component formed by the heating and/or deposition of the powder, or other methodology, and the metal component.
In some embodiments, alloys manufactured into a solid or cored wire (a sheath containing a powder) for welding or for use as a feedstock for another process may be described by specific chemistries herein. For example, the wires can be used for a thermal spray. Further, the compositions disclosed below can be from a single wire or a combination of multiple wires (such as 2, 3, 4, or 5 wires).
In some embodiments, the alloys can be applied by a thermal spray process to form a thermal spray coating, such as HVOF alloys. In some embodiments, the alloys can be applied as a weld overlay. In some embodiments, the alloys can be applied either as a thermal spray or as a weld overlay, e.g., having dual use.
Metal Alloy Composition
In some embodiments, an article of manufacture, such as a composition of a feedstock as disclosed herein, can comprise Ni and in weight percent:
In some embodiments, an article of manufacture, such as a composition of a feedstock as disclosed herein, can comprise Ni and in weight percent:
In some embodiments, an article of manufacture, such as a composition of a feedstock as disclosed herein, can comprise Ni and in weight percent:
In some embodiments, an article of manufacture, such as a composition of a feedstock as disclosed herein, can comprise Ni and in weight percent:
In some embodiments, an article of manufacture, such as a composition of a feedstock as disclosed herein, can comprise Ni and in weight percent:
In some embodiments, an article of manufacture, such as a composition of a feedstock as disclosed herein, can comprise Ni and in weight percent:
In some embodiments, an article of manufacture, such as a composition of a feedstock as disclosed herein, can comprise Ni and in weight percent:
In some embodiments, an article of manufacture, such as a composition of a feedstock as disclosed herein, can comprise one of the following, in weight percent:
In some embodiments, an article of manufacture, such as a composition of a feedstock as disclosed herein, can comprise Ni and in weight percent
In some embodiments, an article of manufacture, such as a composition of a feedstock as disclosed herein, can comprise agglomerated and sintered blends of, in weight percent:
In the above, hard phases are one or more of the following: Tungsten Carbide (WC) and/or Chromium Carbide (Cr3C2). Monel is a nickel copper alloy of the target composition Ni BAL 30 wt. % Cu with a common chemistry tolerance of 20-40 wt. % Cu, or more preferably 28-34 wt. % Cu with known impurities including but not limited to C, Mn, S, Si, and Fe. Monel does not include any carbides, and thus embodiments of the disclosure add in carbides, such as tungsten carbides and/or chromium carbides. Tungsten carbide is generally described by the formula W: BAL, 4-8 wt. % C. In some embodiments, tungsten carbide can be described by the formula W: BAL, 1.5 wt. % C.
In some embodiments with 60-85% WC+Ni30Cu, the article of manufacture can be, in weight percent:
In some embodiments with 60-85% Cr3C2+Ni30Cu, the article of manufacture can be, in weight percent:
Thus, the above feedstock description indicates that tungsten carbide, a known alloy of that simple chemical formula, was mechanically blended with Monel (as described by the simple Ni30Cu formula in the prescribed ratio). During this overall process many particles stick together such that a new ‘agglomerated’ particle is formed. In each case the agglomerated particle is comprised of the described ratios.
Table I lists a number of experimental alloys, with their compositions listed in weight percent.
In some embodiments, P76 alloys can be thermal spray alloys and P82 alloys can be weld overlay alloys (such as PTA or laser). However, the disclosure is not so limited. For example, any of the compositions as disclosed herein can be effective for hardfacing processes, such as for plasma transferred arc (PTA), laser cladding hardfacing processes including high speed laser cladding, and thermal spray processes such as high velocity oxygen fuel (HVOF) thermal spray.
In Table I, all values can be “about” the recited value as well. For example, for P82-X1, Ni: 59 (or about 59).
In some embodiments, the disclosed compositions can be the wire/powder, the coating or other metallic component, or both.
The disclosed alloys can incorporate the above elemental constituents to a total of 100 wt. %. In some embodiments, the alloy may include, may be limited to, or may consist essentially of the above named elements. In some embodiments, the alloy may include 2 wt. % (or about 2 wt. %) or less, 1 wt. % (or about 1 wt. %) or less, 0.5 wt. % (or about 0.5 wt. %) or less, 0.1 wt. % (or about 0.1 wt. %) or less or 0.01 wt. % (or about 0.01 wt. %) or less of impurities, or any range between any of these values. Impurities may be understood as elements or compositions that may be included in the alloys due to inclusion in the feedstock components, through introduction in the manufacturing process.
Further, the Ni content identified in all of the compositions described in the above paragraphs may be the balance of the composition, or alternatively, where Ni is provided as the balance, the balance of the composition may comprise Ni and other elements. In some embodiments, the balance may consist essentially of Ni and may include incidental impurities.
Thermodynamic Criteria
In some embodiments, alloys can be characterized by their equilibrium thermodynamic criteria. In some embodiments, the alloys can be characterized as meeting some of the described thermodynamic criteria. In some embodiments, the alloys can be characterized as meeting all of the described thermodynamic criteria.
A first thermodynamic criterion pertains to the total concentration of extremely hard particles in the microstructure. As the mole fraction of extremely hard particles increases the bulk hardness of the alloy may increase, thus the wear resistance may also increase, which can be advantageous for hardfacing applications. For the purposes of this disclosure, extremely hard particles may be defined as phases that exhibit a hardness of 1000 Vickers or greater (or about 1000 Vickers or greater). The total concentration of extremely hard particles may be defined as the total mole % of all phases that meet or exceed a hardness of 1000 Vickers (or about 1000 Vickers) and is thermodynamically stable at 1500K (or about 1500K) in the alloy.
In some embodiments, the extremely hard particle fraction is 3 mole % or greater (or about 3 mole % or greater), 4 mole % or greater (or about 4 mole % or greater), 5 mole % or greater (or about 5 mole % or greater), 8 mole % or greater (or about 8 mole % or greater), 10 mole % or greater (or about 10 mole % or greater), 12 mole % or greater (or about 12 mole % or greater) or 15 mole % or greater (or about 15 mole % or greater), 20 mole % or greater (or about 20 mole % or greater), 30 mole % or greater (or about 30 mole % or greater), 40 mole % or greater (or about 40 mole % or greater), 50 mole % or greater (or about 50 mole % or greater), 60 mole % or greater (or about 60 mole % or greater), or any range between any of these values.
In some embodiments, the extremely hard particle fraction can be varied according to the intended process of the alloy. For example, for thermal spray alloys, the hard particle fraction can be between 40 and 60 mol. % (or between about 40 and about 60 mol. %). For alloys intended to be welded via laser, plasma transfer arc, or other wire welding application the hard particle phase fraction can be between 15 and 30 mol. % (or between about 15 and about 30 mol. %).
A second thermodynamic criterion pertains to the amount of hypereutectic hard phases that form in the alloy. A hypereutectic hard phase is a hard phase that begins to form at a temperature higher than the eutectic point of the alloy. The eutectic point of these alloys is the temperature at which the FCC matrix begins to form.
In some embodiments, hypereutectic hard phases total to 40 mol. % or more (or about 40% or more), 45 mol. % or more (or about 45% or more), 50 mol. % or more (or about 50% or more), 60 mol. % or more (or about 60% or more), 70 mol. % or more (or about 70% or more), 75 mol. % or more (or about 75% or more) or 80 mol. % or more (or about 80% or more) of the total hard phases present in the alloy, or any range between any of these values.
A third thermodynamic criterion pertains to the corrosion resistance of the alloy. The corrosion resistance of nickel-based alloys may increase with higher weight percentages of chromium and/or molybdenum present in the FCC matrix. This third thermodynamic criterion measures the total weight % of chromium and molybdenum in the FCC matrix at 1500K (or about 1500K).
In some embodiments, the total weight % of chromium and molybdenum in the matrix is 15 weight % or greater (or about 15 weight % or greater), 18 weight % or greater (or about 18 weight % or greater), 20 weight % or greater (or about 20 weight % or greater), 23 weight % or greater (or about 23 weight % or greater), 25 weight % or greater (or about 25 weight % or greater), 27 weight % or greater (or about 27 weight % or greater) or 30 weight % or greater (or about 30 weight % or greater), or any range between any of these values.
A fourth thermodynamic criterion relates to the matrix chemistry of the alloy. In some embodiments, it may be beneficial to maintain a similar matrix chemistry to a known alloy such as, for example, Inconel 622, Inconel 625, Inconel 686, Hastelloy C276, Hastelloy X, or Monel 400. In some embodiments, to maintain a similar matrix chemistry to a known alloy, the matrix chemistry of alloys at 1300K was compared to those of a known alloy. Comparisons of this sort are termed Matrix Proximity. In general, such superalloys can be represented by the formula, in wt. %, Ni: BAL, Cr: 15-25, Mo: 8-20.
In some embodiments, the matrix proximity is 50% (or about 50%) or greater, 55% (or about 55%) or greater, 60% (or about 60%) or greater, 70% (or about 70%) or greater, 80% (or about 80%) or greater, 85% (or about 85%) or greater, 90% (or about 90%) or greater, of any of the above known alloys. Matrix proximity can be determined in a number of ways, such as energy dispersive spectroscopy (EDS).
The equation below can be used to calculate the similarity or proximity of the modelled alloy matrix to an alloy of known corrosion resistance. A value of 100% means an exact match between the compared elements.
A fifth thermodynamic criterion relates to the liquidus temperature of the alloy, which can help determine the alloy's suitability for the gas atomization manufacturing process. The liquidus temperature is the lowest temperature at which the alloy is still 100% liquid. A lower liquidus temperature generally corresponds to an increased suitability to the gas atomization process. In some embodiments, the liquidus temperature of the alloy can be 1850 K (or about 1850 K) or lower. In some embodiments, the liquidus temperature of the alloy can be 1600 K (or about 1600 K) or lower. In some embodiments, the liquidus temperature of the alloy can be 1450 K (or about 1450 K) or lower.
The thermodynamic behavior of alloy P82-X6 is shown in
A M6C type carbide also precipitates at a lower temperature to form a total carbide content of about 15 mol. % at 1300K (12.6% FCC carbide, 2.4% M6C carbide). The FCC carbide representing the isolated carbides in the alloy and forming the majority (>50%) of the total carbides in the alloy. The arrow points specifically to the point at which the composition of the FCC_L12 matrix is mined for insertion into the matrix proximity equation. As depicted in this example, the volume fraction of all hard phases exceeds 5 mole %, with over 50% of the carbide fraction forming as a hypereutectic phase known to form an isolated morphology with the remaining FCC_L12 matrix phase possessing over 60% proximity with Inconel 625.
In this calculation, although not depicted in
The thermodynamic behavior of alloy P76-X23 is shown in
Microstructural Criteria
In some embodiments, alloys can be described by their microstructural criterion. In some embodiments, the alloys can be characterized as meeting some of the described microstructural criteria. In some embodiments, the alloys can be characterized as meeting all of the described microstructural criteria.
A first microstructural criterion pertains to the total measured volume fraction of extremely hard particles. For the purposes of this disclosure, extremely hard particles may be defined as phases that exhibit a hardness of 1000 Vickers or greater (or about 1000 Vickers or greater). The total concentration of extremely hard particles may be defined as the total mole % of all phases that meet or exceed a hardness of 1000 Vickers (or about 1000 Vickers) and is thermodynamically stable at 1500K (or about 1500K) in the alloy. In some embodiments, an alloy possesses at least 3 volume % (or at least about 3 volume %), at least 4 volume % (or at least about 4 volume %), at least 5 volume % (or at least about 5 volume %), at least 8 volume % (or at least about 8 volume %), at least 10 volume % (or at least about 10 volume %), at least 12 volume % (or at least about 12 volume %) or at least 15 volume % (or at least about 15 volume %) of extremely hard particles, at least 20 volume % (or at least about 20 volume %) of extremely hard particles, at least 30 volume % (or at least about 30 volume %) of extremely hard particles, at least 40 volume % (or at least about 40 volume %) of extremely hard particles, at least 50 volume % (or at least about 50 volume %) of extremely hard particles, or any range between any of these values.
In some embodiments, the extremely hard particle fraction can be varied according to the intended process of the alloy. For example, for thermal spray alloys, the hard particle fraction can be between 40 and 60 vol. % (or between about 40 and about 60 vol. %). For alloys intended to be welded via laser, plasma transfer arc, or other wire welding application the hard particle phase fraction can be between 15 and 30 vol. % (or between about 15 and about 30 vol. %).
A second microstructural criterion pertains to the fraction of hypereutectic isolated hard phases in an alloy. Isolated, as used herein, can mean that the particular isolated phase (such as spherical or partially spherical particles) remains unconnected from other hard phases. For example, an isolated phase can be 100% enclosed by the matrix phase. This can be in contrast to rod-like phases which can form long needles that act as low toughness “bridges,” allowing cracks to work through the microstructure.
To reduce the crack susceptibility of an alloy it may be beneficial to form isolated hypereutectic phases rather than continuous grain boundary phases. In some embodiments, isolated hypereutectic hard phases total 40 vol. % (or about 40%) or more, 45 vol. % (or about 45%) or more, 50 vol. % (or about 50%) or more, 60 vol. % (or about 60%) or more, 70 vol. % (or about 70%) or more, 75 vol. % (or about 75%) or more or 80 vol. % (or about 80%) or more of the total hard phase fraction present in the alloy, or any range between any of these values.
A third microstructural criterion pertains to the increased resistance to corrosion in the alloy. To increase the resistance to corrosion in nickel based alloys it may be beneficial to have a high total weight % of chromium and molybdenum in a matrix. An Energy Dispersive Spectrometer (EDS) was used to determine the total weight % of chromium and molybdenum in a matrix. In some embodiments, the total content of chromium and molybdenum in the matrix may be 15 weight % or higher (or about 15 weight % or higher), 18 weight % or higher (or about 18 weight % or higher), 20 weight % or higher (or about 20 weight % or higher), 23 weight % or higher (or about 23 weight % or higher), 25 weight % or higher (or about 25 weight % or higher), 27 weight % or higher (or about 27 weight % or higher) or 30 weight % or higher (or about 30 weight % or higher), or any range between any of these values.
A fourth microstructural criterion pertains to the matrix proximity of an alloy compared to that of a known alloy such as, for example, Inconel 625, Inconel 686, or Monel. An Energy Dispersive Spectrometer (EDS) was used to measure the matrix chemistry of the alloy. In some embodiments, the matrix proximity is 50% (or about 50%) or greater, 55% (or about 55%) or greater, 60% (or about 60%) or greater, 70% (or about 70%) or greater, 80% (or about 80%) or greater, 85% (or about 85%) or greater or 90% (or about 90%) or greater of the known alloy, or any range between any of these values.
The matrix proximity is similar to what is described in the thermodynamic criteria section, in this case it is calculated. The difference between ‘matrix chemistry’ and ‘matrix proximity’ is that the chemistry is the actual values of Cr, Mo or other elements found in solid solution of the Nickel matrix. The proximity is the % value used as a quantitative measure to how closely the Nickel matrix of the designed alloy matches the chemistry of a known alloy possessing good corrosion resistance. For clarification, the known alloys such as Inconel are single phase alloys so the alloy composition is effectively the matrix composition, all the alloying elements are found in solid solution. This is not the case with the alloys described here in which we are precipitating hard phases for wear resistance.
Performance Criteria
In some embodiments, a hardfacing layer is produced via a weld overlay process including but not limited to PTA cladding or laser cladding.
In some embodiments, an alloy can have a number of advantageous performance characteristics. In some embodiments, it can be advantageous for an alloy to have one or more of 1) a high resistance to abrasion, 2) minimal to no cracks when welded via a laser cladding process or other welding method, and 3) a high resistance to corrosion. The abrasion resistance of hardfacing alloys can be quantified using the ASTM G65A dry sand abrasion test. The crack resistance of the material can be quantified using a dye penetrant test on the alloy. The corrosion resistance of the alloy can be quantified using the ASTM G48, G59, and G61 tests. All of the listed ASTM tests are hereby incorporated by reference in their entirety.
In some embodiments, a hardfacing layer may have an ASTM G65A abrasion loss of less than 250 mm3 (or less than about 250 mm3), less than 100 mm3 (or less than about 100 mm3), less than 30 mm3 (or less than about 30 mm3), or less than 20 mm3 (or less than about 20 mm3).
In some embodiments, the hardfacing layer may exhibit 5 cracks per square inch, 4 cracks per square inch, 3 cracks per square inch, 2 cracks per square inch, 1 crack per square inch or 0 cracks per square inch of coating, or any range between any of these values. In some embodiments, a crack is a line on a surface along which it has split without breaking into separate parts.
In some embodiments, the hardfacing layer may have a corrosion resistance of 50% (or about 50%) or greater, 55% (or about 55%) or greater, 60% (or about 60%) or greater, 70% (or about 70%) or greater, 80% (or about 80%) or greater, 85% (or about 85%) or greater, 90% (or about 90%) or greater, 95% (or about 95%) or greater, 98% (or about 98%) or greater, 99% (or about 99%) or greater or 99.5% (or about 99.5%) or greater than a known alloy, or any range between any of these values.
Corrosion resistance is complex and can depend on the corrosive media being used. Preferably, the corrosion rate of embodiments of the disclosed alloys can be nearly equivalent to the corrosion rate of the comparative alloy they are intended to mimic. For example, if Inconel 625 has a corrosion rate of 1 mpy (mil per year). in a certain corrosive media, P82-X6 can have a corrosion resistance of 1.25 mpy or lower to yield a corrosion resistance of 80%. Corrosion resistance is defined as 1/corrosion rate for the purposes of this disclosure.
In some embodiments, the alloy can have a corrosion rate of 1 mpy or less (or about 1 mpy or less) in a 28% CaCl2) electrolyte, pH=9.5 environment. In some embodiments, the alloy can have a corrosion rate of 0.6 mpy or less (or about 0.6 mpy or less) in a 28% CaCl2) electrolyte, pH=9.5 environment. In some embodiments, the alloy can have a corrosion rate of 0.4 mpy or less (or about 0.4 mpy or less) in a 28% CaCl2) electrolyte, pH=9.5 environment.
In some embodiments, the alloy can have a corrosion resistance in a 3.5% sodium chloride solution for 16 hours according to G-59/G-61 of below 0.1 mpy (or below about 0.1 mpy). In some embodiments, the alloy can have a corrosion resistance in a 3.5% sodium chloride solution for 16 hours according to G-59/G-61 of below 0.08 mpy (or below about 0.08 mpy).
In some embodiments, a hardfacing layer is produced via a thermal spray process including but not limited to high velocity oxygen fuel (HVOF) thermal spray.
In some embodiments, the hardness of the coating can be 650 (or about 650) Vickers or higher. In some embodiments, the hardness of the thermal spray process can be 700 (or about 700) Vickers or higher. In some embodiments, the hardness of the thermal spray process can be 900 (or about 900) Vickers or higher.
In some embodiments, the adhesion of the thermal spray coating can be 7,500 (or about 7,500) psi or greater. In some embodiments, the adhesion the adhesion of the thermal spray coating can be 8,500 (or about 8,500) psi or greater. In some embodiments, the adhesion the adhesion of the thermal spray coating can be 9,500 (or about 9,500) psi or greater.
Alloy P82-X6 was gas atomized into a powder of 53-150 μm particle size distribution as suitable for PTA and/or laser cladding. The alloy was laser clad using two parameter sets: 1) 1.8 kW laser power and 20 L/min flow rate, and 2) 2.2 kW laser power and 14 L/min flow rate. In both cases, the coating showed fine isolated niobium/titanium carbide precipitates 401 in a Nickel matrix 402 as intended as shown in
Alloys P76-X23 and P76-X24 were gas atomized into powders of 15-45 μm particle size distribution as suitable for HVOF thermal spray processing. Both powders forms an extremely fine scale morphology where a nickel matrix phase and nickel boride phase appear to be both present as predicted via the computational modelling, but very difficult to distinguish and measure quantitatively.
As shown in
505 highlights a region of primarily nickel/nickel boride eutectic structure in the HVOF sprayed coating, and 506 highlights a region containing many chromium boride precipitates in the coating.
Both alloys were HVOF sprayed to about 200-300 μm coating thickness and formed dense coatings. The 300 grams force Vickers hardness of the coatings were 693 and 726 for P76-X23 and P76-X24 respectively. P76-X23 adhesion tests result in glue failure up to 9,999 psi, and P76-X24 showed 75% adhesion, 25% glue failure in two tests reaching 9,576 and 9,999 psi. ASTM G65A (converted from an ASTM G65B test) testing showed 87 mm3 lost for P76-X24. ASTM G65A testing uses 6,000 revolutions, procedure B uses 2,000 revolutions and is typically used for thin coatings such as thermal spray coatings.
P76-X24 was tested in a 28% CaCl2 electrolyte, pH=9.5 resulting in a measured corrosion rate of 0.4 mpy. In comparison, cracked hard chrome exhibits a rate of 1.06 mpy in a similar environment. Hard Cr is used as a relevant coating for a variety of application requiring both corrosion and abrasion resistance. In some embodiments, the alloy in the form of an HVOF coating produces a corrosion rate of 1 mpy or less in a 28% CaCl2 electrolyte, pH=9.5 environment. In some embodiments, the alloy in the form of an HVOF coating can produce a corrosion rate of 0.6 mpy or less in a 28% CaCl2 electrolyte, pH=9.5 environment. In some embodiments, the alloy in the form of an HVOF coating can produce a corrosion rate of 0.4 mpy or less in a 28% CaCl2 electrolyte, pH=9.5 environment. In some embodiments, the alloy in the form of an HVOF coating produces a non-permeable coating per ECP (electrochemical potential) testing.
A blend of a blend of 80 wt. % WC/Cr3C2 (50/50 vol %) mixed with 20 wt. % Monel was agglomerated and sintered into 15-45 μm as suitable for thermal spray processing. The HVOF coating, as shown in
A weld study was conducted evaluating several alloys of differing carbide contents and morphologies in comparison to Inconel 625. All of the alloys in the study were intended to form a matrix similar to Inconel 625, which is quantified by the matrix proximity, 100% equating to a matrix which is exactly similar to the Inconel 625 bulk composition. All the alloys were laser welded in three overlapping layers to test for crack resistance. Similarly, two layer welds of each alloy were produced via plasma transferred arc welding to test for cracking and other properties.
The P82-X18 represents an embodiment of this disclosure producing favorable results at the conclusion of this study. P82-X18 is significantly harder than Inconel 625 in both processes, PTA and laser. Despite the increased hardness, no cracking was evident in the laser or PTA clad specimens. P82-X18 exhibits improved abrasion resistance as compared to Inconel 625 in both processes. The general trend for increased hardness is true for all the tested alloys as demonstrated in Table 3. However, surprisingly, the increased hardness does not generate an increased abrasion resistance in all cases. P82-X13, P82-X14, and P82-X15 all exhibited higher wear rates than Inconel 625 despite being harder and containing carbides. This result demonstrates the discovered advantageous carbide morphology as compared to total carbide fraction and alloy hardness.
Alloy P82-X18 meets thermodynamic, microstructural, and performance criteria of this disclosure. P82-X18 is predicted to form 8.1 mol. % isolated carbides and indeed forms 8-12% isolated carbides in the studied and industrially relevant weld processes. The alloy is also predicted to form 9.9 mol % grain boundary hard phases, and indeed forms grain boundary hard phases of 10 vol. % or less. The isolated carbide content is in excess of 40% of the total carbide content in the alloy. This elevated ratio of isolated carbide fraction provides enhanced wear resistance beyond what can be expected of total carbide fraction alone.
The matrix of P82-X18 was measured via Energy Dispersive Spectroscopy which yielded Cr: 19-20 wt. %, Mo: 10-12 wt., %, Ni: Balance. Thus, the matrix composition is quite similar and somewhat overlapping with a typical Inconel 625 manufacturing range which is: Cr: 20-23, Mo: 8-10, Nb+Ta: 3.15-4.15, Ni: BAL. P82-X18 was tested in G-48 ferric chloride immersion testing for 24 hours and, similar to Inconel 625, showed no corrosion. P82-X18 was corrosion tested in a 3.5% Sodium Chloride solution for 16 hours according to G-59/G-61 ASTM standard and measured a corrosion rate of 0.075-0.078 mpy (mils per year).
In some embodiments, the measured corrosion rate of the material in a 3.5% Sodium Chloride solution for 16 hours according to G-59/G-61 is below 0.1 mpy. In some embodiments, the measured corrosion rate of the material in a 3.5% Sodium Chloride solution for 16 hours according to G-59/G-61 is below 0.08 mpy.
In some embodiments, the alloys disclosed herein, for example P82-X18, can be used in exchange for nickel or other common materials as the metal component in carbide metal matrix composites (MMCs). Common examples of the type of MMCs include by weight WC 60 wt. %, Ni 40 wt. %. Utilizing P82-X18 in this example would yield an MMC of the type: WC 60 wt. %, P82-X18 40 wt. %. A variety of carbide ratios and carbide types can be used.
P82-X18 was thermally sprayed using the hydrogen fueled HVOF process. The resultant coating had an adhesion strength of 10,000 psi, 700 HV300 Vickers hardness, and an ASTM G65B mass loss of 0.856 (10.4.6 g/mm3 volume loss).
Two powders were manufactured via the agglomeration and sintering process according to the formulas: 1) 65-75% WC/Cr3C2+25-35% NiCu alloy and 2) 65-75% Cr3C2+25-35% NiCu alloy. To clarify the first blend, 65-75% of the total volume fraction of the agglomerated and sintered particle is carbide, the remainder being the NiCu metal alloy. The carbide content of the particle is itself composed of a combination of both WC and Cr3C2 carbide types. In some embodiments, the WC/Cr3C2 ratio is from 0 to 100 by volume. In some embodiments, the WC/Cr3C2 ratio is about 0.33 to 3 by volume. In some embodiments, the WC/Cr3C2 ratio is about 0.25 to 5 by volume. In some embodiments, the WC/Cr3C2 ratio is about 0.67 to 1.5. The composition of the NiCu alloy is Cu: 20-40 wt. %, preferably Cu: 25-35 wt. %, still preferably: Cu: 28-34 wt. %, balance Nickel with other common impurities below 3 wt. % each.
Both powders were sprayed via the HVOF process to form coatings which were then tested. Coatings produced from powder 1 and powder 2 demonstrated corrosion rates 0.15 mpy and 0.694 mpy respectively in the 28% CaCl2) electrolyte, pH=9.5 solution. Coatings produced from powder 1 and powder 2 were non-permeable as measured via ECP testing. Coatings produced from powder 1 and powder 2 demonstrated abrasion volume losses in ASTM G65A of 11.3 mm3 and 16.2 mm3 respectively. Coatings produced from powder 1 and powder 2 demonstrated microhardness values of 816 HV300 and 677 HV300 respectively. Coatings produced from both powders had bond strengths in excess of 12,500 psi.
Applications
The alloys described in this disclosure can be used in a variety of applications and industries. Some non-limiting examples of applications of use include: surface mining, marine, power industry, oil and gas, and glass manufacturing applications.
Surface mining applications include the following components and coatings for the following components: Wear resistant sleeves and/or wear resistant hardfacing for slurry pipelines, mud pump components including pump housing or impeller or hardfacing for mud pump components, ore feed chute components including chute blocks or hardfacing of chute blocks, separation screens including but not limited to rotary breaker screens, banana screens, and shaker screens, liners for autogenous grinding mills and semi-autogenous grinding mills, ground engaging tools and hardfacing for ground engaging tools, wear plate for buckets and dump truck liners, heel blocks and hardfacing for heel blocks on mining shovels, grader blades and hardfacing for grader blades, stacker reclaimers, sizer crushers, general wear packages for mining components and other comminution components.
From the foregoing description, it will be appreciated that inventive nickel-based hardfacing alloys and methods of use are disclosed. While several components, techniques and aspects have been described with a certain degree of particularity, it is manifested that many changes can be made in the specific designs, constructions and methodology herein above described without departing from the spirit and scope of this disclosure.
Certain features that are described in this disclosure in the context of separate implementations can also be implemented in combination in a single implementation. Conversely, various features that are described in the context of a single implementation can also be implemented in multiple implementations separately or in any suitable subcombination. Moreover, although features may be described above as acting in certain combinations, one or more features from a claimed combination can, in some cases, be excised from the combination, and the combination may be claimed as any subcombination or variation of any subcombination.
Moreover, while methods may be depicted in the drawings or described in the specification in a particular order, such methods need not be performed in the particular order shown or in sequential order, and that all methods need not be performed, to achieve desirable results. Other methods that are not depicted or described can be incorporated in the example methods and processes. For example, one or more additional methods can be performed before, after, simultaneously, or between any of the described methods. Further, the methods may be rearranged or reordered in other implementations. Also, the separation of various system components in the implementations described above should not be understood as requiring such separation in all implementations, and it should be understood that the described components and systems can generally be integrated together in a single product or packaged into multiple products. Additionally, other implementations are within the scope of this disclosure.
Conditional language, such as “can,” “could,” “might,” or “may,” unless specifically stated otherwise, or otherwise understood within the context as used, is generally intended to convey that certain embodiments include or do not include, certain features, elements, and/or steps. Thus, such conditional language is not generally intended to imply that features, elements, and/or steps are in any way required for one or more embodiments.
Conjunctive language such as the phrase “at least one of X, Y, and Z,” unless specifically stated otherwise, is otherwise understood with the context as used in general to convey that an item, term, etc. may be either X, Y, or Z. Thus, such conjunctive language is not generally intended to imply that certain embodiments require the presence of at least one of X, at least one of Y, and at least one of Z.
Language of degree used herein, such as the terms “approximately,” “about,” “generally,” and “substantially” as used herein represent a value, amount, or characteristic close to the stated value, amount, or characteristic that still performs a desired function or achieves a desired result. For example, the terms “approximately”, “about”, “generally,” and “substantially” may refer to an amount that is within less than or equal to 10% of, within less than or equal to 5% of, within less than or equal to 1% of, within less than or equal to 0.1% of, and within less than or equal to 0.01% of the stated amount. If the stated amount is 0 (e.g., none, having no), the above recited ranges can be specific ranges, and not within a particular % of the value. For example, within less than or equal to 10 wt./vol. % of, within less than or equal to 5 wt./vol. % of, within less than or equal to 1 wt./vol. % of, within less than or equal to 0.1 wt./vol. % of, and within less than or equal to 0.01 wt./vol. % of the stated amount.
The disclosure herein of any particular feature, aspect, method, property, characteristic, quality, attribute, element, or the like in connection with various embodiments can be used in all other embodiments set forth herein. Additionally, it will be recognized that any methods described herein may be practiced using any device suitable for performing the recited steps.
While a number of embodiments and variations thereof have been described in detail, other modifications and methods of using the same will be apparent to those of skill in the art. Accordingly, it should be understood that various applications, modifications, materials, and substitutions can be made of equivalents without departing from the unique and inventive disclosure herein or the scope of the claims.
This application claims the benefit of priority from PCT App. No. PCT/US2019/058080, filed Oct. 25, 2019, and entitled “CORROSION AND WEAR RESISTANT NICKEL BASED ALLOYS”, which claims the benefit of priority from U.S. App. No. 62/751,020, filed Oct. 26, 2018, and entitled “CORROSION AND WEAR RESISTANT NICKEL BASED ALLOYS”, the entirety of which are incorporated by reference herein.
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/US2019/058080 | 10/25/2019 | WO |
| Publishing Document | Publishing Date | Country | Kind |
|---|---|---|---|
| WO2020/086971 | 4/30/2020 | WO | A |
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