Galvanically-Active In Situ Formed Particles for Controlled Rate Dissolving Tools

FIELD OF THE INVENTION

The invention is directed to a novel material for use as a dissolvable structure in oil drilling. Specifically, the invention is directed to a ball or other structure in a well drilling or completion operation, such as a structure that is seated in a hydraulic operation, that can be dissolved away after use so that that no drilling or removal of the structure is necessary. Primarily, dissolution is measured as the time the ball removes itself from the seat or can become free floating in the system. Secondarily, dissolution is measured in the time the ball is substantially or fully dissolved into submicron particles. Furthermore, the novel material of the present invention can be used in other well structures that also desire the function of dissolving after a period of time. The material is machinable and can be used in place of existing metallic or plastic structures in oil and gas drilling rigs including, but not limited to, water injection and hydraulic fracturing.

BACKGROUND OF THE INVENTION

The ability to control the dissolution of a downhole well component in a variety of solutions is important to the utilization of non-drillable completion tools, such as sleeves, frac balls, hydraulic actuating tooling, and the like. Reactive materials for this application, which dissolve or corrode when exposed to acid, salt, and/or other wellbore conditions, have been proposed for some time. Generally, these components consist of materials that are engineered to dissolve or corrode.

While the prior art well drill components have enjoyed modest success in reducing well completion costs, their consistency and ability to specifically control dissolution rates in specific solutions, as well as other drawbacks such as limited strength and poor reliability, have impacted their widespread adoption. Ideally, these components would be manufactured by a process that is low cost, scalable, and produces a controlled corrosion rate having similar or increased strength as compared to traditional engineering alloys such as aluminum, magnesium, and iron. Ideally, traditional heat treatments, deformation processing, and machining techniques could be used on the components without impacting the dissolution rate and reliability of such components.

Prior art articles regarding calcium use in magnesium are set for in Koltygin et al., “Effect of calcium on the process of production and structure of magnesium melted by flux-free method” Magnesium and Its Alloys (2013): 540-544; Koltygin et al., “Development of a magnesium alloy with good casting characteristics on the basis of Mg—Al—Ca—Mn system, having Mg—Al2Ca structure.” Journal of Magnesium and Alloys 1 (2013): 224-229; Li et al., “Development of non-flammable high strength AZ91+Ca alloys via liquid forging and extrusion.” Materials and Design (2016): 37-43; Cheng et al. “Effect of Ca and Y additions on oxidation behavior of AZ91 alloy at elevated temperatures.” Transactions of Nonferrous Metals Society of China (2009): 299-304; and Qudong et al., “Effects of Ca addition on the microstructure and mechanical properties of AZ91 magnesium alloy.” Journal of Materials Science (2001): 3035-3040.

SUMMARY OF THE INVENTION

The present invention is directed to a novel magnesium composite for use as a dissolvable component in oil drilling and will be described with particular reference to such application. As can be appreciated, the novel magnesium composite of the present invention can be used in other applications (e.g., non-oil wells, etc.). In one non-limiting embodiment, the present invention is directed to a ball or other tool component in a well drilling or completion operation such as, but not limited to, a component that is seated in a hydraulic operation that can be dissolved away after use so that no drilling or removal of the component is necessary. Tubes, valves, valve components, plugs, frac balls, sleeve, hydraulic actuating tooling, mandrels, slips, pips, balls, darts, carriers, valve components, other downhole well components and other shapes of components can also be formed of the novel magnesium composite of the present invention. For purposes of this invention, primary dissolution is measured for valve components and plugs as the time the part removes itself from the seat of a valve or plug arrangement or can become free floating in the system. For example, when the part is a plug in a plug system, primary dissolution occurs when the plug has degraded or dissolved to a point that it can no long function as a plug and thereby allows fluid to flow about the plug. For purposes of this invention, secondary dissolution is measured in the time the part is fully dissolved into submicron particles. As can be appreciated, the novel magnesium composite of the present invention can be used in other well components that also desire the function of dissolving after a period of time. In one non-limiting aspect of the present invention, a galvanically-active phase is precipitated from the novel magnesium composite composition and is used to control the dissolution rate of the component; however, this is not required. The novel magnesium composite is generally castable and/or machinable and can be used in place of existing metallic or plastic components in oil and gas drilling rigs including, but not limited to, water injection and hydraulic fracturing. The novel magnesium composite can be heat treated as well as extruded and/or forged.

In one non-limiting aspect of the present invention, the novel magnesium composite is used to form a castable, moldable, or extrudable component. Non-limiting magnesium composites in accordance with the present invention include at least 50 wt. % magnesium. One or more additives are added to a magnesium or magnesium alloy to form the novel magnesium composite of the present invention. The one or more additives can be selected and used in quantities so that galvanically-active intermetallic or insoluble precipitates form in the magnesium or magnesium alloy while the magnesium or magnesium alloy is in a molten state and/or during the cooling of the melt; however, this is not required. The one or more additives can be in the form of a pure or nearly pure additive element (e.g., at least 98% pure), or can be added as an alloy of two or more additive elements or an alloy of magnesium and one or more additive elements. The one or more additives typically are added in a weight percent that is less than a weight percent of said magnesium or magnesium alloy. Typically, the magnesium or magnesium alloy constitutes about 50.1-99.9 wt. % of the magnesium composite and all values and ranges therebetween. In one non-limiting aspect of the invention, the magnesium or magnesium alloy constitutes about 60-95 wt. % of the magnesium composite, and typically the magnesium or magnesium alloy constitutes about 70-90 wt. % of the magnesium composite. The one or more additives can be added to the molten magnesium or magnesium alloy at a temperature that is less than the melting point of the one or more additives; however, this is not required. The one or more additives generally have an average particle diameter size of at least about 0.1 microns, typically no more than about 500 microns (e.g., 0.1 microns, 0.1001 microns, 0.1002 microns . . . 499.9998 microns, 499.9999 microns, 500 microns) and include any value or range therebetween, more typically about 0.1-400 microns, and still more typically about 10-50 microns. In one non-limiting configuration, the particles can be less than 1 micron. During the process of mixing the one or more additives in the molten magnesium or magnesium alloy, the one or more additives do not typically fully melt in the molten magnesium or magnesium alloy; however, the one or more additives can form a single-phase liquid with the magnesium while the mixture is in the molten state. As can be appreciated, the one or more additives can be added to the molten magnesium or magnesium alloy at a temperature that is greater than the melting point of the one or more additives. The one or more additives can be added individually as pure or substantially pure additive elements or can be added as an alloy that is formed of a plurality of additive elements and/or an alloy that includes one or more additive elements and magnesium. When one or more additive elements are added as an alloy, the melting point of the alloy may be less than the melting point of one or more of the additive elements that are used to form the alloy; however, this is not required. As such, the addition of an alloy of the one or more additive elements could be caused to melt when added to the molten magnesium at a certain temperature, whereas if the same additive elements were individually added to the molten magnesium at the same temperature, such individual additive elements would not fully melt in the molten magnesium.

The one or more additives are selected such that as the molten magnesium cools, newly formed metallic alloys and/or additives begin to precipitate out of the molten metal and form the in situ phase to the matrix phase in the cooled and solid magnesium composite. After the mixing process is completed, the molten magnesium or magnesium alloy and the one or more additives that are mixed in the molten magnesium or magnesium alloy are cooled to form a solid component. In one non-limiting embodiment, the temperature of the molten magnesium or magnesium alloy is at least about 10° C. less than the melting point of the additive that is added to the molten magnesium or magnesium alloy during the addition and mixing process, typically at least about 100° C. less than the melting point of the additive that is added to the molten magnesium or magnesium alloy during the addition and mixing process, more typically about 100-1000° C. (and any value or range therebetween) less than the melting point of the additive that is added to the molten magnesium or magnesium alloy during the addition and mixing process; however, this is not required. As can be appreciated, one or more additives in the form of an alloy or a pure or substantially pure additive element can be added to the magnesium that have a melting point that is less than the melting point of magnesium, but still at least partially precipitate out of the magnesium as the magnesium cools from its molten state to a solid state. Generally, such one or more additives and/or one or more components of the additives form an alloy with the magnesium and/or one or more other additives in the molten magnesium. The formed alloy has a melting point that is greater than a melting point of magnesium, thereby results in the precipitation of such formed alloy during the cooling of the magnesium from the molten state to the solid state. The never melted additive(s) and/or the newly formed alloys that include one or more additives are referred to as in situ particle formation in the molten magnesium composite. Such a process can be used to achieve a specific galvanic corrosion rate in the entire magnesium composite and/or along the grain boundaries of the magnesium composite.

The invention adopts a feature that is usually a negative in traditional casting practices wherein a particle is formed during the melt processing that corrodes the alloy when exposed to conductive fluids and is imbedded in eutectic phases, the grain boundaries, and/or even within grains with precipitation hardening. This feature results in the ability to control where the galvanically-active phases are located in the final casting, as well as the surface area ratio of the in situ phase to the matrix phase, which enables the use of lower cathode phase loadings as compared to a powder metallurgical or alloyed composite to achieve the same dissolution rates. The in situ formed galvanic additives can be used to enhance mechanical properties of the magnesium composite such as ductility, tensile strength, and/or shear strength. The final magnesium composite can also be enhanced by heat treatment as well as deformation processing (such as extrusion, forging, or rolling) to further improve the strength of the final composite over the as-cast material; however, this is not required. The deformation processing can be used to achieve strengthening of the magnesium composite by reducing the grain size of the magnesium composite. Further enhancements, such as traditional alloy heat treatments (such as solutionizing, aging and/or cold working) can be used to enable control of dissolution rates through precipitation of more or less galvanically-active phases within the alloy microstructure while improving mechanical properties; however, this is not required. Because galvanic corrosion is driven by both the electro potential between the anode and cathode phase, as well as the exposed surface area of the two phases, the rate of corrosion can also be controlled through adjustment of the in situ formed particle size, while not increasing or decreasing the volume or weight fraction of the addition, and/or by changing the volume/weight fraction without changing the particle size. Achievement of in situ particle size control can be achieved by mechanical agitation of the melt, ultrasonic processing of the melt, controlling cooling rates, and/or by performing heat treatments. In situ particle size can also or alternatively be modified by secondary processing such as rolling, forging, extrusion and/or other deformation techniques.

In another non-limiting aspect of the invention, a cast structure can be made into almost any shape. During formation, the active galvanically-active in situ phases can be uniformly dispersed throughout the component and the grain or the grain boundary composition can be modified to achieve the desired dissolution rate. The galvanic corrosion can be engineered to affect only the grain boundaries and/or can affect the grains as well (based on composition); however, this is not required. This feature can be used to enable fast dissolutions of high-strength lightweight alloy composites with significantly less active (cathode) in situ phases as compared to other processes.

In still another and/or alternative non-limiting aspect of the invention, ultrasonic processing can be used to control the size of the in situ formed galvanically-active phases; however, this is not required. Ultrasonic energy is used to degass and grain refine alloys, particularly when applied in the solidification region. Ultrasonic and stirring can be used to refine the grain size in the alloy, thereby creating a high strength alloy and also reducing dispersoid size and creating more equiaxed (uniform) grains. Finer grains in the alloy have been found to reduce the degradation rate with equal amounts of additives.

In yet another and/or alternative non-limiting aspect of the invention, the in situ formed particles can act as matrix strengtheners to further increase the tensile strength of the material compared to the base alloy without the one or more additives; however, this is not required. For example, tin can be added to form a nanoscale precipitate (can be heat treated, e.g., solutionized and then precipitated to form precipitates inside the primary magnesium grains). The particles can be used to increase the strength of the alloy by at least 10%, and as much as greater than 100%, depending on other strengthening mechanisms (second phase, grain refinement, solid solution) strengthening present.

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a method of controlling the dissolution properties of a metal selected from the class of magnesium and/or magnesium alloy comprising of the steps of a) melting the magnesium or magnesium alloy to a point above its solidus, b) introducing one or more additives to the magnesium or magnesium alloy in order to achieve in situ precipitation of galvanically-active intermetallic phases, and c) cooling the melt to a solid form. The one or more additives are generally added to the magnesium or magnesium alloy when the magnesium or magnesium alloy is in a molten state and at a temperature that is less than the melting point of one or more additive materials. As can be appreciated, one or more additives can be added to the molten magnesium or magnesium alloy at a temperature that is greater than the melting point of the one or more additives. The one or more additives can be added as individual additive elements to the magnesium or magnesium alloy, or be added in alloy form as an alloy of two or more additives, or an alloy of one or more additives and magnesium or magnesium alloy. The galvanically-active intermetallic phases can be used to enhance the yield strength of the alloy; however, this is not required. The size of the in situ precipitated intermetallic phase can be controlled by a melt mixing technique and/or cooling rate; however, this is not required. It has been found that the addition of the one or more additives (SM) to the molten magnesium or magnesium alloy can result in the formation of MgSM_x, MgxSM, and LPSO and other phases with two, three, or even four components that include one or more galvanically-active additives that result in the controlled degradation of the formed magnesium composite when exposed to certain environments (e.g., salt water, brine, fracking liquids, etc.). The method can include the additional step of subjecting the magnesium composite to intermetallic precipitates to solutionizing of at least about 300° C. to improve tensile strength and/or improve ductility; however, this is not required. The solutionizing temperature is less than the melting point of the magnesium composite. Generally, the solutionizing temperature is less than 50-200° C. of the melting point of the magnesium composite and the time period of solutionizing is at least 0.1 hours. In one non-limiting aspect of the invention, the magnesium composite can be subjected to a solutionizing temperature for about 0.5-50 hours (and all values and ranges therebetween) (e.g., 1-15 hours, etc.) at a temperature of 300-620° C. (and all values and ranges therebetween) (e.g., 300-500° C., etc.). The method can include the additional step of subjecting the magnesium composite to intermetallic precipitates and to artificially age the magnesium composite at a temperature at least about 90° C. to improve the tensile strength; however, this is not required. The artificial aging process temperature is typically less than the solutionizing temperature and the time period of the artificial aging process temperature is typically at least 0.1 hours. Generally, the artificial aging process at is less than 50-400° C. (the solutionizing temperature). In one non-limiting aspect of the invention, the magnesium composite can be subjected to the artificial aging process for about 0.5-50 hours (and all values and ranges therebetween) (e.g., 1-16 hours, etc.) at a temperature of 90-300° C. (and all values and ranges therebetween) (e.g., 100-200° C.).

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is over 50 wt. % magnesium and about 0.5-49.5 wt. % of additive (SM) (e.g., aluminum, zinc, tin, beryllium, boron carbide, copper, nickel, bismuth, cobalt, titanium, manganese, potassium, sodium, antimony, indium, strontium, barium, silicon, lithium, silver, gold, cesium, gallium, calcium, iron, lead, mercury, arsenic, rare earth metals (e.g., yttrium, lanthanum, samarium, europium, gadolinium, terbium, dysprosium, holmium, ytterbium, etc.) and zirconium) (and all values and ranges therebetween) is added to the magnesium or magnesium alloy to form a galvanically-active intermetallic particle. The one or more additives can be added to the magnesium or magnesium alloy while the temperature of the molten magnesium or magnesium alloy is less than or greater than the melting point of the one or more additives. In one non-limiting embodiment, throughout the mixing process, the temperature of the molten magnesium or magnesium alloy can be less than the melting point of the one or more additives. In another non-limiting embodiment, throughout the mixing process, the temperature of the molten magnesium or magnesium alloy can be greater than the melting point of the one or more additives. In another non-limiting embodiment, throughout the mixing process, the temperature of the molten magnesium or magnesium alloy can be greater than the melting point of the one or more additives and less than the melting point of one or more other additives. In another non-limiting embodiment, throughout the mixing process, the temperature of the molten magnesium or magnesium alloy can be greater than the melting point of the alloy that includes one or more additives. In another non-limiting embodiment, throughout the mixing process, the temperature of the molten magnesium or magnesium alloy can be less than the melting point of the alloy that includes one or more additives.

During the mixing process, solid particles of SMMg_x, SM_xMg can be formed. Once the mixing process is complete, the mixture of molten magnesium or magnesium alloy, SMMg_x, SM_xMg, and/or any unalloyed additive is cooled and an in situ precipitate is formed in the solid magnesium composite.

In another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is over 50 wt. % magnesium and about 0.05-49.5 wt. % nickel (and all values or ranges therebetween) is added to the magnesium or magnesium alloy to form intermetallic Mg₂Ni as a galvanically-active in situ precipitate. In one non-limiting arrangement, the magnesium composite includes about 0.05-23.5 wt. % nickel, 0.01-5 wt. % nickel, 3-7 wt. % nickel, 7-10 wt. % nickel, or 10-24.5 wt. % nickel. The nickel is added to the magnesium or magnesium alloy while the temperature of the molten magnesium or magnesium alloy is less than the melting point of the nickel; however, this is not required. In one non-limiting embodiment, throughout the mixing process, the temperature of the molten magnesium or magnesium alloy is less than the melting point of the nickel. During the mixing process, solid particles of Mg₂Ni can be formed; but is not required. Once the mixing process is complete, the mixture of molten magnesium or magnesium alloy, any solid particles of Mg₂Ni, and any unalloyed nickel particles are cooled and an in situ precipitate of any solid particles of Mg₂Ni and any unalloyed nickel particles is formed in the solid magnesium composite. Generally, the temperature of the molten magnesium or magnesium alloy is at least about 200° C. less than the melting point of the nickel added to the molten magnesium or magnesium alloy during the addition and mixing process; however, this is not required.

In still another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is over 50 wt. % magnesium and about 0.05-49.5 wt. % copper (and all values or ranges therebetween) is added to the magnesium or magnesium alloy to form galvanically-active in situ precipitate that includes copper and/or copper alloy. In one non-limiting arrangement, the magnesium composite includes about 0.01-5 wt. % copper, about 0.5-15 wt. % copper, about 15-35 wt. % copper, or about 0.01-20 wt. % copper. The copper is added to the magnesium or magnesium alloy while the temperature of the molten magnesium or magnesium alloy is less than the melting point of the copper; however, this is not required. In one non-limiting embodiment, throughout the mixing process, the temperature of the molten magnesium or magnesium alloy is less than the melting point of the copper; however, this is not required. During the mixing process, solid particles of CuMg₂can be formed; but is not required. Once the mixing process is complete, the mixture of molten magnesium or magnesium alloy, any solid particles of CuMg₂, and any unalloyed copper particles are cooled and an in situ precipitate of any solid particles of CuMg₂and any unalloyed copper particles is formed in the solid magnesium composite. Generally, the temperature of the molten magnesium or magnesium alloy is at least about 200° C. less than the melting point of the copper added to the molten magnesium or magnesium alloy; however, this is not required.

In yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is over 50 wt. % magnesium and about 0.05-49.5% by weight cobalt (and all values and ranges therebetween) is added to the magnesium or magnesium alloy to form galvanically active in situ precipitate that includes cobalt and/or cobalt alloy. In one non-limiting arrangement, the magnesium composite includes about 0.01-5 wt. % cobalt, about 0.5-15 wt. % cobalt, about 15-35 wt. % cobalt, or about 0.01-20 wt. % cobalt. The cobalt is added to the magnesium or magnesium alloy while the temperature of the molten magnesium or magnesium alloy is less than the melting point of the cobalt; however, this is not required. In one non-limiting embodiment, throughout the mixing process, the temperature of the molten magnesium or magnesium alloy is less than the melting point of the cobalt; however, this is not required. During the mixing process, solid particles of CoMg₂and/or Mg_xCo can be formed; but is not required. Once the mixing process is complete, the mixture of molten magnesium or magnesium alloy, any solid particles of CoMg₂, Mg_xCo, any solid particles of any unalloyed cobalt particles are cooled and an in situ precipitate of any solid particles of CoMg₂, Mg_xCo, any solid particles of unalloyed cobalt particles is formed in the solid magnesium composite. Generally, the temperature of the molten magnesium or magnesium alloy is at least about 200° C. less than the melting point of the cobalt added to the molten magnesium or magnesium alloy; however, this is not required.

In another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is over 50 wt. % magnesium and up to about 49.5% by weight bismuth (and all values and ranges therebetween) is added to the magnesium or magnesium alloy to form galvanically-active in situ precipitate that includes bismuth and/or bismuth alloy. Bismuth intermetallics are formed above roughly 0.1 wt. % bismuth, and bismuth is typically useful up to its eutectic point of roughly 11 wt. % bismuth. Beyond the eutectic point, a bismuth intermetallic is formed in the melt. This is typical of additions, in that the magnesium-rich side of the eutectic forms flowable, castable materials with active precipitates or intermetallics formed at the solidus (in the eutectic mixture), rather than being the primary, or initial, phase solidified. In desirable alloy formulations, alpha magnesium (may be in solid solution with alloying elements) should be the initial/primary phase formed upon initial cooling. In one non-limiting embodiment, bismuth is added to the magnesium composite at an amount of greater than 11 wt. %, and typically about 11.1-30 wt. % (and all values and ranges therebetween).

In another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is over 50 wt. % magnesium and up to about 49.5% by weight tin (and all values and ranges therebetween) is added to the magnesium or magnesium alloy to form galvanically-active in situ precipitate that includes tin and/or tin alloy. Tin additions have a significant solubility in solid magnesium at elevated temperatures, forming both a eutectic (at grain boundaries), as well as in the primary magnesium (dispersed). Dispersed precipitates, which can be controlled by heat treatment, lead to large strengthening, while eutectic phases are particularly effective at initiating accelerated corrosion rates. In one non-limiting embodiment, tin is added to the magnesium composite at an amount of at least 0.5 wt. %, typically about 1-30 wt. % (and all values and ranges therebetween), and more typically about 1-10 wt. %.

In another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is over 50 wt. % magnesium and up to about 49.5% by weight gallium (and all values and ranges therebetween) is added to the magnesium or magnesium alloy to form galvanically active in situ precipitate that includes gallium and/or gallium alloy. Gallium additions are particularly effective at initiating accelerated corrosion, in concentrations that form up to 3-5 wt. % Mg₅Ga₂. Gallium alloys are heat treatable forming corrodible high strength alloys. Gallium is fairly unique, in that it has high solubility in solid magnesium, and forms highly corrosive particles during solidification which are located inside the primary magnesium (when below the solid solubility limit), such that both grain boundary and primary (strengthening precipitates) are formed in the magnesium-gallium systems and also in magnesium-indium systems. At gallium concentrations of less than about 3 wt. %, additional superheat (higher melt temperatures) is typically used to form the precipitate in the magnesium alloy. To place Mg₅Ga₂particles at the grain boundaries, gallium concentrations above the solid solubility limit at the pouring temperature are used such that Mg₅Ga₂phase is formed from the eutectic liquid. In one non-limiting embodiment, gallium is added to the magnesium composite at an amount of at least 1 wt. %, and typically about 1-10 wt. % and all values and ranges therebetween), typically 2-8 wt. %, and more typically 3.01-5 wt. %.

In another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is over 50 wt. % magnesium and up to about 49.5% by weight indium (and all values and ranges therebetween) is added to the magnesium or magnesium alloy to form galvanically-active in situ precipitate that includes indium and/or indium alloy. Indium additions have also been found effective at initiating corrosion. In one non-limiting embodiment, indium is added to the magnesium composite at an amount of at least 1 wt. %, and typically about 1-30 wt. % (and all values and ranges therebetween).

In general, precipitates having an electronegativity greater than 1.4-1.5 act as corrosion acceleration points, and are more effective if formed from the eutectic liquid during solidification, than precipitation from a solid solution. Alloying additions added below their solid solubility limit which precipitate in the primary magnesium phase during solidification (as opposed to along grain boundaries), and which can be solutionized are more effective in creating higher strength, particularly in as-cast alloys.

In another and/or alternative non-limiting aspect of the invention, the molten magnesium or magnesium alloy that includes the one or more additives can be controllably cooled to form the in situ precipitate in the solid magnesium composite. In one non-limiting embodiment, the molten magnesium or magnesium alloy that includes the one or more additives is cooled at a rate of greater than 1° C. per minute. In one non-limiting embodiment, the molten magnesium or magnesium alloy that includes the one or more additives is cooled at a rate of less than 1° C. per minute. In one non-limiting embodiment, the molten magnesium or magnesium alloy that includes the one or more additives is cooled at a rate of greater than 0.01° C. per min and slower than 1° C. per minute. In one non-limiting embodiment, the molten magnesium or magnesium alloy that includes the one or more additives is cooled at a rate of greater than 10° C. per minute and less than 100° C. per minute. In one non-limiting embodiment, the molten magnesium or magnesium alloy that includes the one or more additives is cooled at a rate of less than 10° C. per minute. In another non-limiting embodiment, the molten magnesium or magnesium alloy that includes the one or more additives is cooled at a rate 10-100° C/min (and all values and ranges therebetween) through the solidus temperature of the alloy to form fine grains in the alloy.

In another and/or alternative non-limiting aspect of the invention, there is provided a magnesium alloy that includes over 50 wt. % magnesium (e.g., 50.01-99.99 wt. % and all values and ranges therebetween) and includes at least one metal selected from the group consisting of aluminum, boron, bismuth, zinc, zirconium, and manganese. As can be appreciated, the magnesium alloy can include one or more additional metals. In one non-limiting embodiment, the magnesium alloy includes over 50 wt. % magnesium and includes at least one metal selected from the group consisting of aluminum in an amount of about 0.05-10 wt. % (and all values and ranges therebetween), zinc in amount of about 0.05-6 wt. % (and all values and ranges therebetween), zirconium in an amount of about 0.01-3 wt. % (and all values and ranges therebetween), and/or manganese in an amount of about 0.015-2 wt. % (and all values and ranges therebetween). In another non-limiting formulation, the magnesium alloy includes over 50 wt. % magnesium and includes at least one metal selected from the group consisting of zinc in amount of about 0.05-6 wt. %, zirconium in an amount of about 0.05-3 wt. %, manganese in an amount of about 0.05-0.25 wt. %, boron (optionally) in an amount of about 0.0002-0.04 wt. %, and bismuth (optionally) in an amount of about 0.4-0.7 wt. %. In still another and/or alternative non-limiting aspect of the invention, there is provided a magnesium alloy that is over 50 wt. % magnesium and at least one metal selected from the group consisting of aluminum in an amount of about 0.05-10 wt. % (and all values and ranges therebetween), zinc in an amount of about 0.05-6 wt. % (and all values and ranges therebetween), calcium in an amount of about 0.5-8 wt. %% (and all values and ranges therebetween), zirconium in amount of about 0.05-3 wt. % (and all values and ranges therebetween), manganese in an amount of about 0.05-0.25 wt. % (and all values and ranges therebetween), boron in an amount of about 0.0002-0.04 wt. % (and all values and ranges therebetween), and/or bismuth in an amount of about 0.04-0.7 wt. % (and all values and ranges therebetween),

In still another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is over 50 wt. % magnesium and includes one or more additives in the form of a first additive that has an electronegativity that is greater than 1.5, and typically greater than 1.8. The electronegativity of magnesium is 1.31. As such, the first additive has a higher electronegativity than magnesium. The first additive can include one or more metals selected from the group consisting of nickel (1.91), cobalt (1.88), copper (1.90), bismuth (2.02), lead (1.87), tin (1.96), antimony (2.05), indium (1.78), silver (1.93), gold (2.54), and gallium (1.81). It has been found that by adding one or more first additives to a molten magnesium or molten magnesium alloy, galvanically-active phases can be formed in the solid magnesium composite having desired dissolution rates in salt water, fracking liquid or brine environments. The one or more first additives are added to the molten magnesium or molten magnesium alloy such that the final magnesium composite includes 0.05-49.55% by weight of the one or more first additives (and all values and ranges therebetween), and typically 0.5-35% by weight of the one or more first additives. The one or more first additives having an electronegativity that is greater than 1.5 have been found to form galvanically-active phases in the solid magnesium composite to enhance the dissolution rate of the magnesium composite in salt water, fracking liquid or brine environments.

In yet another and/or alternative non-limiting aspect of the invention, it has been found that in addition to the adding of one or more first additives having an electronegativity that is greater than 1.5 to the molten magnesium or molten magnesium alloy to enhance the dissolution rates of the magnesium composite in salt water, fracking liquid or brine environments, one or more second additives that have an electronegativity of 1.25 or less can also be added to the molten magnesium or molten magnesium alloy to further enhance the dissolution rates of the solid magnesium composite. The one or more second additives can optionally be added to the molten magnesium or molten magnesium alloy such that the final magnesium composite includes 0.05-35% by weight of the one or more second additives (and all values and ranges therebetween), and typically 0.5-30% by weight of the one or more second additives. The second additive can include one or more metals selected from the group consisting of calcium (1.0), strontium (0.95), barium (0.89), potassium (0.82), sodium (0.93), lithium (0.98), cesium (0.79), and the rare earth metals such as yttrium (1.22), lanthanum (1.1), samarium (1.17), europium (1.2), gadolinium (1.2), terbium (1.1), dysprosium (1.22), holmium (1.23), and ytterbium (1.1).

Secondary additives are usually added at 0.5-10 wt. %, and generally 0.1-3 wt. %. In one non-limiting embodiment, the amount of secondary additive is less than the primary additive; however, this is not required. For example, calcium can be added up to 10 wt. %, but is added normally at 0.5-3 wt. %. In most cases, the strengthening alloying additions or modifying materials are added in concentrations which can be greater than the high electronegativity corrosive phase forming element. The secondary additions are generally designed to have high solubility, and are added below their solid solubility limit in magnesium at the melting point, but above their solid solubility limit at some lower temperature. These form precipitates that strengthen the magnesium, and may or may not be galvanically active. They may form a precipitate by reacting preferentially with the high electronegativity addition (e.g., binary, ternary, or even quaternary intermetallics) with magnesium, or with other alloying additions.

The one or more secondary additives that have an electronegativity that is 1.25 or less have been found to form galvanically-active phases in the solid magnesium composite to enhance the dissolution rate of the magnesium composite in salt water, fracking liquid or brine environments are. The inclusion of the one or more second additives with the one or more first additives in the molten magnesium or magnesium alloy has been found to enhance the dissolution rate of the magnesium composite by 1) alloying with inhibiting aluminum, zinc, magnesium, alloying additions and increasing the EMF driving force with the galvanically-active phase, and/or 2) reducing the electronegativity of the magnesium (e.g., α-magnesium) phase when placed in solid solution or magnesium-EPE (electropositive element) intermetallics. The addition of materials with an electronegativity that is less than magnesium, such as rare earths, group 1, and group II, and group III elements on the periodic table, can enhance the degradability of the alloy when a high electronegativity addition is also present by reducing the electronegativity (increasing the driving force) in solid solution in magnesium, and/or by forming lower electronegativity precipitates that interact with the higher electronegativity precipitates. This technique/additions is particularly effective at reducing the sensitivity of the corrosion rates to temperature or salt content of the corroding or downhole fluid.

The addition of both electropositive (1.5 or greater) first additives and electronegative (1.25 or less) second additives to the molten magnesium or magnesium alloy can result in higher melting phases being formed in the magnesium composite. These higher melting phases can create high melt viscosities and can dramatically increase the temperature (and therefore the energy input) required to form the low viscosity melts suitable for casting. By dramatically increasing the casting temperature to above 700-780° C., or utilizing pressure to drive mold filling (e.g., squeeze casting), such processes can be used to produce a high quality, low-inclusion and low-porosity magnesium composite casting.

In yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is subjected to heat treatments such as solutionizing, aging and/or cold working to be used to control dissolution rates through precipitation of more or less galvanically-active phases within the alloy microstructure while improving mechanical properties. The artificial aging process (when used) can be for at least about 1 hour, for about 1-50 hours (and all values and ranges therebetween), for about 1-20 hours, or for about 8-20 hours. The solutionizing (when used) can be for at least about 1 hour, for about 1-50 hours (and all values and ranges therebetween), for about 1-20 hours, or for about 8-20 hours. When an alloy with a galvanically-active phase (higher and/or lower electronegativity than Mg) with significant solid solubility is solutionized, substantial differences in corrosion/degradation rates can be achieved through mechanisms of oswald ripening or grain growth (coarsening of the active phases), which increases corrosion rates by 10-100% (and all values and ranges therebewteen). When the solutionizing removes active phase and places it in solid solution, or creates finer precipitates (refined grain sizes), corrosion rates are decreased by 10-50%, up to about 75%.

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a method for controlling the dissolution rate of the magnesium composite wherein the magnesium content is at least about 75% and at least about 0.05 wt. % nickel is added to form in situ precipitation in the magnesium or magnesium alloy and solutionizing the resultant metal at a temperature within a range of 100-500° C. (and all values and ranges therebetween) for a period of 0.25-50 hours (and all values and ranges therebetween), the magnesium composite being characterized by higher dissolution rates than metal without nickel additions subjected to the said artificial aging process.

In another and/or alternative non-limiting aspect of the invention, there is provided a method for improving the physical properties of the magnesium composite wherein the magnesium content is at least about 85% and at least about 0.05 wt. % nickel is added to form in situ precipitation in the magnesium or magnesium alloy and solutionizing the resultant metal at a temperature at about 100-500° C. (and all values and ranges therebetween) for a period of 0.25-50 hours, the magnesium composite being characterized by higher tensile and yield strengths than magnesium base alloys of the same composition, not including the amount of nickel.

In still another and/or alternative non-limiting aspect of the invention, there is provided a method for controlling the dissolution rate of the magnesium composite wherein the magnesium content in the alloy is at least about 75% and at least about 0.05 wt. % copper is added to form in situ precipitation in the magnesium or magnesium alloy and solutionizing the resultant metal at a temperature within a range of 100-500° C. for a period of 0.25-50 hours, the magnesium composite being characterized by higher dissolution rates than metal without copper additions subjected to the said artificial aging process.

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that includes the addition of calcium to galvanically-active magnesium-aluminum-(X) alloys with X being a galvanically-active intermetallic forming phase such as, but not limited to, nickel, copper, or cobalt to further control the degradation rate of the alloys, further increase the use and extrusion temperature of the magnesium composite, and/or reduce the potential for flammability during formation of the magnesium composite, thereby increasing safety. Calcium has a higher standard electrode potential than magnesium at −2.87V as compared to −2.37V for magnesium relative to standard hydrogen electrode (SHE). This electrode potential of calcium makes the galvanic potential between other metallic ions significantly higher, such as nickel (−0.25V), copper (+0.52V) and iron (−0.44V). The difference in galvanic potential also depends on other alloying elements with respect to microstructural location. In alloys where only magnesium and calcium are present, the difference in galvanic potential can change the degradation behavior of the alloy by leading to a greater rate of degradation in the alloy. However, the mechanism for dissolution speed change in the galvanically-active alloys created by intermetallic phases such as magnesium-nickel, magnesium-copper, and magnesium-cobalt is actually different. In the case of the magnesium-aluminum-calcium-(X) with X being a galvanically-active intermetallic forming phase such as nickel, copper, or cobalt with aluminum in the alloy, the calcium typically bonds with the aluminum (−1.66V), and this phase precipitates next to the magnesium matrix. The Mg₁₇Al₁₂phase that is normally precipitated in a magnesium-aluminum-(X) with X being a galvanically-active intermetallic forming phase such as nickel, copper, or cobalt alloy is the primary contributor to a reduced and controlled degradation of the alloy.

By introducing calcium into the alloy, the amount of Mg₁₇Al₁₂is reduced in the alloy, thus increasing the ratio of magnesium-(X) phase to the pure magnesium alloy and thereby reducing the galvanic corrosion resistance of the Mg₁₇Al₁₂phase, which result in the further increase of the degradation rate of the magnesium-aluminum-calcium-(X) alloy as compared to magnesium-aluminum-(X) alloys. This feature of the alloy is new and unexpected because it is not just the addition of a higher standard electrode potential that is causing the degradation, but is also the reduction of a corrosion inhibitor by causing the formation of a different phase in the alloy. The calcium addition within the magnesium alloy forms an alternative phase with aluminum alloying elements. The calcium bonds with aluminum within the alloy to form lamellar Al₂Ca precipitates along the grain boundary of the magnesium matrix. These precipitates act as nucleation sites during cooling (due to their low energy barrier for nucleation) leading to decreased grain size and thereby higher strength for the magnesium alloy. However, the lamellar precipitates on a microscopic level tend to shear or cut into the alloy matrix and lead to crack propagation and can offset the beneficial strengthening of the grain refinement if an excessive amount of the Al₂Ca phase is formed. The offsetting grain structure effects typically lead to a minimal improvement on tensile strength of the magnesium-aluminum-calcium alloy, if any. This seems to lead to no significant reduction in tensile strength of the alloy. The significant advantage for the addition of calcium in a magnesium-aluminum alloy is in the improved incipient melting temperature when the Al₂Ca phase is formed as opposed to Mg₁₇Al₁₂. Al₂Ca has a melting temperature of approximately 1080° C. as opposed to 460° C. for the magnesium-aluminum phase, which means a higher incipient melting point for the alloy. This solution leads to a larger hot deformation processing window or, more specifically, greater speeds during extrusion or rolling. These greater speeds can lead to lower cost production and a safer overall product. Another benefit of the calcium addition into the alloy is reduced oxidation of the melt. This feature is a result of the CaO layer which forms on the surface of the melt. In melt protection, the thickness and density of the calcium layer benefits the melt through formation of a reinforced CaO—MgO oxide layer when no other elements are present. This layer reduces the potential for “burning” in the foundry, thus allows for higher casting temperatures, reduced cover gas, reduced flux use and improved safety and throughput. The oxide layer also significantly increases the ignition temperature by eliminating the magnesium oxide layer typically found on the surface and replacing it with the much more stable CaO. The calcium addition in the magnesium alloy is generally at least 0.05 wt. % and generally up to about 30 wt. % (and all values and ranges therebetween), and typically 0.1-15 wt. %. MN The developed alloys can be degraded in solutions with salt contents as low as 0.01% at a rate of 1-100 mg/cm²-hr. (and all values and ranges therebetween) at a temperature of 20-100° C. (and all values and ranges therebetween). The calcium additions work to enhance degradation in this alloy system, not by traditional means of adding a higher standard electrode potential material as would be common practice, but by actually reducing the corrosion inhibiting phase of Mg₁₇Al₁₂by the precipitation of Al₂Ca phases that are mechanically just as strong, but do not inhibit the corrosion. As such, alloys can be created with higher corrosion rates just as alloys can be created by reducing aluminum content, but without strength degradation and the added benefit of higher use temperature, higher incipient melting temperatures and/or lower flammability. The alloy is a candidate for use in all degradation applications such as downhole tools, temporary structures, etc. where strength and high use temperature are a necessity and it is desirable to have a greater rate of dissolving or degradation rates in low-salt concentration solutions.

In yet another and/or alternative non-limiting aspect of the invention, there is provided a method for improving the physical properties of the magnesium composite wherein the total content of magnesium in the magnesium or magnesium alloy is at least about 85 wt. % and copper is added to form in situ precipitation in the magnesium or magnesium composite and solutionizing the resultant metal at a temperature of about 100-500° C. for a period of 0.25-50 hours. The magnesium composite is characterized by higher tensile and yield strengths than magnesium-based alloys of the same composition, but not including the amount of copper.

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite for use as a dissolvable ball or frac ball in hydraulic fracturing and well drilling.

In another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite for use as a dissolvable tool for use in well drilling and hydraulic control as well as hydraulic fracturing.

In another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that has controlled dissolution or degradation for use in temporarily isolating a wellbore.

In another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that can be used to partially or full form a mandrel, slip, grip, ball, frac ball, dart, sleeve, carrier, or other downhole well component.

In another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that can be used for controlling fluid flow or mechanical activation of a downhole device.

In still another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that includes secondary in situ formed reinforcements that are not galvanically active to the magnesium or magnesium alloy matrix to increase the mechanical properties of the magnesium composite. The secondary in situ formed reinforcements can optionally include a Mg₂Si phase as the in situ formed reinforcement.

In yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is subjected to a greater rate of cooling from the liquidus to the solidus point to create smaller in situ formed particles,

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is subjected to a slower rate of cooling from the liquidus to the solidus point to create larger in situ formed particles.

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a method for controlling the dissolution rate of the magnesium composite wherein the magnesium content is at least about 75 wt. % and at least 0.05 wt. % nickel is added to form in situ precipitation in the magnesium or magnesium alloy and solutionizing the resultant metal at a temperature within a range of 100-500° C. for a period of 0.25-50 hours, the magnesium composite being characterized by higher dissolution rates than metal without nickel additions subjected to the said artificial aging process.

In another and/or alternative non-limiting aspect of the invention, there is provided a method for improving the physical properties of the magnesium composite wherein the magnesium content is at least about 85 wt. % and at least 0.05 wt. % nickel is added to form in situ precipitation in the magnesium or magnesium alloy and solutionizing the resultant metal at a temperature at about 100-500° C. for a period of 0.25-50 hours, the magnesium composite being characterized by higher tensile and yield strengths than magnesium base alloys of the same composition, but not including the amount of nickel.

In still another and/or alternative non-limiting aspect of the invention, there is provided a method for controlling the dissolution rate of the magnesium composite wherein the magnesium content in the alloy is at least about 75 wt. % and at least 0.05 wt. % copper is added to form in situ precipitation in the magnesium or magnesium alloy and solutionizing the resultant metal at a temperature within a range of 100-500° C. for a period of 0.25-50 hours, the magnesium composite being characterized by higher dissolution rates than metal without copper additions subjected to the said artificial aging process.

In yet another and/or alternative non-limiting aspect of the invention, there is provided a method for improving the physical properties of the magnesium composite wherein the total content of magnesium in the magnesium or magnesium alloy is at least about 85 wt. % and at least 0.05 wt. % copper is added to form in situ precipitation in the magnesium or magnesium composite and solutionizing the resultant metal at a temperature of about 100-500° C. for a period of 0.25-50 hours, the magnesium composite being characterized by higher tensile and yield strengths than magnesium base alloys of the same composition, but not including the amount of copper.

In still another and/or alternative non-limiting aspect of the invention, the additive generally has a solubility in the molten magnesium or magnesium alloy of less than about 10% (e.g., 0.01-9.99% and all values and ranges therebetween), typically less than about 5%, more typically less than about 1%, and even more typically less than about 0.5%.

In still another and/or alternative non-limiting aspect of the invention, the additive can optionally have a surface area of 0.001-200 m²/g (and all values and ranges therebetween). The additive in the magnesium composite can optionally be less than about 1 μm in size (e.g., 0.001-0.999 μm and all values and ranges therebetween), typically less than about 0.5 μm, more typically less than about 0.1 μm, and more typically less than about 0.05 μm. The additive can optionally be dispersed throughout the molten magnesium or magnesium alloy using ultrasonic means, electrowetting of the insoluble particles, and/or mechanical agitation. In one non-limiting embodiment, the molten magnesium or magnesium alloy is subjected to ultrasonic vibration and/or waves to facilitate in the dispersion of the additive in the molten magnesium or magnesium alloy.

In still yet another and/or alternative non-limiting aspect of the invention, a plurality of additives in the magnesium composite are located in grain boundary layers of the magnesium composite.

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a method for forniing a magnesium composite that includes a) providing magnesium or a magnesium alloy, b) providing one or more additives that have a low solubility when added to magnesium or a magnesium alloy when in a molten state; c) mixing the magnesium or a magnesium alloy and the one or more additives to form a mixture and to cause the one or more additives to disperse in the mixture; and d) cooling the mixture to form the magnesium composite. The step of mixing optionally includes mixing using one or more processes selected from the group consisting of thixomolding, stir casting, mechanical agitation, electrowetting and ultrasonic dispersion. The method optionally includes the step of heat treating the magnesium composite to improve the tensile strength, elongation, or combinations thereof of the magnesium composite without significantly affecting a dissolution rate of the magnesium composite. The method optionally includes the step of extruding or deforming the magnesium composite to improve the tensile strength, elongation, or combinations thereof of the magnesium composite without significantly affecting a dissolution rate of the magnesium composite. The method optionally includes the step of forming the magnesium composite into a device that a) facilitates in separating hydraulic fracturing systems and zones for oil and gas drilling, b) provides structural support or component isolation in oil and gas drilling and completion systems, or c) is in the form of a frac ball, valve, or degradable component of a well composition tool or other tool. Other types of structures that the magnesium composite can be partially or fully formed into include, but are not limited to, sleeves, valves, hydraulic actuating tooling and the like. Such non-limiting structures or additional non-limiting structure are illustrated in U.S. Pat. Nos. 8,905,147; 8,717,268; 8,663,401; 8,631,876; 8,573,295; 8,528,633; 8,485,265; 8,403,037; 8,413,727; 8,211,331; 7,647,964; U.S. Publication Nos. 2013/0199800; 2013/0032357; 2013/0029886; 2007/0181224; and WO 2013/122712, all of which are incorporated herein by reference.

In still another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that includes secondary in situ formed reinforcements that are not galvanically active to the magnesium or magnesium alloy matrix to increase the mechanical properties of the magnesium composite. The secondary in situ formed reinforcements include a Mg₂Si phase or silicon particle phase as the in situ formed reinforcement.

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is subjected to a slower cooling rate from the liquidus to the solidus point to create larger in situ formed particles.

In another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is subjected to mechanical agitation during the cooling rate from the liquidus to the solidus point to create smaller in situ formed particles.

In still another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is subjected to chemical agitation during the cooling rate from the liquidus to the solidus point to create smaller in situ formed particles.

In yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is subjected to ultrasonic agitation during the cooling rate from the liquidus to the solidus point to create smaller in situ formed particles.

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that is subjected to deformation or extrusion to further improve dispersion of the in situ formed particles.

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that has a dissolve rate or dissolution rate of at least about 30 mg/cm²-hr in 3% KCl solution at 90° C., and typically 30-500 mg/cm²-hr in 3% KCl solution at 90° C. (and all values and ranges therebetween).

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that has a dissolve rate or dissolution rate of at least about 0.2 mg/cm -min a 3% KCl solution at 90° C., and typically 0.2-150 trig/cm -min n a 3% KCl solution at 90° C. (and all values and ranges therebetween).

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that has a dissolve rate or dissolution rate of at least about 0.1 mg/cm²-hr in a 3% KCl solution at 21° C., and typically 0.1-5 mg/cm²-hr in a 3% KCl solution at 21° C. (and all values and ranges therebetween).

In still yet another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that has a dissolve rate or dissolution rate of at least about 0.1 mg/cm²-hr in 3% KCl solution at 20° C., typically 0.1-5 mg/cm²-hr in a 3% KCl solution at 20° C. (and all values and ranges therebetween).

In another and/or alternative non-limiting aspect of the invention, there is provided a method for forming a novel magnesium composite including the steps of a) selecting an AZ91D magnesium alloy having 9 wt. % aluminum, 1 wt. % zinc and 90 wt. % magnesium, b) melting the AZ91 D magnesium alloy to a temperature above 800° C., c) adding up to about 7 wt. % nickel to the melted AZ91D magnesium alloy at a temperature that is less than the melting point of nickel, d) mixing the nickel with the melted AZ91D magnesium alloy and dispersing the nickel in the melted alloy using chemical mixing agents while maintaining the temperature below the melting point of nickel, and e) cooling and casting the melted mixture in a steel mold. The cast material has a tensile strength of about 14 ksi, and an elongation of about 3% and a shear strength of 11 ksi. The cast material has a dissolve rate of about 75 mg/cm²-min in a 3% KCl solution at 90° C. The cast material dissolves at a rate of 1 mg/cm²-hr in a 3% KCl solution at 21° C. The cast material dissolves at a rate of 325 mg/cm -hr. in a 3% KCl solution at 90° C. The cast material can be subjected to extrusion with an 11:1 reduction area. The extruded cast material exhibits a tensile strength of 40 ksi, and an elongation to failure of 12%. The extruded cast material dissolves at a rate of 0.8 mg/cm²-min in a 3% KCl solution at 20° C. The extruded cast material dissolves at a rate of 100 mg/cm²-hr. in a 3% KCl solution at 90° C. The extruded cast material can be subjected to an artificial T5 age treatment of 16 hours between 100-200° C. The aged and extruded cast material exhibits a tensile strength of 48 ksi, an elongation to failure of 5%, and a shear strength of 25 ksi. The aged extruded cast material dissolves at a rate of 110 mg/cm²-hr in 3% KCl solution at 90° C. and 1 mg/cm²-hr in 3% KCl solution at 20° C. The cast material can be subjected to a solutionizing treatment T4 for about 18 hours between 400-500° C. and then subjected to an artificial T6 age treatment for about 16 hours between 100-200° C. The aged and solutionized cast material exhibits a tensile strength of about 34 ksi, an elongation to failure of about 11%, and a shear strength of about 18 ksi. The aged and solutionized cast material dissolves at a rate of about 84 mg/cm²-hr in 3% KCl solution at 90° C., and about 0.8 mg/cm²-hr in 3% KCl solution at 20° C.

In another and/or alternative non-limiting aspect of the invention, there is provided a method for forming a novel magnesium composite including the steps of a) selecting an AZ91D magnesium alloy having 9 wt. % aluminum, 1 wt. % zinc and 90 wt. % magnesium, b) melting the AZ91D magnesium alloy to a temperature above 800° C., c) adding up to about 1 wt. % nickel to the melted AZ91D magnesium alloy at a temperature that is less than the melting point of nickel, d) mixing the nickel with the melted AZ91D magnesium alloy and dispersing the nickel in the melted alloy using chemical mixing agents while maintaining the temperature below the melting point of nickel, and e) cooling and casting the melted mixture in a steel mold. The cast material has a tensile strength of about 18 ksi, and an elongation of about 5% and a shear strength of 17 ksi. The cast material has a dissolve rate of about 45 mg/cm²-min in a 3% KCl solution at 90° C. The cast material dissolves at a rate of 0.5 mg/cm -hr. in a 3% KCl solution at 21° C. The cast material dissolves at a rate of 325 mg/cm²-hr. in a 3% KCl solution at 90° C. The cast material is subjected to extrusion with a 20:1 reduction area. The extruded cast material exhibits a tensile yield strength of 35 ksi, and an elongation to failure of 12%. The extruded cast material dissolves at a rate of 0.8 mg/cm²-min in a 3% KCl solution at 20° C. The extruded cast material dissolves at a rate of 50 mg/cm²-hr in a 3% KCl solution at 90° C. The extruded cast material can be subjected to an artificial T5 age treatment of 16 hours between 100-200° C. The aged and extruded cast material exhibits a tensile strength of 48 ksi, an elongation to failure of 5%, and a shear strength of 25 ksi.

In still another and/or alternative non-limiting aspect of the invention, there is provided a method for forming a novel magnesium composite including the steps of a) selecting an AZ91D magnesium alloy having about 9 wt. % aluminum, 1 wt. % zinc and 90 wt. % magnesium, b) melting the AZ91D magnesium alloy to a temperature above 800° C., c) adding about 10 wt. % copper to the melted AZ91D magnesium alloy at a temperature that is less than the melting point of copper, d) dispersing the copper in the melted AZ91D magnesium alloy using chemical mixing agents at a temperature that is less than the melting point of copper, and e) cooling casting the melted mixture in a steel mold. The cast material exhibits a tensile strength of about 14 ksi, an elongation of about 3%, and shear strength of 11 ksi. The cast material dissolves at a rate of about 50 mg/cm²-hr. in a 3% KCl solution at 90° C. The cast material dissolves at a rate of 0.6 mg/cm²-hr. in a 3% KCl solution at 21° C. The cast material can be subjected to an artificial T5 age treatment for about 16 hours at a temperature of 100-200° C. The aged cast material exhibits a tensile strength of 50 ksi, an elongation to failure of 5%, and a shear strength of 25 ksi. The aged cast material dissolved at a rate of 40 mg/cm²-hr in 3% KCl solution at 90° C. and 0.5 mg/cm²-hr in 3% KCl solution at 20° C.

In still another and/or alternative non-limiting aspect of the invention, there is provided a method for forming a novel magnesium composite including the steps of a) providing magnesium having a purity of at least 99.9%, b) providing antimony having a purity of at least 99.8%, c) adding the magnesium and antimony in the crucible (e.g., carbon steel crucible), d) optionally adding a flux to the top of the metals in the crucible, e) optionally heating the metals in the crucible to 250° C. for about 2-60 minutes, f) heating the metals in the crucible to 650-720° C. to cause the magnesium to melt, and g) cooling the molten magnesium to form a magnesium composite that includes about 7 wt. % antimony. The density of the magnesium composite is 1.69 g/cm³, the hardness is 6.8 Rockwell Hardness B, and the dissolution rate in 3% solution of KCl at 90° C. is 20.09 mg/cm²-hr.

in still another and/or alternative non-limiting aspect of the invention, there is provided a method for forming a novel magnesium composite including the steps of a) providing magnesium having a purity of at least 99.9%, b) providing gallium having a purity of at least 99.9%, c) adding the magnesium and gallium in the crucible (e.g., carbon steel crucible), d) optionally adding a flux to the top of the metals in the crucible, e) optionally heating the metals in the crucible to 250° C. for about 2-60 minutes, f) heating the metals in the crucible to 650-720° C. to cause the magnesium to melt, and g) cooling the molten magnesium to form a magnesium composite that includes about 5 wt. % gallium. The density of the magnesium composite is 1.80 g/cm³, the hardness is 67.8 Rockwell Hardness B, and the dissolution rate in 3% solution of KCl at 90° C. is 093 mg/cm²-hr.

In still another and/or alternative non-limiting aspect of the invention, there is provided a method for forming a novel magnesium composite including the steps of a) providing magnesium having a purity of at least 99.9%, b) providing tin having a purity of at least 99.9%, c) adding the magnesium and tin in the crucible (e.g., carbon steel crucible), d) optionally adding a flux to the top of the metals in the crucible, e) optionally heating the metals in the crucible to 250° C. for about 2-60 minutes, f) heating the metals in the crucible to 650-720° C. to cause the magnesium to melt, and g) cooling the molten magnesium to form a magnesium composite that includes about 13 wt. % tin. The density of the magnesium composite is 1.94 g/cm³, the hardness is 75.6 Rockwell Hardness B, and the dissolution rate in 3% solution of KCl at 90° C. is 0.02 mg/cm²-hr.

In still another and/or alternative non-limiting aspect of the invention, there is provided a method for forming a novel magnesium composite including the steps of a) providing magnesium having a purity of at least 99.9%, b) providing bismuth having a purity of at least 99.9%, c) adding the magnesium and bismuth in the crucible (e.g., carbon steel crucible), d) optionally adding a flux to the top of the metals in the crucible, e) optionally heating the metals in the crucible to 250° C. for about 2-60 minutes, f) heating the metals in the crucible to 650-720° C. to cause the magnesium to melt, and g) cooling the molten magnesium to form a magnesium composite that includes about 10 wt. % bismuth. The density of the magnesium composite is 1.86 g/cm³, the hardness is 16.9 Rockwell Hardness B, and the dissolution rate in 3% solution of KCl at 90° C. is 26.51 mg/cm²-hr.

In still another and/or alternative non-limiting aspect of the invention, there is provided a method for controlling the dissolution properties of a magnesium or a magnesium alloy comprising of the steps of: a) heating the magnesium or a magnesium alloy to a point above its solidus temperature; b) adding an additive to said magnesium or magnesium alloy while said magnesium or magnesium alloy is above said solidus temperature of magnesium or magnesium alloy to form a mixture, said additive including one or more first additives having an electronegativity of greater than 1.5, said additive constituting about 0.05-45 wt. % of said mixture; c) dispersing said additive in said mixture while said magnesium or magnesium alloy is above said solidus temperature of magnesium or magnesium alloy; and, d) cooling said mixture to form a magnesium composite, said magnesium composite including in situ precipitation of galvanically-active intermetallic phases. The first additive can optionally have an electronegativity of greater than 1.8. The step of controlling a size of said in situ precipitated intermetallic phase can optionally be by controlled selection of a mixing technique during said dispersion step, controlling a cooling rate of said mixture, or combinations thereof. The magnesium or magnesium alloy can optionally be heated to a temperature that is less than said melting point temperature of at least one of said additives. The magnesium or magnesium alloy can be heated to a temperature that is greater than said melting point temperature of at least one of said additives. The additive can optionally include one or more metals selected from the group consisting of calcium, copper, nickel, cobalt, bismuth, silver, gold, lead, tin, antimony, indium, arsenic, mercury, and gallium. The additive can optionally include one or more metals selected from the group consisting of calcium, copper, nickel, cobalt, bismuth, tin, antimony, indium, and gallium. The additive can optionally include one or more second additives that have an electronegativity of less than 1.25. The second additive can optionally include one or more metals selected from the group consisting of strontium, barium, potassium, sodium, lithium, cesium, and the rare earth metals such as yttrium, lanthanum, samarium, europium, gadolinium, terbium, dysprosium, holmium, and ytterbium. The additive can optionally be formed of a single composition, and has an average particle diameter size of about 0.1-500 microns. At least a portion of said additive can optionally remain at least partially in solution in an a-magnesium phase of said magnesium composite. The magnesium alloy can optionally include over 50 wt. % magnesium and one or more metals selected from the group consisting of aluminum, boron, bismuth, zinc, zirconium, and manganese. The magnesium alloy can optionally include over 50 wt. % magnesium and one or more metals selected from the group consisting of aluminum in an amount of about 0.5-10 wt. %, zinc in amount of about 0.1-6 wt. %, zirconium in an amount of about 0.01-3 wt. %, manganese in an amount of about 0.15-2 wt. %; boron in amount of about 0.0002-0.04 wt. %, and bismuth in amount of about 0.4-0.7 wt. %. The magnesium alloy can optionally include over 50 wt. % magnesium and one or more metals selected from the group consisting of aluminum in an amount of about 0.5-10 wt. %, zinc in amount of about 0.1-3 wt. %, zirconium in an amount of about 0.01-1 wt. %, manganese in an amount of about 0.15-2 wt. %; boron in amount of about 0.0002-0.04 wt. %, and bismuth in amount of about 0.4-0.7. wt %. The step of solutionizing said magnesium composite can optionally occur at a temperature above 300° C. and below a melting temperature of said magnesium composite to improve tensile strength, ductility, or combinations thereof of said magnesium composite. The step of forming said magnesium composite into a final shape or near net shape can optionally be by a) sand casting, permanent mold casting, investment casting, shell molding, or other pressureless casting technique at a temperature above 730° C., 2) using either pressure addition or elevated pouring temperatures above 710° C., or 3) subjecting the magnesium composite to pressures of 2000-20,000 psi through the use of squeeze casting, thixomolding, or high pressure die casting techniques. The step of aging said magnesium composite can optionally be at a temperature of above 100° C. and below 300° C. to improve tensile strength of said magnesium composite. The magnesium composite can optionally have a hardness above 14 Rockwell Harness B. The magnesium composite can optionally have a dissolution rate of at least 5 mg/cm2-hr. in 3% KCl at 90° C. The additive metal can optionally include about 0.05-35 wt. % nickel. The additive can optionally include about 0.05-35 wt. % copper. The additive can optionally include about 0.05-35 wt. % antimony. The additive can optionally include about 0.05-35 wt. % gallium. The additive can optionally include about 0.05-35 wt. % tin. The additive can optionally include about 0.05-35 wt. % bismuth. The additive can optionally include about 0.05-35 wt. % calcium. The method can optionally further include the step of rapidly solidifying said magnesium composite by atomizing the molten mixture and then subjecting the atomized molten mixture to ribbon casting, gas and water atomization, pouring into a liquid, high speed machining, saw cutting, or grinding into chips, followed by powder or chip consolidation below its liquidus temperature.

In still another and/or alternative non-limiting aspect of the invention, there is provided a magnesium composite that includes in situ precipitation of galvanically-active intermetallic phases comprising a magnesium or a magnesium alloy and an additive constituting about 0.05-45 wt. % of said magnesium composite, said magnesium having a content in said magnesium composite that is greater than 50 wt. %, said additive forming metal composite particles or precipitant in said magnesium composite, said metal composite particles or precipitant forming said in situ precipitation of said galvanically-active intermetallic phases, said additive including one or more first additives having an electronegativity of greater than 1.5. The magnesium composite can optionally further include one or more second additives having an electronegativity of less than 1.25. The first additive can optionally have an electronegativity of greater than 1.8. The first additive can optionally include one or more metals selected from the group consisting of copper, nickel, cobalt, bismuth, silver, gold, lead, tin, antimony, indium, arsenic, mercury, and gallium. The first additive can optionally include one or more metals selected from the group consisting of copper, nickel, cobalt, bismuth, tin, antimony, indium, and gallium. The second additive can optionally include one or more metals selected from the group consisting of calcium, strontium, barium, potassium, sodium, lithium, cesium, and the rare earth metals such as yttrium, lanthanum, samarium, europium, gadolinium, terbium, dysprosium, holmium, and ytterbium. The magnesium alloy can optionally include over 50 wt. % magnesium and one or more metals selected from the group consisting of aluminum, boron, bismuth, zinc, zirconium, and manganese. The magnesium alloy can optionally include over 50 wt. % magnesium and one or more metals selected from the group consisting of aluminum in an amount of about 0.5-10 wt. %, zinc in amount of about 0.1-3 wt. %, zirconium in an amount of about 0.01-1 wt. %, manganese in an amount of about 0.15-2 wt. %, boron in amount of about 0.0002-0.04 wt. %, and bismuth in amount of about 0.4-0.7 wt. %. The additive can optionally include about 0.05-45 wt. % nickel. The first additive can optionally include about 0.05-45 wt. % copper. The first additive can optionally include about 0.05-45 wt. % cobalt. The first additive can optionally include about 0.05-45 wt. % antimony. The first additive can optionally include about 0.05-45 wt. % gallium. The first additive can optionally include about 0.05-45 wt. % tin. The first additive can optionally include about 0.05-45 wt. % bismuth. The second additive can optionally include 0.05-35 wt. % calcium. The magnesium composite can optionally have a hardness above 14 Rockwell Harness B. The magnesium composite can optionally have a dissolution rate of at least 5 mg/cm2-hr. in 3% KCl at 90° C. The magnesium composite can optionally have a dissolution rate of about 5-300 mg/cm2-hr in 3 wt. % KCl water mixture at 90° C. The magnesium composite can optionally be subjected to a surface treatment to improve a surface hardness of said magnesium composite, said surface treatment including peening, heat treatment, aluminizing, or combinations thereof. A dissolution rate of said magnesium composite can optionally be controlled by an amount and size of said in situ formed galvanically-active particles whereby smaller average sized particles of said in situ formed galvanically-active particles, a greater weight percent of said in situ formed galvanically-active particles in said magnesium composite, or combinations thereof increases said dissolution rate of said magnesium composite.

In still another and/or alternative non-limiting aspect of the invention, there is provided a dissolvable component for use in downhole operations that is fully or partially formed of a magnesium composite, said dissolvable component including a component selected from the group consisting of sleeve, frac ball, hydraulic actuating tooling, mandrel, slip, grip, ball, dart, carrier, tube, valve, valve component, plug, or other downhole well component, said magnesium composite includes in situ precipitation of galvanically-active intermetallic phases comprising a magnesium or a magnesium alloy and an additive constituting about 0.05-45 wt. % of said magnesium composite, said magnesium having a content in said magnesium composite that is greater than 50 wt. %, said additive forming metal composite particles or precipitant in said magnesium composite, said metal composite particles or precipitant forming said in situ precipitation of said galvanically-active intermetallic phases, said additive including one or more first additives having an electronegativity of greater than 1.5. The dissolvable component can optionally further include one or more second additives having an electronegativity of less than 1.25. The first additive can optionally have an electronegativity of greater than 1.8. The first additive can optionally include one or more metals selected from the group consisting of copper, nickel, cobalt, bismuth, silver, gold, lead, tin, antimony, indium, arsenic, mercury, and gallium. The first additive can optionally include one or more metals selected from the group consisting of copper, nickel, cobalt, bismuth, tin, antimony, indium, and gallium. The second additive can optionally include one or more metals selected from the group consisting of calcium, strontium, barium, potassium, sodium, lithium, cesium, and the rare earth metals such as yttrium, lanthanum, samarium, europium, gadolinium, terbium, dysprosium, holmium, and ytterbium. The second additive can optionally include 0.05-35 wt. % calcium. The magnesium alloy can optionally include over 50 wt. % magnesium and one or more metals selected from the group consisting of aluminum, boron, bismuth, zinc, zirconium, and manganese. The magnesium composite can optionally have a hardness above 14 Rockwell Harness B. The magnesium composite can optionally have a dissolution rate of at least 5 mg/cm2-hr. in 3% KCl at 90° C. The magnesium composite can optionally have a dissolution rate of at least 10 mg/cm2-hr in a 3% KCl solution at 90° C. The magnesium composite can optionally have a dissolution rate of at least 20 mg/cm2-hr in a 3% KCl solution at 65° C. The magnesium composite can optionally have a dissolution rate of at least 1 mg/cm2-hr in a 3% KCl solution at 65° C. The magnesium composite can optionally have a dissolution rate of at least 100 mg/cm2-hr in a 3% KCl solution at 90° C. The magnesium composite can optionally have a dissolution rate of at least 45 cm2/hr. in 3 wt. % KCl water mixture at 90° C. and up to 325 mg/cm2/hr. in 3 wt. % KCl water mixture at 90° C. The magnesium composite can optionally have a dissolution rate of up to I mg/cm2/hr. in 3 wt. % KCl water mixture at 21° C. The magnesium composite can optionally have a dissolution rate of at least 90 mg/cm2-hr. in 3% KCl solution at 90° C. The magnesium composite can optionally have a dissolution rate of at least a rate of 0.1 mg/cm2-hr. in 0.1% KCl solution at 90° C. The magnesium composite can optionally have a dissolution rate of a rate of <0.1 mg/cm2-hr. in 0.1% KCl solution at 75° C. The magnesium composite can optionally have a dissolution rate of, a rate of <0.1 mg/cm2-hr. in 0.1% KCl solution at 60° C. The magnesium composite can optionally have a dissolution rate of <0.1 mg/cm2-hr. in 0.1% KCl solution at 45° C. The magnesium composite can optionally have a dissolution rate of at least 30 mg/cm2-hr. in 0.1% KCl solution at 90° C. The magnesium composite can optionally have a dissolution rate of at least 20 mg/cm2-hr. in 0.1% KCl solution at 75° C. The magnesium composite can optionally have a dissolution rate of at least 10 mg/cm2-hr. in 0.1% KCl solution at 60° C. The magnesium composite can optionally have a dissolution rate of at least 2 mg/cm2-hr. in 0.1% KCl solution at 45° C. The metal composite particles or precipitant in said magnesium composite can optionally have a solubility in said magnesium of less than 5%, The magnesium alloy can optionally include over 50 wt. % magnesium and one or more metals selected from the group consisting of aluminum, boron, bismuth, zinc, zirconium, and manganese. The magnesium alloy can optionally include over 50 wt. % magnesium and one or more metals selected from the group consisting of aluminum in an amount of about 0.5-10 wt. %, zinc in an amount of about 0.1-6 wt. %, zirconium in an amount of about 0.01-3 wt. %, manganese in an amount of about 0.15-2 wt. %, boron in an amount of about 0.0002-0.04 wt. %, and bismuth in amount of about 0.4-0.7 wt. %. The magnesium alloy can optionally include over 50 wt. % magnesium and one or more metals selected from the group consisting of aluminum in an amount of about 0.5-10 wt. %, zinc in an amount of about 0.1-3 wt. %, zirconium in an amount of about 0.01-1 wt. %, manganese in an amount of about 0.15-2 wt. %, boron in an amount of about 0.0002-0.04 wt. %, and bismuth in an amount of about 0,4-0.7 wt. %. The magnesium alloy can optionally include at least 85 wt. % magnesium and one or more metals selected from the group consisting of 0.5-10 wt. % aluminum, 0.05-6 wt. % zinc, 0.01-3 wt. % zirconium, and 0.15-2 wt. % manganese. The magnesium alloy can optionally include 60-95 wt. % magnesium and 0.01-1 wt. % zirconium. The magnesium alloy can optionally include 60-95 wt. % magnesium, 0.5-10 wt. % aluminum, 0.05-6 wt. % zinc, and 0.15-2 wt. % manganese. The magnesium alloy can optionally include 60-95 wt. % magnesium, 0.05-6 wt. % zinc, and 0.01-1 wt. % zirconium. The magnesium alloy can optionally include over 50 wt. % magnesium and one or more metals selected from the group consisting of 0.5-10 wt. % aluminum, 0.1-2 wt. % zinc, 0.01-1 wt. % zirconium, and 0.15-2 wt. % manganese. The magnesium alloy can optionally include over 50 wt. % magnesium and one or more metals selected from the group consisting of 0.1-3 wt. % zinc, 0.01-1 wt. % zirconium, 0.05-1 wt. % manganese, 0.0002-0.04 wt. % boron, and 0.4-0.7 wt. % bismuth.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable magnesium alloy including 1-15 wt. % aluminum and a dissolution enhancing intermetallic phase between magnesium and cobalt, nickel, and/or copper with the alloy composition containing 0.05-25 wt. % cobalt, nickel, and/or copper, and 0.1-15 wt. % calcium.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable magnesium alloy wherein the alloy composition includes 0.5-8 wt. % calcium, 0.05-20 wt. % nickel, 3-11 wt. % aluminum, and 50-95 wt. % magnesium and the alloy degrades at a rate that is greater than 5 mg/cm2-hr, at temperatures below 90° C. in fresh water (water with less than 1000 ppm salt content).

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable magnesium alloy wherein the alloy composition includes 0-2 wt. % zinc, 0.5-8 wt. % calcium, 0.05-20 wt. % nickel, 5-11wt. % aluminum, and 50-95 wt. % magnesium and the alloy degrades at a rate that is greater than 1 mg/cm2-hr. at temperatures below 45° C. in fresh water (water with less than 1000 ppm salt content).

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy can optionally include calcium, strontium and/or barium addition that forms an aluminum-calcium phase, an aluminum-strontium phase and/or an aluminum-barium phase that leads to an alloy with a higher incipient melting point and increased corrosion rate.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy can optionally include calcium that creates an aluminum-calcium (e.g., AlCa₂phase) as opposed to a magnesium-aluminum phase (e.g., Mg₁₇Al₁₂phase) to thereby enhance the speed of degradation of the alloy when exposed to a conductive fluid vs. the common practice of enhancing the speed of degradation of an aluminum-containing alloy by reducing the aluminum content to reduce the amount of Mg₁₇Al₁₂in the alloy.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy can optionally include calcium addition that forms an aluminum-calcium phase that increases the ratio of dissolution of intermetallic phase to the base magnesium, and thus increases the dissolution rate of the alloy.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy can optionally include calcium addition that forms an aluminum-calcium phase reduces the salinity required for the same dissolution rate by over 2× at 90° C. in a saline solution.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy can optionally include calcium addition that increases the incipient melting temperature of the degradable alloy, thus the alloy can be extruded at higher speeds and thinner walled tubes can be formed as compared to a degradable alloy without calcium additions.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy wherein the mechanical properties of tensile yield and ultimate strength are optionally not lowered by more than 10% or are enhanced as compared to an alloy without calcium addition.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy wherein the elevated mechanical properties of yield strength and ultimate strength of the alloy at temperatures above 100° C. are optionally increased by more than 5% due to the calcium addition.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy wherein the galvanically active phase is optionally present in the form of an LPSO (Long Period Stacking Fault) phase such as Mg₁₂Zn₁−xNi_xRE (where RE is a rare earth element) and that phase is 0.05-5 wt. % of the final alloy composition.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy wherein the mechanical properties at 150° C. are optionally at least 24 ksi tensile yield strength, and are not less than 20% lower than the mechanical properties at room temperature (77° F.).

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy wherein the dissolution rate at 150° C. in 3% KCl brine is optionally 10-150 mg/cm2/hr,

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy that optionally can include 2-4 wt. % yttrium, 2-5 wt. % gadolinium, 0.3-4 wt. % nickel, and 0.05-4 wt. % zinc.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy that can optionally include 0.1-0.8 wt. % manganese and/or zirconium.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy that can optionally be use in downhole applications such as pressure segmentation, or zonal control.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy can optionally be used for zonal or pressure isolation in a downhole component or tool.

In still another and/or alternative non-limiting aspect of the invention, there is provided a method for forming a degradable alloy wherein a base dissolution of enhanced magnesium alloy is optionally melted and calcium is added as metallic calcium above the liquids of the magnesium-aluminum phase and the aluminum preferentially forms AlCa₂vs. Mg₁₇Al₁₂during solidification of the alloy.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy can optionally be formed by adding calcium is in the form of an oxide or salt that is reduced by the molten melt vs. adding the calcium as a metallic element.

In still another and/or alternative non-limiting aspect of the invention, there is provided a degradable alloy can optionally be formed at double the speed or higher as compared to an alloy that does not include calcium due to the rise in incipient melting temperature.

One non-limiting objective of the present invention is the provision of a castable, moldable, or extrudable magnesium composite formed of magnesium or magnesium alloy and one or more additives dispersed in the magnesium or magnesium alloy.

Another and/or alternative non-limiting objective of the present invention is the provision of selecting the type and quantity of one or more additives so that the grain boundaries of the magnesium composite have a desired composition and/or morphology to achieve a specific galvanic corrosion rate in the entire magnesium composite and/or along the grain boundaries of the magnesium composite.

Still yet another and/or alternative non-limiting objective of the present invention is the provision of forming a magnesium composite wherein the one or more additives can be used to enhance mechanical properties of the magnesium composite, such as ductility and/or tensile strength.

Another and/or alternative non-limiting objective of the present invention is the provision of forming a magnesium composite that can be enhanced by heat treatment as well as deformation processing, such as extrusion, forging, or rolling, to further improve the strength of the final magnesium composite.

Yet another and/or alternative non-limiting objective of the present invention is the provision of forming a magnesium composite that can be can be made into almost any shape.

Another and/or alternative non-limiting objective of the present invention is the provision of dispersing the one or more additives in the molten magnesium or magnesium alloy is at least partially by thixomolding, stir casting, mechanical agitation, electrowetting, ultrasonic dispersion and/or combinations of these processes.

Another and/or alternative non-limiting objective of the present invention is the provision of producing a magnesium composite with at least one insoluble phase that is at least partially formed by the additive or additive material, and wherein the one or more additives have a different galvanic potential from the magnesium or magnesium alloy.

Still yet another and/or alternative non-limiting objective of the present invention is the provision of producing a magnesium composite wherein the rate of corrosion in the magnesium composite can be controlled by the surface area via the particle size and morphology of the one or more additions.

Yet another and/or alternative non-limiting objective of the present invention is the provision of producing a magnesium composite that includes one or more additives that have a solubility in the molten magnesium or magnesium alloy of less than about 10%.

Still yet another and/or alternative non-limiting objective of the present invention, there is provided a magnesium composite that can be used as a dissolvable, degradable and/or reactive structure in oil drilling.

These and other objects, features and advantages of the present invention will become apparent in light of the following detailed description of preferred embodiments thereof, as illustrated in the accompanying drawings.

BRIEF DESCRIPTION OF THE DRAWINGS

FIGS. 1-3 show a typical cast microstructure with galvanically-active in situ formed intermetallic phase wetted to the magnesium matrix; and,

FIG. 4 shows a typical phase diagram to create in situ formed particles of an intermetallic Mg_x(M), Mg(M_x) and/or unalloyed M and/or M alloyed with another M where M is any element on the periodic table or any compound in a magnesium matrix and wherein M has a electronegativity that is greater than 1.5 or an electronegativity that is less than 1.25.

DETAILED DESCRIPTION OF THE INVENTION

Referring now to the figures wherein the showings illustrate non-limiting embodiments of the present invention, the present invention is directed to a magnesium composite that includes one or more additives dispersed in the magnesium composite. The magnesium composite of the present invention can be used as a dissolvable, degradable and/or reactive structure in oil drilling. For example, the magnesium composite can be used to form a frac ball or other structure (e.g., sleeves, valves, hydraulic actuating tooling and the like, etc.) in a well drilling or completion operation. Although the magnesium composite has advantageous applications in the drilling or completion operation field of use, it will be appreciated that the magnesium composite can be used in any other field of use wherein it is desirable to form a structure that is controllably dissolvable, degradable and/or reactive.

The present invention is directed to a novel magnesium composite that can be used to form a castable, moldable, or extrudable component. The magnesium composite includes at least 50 wt. % magnesium. Generally, the magnesium composite includes over 50 wt. % magnesium and less than about 99.5 wt. % magnesium and all values and ranges therebetween. One or more additives are added to a magnesium or magnesium alloy to form the novel magnesium composite of the present invention. The one or more additives can be selected and used in quantities so that galvanically-active intermetallic or insoluble precipitates form in the magnesium or magnesium alloy while the magnesium or magnesium alloy is in a molten state and/or during the cooling of the melt; however, this is not required. The one or more additives are added to the molten magnesium or magnesium alloy at a temperature that is typically less than the melting point of the one or more additives; however, this is not required. During the process of mixing the one or more additives in the molten magnesium or magnesium alloy, the one or more additives are not caused to fully melt in the molten magnesium or magnesium alloy; however, this is not required. For additives that partially or fully melt in the molten magnesium or molten magnesium alloy, these additives form alloys with magnesium and/or other additives in the melt, thereby resulting in the precipitation of such formed alloys during the cooling of the molten magnesium or molten magnesium alloy to form the galvanically-active phases in the magnesium composite. After the mixing process is completed, the molten magnesium or magnesium alloy and the one or more additives that are mixed in the molten magnesium or magnesium alloy are cooled to form a solid magnesium component that includes particles in the magnesium composite. Such a formation of particles in the melt is called in situ particle formation as illustrated in FIGS. 1-3. Such a process can be used to achieve a specific galvanic corrosion rate in the entire magnesium composite and/or along the grain boundaries of the magnesium composite. This feature results in the ability to control where the galvanically-active phases are located in the final casting, as well as the surface area ratio of the in situ phase to the matrix phase, which enables the use of lower cathode phase loadings as compared to a powder metallurgical or alloyed composite to achieve the same dissolution rates. The in situ formed galvanic additives can be used to enhance mechanical properties of the magnesium composite such as ductility, tensile strength, and/or shear strength. The final magnesium composite can also be enhanced by heat treatment as well as deformation processing (such as extrusion, forging, or rolling) to further improve the strength of the final composite over the as-cast material; however, this is not required. The deformation processing can be used to achieve strengthening of the magnesium composite by reducing the grain size of the magnesium composite. Further enhancements, such as traditional alloy heat treatments (such as solutionizing, aging and/or cold working) can be used to enable control of dissolution rates though precipitation of more or less galvanically-active phases within the alloy microstructure while improving mechanical properties; however, this is not required. Because galvanic corrosion is driven by both the electrode potential between the anode and cathode phase, as well as the exposed surface area of the two phases, the rate of corrosion can also be controlled through adjustment of the in situ formed particles size, while not increasing or decreasing the volume or weight fraction of the addition, and/or by changing the volume/weight fraction without changing the particle size. Achievement of in situ particle size control can be achieved by mechanical agitation of the melt, ultrasonic processing of the melt, controlling cooling rates, and/or by performing heat treatments. In situ particle size can also or alternatively be modified by secondary processing such as rolling, forging, extrusion and/or other deformation techniques. A smaller particle size can be used to increase the dissolution rate of the magnesium composite. An increase in the weight percent of the in situ formed particles or phases in the magnesium composite can also or alternatively be used to increase the dissolution rate of the magnesium composite. A phase diagram for forming in situ formed particles or phases in the magnesium composite is illustrated in FIG. 4.

In accordance with the present invention, a novel magnesium composite is produced by casting a magnesium metal or magnesium alloy with at least one component to form a galvanically-active phase with another component in the chemistry that forms a discrete phase that is insoluble at the use temperature of the dissolvable component. The in situ formed particles and phases have a different galvanic potential from the remaining magnesium metal or magnesium alloy. The in situ formed particles or phases are uniformly dispersed through the matrix metal or metal alloy using techniques such as thixomolding, stir casting, mechanical agitation, chemical agitation, electrowetting, ultrasonic dispersion, and/or combinations of these methods. Due to the particles being formed in situ to the melt, such particles generally have excellent wetting to the matrix phase and can be found at grain boundaries or as continuous dendritic phases throughout the component depending on alloy composition and the phase diagram. Because the alloys form galvanic intermetallic particles where the intermetallic phase is insoluble to the matrix at use temperatures, once the material is below the solidus temperature, no further dispersing or size control is necessary in the component. This feature also allows for further grain refinement of the final alloy through traditional deformation processing to increase tensile strength, elongation to failure, and other properties in the alloy system that are not achievable without the use of insoluble particle additions. Because the ratio of in situ formed phases in the material is generally constant and the grain boundary to grain surface area is typically consistent even after deformation processing and heat treatment of the composite, the corrosion rate of such composites remains very similar after mechanical processing.

EXAMPLE 1

An AZ91D magnesium alloy having 9 wt. % aluminum, 1 wt. % zinc and 90 wt. % magnesium was melted to above 800° C. and at least 200° C. below the melting point of nickel. About 7 wt. % of nickel was added to the melt and dispersed. The melt was cast into a steel mold. The cast material exhibited a tensile strength of about 14 ksi, an elongation of about 3%, and shear strength of 11 ksi, The east material dissolved at a rate of about 75 mg/cm²-min in a 3% KCl solution at 90° C. The material dissolved at a rate of 1 mg/cm²-hr in a 3% KCl solution at 21° C. The material dissolved at a rate of 325 mg/cm²-hr. in a 3% KCl solution at 90° C.

EXAMPLE 2

The composite in Example 1 was subjected to extrusion with an 11:1 reduction area. The material exhibited a tensile yield strength of 45 ksi, an Ultimate tensile strength of 50 ksi and an elongation to failure of 8%. The material has a dissolve rate of 0.8 mg/cm²-min. in a 3% KCl solution at 20° C. The material dissolved at a rate of 100 mg/cm²-hr. in a 3% KCl solution at 90° C.

EXAMPLE 3

The alloy in Example 2 was subjected to an artificial T5 age treatment of 16 hours from 100-200° C. The alloy exhibited a tensile strength of 48 ksi and elongation to failure of 5% and a shear strength of 25 ksi. The material dissolved at a rate of 110 mg/cm²-hr. in 3% KCl solution at 90° C. and 1 mg/cm²-hr. in 3% KCl solution at 20° C.

EXAMPLE 4

The alloy in Example 1 was subjected to a solutionizing treatment T4 of 18 hours from 400° C-500° C. and then an artificial T6 aging process of 16 hours from 100-200C. The alloy exhibited a tensile strength of 34 ksi and elongation to failure of 11% and a shear strength of 18Ksi.

The material dissolved at a rate of 84 mg/cm²-hr. in 3% KCl solution at 90° C. and 0.8 mg/cm -hr. in 3% KCl solution at 20° C.

EXAMPLE 5

An AZ91 D magnesium alloy having 9 wt. % aluminum, 1 wt. % zinc, and 90 wt. % magnesium was melted to above 800° C. and at least 200° C. below the melting point of copper. About 10 wt. % of copper alloyed to the melt and dispersed. The melt was cast into a steel mold. The cast material exhibited a tensile yield strength of about 14 ksi, an elongation of about 3%, and shear strength of 11 ksi. The cast material dissolved at a rate of about 50 mg/cm -hr. in a 3% KCl solution at 90° C. The material dissolved at a rate of 0.6 mg/cm²-hr. in a 3% KCl solution at 21° C.

EXAMPLE 6

The alloy in Example 5 was subjected to an artificial T5 aging process of 16 hours from 100-200° C. The alloy exhibited a tensile strength of 50 ksi and elongation to failure of 5% and a shear strength of 25 ksi. The material dissolved at a rate of 40 mg/cm²-hr. in 3% KCl solution at 90° C. and 0.5 mg/cm²-hr. in 3% KCl solution at 20° C.

EXAMPLE 7

An AZ91D magnesium alloy having 9 wt. % aluminum, 1 wt. % zinc, and 90 wt. % magnesium was melted to above 700° C. About 16 wt. % of 75 μm iron particles were added to the melt and dispersed. The melt was cast into a steel mold. The cast material exhibited a tensile strength of about 26 ksi, and an elongation of about 3%. The cast material dissolved at a rate of about 2.5 mg/cm²-min in a 3% KCl solution at 20° C. The material dissolved at a rate of 60 mg/cm²-hr in a 3% KCl solution at 65° C. The material dissolved at a rate of 325 mg/cm²-hr. in a 3% KCl solution at 90° C.

EXAMPLE 8

An AZ91D magnesium alloy having 9 wt. % aluminum, 1 wt. % zinc, and 90 wt. % magnesium was melted to above 700° C. About 2 wt. % 75 μm iron particles were added to the melt and dispersed. The melt was cast into steel molds. The material exhibited a tensile strength of 26 ksi, and an elongation of 4%. The material dissolved at a rate of 0.2 mg/cm²-min in a 3% KCl solution at 20° C. The material dissolved at a rate of 1 mg/cm²-hr in a 3% KCl solution at 65° C. The material dissolved at a rate of 10 mg/c -hr in a 3% KCl solution at 90° C.

EXAMPLE 9

An AZ91D magnesium alloy having 9 wt. % aluminum, 1 wt. % zinc, and 90 wt. % magnesium was melted to above 700° C. About 2 wt. % nano iron particles and about 2 wt. % nano graphite particles were added to the composite using ultrasonic mixing. The melt was cast into steel molds. The material dissolved at a rate of 2 mg/cm2-min in a 3% KCl solution at 20° C. The material dissolved at a rate of 20 mg/cm2-hr in a 3% KCl solution at 65° C. The material dissolved at a rate of 100 mg/cm2-hr in a 3% KCl solution at 90° C.

EXAMPLE 10

The composite in Example 7 was subjected to extrusion with an 11:1 reduction area. The extruded metal cast structure exhibited a tensile strength of 38 ksi, and an elongation to failure of 12%. The extruded metal cast structure dissolved at a rate of 2 mg/cm2-min in a 3% KCl solution at 20° C. The extruded metal cast structure dissolved at a rate of 301 mg/cm2-min in a 3% KCl solution at 90° C. The extruded metal cast structure exhibited an improvement of 58% tensile strength and an improvement of 166% elongation with less than 10% change in dissolution rate as compared to the non-extruded metal cast structure.

EXAMPLE 11

Pure magnesium was melted to above 650° C. and below 750° C. About 7 wt. % of antimony was dispersed in the molten magnesium. The melt was cast into a steel mold, The cast material dissolved at a rate of about 20.09 mg/cm²-hr in a 3% KCl solution at 90° C.

EXAMPLE 12

Pure magnesium was melted to above 650° C. and below 750° C. About 5 wt. % of gallium was dispersed in the molten magnesium. The melt was cast into a steel mold. The cast material dissolved at a rate of about 0.93 mg/cm²-hr in a 3% KCl solution at 90° C.

EXAMPLE 13

Pure magnesium was melted to above 650° C. and below 750° C. About 13 wt. % of tin was dispersed in the molten magnesium. The melt was cast into a steel mold. The cast material dissolved at a rate of about 0.02 mg/cm²-hr in a 3% KCl solution at 90° C.

EXAMPLE 14

A magnesium alloy that included 9 wt. % aluminum, 0.7 wt. % zinc, 0.3 wt. % nickel, 0.2 wt. % manganese, and the balance magnesium was heated to 157° C. (315° F.) under an SF₆-CO₂cover gas blend to provide a protective dry atmosphere for the magnesium alloy. The magnesium alloy was then heated to 730° C. to melt the magnesium alloy and calcium was then added into the molten magnesium alloy in an amount that the calcium constituted 2 wt. % of the mixture. The mixture of molten magnesium alloy and calcium was agitated to adequately disperse the calcium within the molten magnesium alloy. The mixture was then poured into a preheated and protective gas-filled steel mold and naturally cooled to form a cast part that was a 9″×32″ billet. The billet was subsequently preheated to ˜350° C. and extruded into a solid and tubular extrusion profile. The extrusions were run at 12 and 7 inches/minute respectively, which is 2×-3× faster than the maximum speed the same alloy achieved without calcium alloying. It was determined that once the molten mixture was cast into a steel mold, the molten surface of the mixture in the mold did not require an additional cover gas or flux protection during solidification. This can be compared to the same magnesium-aluminum alloy without calcium that requires either an additional cover gas or flux during solidification to prevent burning.

The effect of the calcium on the corrosion rate of a magnesium-aluminum-nickel alloy was determined. Since magnesium already has a high galvanic potential with nickel, the magnesium alloy corrodes rapidly in an electrolytic solution such as a potassium chloride brine. The KCl brine was a 3% solution heated to 90° C. (194° F.). The corrosion rate was compared by submerging 1″×0.6″ samples of the magnesium alloy with and without calcium additions in the solution for 6 hours and the weight loss of the alloy was calculated relative to initial exposed surface area. The magnesium alloy that did not include calcium dissolved at a rate of 48 mg/cm²-hr. in the 3% KCl solution at 90° C. The magnesium alloy that included calcium dissolved at a rate of 91 mg/cm²-hr. in the 3% KCl solution at 90° C. The corrosion rates were also tested in fresh water. The fresh water is water that has up to or less than 1000 ppm salt content. A KCl brine solution was used to compare the corrosion rated of the magnesium alloy with and without calcium additions. 1″×0.6″ samples of the magnesium alloy with and without calcium additions were submerged in the 0.1% KCl brine solution for 6 hours and the weight loss of the alloys were calculated relative to initial exposed surface area. The magnesium alloy that did not include calcium dissolved at a rate of 0.1 mg/cm²-hr. in the 0.1®1 KCl solution at 90° C., a rate of <0.1 mg/cm²-hr. in the 0.1% KCl solution at 75° C., a rate of <0.1 mg/cm²-hr. in the 0.1% KCl solution at 60° C., and a rate of <0.1 mg/cm²-hr. in the 0.1% KCl solution at 45° C. The magnesium alloy that did include calcium dissolved at a rate of 34 mg/cm²-hr. in the 0.1% KCl solution at 90° C., a rate of 26 mg/cm²-hr. in the 0.1% KCl solution at 75° C., a rate of 14 mg/cm²-hr. in the 0.1% KCl solution at 60° C., and a rate of 5 mg/cm²-hr. in the 0.1% KCl solution at 45° C.

The effect of calcium on magnesium alloy revealed that the microscopic “cutting” effect of the lamellar aluminum-calcium phase slightly decreases the tensile strength at room temperature, but increased tensile strength at elevated temperatures due to the grain refinement effect of Al₂Ca. The comparative tensile strength and elongation to failure are shown in Table A.

TABLE A

Elongation to
Tensile Strength
Elongation to

Test
Tensile Strength
failure without
with 2 wt. % Ca
failure with 2

Temperature
without Ca (psi)
Ca (%)
(psi)
wt. % Ca (%)

25° C.
23.5
2.1
21.4
1.7

150° C.
14.8
7.8
16.2
6.8

The effect of varying calcium concentration in a magnesium-aluminum-nickel alloy was tested. The effect on ignition temperature and maximum extrusion speed was also tested. For mechanical properties, the effect of 0-2 wt. % calcium additions to the magnesium alloy on ultimate tensile strength (UTS) and elongation to failure (El) is illustrated in Table B.

TABLE B

Calcium
UTS at
E_fat
UTS at
E_fat

Concentration (wt. %)
25° C.
25° C.
150° C.
150° C.

0%
41.6
10.3
35.5
24.5

0.5%
40.3
10.5
34.1
24.0

1.0%
38.5
10.9
32.6
23.3

2.0%
37.7
11.3
31.2
22.1

The effect of calcium additions in the magnesium-aluminum-nickel alloy on ignition temperature was tested and found to be similar to a logarithmic function, with the ignition temperature tapering off The ignition temperature trend is shown in Table C.

TABLE C

Calcium Concentration (wt. %)
0
1
2
3
4
5

Ignition Temperature (° C.)
550
700
820
860
875
875

The incipient melting temperature effect on maximum extrusion speeds was also found to trend similarly to the ignition temperature since the melting temperature of the magnesium matrix is limiting. The extrusion speed for a 4″ solid round extrusion from at 9″ round billet trends as shown in Table D.

TABLE D

Calcium Concentration (wt. %)

0%
0.5%
1%
2%
4%

Extrusion Speed for 4″ solid (in/min)
4
6
9
12
14

Extrusion speed for 4.425″ OD ×
1.5
2.5
4
7
9

2.645″ ID tubular (in/min)

EXAMPLE 15

Pure magnesium is heated to a temperature of 680-720° C. to form a melt under a protective atmosphere of SF6+CO₂+air. 1.5-2 wt. % zinc and 1.5-2 wt. % nickel were added using zinc lump and pelletized nickel to form a molten solution. From 3-6 wt. % gadolinium, as well as about 3-6 wt. % yttrium was added as lumps of pure metal, and 0.5-0.8% zirconium was added as a Mg-25% zirconium master alloy to the molten magnesium, which is then stirred to distribute the added metals in the molten magnesium. The melt was then cooled to 680° C., and degassed using HCN and then poured in to a permanent A36 steel mold and solidified. After solidification of the mixture, the billet was solution treated at 500° C. for 4-8 hours and air cooled. The billet was reheated to 360° C. and aged for 12 hours, followed by extrusion at a 5:1 reduction ratio to form a rod.

It is known that LPSO phases in magnesium can add high temperature mechanical properties as well as significantly increase the tensile properties of magnesium alloys at all temperatures. The Mg₁₂Zn_1−xNi_xRE₁LPSO (long period stacking order) phase enables the magnesium alloy to be both high strength and high temperature capable, as well as to be able to be controllably dissolved using the phase as an in situ galvanic phase for use in activities where enhanced and controllable use of degradation is desired. Such activities include use in oil and gas wells as temporary pressure diverters, balls, and other tools that utilize dissolvable metals.

The magnesium alloy was solution treated at 500° C. for 12 hours and air-cooled to allow precipitation of the 14 H LPSO phase incorporating both zinc and nickel as the transition metal in the layered structure. The solution-treated alloy was then preheated at 350-400° C. for over 12 hours prior to extrusion at which point the material was extruded using a 5:1 extrusion ratio (ER) with an extrusion speed of 20 ipm (inch per minute).

At the nano-layers present between the nickel and the magnesium layers or magnesium matrix, the galvanic reaction took place. The dissolution rate in 3% KCl brine solution at 90° C. as well as the tensile properties at 150° C. of the galvanically reactive alloy are shown in Table E.

TABLE E

Magnesium Alloy

Ultimate Tensile
Tensile Yield
Elongation to

Dissolution rate
Strength at
Strength at
Failure at 150° C.

(mg/cm²-hr.)
150° C. (ksi)
150° C. (ksi)
(%)

62-80
36
24
38

It will thus be seen that the objects set forth above, among those made apparent from the preceding description, are efficiently attained, and since certain changes may be made in the constructions set forth without departing from the spirit and scope of the invention, it is intended that all matter contained in the above description and shown in the accompanying drawings shall be interpreted as illustrative and not in a limiting sense. The invention has been described with reference to preferred and alternate embodiments. Modifications and alterations will become apparent to those skilled in the art upon reading and understanding the detailed discussion of the invention provided herein. This invention is intended to include all such modifications and alterations insofar as they come within the scope of the present invention. It is also to be understood that the following claims are intended to cover all of the generic and specific features of the invention herein described and all statements of the scope of the invention, which, as a matter of language, might be said to fall there between. The invention has been described with reference to the preferred embodiments. These and other modifications of the preferred embodiments as well as other embodiments of the invention will be obvious from the disclosure herein, whereby the foregoing descriptive matter is to be interpreted merely as illustrative of the invention and not as a limitation. It is intended to include all such modifications and alterations insofar as they come within the scope of the appended claims.

Number	Date	Country
62569004	Oct 2017	US
61942879	Feb 2014	US
61981425	Apr 2014	US

	Number	Date	Country
Parent	16149637	Oct 2018	US
Child	17123695		US
Parent	16149637	Oct 2018	US
Child	16149637		US
Parent	14627236	Feb 2015	US
Child	15294957		US
Parent	16149637	Oct 2018	US
Child	14627236		US
Parent	14689295	Apr 2015	US
Child	15641439		US

	Number	Date	Country
Parent	15294957	Oct 2016	US
Child	16149637		US
Parent	15641439	Jul 2017	US
Child	16149637		US

Galvanically-Active In Situ Formed Particles for Controlled Rate Dissolving Tools

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