NICKEL-CONTAINING HIGH-TOUGHNESS CONTROLLABLY DEGRADABLE MAGNESIUM ALLOY MATERIAL, PREPARATION METHOD THEREFOR AND USE THEREOF

Abstract

The present disclosure provides a nickel-containing high-toughness controllably degradable magnesium alloy material, a preparation method therefor and use thereof, and relates to the technical field of magnesium alloys. The magnesium alloy material comprises the following components in percentage by mass: 0.3 to 8.5% of Ni, 0.5 to 28% of RE, with the balance being Mg and unavoidable impurities. RE represents rare earth elements. By adding Ni and RE elements to introduce an Mg.sub.12RENi-type long-period phase, an Mg.sub.2Ni phase and an Mg.sub.xRE.sub.y phase, the magnesium alloy material provided by the present disclosure significantly improves mechanical properties of the alloy material, the tensile strength being up to 510 MPa. At the same time, the presence of the Mg.sub.12RENi-type long-period phase and Mg.sub.2Ni phase enables the alloy material to be controllably degradable, and enables the degradation rate to be adjustable between 360 and 2400 mm/a. Downhole fracturing tools manufactured by using the magnesium alloy alleviates the technical problem existing in current downhole tools and satisfy the requirements in the field of oil and gas exploitation.

Claims

1. A nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, comprising following components in percentage by mass: 0.38.5% of Ni, 0.528% of RE, and a balance of Mg and unavoidable impurities, wherein RE is a rare earth element, and Mg, Ni and RE mainly form an Mg.sub.12RENi-type long-period stacking ordered phase, an Mg.sub.2Ni phase and an Mg.sub.xRE.sub.y phase; a volume fraction of the Mg.sub.12RENi-type long-period stacking ordered phase is 370%, a volume fraction of the Mg.sub.2Ni phase is 0.510%, a volume fraction of the Mg.sub.xRE.sub.y phase is 0.522%, and a value range of x:y is 3:112:1.

2. The nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material according to claim 1, comprising following components in percentage by mass: 0.58.0% of Ni, 1.520% of RE, and a balance of Mg and unavoidable impurities.

3. The nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material according to claim 1 or 2, wherein the RE is at least one selected from the group consisting of Gd, Y, Er, Dy, Ce and Sc; preferably, the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material comprises following components in percentage by mass: 0.38.5% of Ni, 0.528% of RE, 0.0310% of M, and a balance of Mg and unavoidable impurities, wherein M is an element capable of alloying with magnesium.

4. The nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material according to claim 3, wherein a content of the unavoidable impurities, in percentage by mass, is not higher than 0.2% in the magnesium alloy material.

5. The nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material according to claim 3, wherein M is at least one selected from the group consisting of Fe, Cu and Mn.

6. A method for preparing the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material according to claim 1, comprising a following step: uniformly mixing a nickel source, a magnesium source and a rare earth source, and carrying out alloying treatment to obtain the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material.

7. The method according to claim 6, wherein the nickel source is selected from elemental nickel and nickel alloy; wherein, the nickel alloy is at least one selected from the group consisting of magnesium-nickel alloy, nickel-yttrium alloy and zinc-nickel alloy; the magnesium source is selected from elemental magnesium and magnesium alloy; the magnesium alloy is at least one selected from the group consisting of magnesium-gadolinium alloy, magnesium-yttrium alloy, magnesium-zinc alloy, magnesium-nickel alloy, magnesium-calcium alloy and magnesium-iron alloy; and the rare earth source comprises elemental rare earth and/or rare earth intermediate alloy; wherein, the elemental rare earth comprises at least one selected from the group consisting of gadolinium, yttrium, erbium, dysprosium, cerium and scandium; and the rare earth intermediate alloy comprises at least one selected from the group consisting of magnesium-gadolinium alloy, magnesium-yttrium alloy, magnesium-erbium alloy, magnesium-cerium alloy, magnesium-scandium alloy, nickel-yttrium alloy, nickel-gadolinium alloy, nickel-erbium alloy, nickel-cerium alloy and nickel-scandium alloy.

8. The method according to claim 6, wherein the alloying treatment comprises a smelting and casting method and a powder alloying method; wherein, the alloying treatment is carried out by the smelting and casting method, wherein, the smelting and casting method comprises following steps: (a) casting: uniformly mixing a nickel source, a magnesium source and a rare earth source, and carrying out smelting and casting to obtain a magnesium alloy ingot; and (b) heat treatment: carrying out, in sequence, a homogenization treatment and an extrusion heat deformation treatment on the magnesium alloy ingot to obtain the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material; and wherein, the step (b) also comprises an aging heat treatment step, wherein the aging heat treatment step is carried out after the extrusion heat deformation treatment.

9. The method according to claim 8, wherein in the step (a), when the smelting and casting is carried out, temperature is first increased to 690800 C. and maintained, raw materials are stirred to enable them to melt completely, then the temperature is reduced to 630680 C. and maintained for 20120 min, and after cooling, the magnesium alloy ingot is obtained, wherein, an inert gas is used during the smelting and casting for protection; and a cooling method is at least one selected from the group consisting of brine bath, water quenching, furnace cooling and air cooling.

10. The method according to claim 9, wherein the inert gas is at least one selected from the group consisting of helium, argon, carbon dioxide and sulfur hexafluoride.

11. The method according to claim 9, wherein the inert gas is argon.

12. The method according to claim 9, wherein the smelting is carried out using a resistance furnace or a line frequency induction furnace.

13. The method according to claim 6, wherein, in the step (b), the homogenization treatment is carried out at a temperature of 400550 C. for 440 h; and in the step (b), the extrusion heat deformation treatment is carried out at an extrusion ratio of 840; and preferably, the extrusion heat deformation treatment is carried out at a temperature of 360480 C.

14. The method according to claim 6, wherein the aging heat treatment is carried out at a temperature of 150250 C. for 12120 h.

15. The method according to claim 6, wherein the aging heat treatment is carried out at a temperature of 180220 C. for 1560 h.

16. Use of the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material according to claim 1 in a field of oil and gas exploitation.

17. The nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material according to claim 2, wherein the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material comprises an as-cast magnesium alloy, an as-extruded magnesium alloy and an aged magnesium alloy.

18. The nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material according to claim 17, wherein the as-cast magnesium alloy comprises an Mg.sub.12RENi-type long-period stacking ordered phase, an Mg.sub.5RE phase and an Mg.sub.2Ni phase, wherein a volume fraction of the Mg.sub.12RENi-type long-period stacking ordered phase is 365%, a volume fraction of the Mg.sub.2Ni phase is 0.56%, and a volume fraction of the Mg.sub.5RE phase is 0.515%.

19. The nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material according to claim 17, wherein the as-extruded magnesium alloy comprises an Mg.sub.12RENi-type long-period stacking ordered phase, an Mg.sub.2Ni phase and an Mg.sub.5RE phase, wherein a volume fraction of the Mg.sub.12RENi-type long-period stacking ordered phase is 470%, a volume fraction of the Mg.sub.2Ni phase is 1%8%, and a volume fraction of the Mg.sub.5RE phase is 120%.

20. The nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material according to claim 17, wherein the aged magnesium alloy comprises an Mg.sub.12RENi-type long-period stacking ordered phase, an Mg.sub.2Ni phase and an Mg.sub.xRE.sub.y phase, wherein a volume fraction of the Mg.sub.12RENi-type long-period stacking ordered phase is 470%, a volume fraction of the Mg.sub.2Ni phase is 210%, and a volume fraction of the Mg.sub.xRE.sub.y phase is 222%, wherein a value range of x:y is 3:112:1.

Description

DETAILED DESCRIPTION OF EMBODIMENTS

[0046] Embodiments of the present disclosure will be described in detail below in combination with examples, while a person skilled in the art would understand that the following examples are merely used for illustrating the present disclosure, but should not be considered as limitation on the scope of the present disclosure. If no specific conditions are specified in the examples, they are carried out under normal conditions or conditions recommended by manufacturers. If manufacturers of reagents or apparatuses used are not specified, they are all conventional products commercially available.

[0047] According to one aspect of the present disclosure, the present disclosure provides a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, including following components in percentage by mass: 0.38.5% of Ni, 0.528% of RE, and the balance of Mg and unavoidable impurities, wherein RE is a rare earth element, and Mg, Ni and RE mainly form an Mg.sub.12RENi-type long-period stacking ordered phase, an Mg.sub.2Ni phase and an Mg.sub.xRE.sub.y phase.

[0048] A volume fraction of the Mg.sub.12RENi-type long-period stacking ordered phase is 370%, a volume fraction of the Mg.sub.2Ni phase is 0.510%, and a volume fraction of the Mg.sub.xRE.sub.y phase is 0.522%.

[0049] In one or more embodiments, the content of the unavoidable impurities in the magnesium alloy material, in percentage by mass, is not higher than 0.2%.

[0050] In one or more embodiments, the long-period stacking ordered phase (LPSO), a new reinforcing phase in magnesium alloy, is formed by periodic changes in atomic position or chemical composition in a crystal structure, and the long-period structure is divided into two aspects, namely, stacking order and chemical composition order, and the Mg.sub.12RENi-type long-period stacking ordered phase in one or more embodiments is a result of combined effect of both stacking order and chemical composition order.

[0051] In the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material provided in the present disclosure, a typical but non-limited content of Ni (nickel), in percentage by mass, is, for example, 0.3%, 0.5%, 0.8%, 1%, 1.2%, 1.5%, 1.8%, 2%, 2.2%, 2.5%, 2.8%, 3%, 3.2%, 3.5%, 4%, 4.2%, 4.5%, 4.8%, 5%, 5.5%, 6%, 6.5%, 7%, 7.5%, 8% or 8.5%.

[0052] In the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material provided in the present disclosure, a typical but non-limited content of RE, in percentage by mass, is, for example, 0.5%, 1%, 2%, 3%, 4%, 5%, 8%, 10%, 12%, 15%, 18%, 20%, 22%, 25% or 28%.

[0053] In one or more embodiments, the volume fraction of the Mg.sub.12RENi-type long-period stacking ordered phase is 370%, the volume fraction of the Mg.sub.5RE phase is 0.520%, the volume fraction of the Mg.sub.2Ni phase is 0.510%, the volume fraction of the Mg.sub.xRE.sub.y phase is 0.522%, and a value range of x:y is (312):1 (i.e., 3:112:1).

[0054] By setting the volume fraction of the Mg.sub.12RENi-type long-period stacking ordered phase to be 370%, the volume fraction of the Mg.sub.2Ni phase to be 0.510%, and the volume fraction of the Mg.sub.xRE.sub.y phase to be 0.522%, the Mg.sub.12RENi-type long-period stacking ordered phase and the Mg.sub.xRE.sub.y phase remarkably improve the tensile strength of the alloy material, and enable the alloy to maintain certain plasticity; and meanwhile, a relatively large potential difference exists between the Mg.sub.12RENi-type long-period stacking ordered phase and the Mg.sub.2Ni phase, and the magnesium matrix, and a large number of micro-batteries are formed, so that the generated alloy material can be rapidly decomposed, which effectively meets the requirements of the field of oil and gas exploitation on downhole tool materials.

[0055] In one or more embodiments, in the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, a typical but non-limited volume fraction of the Mg.sub.12RENi-type long-period stacking ordered phase is, for example, 3%, 4%, 5%, 8%, 10%, 12%, 15%, 18%, 20%, 25%, 30%, 35%, 40%, 45%, 50%, 55%, 60%, 65% or 70%; a typical but non-limited volume fraction of the Mg.sub.2Ni phase is, for example, 0.5%, 1%, 1.5%, 2%, 3%, 4%, 5%, 6%, 7%, 8%, 9% or 10%; a typical but non-limited volume fraction of the Mg.sub.xRE.sub.y phase is, for example, 0.5%, 1%, 2%, 5%, 8%, 10%, 12%, 15%, 18%, 20% or 22%; and a typical but non-limited numerical value of x:y is 3:1, 4:1, 5:1, 6:1, 7:1, 8:1, 9:1, 10:1, 11:1 or 12:1.

[0056] The nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material provided in the present disclosure takes magnesium as a base material, and the Mg.sub.12RENi-type long-period stacking ordered phase and the Mg.sub.xRE.sub.y phase are formed by adding Ni and RE, so that the tensile strength of the alloy material is remarkably improved; meanwhile, a quite large electronegativity difference exists between the Mg.sub.12RENi-type long-period stacking ordered phase and the Mg.sub.2Ni phase, and the magnesium matrix, and a large number of micro-batteries are formed, so that the generated nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material can be rapidly decomposed, and the downhole fracturing tool made of this magnesium alloy material can effectively meet the requirements of the field of oil and gas exploitation.

[0057] Besides, when applied to the field of oil and gas exploitation, the controllably degradable alloy material provided in the present disclosure can be degraded completely downhole after accomplishing a task, and discharged through a pipe-line, without problems of easy blocking or jam, thus leaving out the drilling and grinding recycling process, reducing the engineering degree of difficulty, and improving the construction efficiency.

[0058] In one or more embodiments of the present disclosure, when Ni is 0.57.5% and RE is 1.519%, in the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material; and the volume fraction of the Mg.sub.12RENi-type long-period stacking ordered phase is 4.865%, the volume fraction of the Mg.sub.5RE phase is 115%, and the volume fraction of the Mg.sub.2Ni phase is 15%, the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material has the tensile strength of 325505 MPa, the yield strength of 156415 MPa, and the elongation of 6.021.8% at room temperature, and the decomposition rate of 363 mm/a2500 mm/a in a 3.5 wt % KCl solution at 90 C.

[0059] In one or more embodiments of the present disclosure, the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material includes as-cast magnesium alloy, as-extruded magnesium alloy and aged magnesium alloy.

[0060] In one or more embodiments of the present disclosure, in the as-cast magnesium alloy, Mg, Ni and RE mainly form an Mg.sub.12RENi-type long-period stacking ordered phase, an Mg.sub.2Ni phase and an Mg.sub.5RE phase, wherein a volume fraction of the Mg.sub.12NiRE-type long-period stacking ordered phase is 365%, a volume fraction of the Mg.sub.2Ni phase is 0.56%, and a volume fraction of the Mg.sub.5RE phase is 0.515%.

[0061] In one or more embodiments of the present disclosure, in the as-cast magnesium alloy, a typical but non-limited volume fraction of the Mg.sub.12NiRE-type long-period stacking ordered phase is, for example, 3%, 4%, 5%, 8%, 10%, 12%, 15%, 18%, 20%, 25%, 30%, 35%, 40%, 45%, 50%, 55%, 60% or 65%; a typical but non-limited volume fraction of the Mg.sub.2Ni phase is, for example, 0.5%, 0.8%, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5%, 5.5% or 6%; and a typical but non-limited volume fraction of the Mg.sub.5RE phase is, for example, 0.5%, 0.8%, 1%, 2%, 5%, 8%, 10%, 12% or 15%.

[0062] In one or more embodiments of the present disclosure, in the as-extruded magnesium alloy, Mg, Ni and RE mainly form an Mg.sub.12RENi-type long-period stacking ordered phase, an Mg.sub.2Ni phase and an Mg.sub.5RE phase, wherein a volume fraction of the Mg.sub.12NiRE-type long-period stacking ordered phase is 470%, a volume fraction of the Mg.sub.2Ni phase is 1%8%, and a volume fraction of the Mg.sub.5RE phase is 120%.

[0063] In one or more embodiments of the present disclosure, in the as-extruded magnesium alloy, a typical but non-limited volume fraction of the Mg.sub.12NiRE-type long-period stacking ordered phase is, for example, 4%, 5%, 8%, 10%, 12%, 15%, 18%, 20%, 25%, 30%, 35%, 40%, 45%, 50%, 55%, 60%, 65% or 70%; a typical but non-limited volume fraction of the Mg.sub.2Ni phase is, for example, 1%, 1.5%, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5%, 5.5%, 6%, 6.5%, 7%, 7.5% or 8%; and a typical but non-limited volume fraction of the Mg.sub.5RE phase is, for example, 1%, 2%, 5%, 8%, 10%, 12%, 15%, 18% or 20%.

[0064] In one or more embodiments of the present disclosure, in the aged magnesium alloy, Mg, Ni and RE mainly form an Mg.sub.12RENi-type long-period stacking ordered phase, an Mg.sub.2Ni phase and Mg.sub.xRE.sub.y phase (x:y=(312):1), wherein a volume fraction of the Mg.sub.12NiRE-type long-period stacking ordered phase is 470%, a volume fraction of the Mg.sub.2Ni phase is 2%10%, and a volume fraction of the Mg.sub.5RE phase is 222%.

[0065] In one or more embodiments of the present disclosure, in the aged magnesium alloy, a typical but non-limited volume fraction of the Mg.sub.12NiRE-type long-period stacking ordered phase is, for example, 4%, 5%, 8%, 10%, 12%, 15%, 18%, 20%, 25%, 30%, 35%, 40%, 45%, 50%, 55%, 60%, 65% or 70%; a typical but non-limited volume fraction of the Mg.sub.2Ni phase is, for example, 2%, 2.5%, 3%, 3.5%, 4%, 4.5%, 5%, 5.5%, 6%, 6.5%, 7%, 7.5%, 8%, 9% or 10%; a typical but non-limited volume fraction of the Mg.sub.xRE.sub.y phase is, for example, 2%, 5%, 8%, 10%, 12%, 15%, 18%, 20% or 22%, wherein a typical but non-limited numerical value of x:y is, for example, 3:1, 4:1, 5:1, 6:1, 7:1, 8:1, 9:1, 10:1, 11:1 or 12:1.

[0066] In one or more embodiments of the present disclosure, RE is one or more selected from the group consisting of Gd, Y, Er, Dy, Ce and Sc.

[0067] In one or more embodiments of the present disclosure, the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material includes following components in percentage by mass: 0.38.5% of Ni, 0.528% of RE, 0.0310% of M, and the balance of Mg and unavoidable impurities, wherein M is an element capable of alloying with magnesium.

[0068] In one or more embodiments of the present disclosure, in the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, a typical but non-limited percentage by mass of Ni is, for example, 0.3%, 0.5%, 0.8%, 1%, 1.2%, 1.5%, 1.8%, 2%, 2.2%, 2.5%, 2.8%, 3%, 3.2%, 3.5%, 4%, 4.2%, 4.5%, 4.8%, 5%, 5.5%, 6%, 6.5%, 7%, 7.5%, 8% or 8.5%; a typical but non-limited percentage by mass of RE is, for example, 0.5%, 1%, 2%, 3%, 4%, 5%, 8%, 10%, 12%, 15%, 18%, 20%, 22%, 25% or 28%; and a typical but non-limited percentage by mass of M is, for example, 0.03%, 0.05%, 0.08%, 0.1%, 0.15%, 0.2%, 0.5%, 0.8%, 1%, 1.5%, 2%, 3%, 4%, 5%, 6%, 7%, 8%, 9% or 10%.

[0069] In one or more embodiments of the present disclosure, M includes, but is not limited to at least one of Fe, Cu and Mn.

[0070] According to a second aspect of the present disclosure, the present disclosure provides a method for preparing the above nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, including the following step:

[0071] uniformly mixing a nickel source, a magnesium source and a rare earth source, and carrying out alloying treatment to obtain the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material.

[0072] The method for preparing a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material provided in the present disclosure is simple in process and convenient in operation, facilitates large-scale industrial production, and reduces the cost.

[0073] In one or more embodiments of the present disclosure, the alloying treatment includes a smelting and casting method and a powder alloying method.

[0074] In one or more embodiments of the present disclosure, the nickel source is selected from elemental nickel and/or nickel alloy.

[0075] In one or more embodiments of the present disclosure, the nickel alloy is one or more selected from the group consisting of magnesium-nickel alloy, nickel-yttrium alloy and zinc-nickel alloy.

[0076] In one or more embodiments of the present disclosure, the magnesium source is selected from elemental magnesium and/or magnesium alloy.

[0077] In one or more embodiments of the present disclosure, the magnesium alloy is one or more selected from the group consisting of magnesium-gadolinium alloy, magnesium-yttrium alloy, magnesium-zinc alloy, magnesium-nickel alloy, magnesium-calcium alloy and magnesium-iron alloy.

[0078] In one or more embodiments of the present disclosure, the rare earth source includes elemental rare earth and/or rare earth intermediate alloy.

[0079] In one or more embodiments of the present disclosure, the elemental rare earth includes one or more selected from the group consisting of gadolinium, yttrium, erbium, dysprosium, cerium and scandium.

[0080] In one or more embodiments of the present disclosure, the rare earth intermediate alloy includes at least one selected from the group consisting of magnesium-gadolinium alloy, magnesium-yttrium alloy, magnesium-erbium alloy, magnesium-cerium alloy, magnesium-scandium alloy, nickel-yttrium alloy, nickel-gadolinium alloy, nickel-erbium alloy, nickel-cerium alloy and nickel-scandium alloy.

[0081] In one or more embodiments of the present disclosure, the alloying treatment is carried out by adopting the smelting and casting method, including following steps:

[0082] (a) casting: uniformly mixing a nickel source, a magnesium source and a rare earth source, and carrying out smelting and casting to obtain a magnesium alloy ingot; and

[0083] (b) heat treatment: carrying out, in sequence, homogenization treatment and extrusion heat deformation treatment on the magnesium alloy ingot to obtain the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material.

[0084] In the method for preparing a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material provided in the present disclosure, by carrying out casting and heat treatment in sequence, Mg, Ni and RE in the prepared alloy material form the Mg.sub.12NiRE-type long-period stacking ordered phase, the Mg.sub.xRE.sub.y phase and the Mg.sub.2Ni phase, not only the tensile strength and plasticity of the alloy material are remarkably improved, but also a large number of micro-batteries are formed in the alloy material, so that the generated nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material can be rapidly decomposed, and a downhole fracturing tool made of this magnesium alloy material can be completely degraded downhole, so that the engineering difficulty is reduced, and the construction efficiency is improved.

[0085] In one or more embodiments of the present disclosure, the step (b) also includes an aging heat treatment step, which is carried out after the extrusion heat deformation treatment, wherein the comprehensive performance of the nickel-containing, high-strength and high-toughness, alloy material is more excellent by carrying out the aging heat treatment step.

[0086] In one or more embodiments of the present disclosure, in the step (a), when the smelting and casting is carried out, the temperature is first increased to 690800 C. and maintained, the raw materials are stirred to enable them to melt completely, then the temperature is reduced to 630680 C. and maintained for 20120 min, and after cooling, the magnesium alloy ingot is obtained.

[0087] In one or more typical but non-limited embodiments of the present disclosure, in the step (a), the temperature after the smelting is, for example, 690, 700, 710, 720, 730, 740, 750, 760, 770, 780, 790 or 800 C.

[0088] In one or more embodiments of the present disclosure, during smelting and casting, after all the raw materials melt, a typical but non-limited temperature after temperature reduction is, for example, 630, 635, 640, 645, 650, 655, 660, 665, 670, 675 or 680 C.; and the temperature is kept for, for example, 20, 25, 30, 35, 40, 45, 50, 60, 70, 80, 90, 100, 110 or 120 min after temperature reduction.

[0089] In one or more embodiments of the present disclosure, the smelting is carried out using a resistance furnace or a line frequency induction furnace.

[0090] In one or more embodiments of the present disclosure, at least one cooling method of brine bath, water bath, water quenching or air cooling is used for cooling.

[0091] In one or more embodiments of the present disclosure, in the step (a), the nickel source, the rare earth source and the magnesium source are accurately weighed according to formula requirements, and uniformly mixed.

[0092] In one or more embodiments of the present disclosure, the inert gas is used during smelting and casting for protection, wherein the inert gas includes, but is not limited to, helium, argon, carbon dioxide and sulfur hexafluoride, for example, argon.

[0093] In one or more embodiments of the present disclosure, in the step (b), the homogenization treatment is carried out at a temperature of 400550 C. for 440 h.

[0094] In one or more typical but non-limited embodiments of the present disclosure, the homogenization treatment is carried out, for example, at a temperature of 400, 410, 420, 430, 440, 450, 460, 470, 480, 490, 500, 510, 520, 530, 540 or 550 C.; and the homogenization treatment is carried out, for example, for 4, 5, 6, 7, 8, 9, 10, 11, 12, 13, 14, 15, 20, 25, 30, 35 or 40 h.

[0095] In one or more embodiments of the present disclosure, the extrusion heat deformation treatment is carried out at an extrusion ratio of 840.

[0096] In one or more typical but non-limited embodiments of the present disclosure, the extrusion ratio is, for example, 8, 9, 10, 11, 12, 13, 14, 15, 16, 17, 18, 20, 22, 24, 25, 26, 27, 28, 30, 32, 35, 38 or 40.

[0097] In one or more embodiments of the present disclosure, the extrusion heat deformation treatment is carried out at a temperature of 360480 C.

[0098] In one or more typical but non-limited embodiments of the present disclosure, the extrusion heat deformation treatment is carried out at, for example, a temperature of 360, 370, 380, 390, 400, 410, 420, 430, 440, 450, 460, 470 or 480 C.

[0099] In one or more embodiments of the present disclosure, in the step (b), the aging heat treatment is carried out at a temperature of 150250 C. for 12120 h.

[0100] In one or more typical but non-limited embodiments of the present disclosure, the aging heat treatment is carried out at, for example, a temperature of 150, 155, 160, 165, 170, 175, 180, 185, 190, 195, 200, 205, 210, 215, 220, 230, 240 or 250 C.; and the aging heat treatment is carried out, for example, for 12, 13, 14, 15, 16, 17, 18, 19, 20, 22, 25, 28, 30, 35, 40, 45, 50, 55, 60, 70, 80, 90, 100, 110 or 120 h.

[0101] According to a third aspect of the present disclosure, the present disclosure provides use of the above nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material in the field of oil and gas exploitation.

[0102] The technical solutions provided in the present disclosure are further described below in connection with embodiments and comparison examples.

Example 1

[0103] The present example provides a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, including following components in percentage by mass: 6.9% of Ni, 18% of Y, and the balance of Mg and unavoidable impurities, wherein Mg, Ni and Y form an Mg.sub.12YNi-type long-period stacking ordered phase, an Mg.sub.5Y phase and an Mg.sub.2Ni phase, a volume fraction of the Mg.sub.12YNi-type long-period stacking ordered phase is 66%, a volume fraction of the Mg.sub.5Y phase is 4%, and a volume fraction of the Mg.sub.2Ni phase is 2%.

[0104] A method for preparing a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material provided in the present example includes following steps:

[0105] (1) accurately blending materials according to formula amounts, wherein a nickel source, a yttrium source and a magnesium source are added in forms of magnesium-yttrium alloy and nickel-yttrium alloy, respectively;

[0106] (2) casting: smelting using a resistance furnace or a line frequency induction furnace, wherein argon is used as a protective gas in the smelting process, increasing the temperature to 770 C. and maintaining the temperature, stirring the raw materials by electromagnetic induction so that components are homogeneous and raw materials melt fully, reducing the temperature to 655 C. after the raw materials melt completely, standing and maintaining the temperature for 25 min, taking out the molten materials to undergo salt bath water cooling to obtain an alloy ingot; and

[0107] (3) heat treatment: carrying out homogenization treatment, extrusion heat deformation treatment and aging heat treatment on the magnesium alloy ingot in sequence, and air-cooling the magnesium alloy ingot to room temperature to obtain the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, wherein the homogenization treatment is carried out at a temperature of 500 C. for 10 h; and the extrusion deformation is carried out at a temperature of 400 C., and an extrusion ratio is 11.

Example 2

[0108] The present example provides a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, including following components in percentage by mass: 2.3% of Ni, 5.3% of Y, and the balance of Mg and unavoidable impurities, wherein Mg, Ni and Y form an Mg.sub.12YNi-type long-period stacking ordered phase, an Mg.sub.5Y phase and an Mg.sub.2Ni phase, a volume fraction of the Mg.sub.12YNi-type long-period stacking ordered phase is 23%, a volume fraction of the Mg.sub.5Y phase is 6%, and a volume fraction of the Mg.sub.2Ni phase is 1.8%.

[0109] A method for preparing a degradable magnesium alloy material provided in the present example is the same as that of Example 1, and unnecessary details will not be given herein.

Example 3

[0110] The present example provides a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, including following components in percentage by mass: 8.5% of Gd, 4.5% of Y, 0.5% of Ni, 0.8% of Mn, and the balance of Mg and unavoidable impurities, wherein Mg, Gd, Y and Ni form an Mg.sub.12YNi-type long-period stacking ordered phase, an Mg.sub.12GdNi-type long-period stacking ordered phase, an Mg.sub.5Gd phase, an Mg.sub.5Y phase and an Mg.sub.2Ni phase, and wherein a volume fraction of the two long-period stacking ordered phases is 15%, a volume fraction of the Mg.sub.5Gd phase and the Mg.sub.5Y phase is 12%, and a volume fraction of the Mg.sub.2Ni phase is 1.2%.

[0111] A method for preparing a degradable magnesium alloy material provided in the present example is different from the preparation method provided in Example 1 in that the homogenization treatment is carried out at a temperature of 540 C. for 4 h; the extrusion deformation is carried out at a temperature of 450 C., and an extrusion ratio is 11; and the aging heat treatment is carried out at a temperature of 200 C. for 50 h. All of other steps are the same as those in the preparation method in Example 1, and unnecessary details will not be given herein.

Example 4

[0112] The present example provides a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, including following components in percentage by mass: 4% of Gd, 4% of Er, 0.8% of Ni, and the balance of Mg and unavoidable impurities, wherein Mg, Gd, Er and Ni form an Mg.sub.12GdNi-type long-period stacking ordered phase, an Mg.sub.12ErNi-type long-period stacking ordered phase, an Mg.sub.5Gd phase, an Mg.sub.5Er phase and an Mg.sub.2Ni phase, and wherein a volume fraction of the two long-period stacking ordered phases is 10.5%, a volume fraction of the Mg.sub.5Gd phase and the Mg.sub.5Er phase is 8%, and a volume fraction of the Mg.sub.2Ni phase is 1.2%.

[0113] A method for preparing a degradable magnesium alloy material provided in the present example is different from the preparation method provided in Example 1 in that the homogenization treatment is carried out at a temperature of 450 C. for 12 h; and the extrusion deformation is carried out at a temperature of 450 C., and an extrusion ratio is 28. All of other steps are the same as those in the preparation method in Example 1, and unnecessary details will not be given herein.

Example 5

[0114] The present example provides a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, including following components in percentage by mass: 19% of Dy, 2.9% of Ni, and the balance of Mg and unavoidable impurities, wherein Mg, Ni and Dy form an Mg.sub.12DyNi-type long-period stacking ordered phase, an Mg.sub.5Dy phase and an Mg.sub.2Ni phase, and wherein a volume fraction of the Mg.sub.12DyNi-type long-period stacking ordered phase is 24%, a volume fraction of the Mg.sub.5Dy phase is 11%, and a volume fraction of the Mg.sub.2Ni phase is 1.5%.

[0115] A method for preparing a degradable magnesium alloy material provided in the present example is different from the preparation method provided in Example 1 in that the homogenization treatment is carried out at a temperature of 540 C. for 6 h; the extrusion deformation is carried out at a temperature of 360 C., and an extrusion ratio is 28; and the aging heat treatment is carried out at a temperature of 200 C. for 60 h. All of other steps are the same as those in the preparation method in Example 1, and unnecessary details will not be given herein.

Example 6

[0116] The present example provides a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, including following components in percentage by mass: 1% of Ce, 0.5% of Zr, 1% of Ni, and the balance of Mg and unavoidable impurities, wherein Mg, Ni, Ce and Zr form an Mg.sub.12CeNi-type long-period stacking ordered phase, an Mg.sub.12ZrNi-type long-period stacking ordered phase, an Mg.sub.5Zr phase, an Mg.sub.5Ce phase and an Mg.sub.2Ni phase, and wherein a volume fraction of the long-period stacking ordered phases is 4.8%, a volume fraction of the Mg.sub.5Zr phase and the Mg.sub.5Ce phase is 2%, and a volume fraction of the Mg.sub.2Ni phase is 4%.

[0117] A method for preparing a degradable magnesium alloy material provided in the present example is the same as the preparation method provided in Example 4, and unnecessary details will not be given herein.

Example 7

[0118] The present example provides a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, including following components in percentage by mass: 6% of Er, 7.5% of Ni, and the balance of Mg and unavoidable impurities, wherein Mg, Er and Ni form an Mg.sub.12ErNi-type long-period stacking ordered phase, an Mg.sub.5Er phase and an Mg.sub.2Ni phase, and wherein a volume fraction of the Mg.sub.12ErNi-type long-period stacking ordered phase is 65%, a volume fraction of the Mg.sub.5Er phase is 3%, and a volume fraction of the Mg.sub.2Ni phase is 5%.

[0119] A method for preparing a degradable magnesium alloy material provided in the present example is different from the preparation method provided in Example 1 in that the homogenization treatment is carried out at a temperature of 500 C. for 10 h; and the extrusion deformation is carried out at a temperature of 400 C., and an extrusion ratio is 11. All of other steps are the same as those in the preparation method in Example 1, and unnecessary details will not be given herein.

Example 8

[0120] The present example provides a controllably degradable magnesium alloy material, including following components in percentage by mass: 8.0% of Gd, 5.0% of Y, 1.5% of Ni, 0.8% of Mn, and the balance of Mg and unavoidable impurities, wherein Mg, Gd, Y and Ni form Mg.sub.12GdNi type and Mg.sub.12GdY-type long-period stacking ordered phases and Mg.sub.24Y.sub.5 and Mg.sub.5Gd phases, and wherein a volume fraction of the Mg.sub.12GdNi-type and Mg.sub.12GdY-type long-period stacking ordered phases is 20%, a volume fraction of the Mg.sub.24Y.sub.5 and Mg.sub.5Gd phases is 12%, and a volume fraction of the Mg.sub.2Ni phase is 2%.

[0121] A method for preparing the degradable magnesium alloy material provided in the present example is different from the preparation method provided in Example 1 in that the homogenization treatment is carried out at a temperature of 540 C. for 4 h; the extrusion deformation is carried out at a temperature of 400 C., and an extrusion ratio is 11; and the aging heat treatment is carried out at a temperature of 200 C. for 50 h. All of other steps are the same as those in the preparation method in Example 1, and unnecessary details will not be given herein.

[0122] In the above Examples 1-8, contents of the unavoidable impurities in the magnesium alloy material are all less than 0.2%.

Comparative Example 1

[0123] The present comparative example provides a magnesium alloy material, which is different from Example 1 in that no Ni is contained, and that the magnesium-yttrium alloy is prepared according to a conventional method.

Comparative Example 2

[0124] The present comparative example provides a magnesium alloy material, which is different from Example 1 in that no Y is contained, and that the magnesium-nickel alloy is prepared according to a conventional method.

Comparative Example 3

[0125] The present comparative example provides a magnesium alloy material, which is different from Example 1 in that Ni is 0.1% in percentage by mass. A method for preparing the magnesium alloy material is the same as that in Example 1, and unnecessary details will not be given herein.

Comparative Example 4

[0126] The present comparative example provides a magnesium alloy material, which is different from Example 1 in that Ni is 10% in percentage by mass. A method for preparing the magnesium alloy material is the same as that in Example 1, and unnecessary details will not be given herein.

Comparative Example 5

[0127] The present comparative example provides a magnesium alloy material, which is different from Example 1 in that Y is 0.1% in percentage by mass. A method for preparing the magnesium alloy material is the same as that in Example 1, and unnecessary details will not be given herein.

Comparative Example 6

[0128] The present comparative example provides a magnesium alloy material, which is different from Example 1 in that Y is 25% in percentage by mass. A method for preparing the magnesium alloy material is the same as that in Example 1, and unnecessary details will not be given herein.

Test Example 1

[0129] The magnesium alloy materials provided in Examples 17 are respectively measured for tensile strength, yield strength, elongation and corrosion rate, wherein the tensile strength, the yield strength and the elongation are measured at room temperature, a test direction of the tensile strength is an extrusion direction (0), a tensile speed is 2 mm/min, and a corrosion rate is measured at 90 C. in a 3.5 wt % KCl solution. Results are shown in Table 1.

TABLE-US-00001 TABLE 1 Table of Property Data of Magnesium Alloy Materials Tensile Yield Corrosion Strength Strength Elongation Rate Group (MPa) (MPa) (%) (mm/a) Example 1 445 345 11.3 1800 Example 2 404 313 8.9 834 Example 3 402 298 10.8 407 Example 4 409 187 20.1 635 Example 5 325 156 21.8 785 Example 6 267 185 21 363 Example 7 355 282 17 2100 Example 8 505 415 6.0 1300 Comparative 410 315 2 10 Example 1 Comparative 140 72 5 2000 Example 2 Comparative 425 320 3.5 98 Example 3 Comparative 405 290 1900 Example 4 Comparative 168 85 5.3 1850 Example 5 Comparative 460 360 1300 Example 6 Notes: indicates that the material is brittle, which has an extremely low elongation and cannot be put into use.

[0130] It can be seen from Table 1 that the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy materials provided in Examples 17 have the tensile strength of 267505 MPa, the yield strength of 156415 MPa, and the elongation of 6.021.8% at room temperature, and has the decomposition rate of 363 mm/a 2100 mm/a in a 3.5 wt % KCl solution at 90 C., which indicates that the magnesium alloy material provided in the present disclosure has remarkably improved mechanical properties by adding specific contents of nickel and rare earth element to magnesium acting as a base material, and the degradation rate of the magnesium alloy material can meet the use requirement of self-ablation of downhole tools in the field of petroleum and natural gas.

[0131] Finally, it should be noted that the various embodiments above are merely used for illustrating the technical solutions of the present disclosure, rather than limiting the present disclosure; although the detailed description is made to the present disclosure with reference to various preceding embodiments, those ordinarily skilled in the art should understand that they still could modify the technical solutions recited in various preceding embodiments, or make equivalent substitutions to some or all of the technical features therein; and these modifications or substitutions do not make the corresponding technical solutions essentially depart from the scope of the technical solutions of various embodiments of the present disclosure.

INDUSTRIAL APPLICABILITY

[0132] The method for preparing a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material provided in the present disclosure can be carried out in batch in industry and is simple in process, convenient in operation, facilitates large-scale industrial production, and reduces the production cost, the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material prepared with this method has remarkably improved tensile strength and plasticity of alloy materials and other advantages, moreover, the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material prepared with this method can be rapidly decomposed, and the downhole fracturing tools made of this magnesium alloy material can effectively meet requirements in the field of oil and gas exploitation.