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 Mg12RENi-type long-period phase, an Mg2Ni phase and an MgxREy 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 Mg12RENi-type long-period phase and Mg2Ni 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.

Description

CROSS-REFERENCE TO RELATED APPLICATION

The present disclosure claims priority of Chinese patent application with the filing number 201811237934.1 filed on Oct. 23, 2018 with the Chinese Patent Office, and entitled “Nickel-containing High-toughness Controllably Degradable Magnesium Alloy Material, Preparation Method therefor and Use thereof”, the contents of which are incorporated herein by reference in entirety.

TECHNICAL FIELD

The present disclosure relates to the technical field of magnesium alloy, in particular to a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, a preparation method therefor and use thereof.

BACKGROUND ART

With the rapid progress of economy, the petroleum problem in China has become one of the important problems with national concern. According to statistical data of the national statistical bureau, the net petroleum import in China is increasing continuously, and the dependency of petroleum in China on foreign countries directly breaks through 60% by 2015. According to international experience and opinion of people in authority, the dependency of petroleum in China on foreign countries must be kept below 60%. China should reduce the dependency of petroleum on foreign countries, both from a strategic point of view and due to concerns about national safety and normal economic operation. Therefore, increasing the mining power of internal petroleum and improving the petroleum mining efficiency is an important measure for building powerful China, and it is urgent to explore new technologies and research and develop new materials.

China has abundant low-permeability oil and gas resources, and possesses great exploration and exploitation potential. The stable production and yield increase of future oil and gas production will depend on unconventional low-permeability oil and gas resources to a great extent. However, most of these unconventional oil and gas resources are distributed in strata with different depths, and the single-well productivity needs to be improved by simultaneously transforming a plurality of strata by adopting a multi-layer and multi-section fracturing technology, so that the yield of oil field and the construction efficiency are improved.

In multi-layer and multi-section fracturing, a packing tool (such as fracturing ball and bridge plug) needs to be used between layers and sections, so as to, after separation, carry out fracturing transformation layer by layer, and after the construction of all layers and all sections is completed, the packing tool is cleaned up from a wellbore, so as to break through a well and realize exploitation of oil and gas. However, most of the existing common packing tools are made of steel, and have the defects of difficult drilling and milling, long-time consumption, difficult removal of powders and fragments after drilling and so on, which greatly increases the construction period and cost.

Therefore, a light-weight fracturing ball capable of bearing a high pressure of fracturing construction and a high temperature of an oil well, and controllably and rapidly being corroded in the fluid environment of the oil well is researched, so that the construction cost and risk can be effectively reduced, the construction period can be shortened, and the construction efficiency can be improved.

SUMMARY OF THE INVENTION

Object of the present disclosure include, for example, providing a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, so as to solve the technical problems that most of the existing common packing tools, made of steel, have the defects of difficult drilling and milling, long time consumption, difficult removal of powders and fragments after drilling and so on, which greatly increases the construction period and the cost.

The nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material provided in the present disclosure includes following components in percentage by mass: 0.3˜8.5% of Ni, 0.5˜28% of RE, and the balance of Mg and unavoidable impurities, wherein RE is a rare earth element, and Mg, Ni and RE form an Mg₁₂RENi-type long-period stacking ordered phase (i.e., Mg₁₂NiRE-type long-period stacking ordered phase), an Mg₂Ni phase and an Mg_xRE_y phase, wherein a volume fraction of the Mg₁₂RENi-type long-period stacking ordered phase is 3˜70%, a volume fraction of the Mg₂Ni phase is 0.5˜10%, a volume fraction of the Mg_xRE_y phase is 0.5˜22%, and a value range of x:y is (3˜12):1.

In one or more embodiments, the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material includes following components in percentage by mass: 0.5˜8.0% of Ni, 1.5˜20% of RE, and the balance of Mg and unavoidable impurities.

In one or more embodiments, 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.

In one or more embodiments, the as-cast magnesium alloy includes an Mg₁₂NiRE-type long-period stacking ordered phase, an Mg₅RE phase and an Mg₂Ni phase, wherein a volume fraction of the Mg₁₂NiRE-type long-period stacking ordered phase is 3˜65%, a volume fraction of the Mg₂Ni phase is 0.5˜6%, and a volume fraction of the Mg₅RE phase is 0.5˜15%.

In one or more embodiments, the as-extruded magnesium alloy includes an Mg₁₂NiRE-type long-period stacking ordered phase, an Mg₂Ni phase and an Mg₅RE phase, wherein a volume fraction of the Mg₁₂NiRE-type long-period stacking ordered phase is 4˜70%, a volume fraction of the Mg₂Ni phase is 1%˜8%, and a volume fraction of the Mg₅RE phase is 1˜20%.

In one or more embodiments, the aged magnesium alloy includes an Mg₁₂NiRE-type long-period stacking ordered phase, an Mg₂Ni phase and an Mg_xRE_y phase, wherein a volume fraction of the Mg₁₂NiRE-type long-period stacking ordered phase is 4˜70%, a volume fraction of the Mg₂Ni phase is 2˜10%, and a volume fraction of the Mg_xRE_y phase is 2˜22%, wherein a value range of x:y is 3:1˜12:1.

In one or more embodiments, the RE is at least one selected from the group consisting of Gd, Y, Er, Dy, Ce and Sc.

In one or more embodiments, the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material includes following components in percentage by mass: 0.3˜8.5% of Ni, 0.5˜28% of RE, 0.03˜10% of M, and the balance of Mg and unavoidable impurities, wherein M is an element capable of alloying with magnesium.

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

In one or more embodiments, M is at least one of Fe, Cu and Mn.

Object of the present disclosure include, for example, providing a method for preparing a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, including the 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.

In one or more embodiments, the nickel source is selected from elemental nickel and/or nickel alloy.

In one or more embodiments, the nickel alloy is at least one selected from the group consisting of magnesium-nickel alloy, nickel-yttrium alloy and zinc-nickel alloy.

In one or more embodiments, the magnesium source is selected from elemental magnesium and/or magnesium alloy.

In one or more embodiments, 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.

In one or more embodiments, the rare earth source includes elemental rare earth and/or rare earth intermediate alloy.

In one or more embodiments, the elemental rare earth includes at least one selected from the group consisting of gadolinium, yttrium, erbium, dysprosium, cerium and scandium.

In one or more embodiments, 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.

In one or more embodiments, the alloying treatment includes a smelting and casting method and a powder alloying method.

In one or more embodiments, the alloying treatment is carried out by adopting the smelting and casting method.

In one or more embodiments, the smelting and casting method includes 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, 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.

In one or more embodiments, the step (b) also includes an aging heat treatment step, wherein the aging heat treatment step is carried out after the extrusion heat deformation treatment.

In one or more embodiments, in the step (a), when the smelting and casting is carried out, the temperature is first increased to 690˜800° C. and maintained, the raw materials are stirred to enable them to melt completely, then the temperature is reduced to 630˜680° C. and maintained for 20˜120 min, and after cooling, the magnesium alloy ingot is obtained.

In one or more embodiments, an inert gas is used during the smelting and casting for protection.

In one or more embodiments, the inert gas is at least one selected from the group consisting of helium, argon, carbon dioxide and sulfur hexafluoride, for example, argon. In one or more embodiments, a cooling method is at least one selected from the group consisting of brine bath, water quenching, furnace cooling and air cooling.

In one or more embodiments, smelting is carried out using a resistance furnace or a line frequency induction furnace.

In one or more embodiments, 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.

In one or more embodiments, in the step (b), the homogenization treatment is carried out at a temperature of 400˜550° C. for 4˜40 h.

In one or more embodiments, in the step (b), an extrusion ratio in the extrusion heat deformation treatment is 8˜40.

In one or more embodiments, the extrusion heat deformation treatment is carried out at a temperature of 360˜480° C.

In one or more embodiments, in the step (b), the aging heat treatment is carried out at a temperature of 150˜250° C. for 12˜120 h.

In one or more embodiments, in the step (b), the aging heat treatment is carried out at a temperature of 180˜220° C. for 15˜60 h.

Object of the present disclosure include, for example, providing use of a nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material in the field of oil and gas exploitation.

The present disclosure at least has following beneficial effects:

(1) 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 Mg₁₂RENi-type long-period stacking ordered phase, the Mg₂Ni phase and the Mg_xRE_y phase are formed by adding Ni and RE, so that the tensile strength and plasticity of the alloy material are remarkably improved; meanwhile, a quite large electronegativity difference exists between the Mg₁₂RENi-type long-period stacking ordered phase and the Mg₂Ni 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.

(2) 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.

DETAILED DESCRIPTION OF EMBODIMENTS

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.

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: 0.3˜8.5% of Ni, 0.5˜28% 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 Mg₁₂RENi-type long-period stacking ordered phase, an Mg₂Ni phase and an Mg_xRE_y phase.

A volume fraction of the Mg₁₂RENi-type long-period stacking ordered phase is 3˜70%, a volume fraction of the Mg₂Ni phase is 0.5˜10%, and a volume fraction of the Mg_xRE_y phase is 0.5˜22%.

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%.

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 Mg₁₂RENi-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.

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%.

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%.

In one or more embodiments, the volume fraction of the Mg₁₂RENi-type long-period stacking ordered phase is 3˜70%, the volume fraction of the Mg₅RE phase is 0.5˜20%, the volume fraction of the Mg₂Ni phase is 0.5˜10%, the volume fraction of the Mg_xRE_y phase is 0.5˜22%, and a value range of x:y is (3˜12):1 (i.e., 3:1˜12:1).

By setting the volume fraction of the Mg₁₂RENi-type long-period stacking ordered phase to be 3˜70%, the volume fraction of the Mg₂Ni phase to be 0.5˜10%, and the volume fraction of the Mg_xRE_y phase to be 0.5˜22%, the Mg₁₂RENi-type long-period stacking ordered phase and the Mg_xRE_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 Mg₁₂RENi-type long-period stacking ordered phase and the Mg₂Ni 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.

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 Mg₁₂RENi-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 Mg₂Ni 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_xRE_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.

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 Mg₁₂RENi-type long-period stacking ordered phase and the Mg_xRE_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 Mg₁₂RENi-type long-period stacking ordered phase and the Mg₂Ni 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.

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.

In one or more embodiments of the present disclosure, when Ni is 0.5˜7.5% and RE is 1.5˜19%, in the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material; and the volume fraction of the Mg₁₂RENi-type long-period stacking ordered phase is 4.8˜65%, the volume fraction of the Mg₅RE phase is 1˜15%, and the volume fraction of the Mg₂Ni phase is 1˜5%, the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material has the tensile strength of 325˜505 MPa, the yield strength of 156˜415 MPa, and the elongation of 6.0˜21.8% at room temperature, and the decomposition rate of 363 mm/a˜2500 mm/a in a 3.5 wt % KCl solution at 90° C.

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.

In one or more embodiments of the present disclosure, in the as-cast magnesium alloy, Mg, Ni and RE mainly form an Mg₁₂RENi-type long-period stacking ordered phase, an Mg₂Ni phase and an Mg₅RE phase, wherein a volume fraction of the Mg₁₂NiRE-type long-period stacking ordered phase is 3˜65%, a volume fraction of the Mg₂Ni phase is 0.5˜6%, and a volume fraction of the Mg₅RE phase is 0.5˜15%.

In one or more embodiments of the present disclosure, in the as-cast magnesium alloy, a typical but non-limited volume fraction of the Mg₁₂NiRE-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 Mg₂Ni 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 Mg₅RE phase is, for example, 0.5%, 0.8%, 1%, 2%, 5%, 8%, 10%, 12% or 15%.

In one or more embodiments of the present disclosure, in the as-extruded magnesium alloy, Mg, Ni and RE mainly form an Mg₁₂RENi-type long-period stacking ordered phase, an Mg₂Ni phase and an Mg₅RE phase, wherein a volume fraction of the Mg₁₂NiRE-type long-period stacking ordered phase is 4˜70%, a volume fraction of the Mg₂Ni phase is 1%˜8%, and a volume fraction of the Mg₅RE phase is 1˜20%.

In one or more embodiments of the present disclosure, in the as-extruded magnesium alloy, a typical but non-limited volume fraction of the Mg₁₂NiRE-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 Mg₂Ni 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 Mg₅RE phase is, for example, 1%, 2%, 5%, 8%, 10%, 12%, 15%, 18% or 20%.

In one or more embodiments of the present disclosure, in the aged magnesium alloy, Mg, Ni and RE mainly form an Mg₁₂RENi-type long-period stacking ordered phase, an Mg₂Ni phase and Mg_xRE_y phase (x:y=(3˜12):1), wherein a volume fraction of the Mg₁₂NiRE-type long-period stacking ordered phase is 4˜70%, a volume fraction of the Mg₂Ni phase is 2%˜10%, and a volume fraction of the Mg₅RE phase is 2˜22%.

In one or more embodiments of the present disclosure, in the aged magnesium alloy, a typical but non-limited volume fraction of the Mg₁₂NiRE-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 Mg₂Ni 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_xRE_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.

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.

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: 0.3˜8.5% of Ni, 0.5˜28% of RE, 0.03˜10% of M, and the balance of Mg and unavoidable impurities, wherein M is an element capable of alloying with magnesium.

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%.

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

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:

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.

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.

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

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

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.

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

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.

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

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.

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.

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:

(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, 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.

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 Mg₁₂NiRE-type long-period stacking ordered phase, the Mg_xRE_y phase and the Mg₂Ni 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.

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.

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 690˜800° C. and maintained, the raw materials are stirred to enable them to melt completely, then the temperature is reduced to 630˜680° C. and maintained for 20˜120 min, and after cooling, the magnesium alloy ingot is obtained.

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.

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.

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

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.

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.

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.

In one or more embodiments of the present disclosure, in the step (b), the homogenization treatment is carried out at a temperature of 400˜550° C. for 4˜40 h.

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.

In one or more embodiments of the present disclosure, the extrusion heat deformation treatment is carried out at an extrusion ratio of 8˜40.

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.

In one or more embodiments of the present disclosure, the extrusion heat deformation treatment is carried out at a temperature of 360˜480° C.

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.

In one or more embodiments of the present disclosure, in the step (b), the aging heat treatment is carried out at a temperature of 150˜250° C. for 12˜120 h.

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.

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.

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

Example 1

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 Mg₁₂YNi-type long-period stacking ordered phase, an Mg₅Y phase and an Mg₂Ni phase, a volume fraction of the Mg₁₂YNi-type long-period stacking ordered phase is 66%, a volume fraction of the Mg₅Y phase is 4%, and a volume fraction of the Mg₂Ni phase is 2%.

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:

(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;

(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

(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

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 Mg₁₂YNi-type long-period stacking ordered phase, an Mg₅Y phase and an Mg₂Ni phase, a volume fraction of the Mg₁₂YNi-type long-period stacking ordered phase is 23%, a volume fraction of the Mg₅Y phase is 6%, and a volume fraction of the Mg₂Ni phase is 1.8%.

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

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 Mg₁₂YNi-type long-period stacking ordered phase, an Mg₁₂GdNi-type long-period stacking ordered phase, an Mg₅Gd phase, an Mg₅Y phase and an Mg₂Ni phase, and wherein a volume fraction of the two long-period stacking ordered phases is 15%, a volume fraction of the Mg₅Gd phase and the Mg₅Y phase is 12%, and a volume fraction of the Mg₂Ni phase is 1.2%.

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

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 Mg₁₂GdNi-type long-period stacking ordered phase, an Mg₁₂ErNi-type long-period stacking ordered phase, an Mg₅Gd phase, an Mg₅Er phase and an Mg₂Ni phase, and wherein a volume fraction of the two long-period stacking ordered phases is 10.5%, a volume fraction of the Mg₅Gd phase and the Mg₅Er phase is 8%, and a volume fraction of the Mg₂Ni phase is 1.2%.

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

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 Mg₁₂DyNi-type long-period stacking ordered phase, an Mg₅Dy phase and an Mg₂Ni phase, and wherein a volume fraction of the Mg₁₂DyNi-type long-period stacking ordered phase is 24%, a volume fraction of the Mg₅Dy phase is 11%, and a volume fraction of the Mg₂Ni phase is 1.5%.

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

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 Mg₁₂CeNi-type long-period stacking ordered phase, an Mg₁₂ZrNi-type long-period stacking ordered phase, an Mg₅Zr phase, an Mg₅Ce phase and an Mg₂Ni phase, and wherein a volume fraction of the long-period stacking ordered phases is 4.8%, a volume fraction of the Mg₅Zr phase and the Mg₅Ce phase is 2%, and a volume fraction of the Mg₂Ni phase is 4%.

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

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 Mg₁₂ErNi-type long-period stacking ordered phase, an Mg₅Er phase and an Mg₂Ni phase, and wherein a volume fraction of the Mg₁₂ErNi-type long-period stacking ordered phase is 65%, a volume fraction of the Mg₅Er phase is 3%, and a volume fraction of the Mg₂Ni phase is 5%.

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

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 Mg₁₂GdNi type and Mg₁₂GdY-type long-period stacking ordered phases and Mg₂₄Y₅ and Mg₅Gd phases, and wherein a volume fraction of the Mg₁₂GdNi-type and Mg₁₂GdY-type long-period stacking ordered phases is 20%, a volume fraction of the Mg₂₄Y₅ and Mg₅Gd phases is 12%, and a volume fraction of the Mg₂Ni phase is 2%.

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.

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

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

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

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

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

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

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

The magnesium alloy materials provided in Examples 1˜7 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 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.

It can be seen from Table 1 that the nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy materials provided in Examples 1˜7 have the tensile strength of 267˜505 MPa, the yield strength of 156˜415 MPa, and the elongation of 6.0˜21.8% 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.

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

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.

Claims

1. A nickel-containing, high-strength and high-toughness, controllably degradable magnesium alloy material, comprising following components in percentage by mass: 0.3˜8.5% of Ni, 0.5˜28% 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 Mg12RENi-type long-period stacking ordered phase, an Mg2Ni phase and an MgxREy phase; a volume fraction of the Mg12RENi-type long-period stacking ordered phase is 3˜70%, a volume fraction of the Mg2Ni phase is 0.5˜10%, a volume fraction of the MgxREy phase is 0.5˜22%, and a value range of x:y is 3:1˜12:1.

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: 0.5˜8.0% of Ni, 1.5˜20% 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: 0.3˜8.5% of Ni, 0.5˜28% of RE, 0.03˜10% 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 690˜800° C. and maintained, raw materials are stirred to enable them to melt completely, then the temperature is reduced to 630˜680° C. and maintained for 20˜120 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 400˜550° C. for 4˜40 h; and

in the step (b), the extrusion heat deformation treatment is carried out at an extrusion ratio of 8˜40; and preferably, the extrusion heat deformation treatment is carried out at a temperature of 360˜480° C.

14. The method according to claim 6, wherein the aging heat treatment is carried out at a temperature of 150˜250° C. for 12˜120 h.

15. The method according to claim 6, wherein the aging heat treatment is carried out at a temperature of 180˜220° C. for 15˜60 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 Mg12RENi-type long-period stacking ordered phase, an Mg5RE phase and an Mg2Ni phase, wherein a volume fraction of the Mg12RENi-type long-period stacking ordered phase is 3˜65%, a volume fraction of the Mg2Ni phase is 0.5˜6%, and a volume fraction of the Mg5RE phase is 0.5˜15%.

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 Mg12RENi-type long-period stacking ordered phase, an Mg2Ni phase and an Mg5RE phase, wherein a volume fraction of the Mg12RENi-type long-period stacking ordered phase is 4˜70%, a volume fraction of the Mg2Ni phase is 1%˜8%, and a volume fraction of the Mg5RE phase is 1˜20%.

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 Mg12RENi-type long-period stacking ordered phase, an Mg2Ni phase and an MgxREy phase, wherein a volume fraction of the Mg12RENi-type long-period stacking ordered phase is 4˜70%, a volume fraction of the Mg2Ni phase is 2˜10%, and a volume fraction of the MgxREy phase is 2˜22%, wherein a value range of x:y is 3:1˜12:1.