Note: Descriptions are shown in the official language in which they were submitted.
Nickel-containing High-toughness Controllably Degradable Magnesium Alloy
Material, Preparation Method therefor and Use thereof
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,
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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,
1 a
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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
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 Mgi2RENi-type long-
period stacking ordered phase (i.e., Mg12NiRE-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 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 (3-12):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%.
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In one or more embodiments, the aged magnesium alloy includes an
Mg12N1RE-type long-period stacking ordered phase, an Mg2Ni phase and an
MgxREy 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 MgxREy 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,
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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.
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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,REy 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.
***
Various other aspects of the invention are defined with reference to the
following
preferred embodiments [1] to [30].
Date Recue/Date Received 2023-07-28
[1] A
method for preparing a magnesium alloy material which is a nickel-containing,
high-strength and high-toughness, controllably degradable magnesium alloy
material, said magnesium alloy material comprising following components in
percentage by mass:
0.3% to 8.5% of Ni,
0.5% to 28% of RE, and
a balance of Mg and unavoidable impurities,
wherein RE is at least one rare earth element, and Mg, Ni and RE form an
Mg12RENi long-period stacking ordered phase, an Mg2Ni phase and an Mg,REy
phase; wherein a volume fraction of the Mg12RENi long-period stacking ordered
phase is 3% to 70%, a volume fraction of the Mg2Ni phase is 0.5% to 10%, a
volume fraction of the Mg,REy phase is 0.5 to 22%, and a value range of x:y is
3:1 to 12:1;
said method comprising the following steps of (i) uniformly mixing a nickel
source, a magnesium source and at least one rare earth element source, and
(ii)
carrying out an alloying treatment by a smelting and casting method, to
provide
the magnesium alloy material; and
wherein the smelting and casting method comprises:
(a) a casting step, after step (i) mentioned above, carrying out a smelting
and
casting comprising firstly increasing temperature to 690 C to 800 C,
maintaining the temperature at 690 C to 800 C and stirring raw materials
until said raw materials completely melt, reducing temperature to 630 C to
680 C and maintaining for 20 min to 120 min, and then cooling to provide a
magnesium alloy ingot; and
(b) a heat treatment comprising carrying out a homogenization treatment, an
extrusion heat deformation treatment and an aging heat treatment on the
magnesium alloy ingot in sequence to provide the nickel-containing, high-
strength and high-toughness, controllably degradable magnesium alloy
material.
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[2] The method according to [1], wherein the magnesium alloy material
comprises
following components in percentage by mass:
0.5% to 8.0% of Ni,
1.5% to 20% of RE,
a balance of Mg and unavoidable impurities.
[3] The method according to [1], wherein the magnesium alloy material
comprises
at least one of an as-cast magnesium alloy, an as-extruded magnesium alloy
and an aged magnesium alloy.
[4] The method according to [3], wherein the as-cast magnesium alloy
comprises
the Mg12RENi long-period stacking ordered phase, the Mg5RE phase and the
Mg2Ni phase, wherein the volume fraction of the Mg12RENi long-period stacking
ordered phase is 3% to 65%, the volume fraction of the Mg2Ni phase is 0.5% to
6%, and the volume fraction of the Mg5RE phase is 0.5% to 15%.
[5] The method according to [3], wherein the as-cast magnesium alloy
comprises
the Mg12RENi long-period stacking ordered phase, the Mg2Ni phase and the
Mg5RE phase, wherein the volume fraction of the Mg12RENi long-period stacking
ordered phase is 4% to 70%, the volume fraction of the Mg2Ni phase is 1% to
8%, and the volume fraction of the Mg5RE phase is 1% to 20%.
[6] The method according to [3], wherein the as-cast magnesium alloy
comprises
the Mg12RENi long-period stacking ordered phase, the Mg2Ni phase and the
MgxREy phase, wherein the volume fraction of the Mg12RENi long-period
stacking ordered phase is 4% to 70%, the volume fraction of the Mg2Ni phase is
2% to 10%, and the volume fraction of the Mg,REy phase is 2% to 22%.
[7] The method according to any one of [1] to [6], wherein the RE is at
least one
selected from the group consisting of Gd, Y, Er, Dy, Ce and Sc.
[8] The method according to [7], wherein the content of the unavoidable
impurities,
in percentage by mass, is not higher than 0.2% in the magnesium alloy
material.
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[9] The method according to [7] , wherein the magnesium alloy material
further
comprises a component M which is at least one element capable of alloying with
magnesium, and wherein the magnesium alloy material comprises following
components in percentage by mass:
0.3% to 8.5% of Ni,
0.5% to 28% of RE,
0.03% to 10% of the component M, and
a balance of Mg and unavoidable impurities.
[10] The method according to [9], wherein the content of the unavoidable
impurities,
in percentage by mass, is not higher than 0.2% in the magnesium alloy
material.
[11] The method according to [9] or [10] , wherein component M is selected
from the
group consisting of Fe, Cu and Mn.
[12] The method according to any one of [1] to [11] , wherein the nickel
source is
selected from the group consisting of elemental nickel, nickel alloy and
mixtures
thereof.
[13] The method according to [12] , wherein the nickel alloy is at least one
selected
from the group consisting of magnesium-nickel alloy, nickel-yttrium alloy and
zinc-nickel alloy.
[14] The method according to [11] , wherein the magnesium source is selected
from
the group consisting of elemental magnesium, magnesium alloy and mixtures
thereof.
[16] The method according to [14] , wherein 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.
[16] The method according to [11] , wherein the at least one rare earth
element
source comprises elemental rare earth and/or rare earth intermediate alloy.
5c
Date Recue/Date Received 2023-07-28
[17] The method according to [16], wherein the elemental rare earth comprises
at
least one selected from the group consisting of gadolinium, yttrium, erbium,
dysprosium, cerium and scandium.
[18] The method according to [16], wherein 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-yttri urn alloy,
nickel-
gadolini urn alloy, nickel-erbium alloy, nickel-cerium alloy and nickel-
scandium
alloy.
[19] The method according to [11], wherein the aging heat treatment is carried
out at
a temperature of 150 C to 250 C for 12 h to 120 h.
[20] The method according to [11] or [19], wherein the aging heat treatment is
carried out at a temperature of 180 C to 220 C for 15 h to 60 h.
[21] The method according to [11], wherein the cooling is obtained by a
cooling
method which is at least one selected from the group consisting of brine bath,
water quenching, furnace cooling and air cooling.
[22] The method according to any one of [11] to [21], wherein an inert gas is
used
during the smelting and casting for protection.
[23] The method according to [22], wherein the inert gas is at least one
selected from
the group consisting of helium, argon, carbon dioxide and sulfur hexafluoride.
[24] The method according to [23], wherein the inert gas is argon.
[25] The method according to any one of [11] to [24], wherein the smelting is
carried
out using a resistance furnace or a line frequency induction furnace.
[26] The method according to any one of [11] to [25], wherein in the step (b),
the
homogenization treatment is carried out at a temperature of 400 C to 550 C for
4h to 40h.
[27] The method according to [26], wherein in the step (b), the extrusion heat
deformation treatment is carried out at an extrusion ratio of 8 to 40.
5d
Date Recue/Date Received 2023-07-28
[28] The method according to [27], wherein the extrusion heat deformation
treatment
is carried out at a temperature of 360 C to 480 C.
[29] A magnesium alloy material which is a nickel-containing, high-strength
and high-
toughness, controllably degradable magnesium alloy material, obtained from the
method defined in any one of [1] to [28].
[30] A use of the magnesium alloy material as defined in [29] in a field of
oil and gas
exploitation.
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
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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%, and a volume
fraction of the MgxREy 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 Mgi2REN1-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 MgxREy 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 MgxREy phase to be 0.5-22%, the
Mg12RENi-type long-period stacking ordered phase and the MgxREy 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
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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 MgxREy 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 MgxREy 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 mmia - 2500 rnm/a in a 3.5wt% KCI 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 Mgi2RENi-type long-period
stacking ordered phase, an Mg2Ni phase and an Mg5RE phase, wherein a
volume fraction of the Mgi2NiRE-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%.
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In one or more embodiments of the present disclosure, in the as-cast
magnesium alloy, a typical but non-limited volume fraction of the Mg12N1RE-
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 Mgi2RENi-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 MgxREy 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 MgxREy 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.
8
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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.
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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 MgxREy 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.
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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 01 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.
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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 Mgi2YNi-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
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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
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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 Mgi2DyNi-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
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Mgi2ErNi-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 Mgi2GdY-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
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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 3.5wt% KCl solution. Results are shown in Table 1.
Table 1 Table of Property Data of Magnesium Alloy Materials
Tensile Group Strength Yield Strength Elongation Corrosion Rate
(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
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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 3.5wt% KCI
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.
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