CN106967915B - A kind of readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus and preparation method thereof - Google Patents
A kind of readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus and preparation method thereof Download PDFInfo
- Publication number
- CN106967915B CN106967915B CN201710408283.7A CN201710408283A CN106967915B CN 106967915 B CN106967915 B CN 106967915B CN 201710408283 A CN201710408283 A CN 201710408283A CN 106967915 B CN106967915 B CN 106967915B
- Authority
- CN
- China
- Prior art keywords
- strength
- alloy
- magnesium alloy
- readily soluble
- modulus
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
- C22C23/06—Alloys based on magnesium with a rare earth metal as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
Abstract
A kind of readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus and preparation method thereof, it and a kind of superelevation readily soluble magnesium alloy and preparation method thereof by force.The purpose of the present invention will solve the problems, such as the readily soluble magnesium alloy of prior art preparation, and that there are intensity is low low with elasticity modulus.A kind of readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus, is prepared by Y, Ni, Zr, Ca and Mg.Preparation method: one, it stocks up；Two, melting；Three, ingot casting shaping；Four, extrusion forming to get arrive the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus.Advantage: the content by regulating and controlling Y and Ni controls the corrosion rate of alloy.Compound addition fining agent Zr and Ca, better refining alloy tissue improve alloy mechanical property.Present invention is mainly used for prepare the super readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of high-strength and high-modulus.
Description
Technical field
The present invention relates to a kind of superelevation readily soluble magnesium alloys and preparation method thereof by force.
Background technique
Material needed for hydraulic fracturing ball need to have high intensity, lightweight, controllably dissolve in oil and natural gas exploitation
Feature.Hydraulic fracturing ball is manufactured frequently with resin or aluminum matrix composite at present.Although both materials are able to satisfy in intensity
It is required that but need special corrosive liquid dissolution, and the not easy-regulating of rate of dissolution in water.The density ratio aluminium of magnesium is small, in water
Easily corrode, and corrosion product consistency is lower, the progress of subsequent corrosion will not be hindered.It can be said that magnesium alloy exists compared with aluminium alloy
Light and soluble aspect has natural advantage.But the intensity of ordinary magnesium alloy is not high, limits it on pressure break ball
Using.Therefore there are intensity, low (tensile strength is generally below 400MPa to existing readily soluble magnesium alloy, and yield strength is generally below
The problem of (elasticity modulus is generally below 45GPa) 300MPa) low with elasticity modulus.
Summary of the invention
The purpose of the present invention will solve the readily soluble magnesium alloy of prior art preparation and ask there are intensity is low low with elasticity modulus
Topic, and a kind of readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus is provided and preparation method thereof.
A kind of readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus, it is characterised in that the super readily soluble Mg-Y- of high-strength and high-modulus
Ni-Zr-Ca magnesium alloy is by mass fraction by 2%~20%Y, 0.5%~9%Ni, 0.1~1%Zr, 0.1~1%Ca and surplus
It is prepared for Mg；The tensile strength of the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of the super high-strength and high-modulus be 410MPa~
521MPa, yield strength are 350MPa~439MPa, and elasticity modulus is 45GPa~55GPa；The super high-strength and high-modulus is readily soluble
Corrosion rate of the Mg-Y-Ni-Zr-Ca magnesium alloy in the NaCl aqueous solution that mass fraction is 5% is 90mgcm-2·d-1~
300mg·cm-2·d-1。
A kind of preparation method of the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus, is specifically realized by the following steps
:
One, it stocks up: pressing 3%~20%Y of mass fraction, 0.5%~9%Ni, 0.1~1%Zr, 0.1~1%Ca and surplus
Material is matched for Mg, the material is pure Mg ingot, Mg-30%Y intermediate alloy, Mg-30%Zr intermediate alloy, Mg-30%Ca
Intermediate alloy and pure Ni material；
Two, melting: 1., by the pure Mg ingot of step steady being put into smelting furnace, is 700 DEG C~850 DEG C and SF in temperature6
Melting to pure Mg ingot is completely melt under gas shield；2., after pure Mg ingot is completely melt in 1., step 1 is added into smelting furnace
The Mg-30%Y intermediate alloy of preparation, and be 750 DEG C~850 DEG C and SF in temperature6Melting is into Mg-30%Y under gas shield
Between alloy be completely melt；3., after Mg-30%Y intermediate alloy is completely melt in 2., step steady is added into smelting furnace
Pure Ni material, and be 750 DEG C~850 DEG C and SF in temperature6Melting to pure Ni material is completely melt under gas shield；4., to 3.
In after pure Ni material is completely melt, the Mg-30%Zr intermediate alloy and Mg-30%Ca of step steady are sequentially added to smelting furnace
Intermediate alloy, and be 750 DEG C~850 DEG C and SF in temperature6Melting is to Mg-30%Zr intermediate alloy and Mg- under gas shield
30%Ca intermediate alloy is completely melt；5., melting in-furnace temperature is adjusted to 730 DEG C~750 DEG C, and temperature be 730 DEG C~
5min~15min is stood at 750 DEG C, obtains melt；
Three, ingot casting shaping: it is 680 DEG C~725 DEG C that the melt that step 2 is obtained, which cools to temperature with the furnace, then uses water
Cold mode is cooling, obtains ingot casting；
Four, extrusion forming: being processed into cylindrical body for the ingot casting in step 3, at being first 470 DEG C~490 DEG C in temperature at heat
15h~17h is managed, heat preservation 50min~70min at being then 400 DEG C in temperature, is finally 12:1 in extrusion ratio and extruding rate is
The backward extrusion of 0.1mm/s deforms to obtain bar to get the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus is arrived.
Advantages of the present invention:
1, magnesium alloy of the present invention uses Y and Ni as essential element, forms reinforced phase LPSO.Meeting alloy strength requirement
While, the characteristics of Ni can accelerate Corrosion Behaviors of Magnesium Alloys rate is played, the corrosion of alloy is then controlled by the content of regulation Y and Ni
Rate.
2, magnesium alloy of the present invention compound addition fining agent Zr and Ca combines advantage and Ca of the Zr in terms of lattice misfit rate
Advantage in terms of crystal growth inhibiting factor, better refining alloy tissue improve alloy mechanical property.
3, heavy rare earth element is not used in magnesium alloy of the present invention, reduces cost of alloy.Meanwhile without the processing such as subsequent timeliness
Technique substantially reduces the period.
4, magnesium alloy of the present invention is that casting obtains alloy cast ingot under conventional melting, (is 470 in temperature through Homogenization Treatments
DEG C~490 DEG C at be heat-treated 15h~17h), then squeezed to obtain bar.Technique and equipment used are simple, and operate and be easy,
It is portable strong.
5, the tensile strength of magnesium alloy prepared by the present invention be 410MPa~521MPa, yield strength be 350MPa~
439MPa, elasticity modulus are 45GPa~55GPa, and elongation is 4.1~11%；The tensile strength compared with existing readily soluble magnesium alloy
30% or so are averagely improved, yield strength averagely improves 45% or so, and elasticity modulus averagely improves 22% or so.
6, corrosion rate of the magnesium alloy prepared by the present invention in the NaCl aqueous solution that mass fraction is 5% is 90mg
cm-2·d-1~300mgcm-2·d-1, 2 times or more is averagely improved compared with existing readily soluble magnesium alloy.
Application field of the present invention for strong fusible alloy demands of lightweights superelevation such as pressure break balls.
Specific embodiment
Specific embodiment 1: present embodiment is a kind of readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus, it is special
Sign be the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus by mass fraction by 2%~20%Y, 0.5%~9%Ni,
0.1~1%Zr, 0.1~1%Ca and surplus are prepared for Mg；The readily soluble Mg-Y-Ni-Zr-Ca magnesium of the super high-strength and high-modulus closes
The tensile strength of gold is 410MPa~521MPa, and yield strength is 350MPa~439MPa, and elasticity modulus is 45GPa~55GPa；
Corrosion speed of the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of the super high-strength and high-modulus in the NaCl aqueous solution that mass fraction is 5%
Rate is 90mgcm-2·d-1~300mgcm-2·d-1。
For the intensity for improving magnesium alloy, be added into magnesium alloy Y and Gd, Y and Gd in magnesium with excellent solid solution and when
Strengthening effect is imitated, specific transition element (Zn, Cu, Ni etc.) is added in Mg-Gd/Y magnesium alloy will form long period stacking
Ordered structure (LPSO), can further improve the obdurability of alloy.This magnesium-rare earth containing LPSO is by plastic deformation
There is excellent room temperature and mechanical behavior under high temperature afterwards.
In the selection of rare earth element, because the density ratio Gd of Y is low, alloy lighting requirement is considered, present embodiment adds Y
For main alloy element.Mg-Y-Zn magnesium alloy containing LPSO has excellent mechanical property, but its corrosion resistance is also preferable,
Cause the corrosion rate of magnesium alloy lower.Therefore transition element Ni, which is added, in present embodiment in the magnesium alloy can substantially speed up corruption
Erosion；As-extruded Mg-Y-Ni alloy has optimal mechanical property in all Mg-Y-TM (Y, Ni, Cu etc.).Therefore, Mg-Y-Ni
Wrought magnesium alloy has superhigh intensity and ease of solubility simultaneously.Present embodiment can be widely applied to containing for pressure break ball to prepare
The superelevation of Y and Ni is strong, soluble magnesium alloy, also compound addition Zr and Ca, and further thinning microstructure improves mechanical property.And pass through
The proportion of reasonably optimizing Y and Ni realize the regulation of the corrosion rate of the super readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of high-strength and high-modulus.Cause
This present embodiment uses Y and Ni as essential element, forms reinforced phase LPSO.While meeting alloy strength requirement, hair
The characteristics of Ni can accelerate Corrosion Behaviors of Magnesium Alloys rate is waved, the corrosion rate of alloy is then controlled by the content of regulation Y and Ni.It is compound
Be added fining agent Zr and Ca, combine Zr in terms of lattice misfit rate advantage and Ca it is excellent in terms of crystal growth inhibiting factor
Gesture, better refining alloy tissue improve alloy mechanical property.Heavy rare earth element is not used, reduces cost of alloy.
Specific embodiment 2: the difference of present embodiment and specific embodiment one is: the super high-strength and high-modulus is easy
Molten Mg-Y-Ni-Zr-Ca magnesium alloy is Mg preparation by 6.9%Y, 7.1%Ni, 0.3%Zr, 0.5%Ca and surplus by mass fraction
It forms.Other are same as the specific embodiment one.
Specific embodiment 3: the difference of present embodiment and specific embodiment one is: the super high-strength and high-modulus is easy
Molten Mg-Y-Ni-Zr-Ca magnesium alloy is Mg preparation by 7.2%Y, 2.3%Ni, 0.3%Zr, 0.6%Ca and surplus by mass fraction
It forms.Other are same as the specific embodiment one.
Specific embodiment 4: the difference of present embodiment and specific embodiment one is: the super high-strength and high-modulus is easy
Molten Mg-Y-Ni-Zr-Ca magnesium alloy is Mg system by 10.8%Y, 2.1%Ni, 0.3%Zr, 0.6%Ca and surplus by mass fraction
It is standby to form.Other are same as the specific embodiment one.
Specific embodiment 5: the difference of present embodiment and specific embodiment one is: the super high-strength and high-modulus is easy
Molten Mg-Y-Ni-Zr-Ca magnesium alloy is Mg system by 15.5%Y, 1.8%Ni, 0.35%Zr, 0.6%Ca and surplus by mass fraction
It is standby to form.Other are same as the specific embodiment one.
Specific embodiment 6: present embodiment is a kind of system of readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus
Preparation Method is specifically realized by the following steps:
One, it stocks up: pressing 3%~20%Y of mass fraction, 0.5%~9%Ni, 0.1~1%Zr, 0.1~1%Ca and surplus
Material is matched for Mg, the material is pure Mg ingot, Mg-30%Y intermediate alloy, Mg-30%Zr intermediate alloy, Mg-30%Ca
Intermediate alloy and pure Ni material；
Two, melting: 1., by the pure Mg ingot of step steady being put into smelting furnace, is 700 DEG C~850 DEG C and SF in temperature6
Melting to pure Mg ingot is completely melt under gas shield；2., after pure Mg ingot is completely melt in 1., step 1 is added into smelting furnace
The Mg-30%Y intermediate alloy of preparation, and be 750 DEG C~850 DEG C and SF in temperature6Melting is into Mg-30%Y under gas shield
Between alloy be completely melt；3., after Mg-30%Y intermediate alloy is completely melt in 2., step steady is added into smelting furnace
Pure Ni material, and be 750 DEG C~850 DEG C and SF in temperature6Melting to pure Ni material is completely melt under gas shield；4., to 3.
In after pure Ni material is completely melt, the Mg-30%Zr intermediate alloy and Mg-30%Ca of step steady are sequentially added to smelting furnace
Intermediate alloy, and be 750 DEG C~850 DEG C and SF in temperature6Melting is to Mg-30%Zr intermediate alloy and Mg- under gas shield
30%Ca intermediate alloy is completely melt；5., melting in-furnace temperature is adjusted to 730 DEG C~750 DEG C, and temperature be 730 DEG C~
5min~15min is stood at 750 DEG C, obtains melt；
Three, ingot casting shaping: it is 680 DEG C~725 DEG C that the melt that step 2 is obtained, which cools to temperature with the furnace, then uses water
Cold mode is cooling, obtains ingot casting；
Four, extrusion forming: being processed into cylindrical body for the ingot casting in step 3, at being first 470 DEG C~490 DEG C in temperature at heat
15h~17h is managed, heat preservation 50min~70min at being then 400 DEG C in temperature, is finally 12:1 in extrusion ratio and extruding rate is
The backward extrusion of 0.1mm/s deforms to obtain bar to get the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus is arrived.
The mass fraction of Y element is 30% in Mg-30%Y intermediate alloy described in present embodiment step 1.
The mass fraction of Zr element is 30% in Mg-30%Zr intermediate alloy described in present embodiment step 1.
The mass fraction of Ca element is 30% in Mg-30%Ca intermediate alloy described in present embodiment step 1.
Present embodiment magnesium alloy uses Y and Ni as essential element, forms reinforced phase LPSO.It is wanted meeting alloy strength
While asking, the characteristics of Ni can accelerate Corrosion Behaviors of Magnesium Alloys rate is played, the corruption of alloy is then controlled by the content of regulation Y and Ni
Lose rate.
Present embodiment magnesium alloy compound addition fining agent Zr and Ca, combine advantage of the Zr in terms of lattice misfit rate and
Advantage of the Ca in terms of crystal growth inhibiting factor, better refining alloy tissue improve alloy mechanical property.
Heavy rare earth element is not used in present embodiment magnesium alloy, reduces cost of alloy.Meanwhile without subsequent timeliness etc.
Science and engineering skill, substantially reduces the period.
Present embodiment magnesium alloy is that casting obtains alloy cast ingot under conventional melting, (is in temperature through Homogenization Treatments
15h~17h is heat-treated at 470 DEG C~490 DEG C), then squeezed to obtain bar.Technique and equipment used are simple, and operate and hold
Easily, portable strong.
Present embodiment preparation magnesium alloy tensile strength be 410MPa~521MPa, yield strength be 350MPa~
439MPa, elasticity modulus are 45GPa~55GPa, and elongation is 4.1~11%；The tensile strength compared with existing readily soluble magnesium alloy
30% or so are averagely improved, yield strength averagely improves 45% or so, and elasticity modulus averagely improves 22% or so.
Corrosion rate of the magnesium alloy of present embodiment preparation in the NaCl aqueous solution that mass fraction is 5% is 90mg
cm-2·d-1~300mgcm-2·d-1, 2 times or more is averagely improved compared with existing readily soluble magnesium alloy.
Specific embodiment 7: the difference of present embodiment and specific embodiment six is: by quality point in step 1
Number 6.9%Y, 7.1%Ni, 0.3%Zr, 0.5%Ca and surplus are that Mg matches material.Other are identical as specific embodiment six.
Specific embodiment 8: the difference of present embodiment and specific embodiment six is: by quality point in step 1
Number 7.2%Y, 2.3%Ni, 0.3%Zr, 0.6%Ca and surplus are that Mg matches material.Other are identical as specific embodiment six.
Specific embodiment 9: the difference of present embodiment and specific embodiment six is: by quality point in step 1
Number 10.8%Y, 2.1%Ni, 0.3%Zr, 0.6%Ca and surplus are that Mg matches material.Other are identical as specific embodiment six.
Specific embodiment 10: the difference of present embodiment and specific embodiment six is: by quality point in step 1
Number 15.5%Y, 1.8%Ni, 0.35%Zr, 0.6%Ca and surplus are that Mg matches material.Other and six phase of specific embodiment
Together.
The content of present invention is not limited only to the content of the respective embodiments described above, the group of one of them or several specific embodiments
The purpose of invention also may be implemented in contract sample.
Using following verification experimental verifications effect of the present invention
Embodiment 1: a kind of preparation method of the super readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of high-strength and high-modulus, specifically by following
What step was completed:
One, it stocks up: being that Mg matches material, institute by mass fraction 6.1%Y, 0.8%Ni, 0.3%Zr, 0.5%Ca and surplus
The material stated is pure Mg ingot, Mg-30%Y intermediate alloy, Mg-30%Zr intermediate alloy, Mg-30%Ca intermediate alloy and pure Ni material
Material；
Two, melting: 1., by the pure Mg ingot of step steady being put into smelting furnace, is 750 DEG C and SF in temperature6Gas is protected
Lower melting to pure Mg ingot is protected to be completely melt；2., after pure Mg ingot is completely melt in 1., step steady is added into smelting furnace
Mg-30%Y intermediate alloy, and be 800 DEG C and SF in temperature6Melting is completely molten to Mg-30%Y intermediate alloy under gas shield
Change；3., after Mg-30%Y intermediate alloy is completely melt in 2., the pure Ni material of step steady is added into smelting furnace, and
It is 800 DEG C and SF in temperature6Melting to pure Ni material is completely melt under gas shield；4., be completely melt to pure Ni material in 3.
Afterwards, the Mg-30%Zr intermediate alloy and Mg-30%Ca intermediate alloy of step steady are sequentially added to smelting furnace, and in temperature
For 800 DEG C and SF6Melting to Mg-30%Zr intermediate alloy and Mg-30%Ca intermediate alloy is completely melt under gas shield；⑤,
Melting in-furnace temperature is adjusted to 740 DEG C, and stands 10min at being 740 DEG C in temperature, obtains melt；
Three, ingot casting shaping: it is 700 DEG C that the melt that step 2 is obtained, which cools to temperature with the furnace, then uses water-cooling pattern
It is cooling, obtain ingot casting；
Four, extrusion forming: being processed into cylindrical body for the ingot casting in step 3, is heat-treated 16h at being first 480 DEG C in temperature,
Then 60min is kept the temperature at being 400 DEG C in temperature, is finally become in the backward extrusion that extrusion ratio is 12:1 and extruding rate is 0.1mm/s
Shape obtains bar to get the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus is arrived.
The mass fraction of Y element is 30% in Mg-30%Y intermediate alloy described in present embodiment step 1.
The mass fraction of Zr element is 30% in Mg-30%Zr intermediate alloy described in present embodiment step 1.
The mass fraction of Ca element is 30% in Mg-30%Ca intermediate alloy described in present embodiment step 1.
Embodiment 2: the present embodiment and the difference of embodiment 1 are: in step 1 by mass fraction 6.5%Y, 1.5%Ni,
0.3%Zr, 0.6%Ca and surplus are that Mg matches material.Other are same as Example 1.
Embodiment 3: the present embodiment and the difference of embodiment 1 are: in step 1 by mass fraction 6.9%Y, 7.1%Ni,
0.3%Zr, 0.5%Ca and surplus are that Mg matches material.Other are same as Example 1.
Embodiment 4: the present embodiment and the difference of embodiment 1 are: in step 1 by mass fraction 7.2%Y, 2.3%Ni,
0.3%Zr, 0.6%Ca and surplus are that Mg matches material.Other are same as Example 1.
Embodiment 5: the present embodiment and the difference of embodiment 1 are: by mass fraction 10.8%Y, 2.1% in step 1
Ni, 0.3%Zr, 0.6%Ca and surplus are that Mg matches material.Other are same as Example 1.
Embodiment 6: the present embodiment and the difference of embodiment 1 are: by mass fraction 15.5%Y, 1.8% in step 1
Ni, 0.35%Zr, 0.6%Ca and surplus are that Mg matches material.Other are same as Example 1.
The readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy mechanical property of super high-strength and high-modulus prepared by embodiment 1 to 6 is detected, in quality
The readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus that in the NaCl aqueous solution that score is 5% prepared by detection embodiment 1 to 6
Corrosion rate, testing result is as shown in table 1.Reached by the tensile strength of magnesium alloy prepared by the present invention known to table 1
410MPa or more, yield strength reach 350MPa or more, and elasticity modulus reaches 45GPa or more, and elongation is 4.1~11%,
The corrosion rate in NaCl aqueous solution that mass fraction is 5% is 98mgcm-2·d-1More than.So prepared by the present invention super
Not only corrosion rate is good for the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of high-strength and high-modulus, but also tensile strength reaches, yield strength and springform
Amount has all obtained significant raising.
Table 1
Claims (5)
1. a kind of preparation method of the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus, it is characterised in that a kind of superelevation is high by force
The preparation method of the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of mould is completed by the following steps:
One, it stocks up: being Mg by 3%~20%Y of mass fraction, 0.5%~9%Ni, 0.1~1%Zr, 0.1~1%Ca and surplus
Material is matched, the material is pure Mg ingot, among Mg-30%Y intermediate alloy, Mg-30%Zr intermediate alloy, Mg-30%Ca
Alloy and pure Ni material；
Two, melting: 1., by the pure Mg ingot of step steady being put into smelting furnace, is 700 DEG C~850 DEG C and SF in temperature6Gas
Lower melting to pure Mg ingot is protected to be completely melt；2., after pure Mg ingot is completely melt in 1., step steady is added into smelting furnace
Mg-30%Y intermediate alloy, and temperature be 750 DEG C~850 DEG C and SF6It is closed among melting to Mg-30%Y under gas shield
Gold is completely melt；3., after Mg-30%Y intermediate alloy is completely melt in 2., the pure Ni of step steady is added into smelting furnace
Material, and be 750 DEG C~850 DEG C and SF in temperature6Melting to pure Ni material is completely melt under gas shield；4., to pure in 3.
After Ni material is completely melt, sequentially added among the Mg-30%Zr intermediate alloy and Mg-30%Ca of step steady to smelting furnace
Alloy, and be 750 DEG C~850 DEG C and SF in temperature6Melting is to Mg-30%Zr intermediate alloy and Mg-30%Ca under gas shield
Intermediate alloy is completely melt；5., melting in-furnace temperature is adjusted to 730 DEG C~750 DEG C, and in the case where temperature is 730 DEG C~750 DEG C
5min~15min is stood, melt is obtained；
Three, ingot casting shaping: it is 680 DEG C~725 DEG C that the melt that step 2 is obtained, which cools to temperature with the furnace, then uses water cooling side
Formula is cooling, obtains ingot casting；
Four, extrusion forming: being processed into cylindrical body for the ingot casting in step 3, is heat-treated at being first 470 DEG C~490 DEG C in temperature
15h~17h, heat preservation 50min~70min at being then 400 DEG C in temperature, is finally 12:1 in extrusion ratio and extruding rate is
The backward extrusion of 0.1mm/s deforms to obtain bar to get the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus is arrived；Described is super
The tensile strength of the readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of high-strength and high-modulus be 410MPa~521MPa, yield strength be 350MPa~
439MPa, elasticity modulus are 45GPa~55GPa；The readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of the super high-strength and high-modulus is in quality point
Number is 90mgcm for the corrosion rate in 5% NaCl aqueous solution-2·d-1~300mgcm-2·d-1。
2. a kind of preparation method of super readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of high-strength and high-modulus according to claim 1, special
Sign is in step 1 by mass fraction 6.9%Y, 7.1%Ni, 0.3%Zr, 0.5%Ca and surplus to be that Mg matches material.
3. a kind of preparation method of super readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of high-strength and high-modulus according to claim 1, special
Sign is in step 1 by mass fraction 7.2%Y, 2.3%Ni, 0.3%Zr, 0.6%Ca and surplus to be that Mg matches material.
4. a kind of preparation method of super readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of high-strength and high-modulus according to claim 1, special
Sign is in step 1 by mass fraction 10.8%Y, 2.1%Ni, 0.3%Zr, 0.6%Ca and surplus to be that Mg matches material.
5. a kind of preparation method of super readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of high-strength and high-modulus according to claim 1, special
Sign is in step 1 by mass fraction 15.5%Y, 1.8%Ni, 0.35%Zr, 0.6%Ca and surplus to be that Mg matches material.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710408283.7A CN106967915B (en) | 2017-06-02 | 2017-06-02 | A kind of readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710408283.7A CN106967915B (en) | 2017-06-02 | 2017-06-02 | A kind of readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN106967915A CN106967915A (en) | 2017-07-21 |
| CN106967915B true CN106967915B (en) | 2019-03-12 |
Family
ID=59326189
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201710408283.7A Active CN106967915B (en) | 2017-06-02 | 2017-06-02 | A kind of readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN106967915B (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113564440A (en) * | 2021-08-02 | 2021-10-29 | 西安四方超轻材料有限公司 | High-performance easily-forged magnesium alloy material and preparation method thereof |
| CN114892056A (en) * | 2022-06-15 | 2022-08-12 | 兰州理工大学 | LPSO strengthening phase-containing soluble magnesium alloy for fracturing temporary plugging tool and preparation method thereof |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4846090B2 (en) * | 2000-12-14 | 2011-12-28 | 日本重化学工業株式会社 | Mg-based high storage amount hydrogen storage alloy |
| AUPS311202A0 (en) * | 2002-06-21 | 2002-07-18 | Cast Centre Pty Ltd | Creep resistant magnesium alloy |
| CN1515697A (en) * | 2003-01-07 | 2004-07-28 | 死海镁有限公司 | Creep eresistant magnesium alloy with improved casting property |
| CN100387743C (en) * | 2005-04-21 | 2008-05-14 | 上海交通大学 | High-strength heat-resisting magnesium alloy and its preparing method |
| CN101191168B (en) * | 2006-11-23 | 2011-03-30 | 北京有色金属研究总院 | Magnesium alloy and preparation method thereof |
| CN101463441A (en) * | 2009-01-15 | 2009-06-24 | 上海交通大学 | Rare earth-containing high strength heat resisting magnesium alloy and preparation thereof |
-
2017
- 2017-06-02 CN CN201710408283.7A patent/CN106967915B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN106967915A (en) | 2017-07-21 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN106148792B (en) | The wrought magnesium alloy and preparation method thereof of high-intensitive high Gd content | |
| CN105838945B (en) | A kind of superpower high-ductility corrosion aluminium alloy of anti-recrystallizing and preparation method thereof | |
| CN101193839B (en) | High strength aluminum alloys and process for making the same | |
| CN103667825B (en) | A kind of ultra-high-strength/tenacity anticorodal and manufacture method thereof | |
| CN110004341A (en) | The high-intensitive magnesium alloy and preparation method thereof containing rare earth | |
| CN100455687C (en) | Process of making zinc-base alloy wire and rod with high strength and high toughness | |
| CN106756330B (en) | The aluminium alloy extrusions and manufacture method of a kind of body of a motor car | |
| CN106929720B (en) | A kind of high strength easy recrystallization wrought aluminium alloy and preparation method thereof | |
| CN103014459A (en) | High-Zn, high-Mg and low-Cu ultrahigh-strength corrosion-resisting aluminum alloy and heat treatment method | |
| CN110129644A (en) | Heat-resisting dissolvable magnesium alloy of one kind and its preparation method and application | |
| CN107488823B (en) | Method that is a kind of while improving intensity of aluminum alloy and elongation percentage | |
| CN107058924B (en) | Regulate and control the high-strength high-plastic heat resistance magnesium alloy and preparation method thereof of LPSO structures and nanoprecipitation phase | |
| CN105039817B (en) | The preparation method and multicomponent heat-resistant magnesium alloy of a kind of multicomponent heat-resistant magnesium alloy | |
| CN101353744A (en) | Stress corrosion resistant Al-Zn-Mg-(Cu) alloy and preparation thereof | |
| Chen et al. | Microstructure evolution and tensile mechanical properties of thixoformed high performance Al-Zn-Mg-Cu alloy | |
| CN106967915B (en) | A kind of readily soluble Mg-Y-Ni-Zr-Ca magnesium alloy of super high-strength and high-modulus and preparation method thereof | |
| CN107245619A (en) | A kind of strong high temperature resistant magnesium alloy of superelevation | |
| CN109666830A (en) | A kind of deformation aluminium lithium ormolu and preparation method thereof | |
| CN110331319A (en) | It is a kind of containing scandium and the high-strength of erbium, high-ductility Alcoa and preparation method thereof | |
| CN109694976A (en) | A kind of low cost soluble magnesium alloy and its preparation method and application | |
| WO2005003398A2 (en) | High strength aluminum alloys and process for making the same | |
| CN106521241A (en) | Deformable zinc alloy capable of achieving cold heading and application of deformable zinc alloy | |
| CN106319409A (en) | Method for producing 6000 series aluminum alloy | |
| CN114277291B (en) | Al-Zn-Mg-Cu aluminum alloy extrusion material for aerospace and preparation method thereof | |
| CN107723548A (en) | A kind of high intensity Mg Y Ni Zr alloys and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |