CN108913948A - A kind of high-strength titanium alloy and preparation method thereof - Google Patents
A kind of high-strength titanium alloy and preparation method thereof Download PDFInfo
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- CN108913948A CN108913948A CN201810876568.8A CN201810876568A CN108913948A CN 108913948 A CN108913948 A CN 108913948A CN 201810876568 A CN201810876568 A CN 201810876568A CN 108913948 A CN108913948 A CN 108913948A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
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- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C16/00—Alloys based on zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
- C22C30/04—Alloys containing less than 50% by weight of each constituent containing tin or lead
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- 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
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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- 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
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/186—High-melting or refractory metals or alloys based thereon of zirconium or alloys based thereon
Abstract
The present invention provides a kind of high-strength titanium alloy and preparation method thereof, the high-strength titanium alloy, based on mass content, the Ti including Al 4.5~5.5%, Mo 3.5~4.5%, Cr 3.5~4.5%, Sn 1.5~2.5%, Zr 10~50% and surplus.The content of strict control each element of the present invention, promote the mechanical property of titanium alloy, wherein, the addition of Cr element, stablize β phase, the room temperature intensity of titanium alloy substrate can be significantly improved, element al greatly improves the stability and β-α transition temperature of α phase, it is tiny α phase convenient for what is obtained after quenching during solution treatment, the specific strength of titanium alloy can be greatly improved；And since the addition of Zr element can cause distortion of lattice, these defects be will lead in nucleation process, and nucleation point increases, and the density of forming core increases, and play the role of crystal grain refinement to carrying out realization refined crystalline strengthening.
Description
Technical field
The present invention relates to titanium alloy technical field, in particular to a kind of high-strength titanium alloy and preparation method thereof.
Background technique
Titanium alloy has a wide range of applications advantage with a series of advantages such as its high specific strength, high ratio modulus, corrosion-resistant,
The numerous areas such as ocean engineering, aerospace, biomedicine, metallurgy, chemical industry, light industry are paid attention to.
Structural titanium alloy is with its excellent machinability and mechanical property, and intensity height, shape are multiple in aerospace industry
Miscellaneous part manufacturing, such as Wing Joint structural member, fuselage and the undercarriage of space shuttle connect frame, hanging engine connector portion
Position, and the production of the important or crucial load component high to intensity and life requirement.But traditional titanium as aeronautic structure
For alloy, strength level is still difficult to meet increasingly harsh industrial military service standard, and titanium alloy aeronautic structure is caused to use week
Phase is short, and limitation is further applied.
Summary of the invention
In view of this, the purpose of the present invention is to provide a kind of high-strength titanium alloys and preparation method thereof.It is provided by the invention
Titanium alloy strength character is excellent, meets the requirement of aeronautic structure titanium alloy.
The present invention provides a kind of high-strength titanium alloys, based on mass content, including Al 4.5~5.5%, Mo 3.5~
4.5%, the Ti of Cr 3.5~4.5%, Sn 1.5~2.5%, Zr 10~50% and surplus.
Preferably, the high-strength titanium alloy includes Al 4.5~4.8%, Mo 3.6~3.8%, Cr 3.6~3.8%, Sn
1.5~1.8%, the Ti of Zr 10~50% and surplus.
Preferably, the tissue of the high-strength titanium alloy includes acicular α phase martensite and lamellar α ' martensite.
The present invention also provides the preparation methods of the high-strength titanium alloy described in above-mentioned technical proposal, include the following steps：
(1) cast alloy base will be obtained after alloy raw material melting；
(2) it is deformed after the cast alloy base that the step (1) obtains being carried out isothermal holding, obtains densification alloy preform；
(3) the densification alloy preform for obtaining the step (2) carries out solution treatment, obtains high-strength titanium alloy.
Preferably, melting is vacuum arc melting in the step (1), the temperature of the vacuum arc melting is 2000~
2900℃。
Preferably, melting number is at 5 times or more in the step (1), and each smelting time is in 1min or more.
Preferably, the temperature of isothermal holding is 860~900 DEG C in the step (2), time of isothermal holding is 0.5~
1.0h。
Preferably, rolling deformation is deformed into the step (2)；The total deformation of the rolling deformation is 65~70%,
The temperature of rolling deformation is 860~900 DEG C.
Preferably, the rolling deformation is multi- pass rolling, and drafts per pass is 2~3mm；
When using multi- pass rolling, per pass roll after, by alloy preform after rolling rolling deformation at a temperature of heat preservation 5~
10min。
Preferably, the holding temperature of solution treatment is 860~900 DEG C in the step (3), the soaking time of solution treatment
For 3~7min, the type of cooling of solution treatment is water quenching.
The present invention provides a kind of high-strength titanium alloys, based on mass content, including Al 4.5~5.5%, Mo 3.5~
4.5%, the Ti of Cr3.5~4.5%, Sn 1.5~2.5%, Zr 10~50% and surplus.Strict control each element of the present invention
Content promotes the mechanical property of titanium alloy, wherein the addition of Cr element stablizes β phase, can significantly improve the room of titanium alloy substrate
Warm intensity, while Al is used to form the δ phase constitution of titanium-aluminium alloy；Element al greatly improves the stability and β-α transformation of α phase
Temperature is tiny α phase convenient for what is obtained after quenching during solution treatment, and the ratio that can greatly improve titanium alloy is strong
Degree；And since the addition of Zr element can cause distortion of lattice, these defects be will lead in nucleation process, and nucleation point increases,
The density of forming core increases, and plays the role of crystal grain refinement to carrying out realization refined crystalline strengthening.The present invention, the solution strengthening effect of Al element
Fruit is significant, and thinks that phase composition is adjusted to alloy together with Mo and Cr element, optimizes the phase constitution of alloy；Sn element adds
α → β phase transition temperature can suitably be reduced by adding, and be moulded while titanium alloy intensity can be substantially improved by solution strengthening effect to alloy
Property influence it is little；The addition of a large amount of Zr elements also suitably reduces α → β phase of alloy other than playing the role of solution strengthening
Transition temperature, so that alloy remains more β phases, β phase is body-centered cubic structure relative to its cunning of the α phase of close-packed hexagonal structure
Shifting be it is more, show as that plasticity is preferable, and the Original β grain of alloy is refined, original β grain boundary density increases, so that dislocation
Movement receives obstruction, and intensity further gets a promotion.The experimental results showed that the tensile strength for the titanium alloy that the present invention obtains improves
21.3%.
Detailed description of the invention
Fig. 1 is the metallographic optical microscopy map of titanium alloy made from embodiment 1；
Fig. 2 is the metallographic optical microscopy map of titanium alloy made from embodiment 2；
Fig. 3 is the metallographic optical microscopy map of titanium alloy made from embodiment 3；
Fig. 4 is the metallographic optical microscopy map of titanium alloy made from embodiment 4；
Fig. 5 is the metallographic optical microscopy map of titanium alloy made from embodiment 5；
Fig. 6 is tensile property of the present invention test tensile sample dimensional drawing.
Specific embodiment
The present invention provides the present invention provides a kind of high-strength titanium alloys, based on mass content, including Al 4.5~
5.5%, the Ti of Mo 3.5~4.5%, Cr 3.5~4.5%, Sn 1.5~2.5%, Zr 10~50% and surplus.
High-strength titanium alloy provided by the invention, based on mass content, including Al 4.5~5.5%, preferably 4.5~
4.8% or 5.2~5.3%.In the present invention, the Al is used to form the δ phase constitution of titanium-aluminium alloy；Element al greatly improves
The stability and β-α transition temperature of α phase, convenient for what is obtained after quenching during solution treatment are tiny α phase, can
To greatly improve the specific strength of titanium alloy, achieve the effect that refined crystalline strengthening；Alloy can also be made to realize to a certain extent simultaneously
Lightweight；And the addition of aluminium is greatly improved the corrosion resistance of zirconium.
High-strength titanium alloy provided by the invention, based on mass content, including Mo 3.5~4.5%, preferably 3.6~
3.8% or 4.3~4.4%, further preferably 3.65~3.75%.In the present invention, the Mo solution strengthening β phase reduces
Transformation temperature enhances harden ability, to enhance heat treatment reinforcement effect；The addition of Mo element can also improve the corrosion resistance of alloy.
And due to the low diffusivity of Mo, temperature sensitivity of the alloy in two-phase section rolling can also be reduced, alloy process window is expanded
Mouthful；Low Mo equivalent improves the nuclear driving force of α phase, changes alloy aging dynamics, so that α phase is more evenly distributed, from
And it can get excellent mechanical property.
High-strength titanium alloy provided by the invention, based on mass content, including Cr 3.5~4.5%, preferably 3.6~
3.8% or 4.3~4.4%, further preferably 3.65% or 4.45%.In the present invention, it is steady to belong to eutectoid type β phase by the Cr
Determine element, can not only widen coexistence region, the corrosion resistance of alloy can also be enhanced as self-passivating metal.Cr element adds
Add, stablizes β phase, the room temperature intensity of titanium alloy substrate can be significantly improved；Cr can reduce alpha-beta transition temperature, regulate and control TC titanium alloy
In tissue composition, solubility solubility of the Cr in α-Ti and α-Zr is all very low；The intensity of titanium alloy can be improved in Cr, but strong
Change effect is weaker than Sn, and chromium also has improvement result for the intensity creep resistance of titanium alloy；Cr, which is added, not only has strong β to stablize
Effect, and stablize beta stable element with higher ductility and toughness compared to other isomorphisms by Cr stable β.
High-strength titanium alloy provided by the invention, based on mass content, including Sn 1.5~2.5%, preferably 1.6~
1.9% or 2.2~2.5%, further preferably 1.8%.In the present invention, solubility of the Sn in α/β-Ti is higher,
And Sn reduces alloy to the sensibility of hydrogen embrittlement, and plays supplement invigoration effect to alloy together with Zr.
High-strength titanium alloy provided by the invention, based on mass content, including Zr 10~50%, preferably 2.5~50%,
Further preferably 2.5~30%, more preferably 5~28%, it is further preferably 8~15%.In the present invention, due to Zr element
Addition can cause distortion of lattice, these defects will lead in nucleation process, and nucleation point increases, and the density of forming core increases, and play
Crystal grain refinement carries out realization refined crystalline strengthening to effect；It is added to element Zr in matrix titanium, phase transition temperature is influenced in less
Property element Zr and Ti formed unlimited solid solution, so that solution strengthening is realized, and the blunt current potential of cause of Zr is more negative compared with Ti, even if in weak oxygen
Changing can still be passivated in conditions environmental, improve the ability of Surface Creation dense oxidation film, improve its corrosion resistance
Energy.
High-strength titanium alloy provided by the invention, based on mass content, in addition to above-mentioned each element, the Ti including surplus.
It simultaneously include α phase stable element, β phase stable element and neutral element, a variety of alloys in alloying element of the invention
While element has adjusted alloy phase composition simultaneously, the mechanical property of alloy is improved by the effect of refined crystalline strengthening and solution strengthening
Energy；Wherein Al element is a kind of α stable element, and solid solution strengthening effect is significant, and the addition of a small amount of Al element can be substantially improved
Alloy strength, and alloy density is reduced to a certain extent, but is affected to plasticity；Mo and Cr element are beta stable elements, can
Collaboration expands β phase region range, makes heat treatment process be easier to carry out by adjusting phase transition temperature, and enhance when alloy is heat-treated
Harden ability；Sn element is heavy element, but the addition of Sn can properly increase α → β phase transition temperature, pass through solution strengthening effect
Alloy plasticity is influenced while titanium alloy intensity can be substantially improved little；Al, Mo, Cr, Sn and Zr element pairing metallographic together
Composition is adjusted, and optimizes the phase constitution of alloy；The addition of a large amount of Zr elements is in addition to playing solution strengthening and refined crystalline strengthening
Effect is outer, also suitably reduces α → β phase transition temperature of alloy, so that alloy remains more β phases, β phase is body-centered cubic
Structure is more relative to its slip system of the α phase of close-packed hexagonal structure, shows as that plasticity is preferable, and the Original β grain of alloy obtains
Refinement, original β grain boundary density increase, so that dislocation motion is hindered, intensity further gets a promotion.
In the present invention, the tissue of the high-strength titanium alloy preferably includes acicular α phase martensite and lamellar α ' martensite.
The present invention also provides the preparation methods of the high-strength titanium alloy described in above-mentioned technical proposal, include the following steps：
(1) cast alloy base will be obtained after alloy raw material melting；
(2) it is deformed after the cast alloy base that the step (1) obtains being carried out isothermal holding, obtains densification alloy preform；
(3) the densification alloy preform for obtaining the step (2) carries out solution treatment, obtains high-strength titanium alloy.
The present invention will obtain cast alloy base after alloy raw material melting.The present invention is to the type of the alloy raw material without spy
Different restriction uses alloy raw material well known to those skilled in the art to be subject to the titanium alloy that can obtain target components.In this hair
In bright, the alloy raw material preferably includes titanium sponge, sponge zirconium, fine aluminium, pure chromium, High-Purity Molybdenum and high purity tin.The present invention is to various
The ratio of alloy raw material does not have special restriction, and final alloying component can be made to meet the requirements.
In the present invention, the melting is preferably vacuum arc melting, and the temperature of the vacuum arc melting is preferably
2000~2900 DEG C, more preferably 2200~2400 DEG C, most preferably 2250~2300 DEG C.In the present invention, the vacuum electric
The vacuum degree of arc melting is preferably 0.04~0.05MPa, is carried out under the conditions of argon gas.When using vacuum arc melting, this hair
It is bright that vacuum degree in furnace chamber is first preferably evacuated to 9 × 10-3Pa hereinafter, be passed through argon gas again；The intake of the argon gas is to meet
The amount of electric arc melting ionized gas.In the present invention, the electric current of the vacuum arc melting is preferably 400~450A,
Further preferably 420~435A.The present invention does not have particular/special requirement to the specific embodiment of the vacuum arc melting, uses
It is well-known to those skilled in the art.The present invention using first vacuumize be passed through argon gas again by the way of can be avoided first Ti with
Zr is in the event of high temperatures, a large amount of to inhale hydrogen oxygen uptake suction nitrogen, aoxidizes, moreover it is possible to provide ionized gas for electric arc melting.In this hair
In bright, the number of the melting further preferably 6~10 times, obtains cast alloy base preferably at 5 times or more after melting；Often
The time of secondary melting is preferably in 3min or more, further preferably 3~5min, more preferably 4min.In the present invention, when repeatedly
When carrying out melting, progress of the melting preferably in vacuum arc melting furnace；Specifically：By raw metal in arc-melting furnace
Middle carry out melting, obtains melting liquid；Then cooling obtains slab, then carries out melting after overturning slab, obtains melting liquid again, then
Secondary cooling melting liquid, obtains slab, with this 5 times or more repeatedly, it is ensured that obtained as cast condition base ingredient is uniform.
The present invention in melting, grow up to the preferential forming core of β phase during Solid State Transformation by melting liquid, obtains β phase green body, is
Subsequent solution treatment provides basis to obtain α ' martensitic phase；And the fusion process enables to as cast condition base ingredient uniform,
Effectively eliminate stomata and defect.
Before the melting, the alloy raw material is preferably cleaned by ultrasonic by the present invention；The present invention is to the ultrasonic cleaning
Specific embodiment there is no particular/special requirement, using well-known to those skilled in the art.
After obtaining cast alloy base, the present invention deforms after the cast alloy base is carried out isothermal holding, is densified
Alloy preform.The present invention carries out deformation process after cast alloy base is first carried out isothermal holding again, so that titanium alloy in deformation process
Ingot is able to maintain higher temperature, realizes thermal deformation.The present invention can preferably eliminate casting flaw using thermal deformation, dense organization,
Refining alloy Original β grain promotes alloy to generate a large amount of α ' martensitic phases during solid solution, improves tensile strength, and can
To generate a large amount of dislocations, the mechanical property of alloy in the rolling direction can be improved.
In the present invention, the temperature of the isothermal holding is preferably 860~900 DEG C, and further preferably 865~895 DEG C,
More preferably 870~880 DEG C.In the present invention, the soaking time of the isothermal holding is preferably 0.5~1.0h, further excellent
It is selected as 0.6~0.9h.
After the isothermal holding, the present invention deforms titanium alloy ingot after the heat preservation, the densification alloy preform obtained.?
In the present invention, the deformation is preferably rolling deformation, and the total deformation of the rolling deformation is preferably 65~70%, further excellent
It is selected as 67~68%；The temperature of the rolling deformation is preferably 860~900 DEG C, and further preferably 865~895 DEG C, more preferably
It is 870~880 DEG C, is consistent with the temperature during isothermal holding.In the present invention, the deformation process makes metastable β
Phase crystal grain refinement, and a large amount of dislocations are generated, it is (strong herein since phase constituent is mainly β phase to help to improve alloy obdurability
Degree moulding can have promotion).
In the present invention, the rolling deformation is more preferably multi- pass rolling, and deflection per pass is preferably 2~
3mm；The present invention does not have particular/special requirement to the rolling number of the multi- pass rolling, can complete target distortion amount.This hair
When bright progress multi- pass rolling, every time rolling after, the present invention preferably by alloy preform after the rolling rolling deformation at a temperature of
Keep the temperature 5~10min, further preferably 6~7min.The present invention does not have special want to the specific embodiment of the rolling deformation
It asks, using well-known to those skilled in the art.
After obtaining densification alloy preform, the densification alloy preform is carried out solution treatment by the present invention, is obtained high-strength titanium and is closed
Gold.In the present invention, the holding temperature of the solution treatment is preferably 860~900 DEG C, and further preferably 865~895 DEG C,
More preferably 870~880 DEG C；The soaking time of the solution treatment is preferably 3~7min, further preferably 4~5min.?
In the present invention, the type of cooling of the solution treatment is preferably water quenching, and water quenching is carried out further preferably in room temperature water.The present invention
There is no particular/special requirement to the specific embodiment of the solution treatment, is using embodiment well-known to those skilled in the art
It can.In the present invention, the insulating process of the solution treatment preferably carries out under protective atmosphere, and the protective atmosphere is specially argon
Gas shielded atmosphere.In the present invention, the residual stress caused by the solution treatment can be eliminated as much as because of thermal deformation improves
Plasticity can also effectively control the form of α phase and β phase in alloy, size, ratio and phase interface, change point of micro-area composition
Cloth preferably regulates and controls the performance of alloy.
In the present invention, the type of cooling of the solution treatment is preferably water quenching.The present invention is specific to the solution treatment
Embodiment does not have particular/special requirement, using embodiment well-known to those skilled in the art.In the present invention, described solid
The insulating process of molten processing preferably carries out under protective atmosphere, and the protective atmosphere is specially argon atmosphere.The present invention adopts
With the solution treatment, solid solubility temperature is low and solid solution period, Zr can be made to be solid-solubilized in alloy substrate in the solution treatment,
And the metastable β phase of physical strength cubic structure can be retained, so as to improve the mechanical property of alloy, the tension for improving titanium alloy is strong
Degree.
After solution treatment, solid solution state base is preferably removed surface scale by the present invention, obtains high-strength corrosion-resistant erosion steel alloy.This
Invention preferably removes surface scale by the way of polishing.
In order to further illustrate the present invention, below with reference to embodiment to high-strength titanium alloy provided by the invention and its preparation side
Method is described in detail, but they cannot be interpreted as limiting the scope of the present invention.
Embodiment 1
Alloying component alloying component by mass percentage：Ti surplus, Zr：10%, Al：4.5%, Sn：1.5%, Mo：
3.5%, Cr：3.5% (Ti-10Zr-4.5Al-3.5Mo-3.5Cr-1.5Sn) ingredient, weighs (total mass of raw material 100g) work
Industry grade sponge zirconium 10g, rafifinal 4.5g, high purity tin 1.5g, High-Purity Molybdenum 3.5g, High Pure Chromium 3.5g are dipped in dehydrated alcohol and are surpassed
Sound wave cleans, and air-dries after ultrasonic cleaning, is placed in the water jacketed copper crucible of non-consumable vacuum arc melting furnace, the vacuum in furnace chamber
Degree will be extracted into 8 × 10-3Pa is hereinafter, be filled with high-purity argon gas as protection gas before electric arc melting (vacuum degree is in 0.04~0.05MPa)
Afterwards, arc temperature is about 2500 DEG C or so when each melting, and each smelting time is about 3 minutes or so, and each melting finishes
It is cooling afterwards to obtain ingot casting, then overturning processing is carried out to ingot casting and carries out melting, with this melting-casting ingot casting melt back and overturning casting
Ingot 8 times to guarantee that the ingot casting ingredient finally obtained is uniform.
Then rolling temperature is heated to the alloy cast ingot of taking-up and keeps the temperature 30 minutes, rolling temperature is 900 DEG C, rolls and is
Multi- pass rolling deformation, drafts per pass is about 2mm, after rolling per pass, is put into Muffle furnace and is reheated to 900 DEG C simultaneously
Heat preservation 5 minutes, final deformation amount is made up to 66% sheet alloy in alloy cast ingot, and obtained sheet alloy is with a thickness of 5mm.At end
After passes, solution treatment is carried out：900 DEG C are reheated to, 3 minutes is kept the temperature, is then quenched in room temperature water rapidly
Processing, etc. alloy sheets it is completely cooling after take out, careful polishes off the oxide layer of alloy ingot surface, and is cleaned air-dried, obtains
To high-strength titanium alloy.
Embodiment 2
Alloying component alloying component by mass percentage：Ti surplus, Zr：20%, Al：4.8%, Sn：1.8%, Mo：
3.7%, Cr：3.7% (Ti-20Zr-4.8Al-3.7Mo-3.7Cr-1.8Sn) ingredient, weighs (total mass of raw material 100g) work
Industry grade sponge zirconium 20g, rafifinal 4.8g, high purity tin 1.8g, High-Purity Molybdenum 3.7g, High Pure Chromium 3.7g are dipped in dehydrated alcohol, ultrasound
It air-drying, is placed in the water jacketed copper crucible of non-consumable vacuum arc melting furnace after wave cleaning, the vacuum degree in furnace chamber will be extracted into 8 ×
10-3Pa is hereinafter, be filled with high-purity argon gas as protection gas (vacuum degree is in 0.04~0.05MPa) before electric arc melting after, each melting
When arc temperature be about 2900 DEG C or so, smelting time is about 3 minutes or so, after each melting cooling obtain ingot casting,
Overturning processing is carried out to ingot casting again and carries out melting, it is final to guarantee with this melting-casting ingot casting melt back and overturning ingot casting 6 times
The ingot casting ingredient of acquisition is uniform.
Then rolling temperature is heated to the alloy cast ingot of taking-up and keeps the temperature 0.6h, rolling temperature is 890 DEG C, and it is more for rolling
Passes deformation, finally obtained plate thickness are 5mm, and drafts per pass is about 2mm, after rolling per pass, are put into
Muffle furnace is reheated to 890 DEG C and keeps the temperature 6 minutes, and final deformation amount is made up to 65% sheet alloy in alloy cast ingot.At end
After passes, solution treatment is carried out：890 DEG C are reheated to, 4 minutes is kept the temperature, is then quenched in room temperature water rapidly
Processing, etc. alloy sheets it is completely cooling after take out, careful polishes off the oxide layer of alloy ingot surface, and is cleaned air-dried, obtains
To high-strength titanium alloy.
Embodiment 3
Alloying component alloying component by mass percentage：Ti surplus, Zr：30%, Al：5.0%, Sn：2.0%, Mo：
4.0%, Cr：4.0% (Ti-30Zr-5.0Al-4.0Mo-4.0Cr-2.0Sn) ingredient, weighs (total mass of raw material 100g) work
Industry grade sponge zirconium 30g, rafifinal 5.0g, high purity tin 2.0g, High-Purity Molybdenum 4.0g, High Pure Chromium 4.0g are dipped in dehydrated alcohol, ultrasound
It air-drying, is placed in the water jacketed copper crucible of non-consumable vacuum arc melting furnace after wave cleaning, the vacuum degree in furnace chamber will be extracted into 8 ×
10-3Pa is hereinafter, be filled with high-purity argon gas as protection gas (vacuum degree is in 0.04~0.05MPa) before electric arc melting after, each melting
When arc temperature be about 2500 DEG C or so, each smelting time is about 3 minutes or so, after each melting cooling cast
Ingot, then overturning processing is carried out to ingot casting and carries out melting, with this melting-casting ingot casting melt back and overturning ingot casting 9 times to guarantee
The ingot casting ingredient finally obtained is uniform.
Then rolling temperature is heated to the alloy cast ingot of taking-up and keeps the temperature 0.7h, rolling temperature is 880 DEG C, and it is more for rolling
Passes deformation, drafts per pass is about 2mm, after rolling per pass, is put into Muffle furnace and is reheated to 880 DEG C and protects
Temperature 5 minutes, final deformation amount is made up to 67% sheet alloy in alloy cast ingot, obtains the plate with a thickness of 5mm.It is rolled in whole passage
After system, solution treatment is carried out：880 DEG C are reheated to, 5 minutes is kept the temperature, is then quenched in room temperature water rapidly, etc.
Alloy sheets are taken out after cooling down completely, and careful polishes off the oxide layer of alloy ingot surface, and are cleaned and air-dried, and high-strength titanium is obtained
Alloy.
Embodiment 4
Alloying component alloying component by mass percentage：Ti surplus, Zr：40%, Al：5.2%, Sn：2.3%, Mo：
4.2%, Cr：4.3% (Ti-40Zr-5.2Al-4.2Mo-4.3Cr-2.3Sn) ingredient, weighs (total mass of raw material 100g) work
Industry grade sponge zirconium 40g, rafifinal 5.2g, high purity tin 2.3g, High-Purity Molybdenum 4.2g, High Pure Chromium 4.3g are dipped in dehydrated alcohol, ultrasound
It air-drying, is placed in the water jacketed copper crucible of non-consumable vacuum arc melting furnace after wave cleaning, the vacuum degree in furnace chamber will be extracted into 8 ×
10-3Pa is hereinafter, be filled with high-purity argon gas as protection gas (vacuum pressure reaches 0.04~0.05MPa) before electric arc melting after, every time
Arc temperature is about 2900 DEG C or so when melting, and each smelting time is about 1 minute or so, cooling after each melting
To ingot casting, then overturning processing is carried out to ingot casting and carries out melting, with this melting-casting ingot casting melt back and overturning ingot casting 5 times with
Guarantee that the ingot casting ingredient finally obtained is uniform.
Then rolling temperature is heated to the alloy cast ingot of taking-up and keeps the temperature 0.9h, rolling temperature is 870 DEG C, and it is more for rolling
Passes deformation, drafts per pass is about 2mm, after rolling per pass, is put into Muffle furnace and is reheated to 870 DEG C and protects
Final deformation amount is made up to 69% sheet alloy in temperature 9 minutes, alloy cast ingot, plate with a thickness of 5mm.In whole passes
Afterwards, solution treatment is carried out：870 DEG C are reheated to, 6 minutes is kept the temperature, is then quenched in room temperature water rapidly, waits conjunction
Golden plate is taken out after cooling down completely, and careful polishes off the oxide layer of alloy ingot surface, and is cleaned and air-dried, and obtains high-strength titanium and closes
Gold.
Embodiment 5
Alloying component alloying component by mass percentage：Ti surplus, Zr：50%, Al：5.5%, Sn：2.5%, Mo：
4.5%, Cr：4.5% (Ti-50Zr-5.5Al-4.5Mo-4.5Cr-2.5Sn) ingredient, weighs (total mass of raw material 100g) work
Industry grade sponge zirconium 50g, rafifinal 5.5g, high purity tin 2.5g, High-Purity Molybdenum 4.5g, High Pure Chromium 4.5g are dipped in dehydrated alcohol, ultrasound
It air-drying, is placed in the water jacketed copper crucible of non-consumable vacuum arc melting furnace after wave cleaning, the vacuum degree in furnace chamber will be extracted into 8 ×
10-3Pa is hereinafter, be filled with high-purity argon gas as protection gas before electric arc melting after, arc temperature is about 2800 DEG C of left sides when each melting
The right side, each smelting time are about 3 minutes or so, and cooling obtains ingot casting after each melting, then carries out overturning processing to ingot casting
Melting is carried out, with this melting-casting ingot casting melt back and overturning ingot casting 8 times to guarantee that the ingot casting ingredient finally obtained is uniform.
Then rolling temperature is heated to the alloy cast ingot of taking-up and keeps the temperature 1h, rolling temperature is 860 DEG C, is rolled as multiple tracks
Secondary rolling deformation, drafts per pass are about 2mm, after rolling per pass, are put into Muffle furnace and are reheated to 860 DEG C and keep the temperature
10 minutes, final deformation amount was made up to 70% sheet alloy, plate thickness 5mm in alloy cast ingot.After whole passes, into
Row solution treatment：Be reheated to 860 DEG C, keep the temperature 7 minutes, be then quenched in room temperature water rapidly, etc. alloy sheets
It is taken out after cooling completely, careful polishes off the oxide layer of alloy ingot surface, and is cleaned and air-dried, and high-strength titanium alloy is obtained.
Comparative example 1
It is Ti-5Al-4Mo-4Cr-2Sn titanium alloy that composition of alloy is prepared in the way of embodiment 1.
Using wire cutting tensile sample (national standard will be cut out to the titanium alloy of Examples 1 to 5 and comparative example 1：
GBT228-2002), tensile sample as shown in FIG. 6.Each sample at least cuts out 5 stretching samples, it is ensured that data repeat
Property, it is measured using room temperature uniaxial tensile test, the universal testing machine of test equipment model Instron5982 is (raw
Business men：Instron, the U.S.), the whole stretching displacement with extensometer monitoring sample, rate of extension is set as 5 × 10-3s-1, into
Row tension test, thus to obtain its mechanical property related data, test result is as shown in table 1.
The Mechanics Performance Testing for the titanium alloy that 1 Examples 1 to 5 of table and comparative example 1 obtain
As shown in Table 1, real in the titanium alloy that the present invention obtains compared with the Ti-5Al-4Mo-4Cr-2Sn titanium alloy of actual measurement
Apply the yield strength for the titanium alloy that example 1~5 obtains：1110.6~1294.5MPa, tensile strength：1195.6~1382.4MPa；
Due to alloy strength is promoted obvious and plasticity only declines by a small margin, it is possible to be referred to as obdurability and get a promotion.
Metallographic structure observation is carried out to the titanium alloy that Examples 1 to 5 obtains respectively, as a result respectively as shown in Fig. 1~5.
As shown in Figure 1, titanium-base alloy obtained by the present embodiment is by by matrix of β phase and tiny acicular α phase group
At with 1 titanium alloy of comparative example, acicular α phase refinement is obvious.In conjunction with 1 mechanical experimental results of table, tiny acicular α phase makes
The intensity of alloy is greatly improved, and compared with Ti-5Al-4Mo-4Cr-2Sn titanium alloy, tensile strength is improved
4.9%.
As shown in Figure 2, titanium-base alloy obtained by the embodiment is equally by by matrix of β phase and tiny acicular α phase
Composition, compared with 1 titanium alloy of comparative example, acicular α phase is further refined, and part acicular α phase is changed into α ' the geneva of lamellar
Body.In conjunction with 1 mechanical experimental results of table as it can be seen that tiny acicular α phase and lamellar α ' martensite obtains the intensity of alloy
Great improvement is arrived, compared with Ti-5Al-4Mo-4Cr-2Sn titanium alloy, tensile strength improves 10.5%.
As shown in Figure 3, titanium-base alloy obtained by the embodiment is by by matrix of β phase and tiny acicular α phase group
At compared with 1 titanium alloy T i-5Al-4Mo-4Cr-2Sn of comparative example, acicular α phase reduces very much, and part acicular α phase is changed into layer
α ' the martensite of sheet, and as α ' the geneva body thickness of the increase lamellar of Zr content decreases.In conjunction with 1 mechanical property of table
Test result as it can be seen that tiny acicular α phase and lamellar α ' martensite makes the intensity of alloy be greatly improved, with
Ti-5Al-4Mo-4Cr-2Sn titanium alloy is compared, and tensile strength improves 13.7%.
As shown in figure 4, titanium-base alloy obtained by the embodiment is by by matrix of β phase and tiny acicular α phase group
At compared with 1 titanium alloy T i-5Al-4Mo-4Cr-2Sn of comparative example, acicular α phase reduces very much, and part acicular α phase is changed into layer
α ' the martensite of sheet and as α ' the geneva body thickness of the increase lamellar of Zr content decreases.In conjunction with 1 mechanical property of table
Test result it is found that tiny acicular α phase and lamellar α ' martensite makes the intensity of alloy be greatly improved, with
Ti-5Al-4Mo-4Cr-2Sn titanium alloy is compared, and tensile strength improves 16.6%.
As shown in figure 5, titanium-base alloy obtained by the embodiment is by by matrix of β phase and tiny acicular α phase group
At compared with 1 titanium alloy T i-5Al-4Mo-4Cr-2Sn of comparative example, acicular α phase reduces very much, and part acicular α phase is changed into layer
α ' the martensite of sheet and as α ' the geneva body thickness of the increase lamellar of Zr content decreases.In conjunction with 1 mechanical property of table
Test result as it can be seen that tiny acicular α phase and lamellar α ' martensite makes the intensity of alloy be greatly improved, with
Ti-5Al-4Mo-4Cr-2Sn titanium alloy is compared, and tensile strength improves 21.3%.
As Fig. 1~5 it is found that the tissue of titanium alloy obtained by different embodiments of the invention occur apparent β crystal boundary and
There is a large amount of acicular α " martensitic phase in β crystal grain；The main composition of alloy is mutually α ' martensitic phase and α " martensitic phase, and
Both martensitic phases are tiny acicular structure on tissue morphology, therefore it can be seen that a large amount of acicular structures in metallographic
Presence.And as the acicular α phase of increase of Zr content is gradually replaced by α ' the martensitic phase of lamellar, and this lamellar
The thickness of α ' martensitic phase gradually decrease so that the intensity of alloy increases.
Can be seen that by Fig. 1~5 can only find out that the embodiment of on the one hand refinement crystal grain is the number of original β crystal boundary from metallograph
Amount increases；On the other hand, although tiny α ' phase crystallite dimension is difficult to count, in picture in unit area α ' phase quantity
Also increasing, so obtaining the result of crystal grain refinement by intuitively observing metallograph.
As can be seen from the above embodiments, the present invention promotes the mechanical property of titanium alloy by the content of control each element,
The intensity for significantly improving titanium alloy makes it meet the requirement of aviation component, can be applied in automobile, ship, medical treatment, meal
Tool, the fields such as mobile phone frame and frame.
The above is only a preferred embodiment of the present invention, it is not intended to limit the present invention in any form.It should
It points out, for those skilled in the art, without departing from the principle of the present invention, if can also make
Dry improvements and modifications, these modifications and embellishments should also be considered as the scope of protection of the present invention.
Claims (10)
1. a kind of high-strength titanium alloy, based on mass content, including Al 4.5~5.5%, Mo 3.5~4.5%, Cr 3.5~
4.5%, the Ti of Sn 1.5~2.5%, Zr 10~50% and surplus.
2. high-strength titanium alloy according to claim 1, which is characterized in that the high-strength titanium alloy include Al 4.5~
4.8%, the Ti of Mo 3.6~3.8%, Cr 3.6~3.8%, Sn 1.5~1.8%, Zr 10~50% and surplus.
3. high-strength titanium alloy according to claim 1 or 2, which is characterized in that the tissue of the high-strength titanium alloy includes needle
Shape α phase martensite and lamellar α ' martensite.
4. the preparation method of high-strength titanium alloy described in claims 1 to 3 any one, which is characterized in that include the following steps：
(1) cast alloy base will be obtained after alloy raw material melting；
(2) it is deformed after the cast alloy base that the step (1) obtains being carried out isothermal holding, obtains densification alloy preform；
(3) the densification alloy preform for obtaining the step (2) carries out solution treatment, obtains high-strength titanium alloy.
5. the preparation method according to claim 4, which is characterized in that melting is vacuum arc melting in the step (1),
The temperature of the vacuum arc melting is 2000~2900 DEG C.
6. preparation method according to claim 4 or 5, which is characterized in that in the step (1) melting number 5 times with
On, each smelting time is in 1min or more.
7. the preparation method according to claim 4, which is characterized in that the temperature of isothermal holding is 860 in the step (2)
~900 DEG C, the time of isothermal holding is 0.5~1.0h.
8. the preparation method according to claim 4, which is characterized in that be deformed into rolling deformation in the step (2)；It is described
The total deformation of rolling deformation is 65~70%, and the temperature of rolling deformation is 860~900 DEG C.
9. preparation method according to claim 8, which is characterized in that the rolling deformation is multi- pass rolling, per pass
Drafts be 2~3mm；
When using multi- pass rolling, per pass roll after, by alloy preform after rolling rolling deformation at a temperature of heat preservation 5~
10min。
10. the preparation method according to claim 4, which is characterized in that the holding temperature of solution treatment in the step (3)
It is 860~900 DEG C, the soaking time of solution treatment is 3~7min, and the type of cooling of solution treatment is water quenching.
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| CN111014675A (en) * | 2019-12-31 | 2020-04-17 | 长沙理工大学 | Method for obtaining laser 3D printing double-phase titanium alloy superfine needle-shaped α phase |
| CN111458360A (en) * | 2020-04-30 | 2020-07-28 | 中国航发北京航空材料研究院 | Preparation method of EBSD sample for Ti6242 bar two-phase texture determination |
| CN111910103A (en) * | 2019-05-10 | 2020-11-10 | 大田精密工业股份有限公司 | Titanium alloy sheet material and method for producing same |
| CN113378446A (en) * | 2021-06-09 | 2021-09-10 | 辽宁石油化工大学 | Titanium alloy beta-phase high-temperature solid solution structure simulation method based on Leeb's theory |
| CN114622112A (en) * | 2022-03-15 | 2022-06-14 | 东北大学 | High-impact-toughness titanium alloy and preparation method thereof |
| CN115874082A (en) * | 2022-12-05 | 2023-03-31 | 燕山大学 | Titanium alloy and preparation method thereof |
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| CN111458360B (en) * | 2020-04-30 | 2023-08-04 | 中国航发北京航空材料研究院 | Preparation method of EBSD sample for measuring two-phase texture of Ti6242 bar |
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| CN113378446B (en) * | 2021-06-09 | 2023-04-25 | 辽宁石油化工大学 | Titanium alloy beta-phase high-temperature solid solution tissue simulation method based on Phyllanthus theory |
| CN114622112A (en) * | 2022-03-15 | 2022-06-14 | 东北大学 | High-impact-toughness titanium alloy and preparation method thereof |
| CN115874082A (en) * | 2022-12-05 | 2023-03-31 | 燕山大学 | Titanium alloy and preparation method thereof |
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