CN106591625A - Titanium alloy with matched high strength and toughness and preparation process of titanium alloy - Google Patents
Titanium alloy with matched high strength and toughness and preparation process of titanium alloy Download PDFInfo
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- CN106591625A CN106591625A CN201510680431.1A CN201510680431A CN106591625A CN 106591625 A CN106591625 A CN 106591625A CN 201510680431 A CN201510680431 A CN 201510680431A CN 106591625 A CN106591625 A CN 106591625A
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- 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
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Abstract
The invention relates to a titanium alloy and the field of forming processes, in particular to titanium alloy with matched high strength and toughness and a preparation process of the titanium alloy. The alloy comprises the following components in percentages by weight: 5.5-6.5% of Al, 1.5-2.5% of Sn, 1.5-2.5% of Zr, 2.5-3.5% of Mo, 0.5-1.5% of Cr, 0.5-1.5% of V, 0.1-0.3% of Fe, 0.1-0.2% of O and the balance of Ti and inevitable impurities. The preparation process of the alloy comprises the following steps: step one, carrying out one-heating-number forging in a beta single-phase region at the temperature of 20-50 DEG C above an alloy phase transformation point, wherein forging deformation is about 40%-80%; step two, forging and forming in an alpha+ beta two-phase region at the temperature of 20-50 DEG C below the alloy phase transformation point, wherein the heating number of forging of the two-phase region is controlled to be 1-3, and the accumulative deformation does not exceed 20%; and step three, carrying out heat treatment in a temperature range of 500-600 DEG C. The titanium alloy can be used for manufacturing various types of products such as rods and wires, plates and forge pieces of high-strength and high-toughness titanium alloy, and is applied to the fields of aviation, aerospace, ships and warships and the like with requirements on structure weight reduction and corrosion resistance.
Description
Technical field
The present invention relates to titanium alloy and its forming technology field, specifically refer to it is a kind of comprising Multiple components with height
The titanium alloy and its preparation technology and forging Technology for Heating Processing of strength high toughness matching, can be applicable to a new generation of China
The key construction part of aircraft, and space flight, naval vessel etc. have the skill of demand to structure loss of weight, corrosion resistance
Art field.
Background technology
Mainly have intensity good etc. the titanium alloy of shaft-like α phase comprising α phases and β phases in common diphasic titanium alloy
But the characteristics of fracture toughness is slightly worse, and the titanium alloy with lamellar structure then has good toughness, but intensity
And it is moulding slightly poor compared with equiaxed structure.Equiaxed structure is realized by chemical composition adjustment and corresponding forging and forming technology
And the combination of lamellar structure mechanical property is the target pursued in the industry.
In titanium alloy component, composition, ratio, the size shape of different chemical element to titanium alloy α phases and β phases
Looks have an impact, and so as to the titanium alloy with different chemical composition, its mechanical behavior differs greatly.Al elements are titaniums
Add widest alloying element in alloy, belong to displaced type α phase stable elements, pairing gold utensil has solution strengthening
Effect, and can form α with Ti in alloy aging process2Phase, further strengthens α phases.Mo、V、Cr、
Fe elements belong to displaced type β phase stable elements, and wherein Mo, V belongs to β isomorphous elements, and Cr, Fe
Belong to β eutectic elements.By adding a certain amount of β phases stable element, stable β can be at room temperature obtained
Phase, the α of the diffusion-precipitation gold utensils that are involutory have obvious invigoration effect in β phases in follow-up ag(e)ing process.Zr, Sn are first
Element belongs to displaced type neutral element, has certain castering action to the mechanical behavior under high temperature of titanium alloy.
At present, have been reported or formed material standard is related to Al, Mo, Cr, V, Fe, Sn, Zr alloy
The titanium alloy of element mainly has：Ti-6Al-4V alloys, Ti-6Al-2Sn-2Zr-2Mo-2Cr alloys,
Ti-6Al-2Sn-4Zr-2Mo, Ti-6Al-2Sn-4Zr-6Mo, Ti-6Al-2.5Mo-1.5Cr-0.5Fe etc..Wherein,
Most widely used titanium alloy is Ti-6Al-4V alloys (domestic alloy designations are TC4 alloys), and the alloy contains
There are the Al elements of about 6% percentage by weight and the V element of about 4% percentage by weight.TC4 alloys are by widely
Apply in aerospace structural members and in not higher than 400 DEG C of high-temperature component.Structural material generally needs higher
Strength and toughness matching, in TC4 alloy component ranges, alloy strength be 800～1000MPa, break
Split 80～95MPam of toughness1/2.Due to the tight demand of the field structure loss of weight such as Aeronautics and Astronautics, current TC4
Alloy, its strength and toughness matching level can not meet future usage demand, be badly in need of a kind of high intensity of development, height
The new titanium alloy material of toughness.
Significantly affect except alloy composition and its die forging forming process have on titanium alloy product mechanical property, mesh
Front widely used titanium alloy forging forming technology and Technology for Heating Processing have two kinds.Titanium alloy forging die forging into
Shape process aspect, the first forging mode enforcement it is as follows, titanium alloy alpha+beta two-phase section one it is fiery or it is many fire time forge
Cause shape, forging that there is equiaxial or bifurcation microstructure；Second forging mode implements as follows, closes in titanium
β monophase fields one heat forging shaping (many fire time heats forgeds in β monophase fields must be avoided) more than metallographic height,
Forging has basket institutional framework.Titanium alloy forging Technology for Heating Processing aspect, the first heat treatment mode is in phase transformation
Following 20 DEG C～50 DEG C of point carries out solution treatment, subsequently using Ageing Treatment；Second heat treatment transformation temperature with
Lower 100 DEG C～300 DEG C carry out stress-removal process of annealing.
Resistance of deformation of the titanium alloy in alpha+beta two-phase section die forging process is higher by about 50%, therefore β compared with β monophase fields
Monophase field forging and molding is more easy to make forging be full of die cavity.In addition the equiaxial or bifurcation for obtaining is forged with alpha+beta two-phase section
Tissue is compared, basket matching of the tissue with more excellent strength and toughness obtained after the forging of β monophase fields.So
And high-strength high-ductility titanium alloy die forging test involved in the present invention shows, even with the forging of β monophase fields, one is fiery
Secondary deformation there is no guarantee that forging is completely filled with die cavity, and the forging of β monophase fields must avoid the second fire time in β
Monophase field shapes, therefore at present existing two kinds of titanium alloy forging forging technologies can not meet involved in the present invention
The needs of high-strength high-ductility titanium alloy forging production, it is necessary to develop a kind of new, for the high-strength high-ductility titanium alloy
Die-forging forming mode.
To sum up analyze, the problem of solution is needed at present is：1) the structure loss of weight demand in the field such as Aero-Space is to institute
The intensity and toughness for selecting structural titanium alloy proposes requirements at the higher level, need to develop and simultaneously have high intensity, high tenacity
Titanium alloy material.But the fracture toughness of titanium alloy tends to vary with the rising of intensity and reduces, therefore need to be disconnected from affecting
The essential mechanism for splitting toughness is set out, and by the matching of design of alloy and contour forging technique, is lifting the strength of materials
While, keep its fracture toughness；2) high-strength high-ductility titanium alloy is adapted to adopt β monophase fields die-forging forming, but β
Monophase field one heat forging can not completely be such that forging avoids in β monophase fields full of die cavity, and the die forging mode
Heating and die forging more than one fire time.Therefore a kind of new, mould that is being adapted to the high-strength high-ductility titanium alloy must be developed
Forging forming mode, should additionally develop the heat treatment mode with this alloy forging process matching to ensure the comprehensive of forging
Close performance.
The content of the invention
For this purpose, it is an object of the invention to provide a kind of titanium alloy with high-intensity high-tenacity matching and its preparation
Technique.New titanium alloy chemical composition ranges proposed by the present invention, with most widely used Ti-6Al-4V alloys
Compare, in the case of tensile strength is significantly improved, the Fracture Toughness of material is suitable, with excellent obdurability
Matching；Meanwhile, by larger using forging forming difficulty is solved for the titanium alloy certain moduli forging process
Problem.
Technical scheme is as follows：
It is a kind of with high-intensity high-tenacity matching titanium alloy, by match titanium alloy chemical composition, its chemistry into
Split system is：Ti-Al-Sn-Zr-Mo-Cr-V-Fe-O, the percentage by weight of each component is：
Al：5.5～6.5%, Sn：1.5～2.5%, Zr：1.5～2.5%, Mo：2.5～3.5%, Cr：0.5～
1.5%, V：0.5～1.5%, Fe：0.1～0.3%, O：0.1～0.2%, balance of Ti and inevitably
Impurity element；In alloy system, Al equivalent weight ranges meet：7.6wt.%≤[Al] eq≤8.5wt.%, while Mo
Equivalent weight range meets：5.0wt.%≤[Mo] eq≤5.5wt.%.
The described titanium alloy with high-intensity high-tenacity matching, inevitable impurity element be C, N, H,
Si, percentage by weight is respectively less than 0.1%.
The preparation technology of the described titanium alloy with high-intensity high-tenacity matching, comprises the following steps that：
1) electrode compacting：Electrode compacting is completed on a hydraulic press according to charger sheet；
2) ingot casting melting：Electrode melts out composition and uniformly casts through three vacuum consumables or plasma cold pool furnace
Ingot；
3) ingot formation：By the transformation temperature of Metallography method determination alloy, ingot casting is respectively 150 DEG C more than transformation temperature
And more than transformation temperature 50 DEG C of cogging forgings that two fire time are carried out to ingot casting；
4) forging forming：Forging stock 20 DEG C～50 DEG C of β monophase fields one heat forging more than alloy phase change point,
Forging deformation amount is 40%～80%, it is ensured that forging shapes substantially after β monophase fields one heat forging；In phase transformation
Following 20～50 DEG C of point carries out the secondary forging deformation of 1～3 fire, fully crushes microscopic structure, and cumulative deformation is not
More than 20%, while realizing forging forming and forging solution heat treatment；
5) according to required mechanical property, choosing in 500 DEG C～600 DEG C temperature ranges carries out forging timeliness, goes
Stress is heat-treated, and heat treatment time is 4～8 hours, while realizing forging ageing strengthening.
Advantages of the present invention and have the beneficial effect that：
1st, the mechanism of action of the present invention according to different-alloy element to titanium alloy, the Al equivalents of comprehensive matching alloy
And Mo equivalents, optimize Crack Tip Plastic rheology characteristic, do not reduce Crack Tip while the strength of materials is improved
End plastic zone scope, and then relatively reasonable chemical composition and content is devised, obtain a kind of high-strength and high ductility titanium
The chemical composition of alloy.By matching titanium alloy chemical composition, the phase composition of alloy is adjusted, optimize crack tip
Plastic flow feature, so as to improve the intensity and toughness of material simultaneously.
2nd, the present invention develops tension strong on the basis of Ti-Al-Sn-Zr-Mo-Cr-V-Fe-O chemical compositions system
Degree is more than 80MPam more than 1100MPa, fracture toughness1/2High-strength high-ductility titanium alloy.With it is now widely used
Ti-6Al-4V alloys are compared, and the Ti-Al-Sn-Zr-Mo-Cr-V-Fe-O systems alloy of present invention development optimization is substantially carried
In the case of high tensile, the Fracture Toughness of material quite or changes less, and its obdurability matching is better than
Ti-6Al-4V alloys.
3rd, high intensity of the present invention, high-tenacity titanium alloy meet the demand of modular construction loss of weight, and with higher peace
Full property and reliability, with the potentiality applied in fields such as Aeronautics and Astronautics, ship, chemical industry.
4th, for high-strength high-ductility titanium alloy composition according to the present invention, one kind has been developed and has been suitable for the conjunction of high-strength and high ductility titanium
Golden forging forming and Technology for Heating Processing, are ensured by coordinating the forging deformation amount of β monophase fields and alpha+beta two-phase section
The shaping of forging, by the solution treatment of forging the forging process of alpha+beta two-phase section is dissolved into, and has reduced or remitted independent two-phase
There is area's solution treatment, the forging Technology for Heating Processing for designing in addition timeliness, stress-removal process to act on simultaneously.This
The forging forming and Technology for Heating Processing of bright design is applicable not only to alloy according to the present invention, while also solving other
High-strength titanium alloy forging process for fuel shapes a difficult problem, and distinguishes and existing conventional titanium alloy forging production technology.
Description of the drawings
Fig. 1 is 1# composition alloys in table 1 Ti Jing after fixation rates3The size distribution plot of Al phases；Wherein,
Abscissa diameter along represent Ti3Equivalent diameter (the unit of Al phases：Nanometer), ordinate relative
Frequency represents the Ti of a certain equivalent diameter in statistics visual field3The quantity of Al phases.
Fig. 2 is 2# composition alloys in table 1 Ti Jing after fixation rates3The size distribution plot of Al phases；Wherein,
Abscissa diameter along represent Ti3Equivalent diameter (the unit of Al phases：Nanometer), ordinate relative
Frequency represents the Ti of a certain equivalent diameter in statistics visual field3The quantity of Al phases.
Fig. 3 is the microscopic structure that alloy is obtained when 30% deflection of β monophase fields, and crystal boundary is not all broken
It is broken；
Fig. 4 is the microscopic structure that alloy is obtained when 90% deflection of β monophase fields, part microscopic structure etc.
Axiation；
Fig. 5 is the preferable basket tissue topography that alloy is obtained when 60% deflection of β monophase fields；
Fig. 6 is that basket organizes the displaing micro tissue topography obtained Jing after the two-phase section forging of 15% deflection；
Fig. 7 is that basket organizes the displaing micro tissue topography obtained Jing after the two-phase section forging of 30% deflection；
Fig. 8 is special high-strength, toughness titanium alloy forging the typical basket tissue topography of aviation.
Specific embodiment
In a specific embodiment, in order to keep its fracture toughness while the strength of materials is improved, the present invention is high
Intensity, the titanium alloy of high tenacity matching, by matching titanium alloy chemical composition, its chemical composition system is：
Ti-Al-Sn-Zr-Mo-Cr-V-Fe-O.In following examples and comparative example, nine kinds of different chemical compositions of melting
Ti-Al-Sn-Zr-Mo-Cr-V-Fe-O series titanium alloys, alloying component is shown in Table 1.Each alloy raw material is through ingot formation
Forging, bar finish forge, finally prepare the bar of diameter 60mm, and detailed process is：According to chemical composition group
Into dispensing is simultaneously prepared for smelting electrode, and using 3 vacuum consumable method smelting titanium alloys, ingot casting specification is
100kg.The α/β phase transition temperature T completely of alloy is measured using metallographic methodβ(being shown in Table 1), by ingot casting 1150
DEG C cogging forging, in 1050 DEG C of upsetting pull Broken Crystals, then in alloy TβHereinafter 40 DEG C are forged into diameter 120mm
Bar, eventually through finish forge operation in Tβ40 DEG C of bars for being forged into diameter 60mm below.By diameter 60mm
Bar is heat-treated, and the thermally treated (T of nine kinds of composition bar Jing is listed in table 2βHereinafter 40 DEG C of insulations 1 are little
When after air cooling, the then air cooling after 500 DEG C, 540 DEG C, 580 DEG C of insulations 4 hours respectively) afterwards test obtain
Room temperature tensile properties and fracture toughness.It is strong that table 2 lists tension of nine kinds of alloys at a temperature of different solid solution agings
Degree Rm, yield strength Rp0.2And fracture toughness KIC。
1 nine kinds of Ti-Al-Sn-Zr-Mo-Cr-V-Fe-O systems alloy compositions of table, percentage by weight %
Mechanical property under 2 nine kinds of Ti-Al-Sn-Zr-Mo-Cr-V-Fe-O systems alloy difference aging temps of table
The design principle of alloy composition is as follows in the present invention：
The fracture toughness of material is for evaluating the ability that material to be attracted extraneous acting.The fracture of titanium alloy
Toughness is subject to the combined influence of intensity and crack tip plastic zone scope, if intensity can be improved, and while keeps
Or increase crack tip plastic zone scope, then the ability that material absorbs extraneous acting can be lifted, so as to improve fracture
Toughness.For titanium alloy, then to avoid generating the Ti of fragility3Al or TiCr2Phase, while avoid intensity too high,
Significantly reduce moulding area's scope.
Ti3The precipitation of Al phases is not only relevant with Al constituent contents, also related to the element such as Sn, Zr, O, can lead to
Cross calculate Al equivalents evaluate in alloy with Al with effect element impact, computing formula is
[Al] eq=[Al]+[Zr]/6+ [Sn]/3+10 [O].Cr elements can react with Ti, generate orderly on a large scale
Fragility precipitated phase, the precipitated phase of the type can significantly reduce the scope of material crack tip plastic zone.Mo、V、
Fe, O element also has significantly reinforcing effect to titanium alloy, but eutectoid reaction generation fragility will not occur with Ti
Phase, therefore ought strictly control or reduce Cr constituent contents.For Mo, Cr, V, Fe constituent content, introduce
Evaluating castering action of the four kinds of elements of the above to alloy strength, Mo equivalent computing formula are Mo equivalents
[Cr]/7 of+2 [V]/3+2 [Fe] of [Mo] eq=[Mo]+10.The elements such as Sn, Zr are modal several in titanium alloy
Element, for the room temperature mechanical behavior under high temperature of the alloy that balances each other, ensures for stablizing titanium alloy has important function.
In addition, strictly being controlled Si as impurity element in the present invention, its reason is as follows, and Si is used as micro unit
Element can lift titanium alloy high-temperature mechanical property, particularly creep resisting ability, but for room temperature or lower temperature are used
Structural titanium alloy, the Si contents of even 0.2% (wt.%) can also form the compound of Si, and chemical combination
Thing grain boundaries be enriched with, reduce material toughness, therefore in the present invention using Si as impurity element, and control exist
0.1% (wt.%) is below.
By impact of the different individual elements of analysis to alloy mechanical property, and plan as a whole to adjust the synthesis of different elements
Effect, is to obtain preferable alloy strength toughness matching, and Al equivalents and Mo equivalents should be made to control suitable simultaneously
In the range of.Wherein, Al equivalent weight ranges should meet 7.6 (wt.%)≤[Al] eq≤8.5 (wt.%), while
Mo equivalent weight ranges should meet 5.0 (wt.%)≤[Mo] eq≤5.5 (wt.%).By Al equivalents and Mo equivalents
Coordination matching, improve the strength of materials while, it is ensured that crack tip plastic zone scope will not be reduced, optimization
Crack Tip Plastic rheology characteristic, so as to improve the intensity and toughness of material simultaneously.
Below in conjunction with accompanying drawing, comparative example and embodiment in detail the present invention is described in detail.
Embodiment 1-4
In table 1, numbering is the Ti-Al-Sn-Zr-Mo-Cr-V-Fe-O systems alloy of 2#, 4#, 5#, 9# composition,
Strength and toughness is obtained by solid-solution and aging heat treatment preferably to match.As can be seen from Table 2, the above four
The strength of alloy for planting composition is more than 1100MPa, and fracture toughness is higher than 80MPam1/2。
In Tables 1 and 2, numbering is the alloy of 2#, 4#, 5#, 9# composition, and its strength and toughness is matched compared with TC4
Alloy has obvious advantage, the wherein Fracture Toughness of 2#, 4#, 5#, 9# composition alloy and TC4 alloys
Quite, and intensity about improves 100～200MPa, security is ensured, can obtain on the premise of reliability
Obvious structure weight loss effect.
Comparative example 1
In table 1, the Al equivalents of 1# composition alloys are 9.3, hence it is evident that higher than other composition alloys.Al equivalents are higher
When, it is beneficial to promote fragility Ti3The roughening of Al phases, forms large-scale fragility ordered phase, so as to reduce closing
The fracture of gold is wilful.Fig. 1 is the size distribution plot of 1# composition alloys Ti3Al phases Jing after fixation rates, schemes
2 is Ti in 2# alloys3The size distribution plot of Al phases, it can be seen that the size of Ti3Al phases is bright when Al equivalents are higher
It is aobvious larger.With reference to table 2 as can be seen that the strength difference of 1# and 2# composition alloys is less, but the fracture of 2# alloys
Toughness is significantly higher.Therefore, Al equivalents should be controlled unsuitable too high, O constituent contents is strictly controlled among these
No more than 0.2%.
Comparative example 2-4
In Tables 1 and 2,3#, 6#, 7# composition alloy is compared with other composition alloys, and its tensile strength is higher,
But fracture toughness is relatively low, this key factor is in too high, the higher Mo of 3#, 6#, 7# composition alloy Mo equivalents
Although equivalent has been obviously improved alloy strength, but while reduce the moulding area's scope of crack tip, makes alloy ductility
Reduce.Therefore the Mo equivalents of alloy also should not be too high, and the content of Fe, V element is strictly limited among these.
Comparative example 5
In Tables 1 and 2, compare with 4#, 5# alloying component, the Fracture Toughness of 8# compositions is higher, but intensity
It is low.This key factor in the Al equivalents and Mo equivalents of 8# alloys be in reduced levels, particularly Fe,
The content of O elements is relatively low, result in alloy strength low.Therefore while the elements such as Fe, O are limited,
This two kinds of constituent contents should not be made too low, all should be more than 0.1%.
By embodiment 1-4 and comparative example 1-5, optimize the alloy compositions weight with high-strength and high ductility characteristic for determining
Percentage is：Al：5.5～6.5%, Sn:1.5～2.5%, Zr：1.5～2.5%, Mo：2.5～3.5%, Cr：
0.5～1.5%, V：0.5～1.5%, Fe：0.1～0.3%, O：0.1～0.2%, other elements such as C, N,
The elements such as H, Si are impurity element, and percentage by weight is respectively less than 0.1%, balance of Ti, and follows alloy system
Middle Al equivalent weight ranges meet 7.6 (wt.%)≤[Al] eq≤8.5 (wt.%), while Mo equivalent weight ranges meet
5.0 (wt.%)≤[Mo] eq≤5.5 (wt.%).
It is to obtain higher toughness for the high-strength, high-tenacity titanium alloy that the invention described above is related to, target should be made
Microstructures Control is the basket tissue morphology that lamella intersects, while avoiding straight grain boundary α and microscopic structure etc.
Axiation.More than being based on, during design forging technology, following aspect is mainly considered：1) β monophase fields forging
Deflection；2) alpha+beta two-phase section forging times and deflection；3) heat treatment is processed with forging technology and destressing
Matching.On the basis of higher alloy obdurability matching is obtained, it is necessary to be aided with and match with the alloy property
Die forging forming process, just can guarantee that being fully formed for high-intensity high-tenacity forging.Therefore, it is high-strength in order to solve
The die-forging forming difficult point of degree high-tenacity titanium alloy, the die forging forming process of employing is as follows：
1st step：First by titanium alloy blank more than alloy phase change point 20 DEG C～50 DEG C of the fire of β monophase fields one
Forging, forging deformation amount is about 40%～80%, it is ensured that forging shapes substantially after β monophase fields one heat forging；
2nd step：By the forging of basic shaping, 20 DEG C～50 DEG C of alpha+beta two-phase section is forged below alloy phase change point
Shaping, two-phase section forging times control is less than 20% in 1～3 fire, two-phase section forging cumulative deformation,
The step realizes the effect of forging forming and forging solution heat treatment simultaneously；
3rd step：Carry out forging timeliness, destressing in 500 DEG C～600 DEG C temperature ranges to process, the step is same
When realize forging ageing strengthening.
Below in conjunction with accompanying drawing, comparative example and embodiment in detail alloy Design of die forging process in the present invention is described in detail.
Using more than transformation temperature 20 DEG C～50 DEG C of the fire time moderate finite deformation amount forging of β monophase fields one, make forging basic
Shaping, can be greatly lowered resistance of deformation, promote flowing of the material in die cavity, make alloy as far as possible full of type
Chamber, reduces deformation after unloading fire；And 40%～80% forging deformation amount can obtain preferable crystal boundary and be broken
Basket tissue, so as to ensure high-strength, high tenacity the matching of forging.When β monophase fields deflection is less than 40%
Crystal boundary is substantially complete (Fig. 3), when reducing the tensile strength of forging, and deflection higher than 80% (Fig. 4), shows
Micro-assembly robot is too refined, and reduces the toughness of forging.What Fig. 5 was obtained when being 60% by β monophase fields deflection
Preferable basket tissue topography.
After first fire time die forging, to carry out 1～3 fiery for 20 DEG C～50 DEG C of alpha+beta two-phase section below alloy phase change point
Secondary forging and molding.Two-phase section forging times are ensureing the reduction that should try one's best on the premise of die cavity is full of, so as to reduce
Production cost, so control is advisable in 1～3 fire.Two-phase section forges cumulative deformation less than 20% guarantor
The lamella in basket tissue is demonstrate,proved not by notable isometry, so as to ensure that the toughness of forging.Fig. 6, Fig. 7 point
It is not the displaing micro tissue topography for being obtained, it is seen that two-phase when two-phase section forging deformation amount is 15%, 30%
Area's deflection obtains preferable basket tissue when being 15%, partial plies are by isometry when deflection is 30%.
The solution treatment of existing titanium alloy forging is individually carried out after forging, in the forging technology of present invention design,
Because two-phase section forging deformation amount is less, simultaneously solution treatment effect is taken into account in two-phase section insulation forging process,
Without additionally individually carrying out solution treatment to forging.
Compared with existing titanium alloy forging and Technology for Heating Processing, the technical scheme in the present invention is mono- by coordinating β
The forging deformation amount of phase region and alpha+beta two-phase section obtains preferable forging basket tissue ensureing the shaping of forging
Type, additionally unites two into one the solution treatment of forging with the forging of alpha+beta two-phase section, has reduced or remitted forging two
The independent solution treatment of phase region, is heat-treated in the range of final 500 DEG C～600 DEG C and also have simultaneously timeliness, stress-removal
Process is acted on.
Embodiment 5
It is as follows that the specific high-strength high-ductility titanium alloy forging of the present embodiment prepares embodiment：Including into component selections, electrode
The operations such as compacting, ingot casting melting, ingot formation, bar or sheet material forming.
1) alloying component dispensing is carried out according to following target component, the percentage by weight of each component is：Al：5.8%,
Sn:2.1%, Zr：2.0%, Mo：3%, Cr：1%, V：1%, Fe：0.16%, O：0.15%, other
The elements such as element such as C, N, H, Si are impurity element, and percentage by weight is respectively less than 0.1%, balance of Ti.
2) electrode compacting：By composition design, select the different intermediate alloy proportionings of intermediate alloy, calculating finally true
Determine charger sheet, electrode compacting is completed on a hydraulic press according to charger sheet.
3) ingot casting melting：Through three vacuum consumables or plasma cold pool furnace, the uniform ingot casting of composition is melted out.
4) ingot formation：By the transformation temperature of Metallography method determination alloy, ingot casting is respectively in transformation temperature temperature higher above
Degree (150 DEG C) and transformation temperature above lower temperature (50 DEG C) carry out the cogging forging of two fire time to ingot casting.
5) forging forming：Forging stock about 50 DEG C of β monophase fields one heat forging more than alloy phase change point, forging
Deflection is about 40%～80%, it is ensured that forging shapes substantially after β monophase fields one heat forging；In transformation temperature
Hereinafter 20～50 DEG C of forging deformations for carrying out 1～3 fire time, fully crush microscopic structure, and cumulative deformation does not surpass
Cross 20%.
6) according to required mechanical property, choosing a certain temperature in 500 DEG C～600 DEG C temperature ranges carries out forging
Timeliness, destressing are processed.
According to the high-strength high-ductility titanium alloy chemical composition for determining, 4 tons of ingot castings of melting, table 3 is ingot casting difference position
Put the chemical composition at place.The aviation special titanium alloy forging of two kinds of specifications is have developed using the ingot casting, Fig. 8 is forging
The typical basket tissue topography that part is obtained.The room temperature mechanical property of 1#, 2# aero titanium alloy forging is listed in table 4
Can, intensity and the fracture toughness match of forging are substantially better than TC4 titanium alloys.
The high-strength high-ductility titanium alloy ingot chemistry analysis result of the melting of table 3
4 high-strength high-ductility titanium alloy of table, two kinds of specification forging room-temperature mechanical properties
Embodiment result shows that the present invention keeps its fracture toughness while the strength of materials is improved, and can be used to make
Make the polytype product such as rod silk material, sheet material, forging of high-strength high-ductility titanium alloy, be applied to Aeronautics and Astronautics,
Naval vessel etc. is to structure loss of weight, the anti-corrosion technical field with demand.
Claims (3)
1. it is a kind of with high-intensity high-tenacity matching titanium alloy, it is characterised in that by match titanium alloy chemistry
Composition, its chemical composition system is：Ti-Al-Sn-Zr-Mo-Cr-V-Fe-O, the percentage by weight of each component
For：
Al：5.5～6.5%, Sn：1.5～2.5%, Zr：1.5～2.5%, Mo：2.5～3.5%, Cr：0.5～
1.5%, V：0.5～1.5%, Fe：0.1～0.3%, O：0.1～0.2%, balance of Ti and inevitably
Impurity element；In alloy system, Al equivalent weight ranges meet：7.6wt.%≤[Al] eq≤8.5wt.%, while Mo
Equivalent weight range meets：5.0wt.%≤[Mo] eq≤5.5wt.%.
2. according to the titanium alloy with high-intensity high-tenacity matching described in claim 1, it is characterised in that no
Evitable impurity element is C, N, H, Si, and percentage by weight is respectively less than 0.1%.
3. the preparation technology of the titanium alloy with high-intensity high-tenacity matching described in a kind of claim 1, it is special
Levy and be, comprise the following steps that：
1) electrode compacting：Electrode compacting is completed on a hydraulic press according to charger sheet；
2) ingot casting melting：Electrode melts out composition and uniformly casts through three vacuum consumables or plasma cold pool furnace
Ingot；
3) ingot formation：By the transformation temperature of Metallography method determination alloy, ingot casting is respectively 150 DEG C more than transformation temperature
And more than transformation temperature 50 DEG C of cogging forgings that two fire time are carried out to ingot casting；
4) forging forming：Forging stock 20 DEG C～50 DEG C of β monophase fields one heat forging more than alloy phase change point,
Forging deformation amount is 40%～80%, it is ensured that forging shapes substantially after β monophase fields one heat forging；In phase transformation
Following 20～50 DEG C of point carries out the secondary forging deformation of 1～3 fire, fully crushes microscopic structure, and cumulative deformation is not
More than 20%, while realizing forging forming and forging solution heat treatment；
5) according to required mechanical property, choosing in 500 DEG C～600 DEG C temperature ranges carries out forging timeliness, goes
Stress is heat-treated, and heat treatment time is 4～8 hours, while realizing forging ageing strengthening.
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