CN106756688A - One kind deformation TiAl alloy structure property accuracy control method - Google Patents
One kind deformation TiAl alloy structure property accuracy control method Download PDFInfo
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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
Abstract
The invention belongs to high-temperature structural material hot-working preparing technical field, it is related to a kind of deformation TiAl alloy structure property accuracy control method.Of the invention direct by TiAl alloy blank heating to different deformation temperatures, insulation carries out thermal deformation processing after a period of time；By controlling heat distortion temperature, the typical TiAl alloy microscopic structure of four kinds of nearly γ, bifurcation, nearly lamella and full sheet layer is obtained, and then obtain the TiAl alloy deformable member of different mechanical properties.Using this method, tissue and performance are controlled in thermal deformation prepares process, and the heat treatment link after eliminating reduces operation.Simultaneously, prepared nearly lamella and complete lamellar structure fine uniform, have intensity and moulding advantage concurrently, breach the technical bottleneck that deformation TiAl alloy subsequent heat treatment method is difficult to obtain tiny complete lamellar structure, it is a kind of short route, high performance TiAl alloy hot-working method, has broad application prospects.
Description
Technical field
The invention belongs to high-temperature structural material hot-working preparing technical field, TiAl alloy hot-working change is in particular, provided
The control method of structure property during shape.
Research background
Aerospace field is developed rapidly, to the performance requirement of material also more and more higher.Especially to high-temperature structural material,
On the one hand its heat resisting temperature more and more higher is required, on the other hand needs to mitigate its weight.The high-temperature titanium alloy for being used at present, it is resistance to
Hot temperature is limited.And nickel base superalloy density is larger, it is impossible to meet loss of weight demand, therefore, study novel light thermal structure
Material is extremely urgent.
The characteristics of TiAl alloy has density low and high temperature intensity high, creep resistant and excellent oxidation resistance, it is considered to be
650~900 DEG C of ideal materials of replacement nickel base superalloy.Dividing plate and housing at present in Aeronautics and Astronautics engine, space flight fly
Widely used nickel base superalloy on the hot-zone covering of machine, the shortcomings of generally existing density is bigger than normal, specific strength is not enough, limits
The development of high performance aircraft.TiAl alloy has a extensive future as a kind of lightweight high-temperature structural material.But because TiAl is closed
, in intermetallic compound, room temperature and high temperature machinability are all poor, seriously constrain the extensive use of TiAl alloy for metal.
Current TiAl alloy heat processing and forming technology is presented pluralistic trend, main method be still metallurgy ingot casting method and
Powder metallurgic method.Using metallurgy ingot casting method preparation processing TiAl alloy, it is necessary to TiAl alloy ingot casting is prepared in first melting, then adopt
The tissue defects such as Micro porosity, the loose and component segregation eliminated in ingot casting are processed with high temperature insostatic pressing (HIP) and homogenizing annealing, then
Uniform temperature interval ((α+γ) two-phase section) and certain strain rate (<10-2s-1) under the conditions of, forged using one or many
To refine cast sturcture.The structural strain's amount of generally forging reaches more than 80%.In the subsequent operation of rolling, the rolling of sheet material
Temperature range is typically chosen in (α+γ) two-phase section.Two technique ginsengs of mill speed and pass deformation are taken into full account during rolling
Number.Mill speed is too fast, and pass deformation is excessive, and sheet material easily occurs cracking phenomena, causes rolling to fail.If mill speed is too
Slowly, temperature is scattered and disappeared again too soon, so that the resistance of deformation of TiAl alloy material is improved, sheet material is also susceptible to cracking phenomena.
TiAl alloy sheet material is prepared using powder metallurgic method, compared with metallurgy ingot casting method, the powder before forging is increased and is prepared, and
Hip treatment link after powder jacket soldering and sealing, forging and rolling afterwards are also carried out in (α+γ) two-phase section.At (α+γ)
After two-phase section thermo-mechanical processi, TiAl alloy tissue is generally bifurcation tissue, can be heat-treated accordingly according to application demand.
TiAl alloy can obtain four kinds of typical microscopic structures by heat treatment：Nearly γ (NG), bifurcation (DP), nearly lamella (NFL) and
Full sheet layer (FL) tissue.
Annealing and be then slowly cooled to room temperature in the α+γ two-phase sections higher than eutectoid temperature can form nearly γ tissues, cooling
It is by γ equiax crystal afterwards and is distributed in the α of γ phase crystal boundaries on a small quantity2Phase composition.When in alloy α+γ tow-phase region heat treatments, α and γ phases
Formed when volume fraction is roughly equal, after cooling by γ crystal grain and α2The bifurcation tissue of/γ lamellas composition.When annealing temperature reaches
Below α transition temperatures at 10 DEG C or so, nearly lamellar structure is formed after cooling, γ crystal particle volumes fraction is little at this moment organizing,
It is α2The NL tissues of+γ lamellas and a small amount of equiaxial γ crystal grain composition being distributed between lamella group.More than α transition temperatures, i.e., α is mono-
Phase region is heat-treated and Slow cooling can form complete lamellar structure.Because when α monophase fields are heat-treated, temperature is higher, and do not have
The pinning effect of the second phase, α meets and grow up rapidly, finally gives completely by α2The FL tissues that+γ lamellas are constituted, simultaneously because piece
Layer group size is larger, and its plasticity becomes very poor.
In this several typical organization, bifurcation tissue is tiny due to crystal grain, with intensity and temperature-room type plasticity higher, but
Fracture toughness is very low；The tensile strength and plasticity of nearly γ tissues are less than bifurcation tissue；Full sheet layer and nearly lamellar structure are due to lamella
Group's size is larger, and its tensile strength and plasticity are relatively low, and uniform tiny complete lamellar structure has preferable plasticity and fracture
Toughness, comprehensive mechanical property is best.Therefore, focus and target that uniform tiny complete lamellar structure is current research are obtained.
Current TiAl alloy hot processing temperature is general in (α+γ) two-phase section, and bifurcation tissue is obtained after hot-working.Need afterwards
Nearly lamella or full sheet layer heat treatment are carried out, so as to improve the fracture toughness and creep resisting ability of TiAl alloy.
The content of the invention
The present invention proposes a kind of structure property control method for deforming TiAl alloy, i.e., by controlling thermal processing distortion process
In deformation temperature, precise control deformation after alloy microscopic structure, obtain nearly γ, bifurcation, nearly lamella and complete lamellar structure.
TiAl alloy tissue and performance are controlled by thermal deformation process, eliminate the heat treatment link after thermal deformation, reduce work
Sequence.Meanwhile, prepared Deformation structure's fine uniform has intensity and moulding advantage concurrently, is a kind of short route, high performance TiAl
Alloy hot-working preparation method, has broad application prospects.
One kind deformation TiAl alloy structure property accuracy control method, it is characterised in that directly by TiAl alloy blank heating
To different deformation temperatures, insulation carries out thermal deformation processing after a period of time；By controlling heat distortion temperature, nearly γ, double is obtained
The typical TiAl alloy microscopic structure of four kinds of state, nearly lamella and full sheet layer, and then obtain the TiAl alloy deformation of different mechanical properties
Part.Specifically, in α+γ two-phase sections lower end thermal deformations (Te≤ deformation temperature ＜ Te+1/3(Tα-Te)), nearly γ is obtained after thermal deformation
Tissue；In α+γ two-phase sections stage casing thermal deformations (Te+1/3(Tα-Te)≤deformation temperature ＜ Te+2/3(Tα-Te)), obtain brilliant by γ
Grain and α2The bifurcation tissue of/γ lamellas composition；In α+γ two-phase section epimere thermal deformations (Te+2/3(Tα-Te)≤deformation temperature ＜
Tα), obtain α2The NL tissues of/γ lamellas and a small amount of equiaxial γ crystal grain composition；In α transition temperature above thermal deformations (Tα≤ deformation temperature
Degree ＜ Tα+ (30~50) DEG C), obtain α2/ γ complete lamellar structures；Wherein TeIt is α → α2The eutectoid temperature of+γ, TαIt is single-phase into α
The temperature in area.
Control method of the present invention is applied to using metallurgy ingot casting method, the TiAl alloy sense of organization in precise control hot procedure
Can, while being also applied for utilizing powder metallurgic method, TiAl alloy structure property in precise control hot procedure；Wherein hot-working
Method includes forging, extruding, the operation of rolling.
Described TiAl alloy is Beta coagulating types TiAl alloy and Alpha coagulating type TiAl alloys；Beta coagulating types
TiAl alloy includes：Ti-(43-45)Al-(2-9)Nb-(0-6)(Mn,Cr,Mo,V)-(0-0.4)(B,C)；Alpha coagulating types
TiAl alloy includes：Ti-(45-48)Al-(0-7)Nb-(0-4)(Cr,Mn)-(0-0.4)(B,C).
These TiAl alloys, being typically chosen in (α+γ) coexistence region interlude carries out hot-working, obtains bifurcation tissue, then
Carry out nearly lamella or full sheet layer heat treatment.
The advantage of the invention is that：
1. by controlling heat distortion temperature so as to the tissue and performance of precise control TiAl alloy.By this method can be with
By being heat-treated just obtainable typical TiAl alloy tissue, i.e., near γ, bifurcation, nearly lamella and full sheet layer group before acquisition
Knit.In deformation process, structure property precise control, the subsequent heat treatment for eliminating deformation TiAl alloy is follow-up, simplifies for blank
Flow.
2., by the method for On-line Control TiAl alloy tissue in thermal deformation process, uniform tiny tissue can be obtained,
The intensity of sheet material and moulding is improved simultaneously.This uniform tiny tissue includes nearly γ, bifurcation, nearly lamella and complete lamellar structure.
For tiny nearly lamella and complete lamellar structure, it is difficult that the method breaches deformation TiAl alloy subsequent heat treatment method
To obtain the technical bottleneck of tiny complete lamellar structure.
3. this method is applied to deformation TiAl alloy, and being based particularly on heat treatment regulation and control can obtain four kinds of typical organizations
TiAl alloy, TiAl alloy is processed using the thermal deformation of metallurgy ingot casting method, is also processed using powder metallurgic method thermal deformation
TiAl alloy.Due to simplifying flow, control method is simple and easy to apply, it is adaptable to large-scale production.
Brief description of the drawings
Fig. 1 TiAl alloy Hot Deformation Microstructure control schematic diagrams, temperature range 1 is represented in α+γ two-phase section hypomere thermal deformations
(Te≤ deformation temperature ＜ Te+1/3(Tα-Te)), 2 represent in α+γ two-phase sections stage casing thermal deformations (Te+1/3(Tα-Te)≤deformation temperature
Degree ＜ Te+2/3(Tα-Te)), 3 represent in α+γ two-phase section epimere thermal deformations (Te+2/3(Tα-Te)≤deformation temperature ＜ Tα), 4 tables
Show in α transition temperature above thermal deformations (Tα≤ deformation temperature ＜ Tα+ (30~50) DEG C), after this four temperature range thermal deformations
The Deformation structure of acquisition corresponds to nearly γ, bifurcation, nearly lamella and complete lamellar structure respectively.
The typical microscopic structure that the interval thermal deformation of Fig. 2 TiAl alloys different temperatures is obtained：(a) nearly γ, (b) bifurcation,
(c) nearly lamella, (d) full sheet layer
Fig. 3 TiAl alloys thin plate typical case's room-temperature mechanical property (As-Cast：As cast condition, NFL：Nearly lamellar structure, DP：Bifurcation
Tissue, NG：Nearly γ tissues).
Specific embodiment
Embodiment 1
By taking high Nb containing TiAl based alloy as an example, alloy nominal composition is Ti-45Al-8.5Nb (atomic percent), through plasma
Cold hearth melting is made alloy pig.Blank is cut from alloy pig, hot rolling blank is cut after carrying out isothermal forging.The hot rolling for cutting
Blank, with 304 stainless steels as jacket, is welded after being wrapped up using sandwich structure.
Hot-rolled temperature selects α+γ two-phase section hypomeres, such as temperature range 1 of accompanying drawing 1.The present embodiment chooses 1230 DEG C, is incubated 1h
Open rolling afterwards.Heating is melted down after every time rolling, 20~30min of soaking time, draught per pass 20~30%, judgement of speed change is melted down
Rate is controlled in 1~5s-1, melted down after 5 passages of rolling and be cooled to 900 DEG C, it is air cooled to room temperature after insulation 1h.Removed using machine-tooled method
Sheath material, obtains TiAl alloy rolled plate.Surface quality is good, without cracking.Its microscopic structure is uniform tiny nearly γ
Shown in tissue, such as accompanying drawing 2 (a).Sheet material has room temperature strength and good temperature-room type plasticity higher, as shown in Figure 3.950
~1100 DEG C, strain rate 2 × 10-4~5 × 10-4s-1Under the conditions of sheet material there is good superplastic deformation ability.
Embodiment 2
By taking high Nb containing TiAl based alloy as an example, alloy nominal composition is Ti-45Al-8.5Nb (atomic percent), through plasma
Cold hearth melting is made alloy pig.Blank is cut from alloy pig, hot rolling blank is cut after carrying out isothermal forging.The hot rolling for cutting
Blank, with 304 stainless steels as jacket, is welded after being wrapped up using sandwich structure.
Hot-rolled temperature selection α+γ two-phase sections stage casing, such as temperature range 2 of accompanying drawing 1.The present embodiment chooses 1250 DEG C, is incubated 1h
Open rolling afterwards.Heating is melted down after every time rolling, 20~30min of soaking time, draught per pass 20~30%, judgement of speed change is melted down
Rate is controlled in 1~5s-1, melted down after 5 passages of rolling and be cooled to 900 DEG C, it is air cooled to room temperature after insulation 1h.Removed using machine-tooled method
Sheath material, obtains TiAl alloy rolled plate.Surface quality is good, without cracking.Its microscopic structure is uniform tiny bifurcation
Shown in tissue, such as accompanying drawing 2 (b).Sheet material has room temperature strength and good temperature-room type plasticity higher, as shown in Figure 3.950
~1100 DEG C, strain rate 2 × 10-4~5 × 10-4s-1Under the conditions of sheet material there is good superplastic deformation ability.
Embodiment 3
By taking high Nb containing TiAl based alloy as an example, alloy nominal composition is Ti-45Al-8.5Nb (atomic percent), through plasma
Cold hearth melting is made alloy pig.Hot rolling blank is directly cut from alloy pig.The hot rolling blank for cutting, is made with 304 stainless steels
It is jacket, is welded after being wrapped up using sandwich structure.
Hot-rolled temperature selects α+γ two-phase section epimeres, such as temperature range 3 of accompanying drawing 1.The present embodiment chooses 1300 DEG C, is incubated 1h
Open rolling afterwards.Heating is melted down after every time rolling, 20~30min of soaking time, draught per pass 20~30%, judgement of speed change is melted down
Rate is controlled in 1~5s-1, melted down after 5 passages of rolling and be cooled to 900 DEG C, it is air cooled to room temperature after insulation 1h.Removed using machine-tooled method
Sheath material obtains TiAl alloy rolled plate, and surface quality is good, without cracking.Its microscopic structure is uniform tiny nearly lamella
Shown in tissue, such as accompanying drawing 2 (c).Sheet material has room temperature strength and good temperature-room type plasticity higher, as shown in Figure 3.Sheet material has
There is excellent elevated temperature strength, tensile strength is more than 850MPa at 800 DEG C.
Embodiment 4
By taking high Nb containing TiAl based alloy as an example, alloy nominal composition is Ti-45Al-8.5Nb (atomic percent), through plasma
Cold hearth melting is made alloy pig.Hot rolling blank is directly cut from alloy cast ingot.The hot rolling blank for cutting, uses 304 stainless steels
As jacket, welded after being wrapped up using sandwich structure.
Hot-rolled temperature is selected more than α transition temperatures, such as the temperature range 4 of accompanying drawing 1.The present embodiment chooses 1320 DEG C, insulation
Open rolling after 1h.Heating is melted down after every time rolling, 20~30min of soaking time, draught per pass 20~30%, strain is melted down
Speed control is in 1~5s-1, melted down after 5 passages of rolling and be cooled to 900 DEG C, it is air cooled to room temperature after insulation 1h.Gone using machine-tooled method
Except sheath material, TiAl alloy rolled plate is obtained, surface quality is good, without cracking.Its microscopic structure is uniform tiny complete
Lamellar structure, lamella group average-size is less than 100 μm, such as shown in accompanying drawing 2 (d).Sheet material has excellent elevated temperature strength, 800 DEG C
When tensile strength more than 850MPa.
Claims (4)
1. it is a kind of to deform TiAl alloy structure property accuracy control method, it is characterised in that directly by TiAl alloy blank heating extremely
Different deformation temperatures, insulation carries out thermal deformation processing after a period of time；By controlling heat distortion temperature, obtain nearly γ, bifurcation,
Nearly lamella and the typical TiAl alloy microscopic structure of four kinds of full sheet layer, and then obtain the TiAl alloy deformable member of different mechanical properties.
2. it is a kind of as claimed in claim 1 to deform TiAl alloy structure property accuracy control method, it is characterised in that specific step
Suddenly it is：In α+γ two-phase sections lower end thermal deformations, Te≤ deformation temperature ＜ Te+1/3(Tα-Te), nearly γ tissues are obtained after thermal deformation；
In α+γ two-phase sections stage casing thermal deformations (Te+1/3(Tα-Te)≤deformation temperature ＜ Te+2/3(Tα-Te)), obtain by γ crystal grain and
α2The bifurcation tissue of/γ lamellas composition；In α+γ two-phase section epimere thermal deformations (Te+2/3(Tα-Te)≤deformation temperature ＜ Tα), obtain
Obtain α2The NL tissues of/γ lamellas and a small amount of equiaxial γ crystal grain composition；In α transition temperature above thermal deformations (Tα≤ deformation temperature ＜ Tα
+ (30~50) DEG C), obtain α2/ γ complete lamellar structures；Wherein TeIt is α → α2The eutectoid temperature of+γ, TαIt is into α monophase fields
Temperature.
3. it is a kind of as claimed in claim 1 or 2 to deform TiAl alloy structure property accuracy control method, it is characterised in that controlling party
Method is applied to using metallurgy ingot casting method, TiAl alloy structure property in precise control hot procedure, while being also applied for utilizing
Powder metallurgic method, TiAl alloy structure property in precise control hot procedure；Wherein hot-working method include forging, extruding,
The operation of rolling.
4. it is a kind of as claimed in claim 1 or 2 to deform TiAl alloy structure property accuracy control method, it is characterised in that described
TiAl alloy is Beta coagulating types TiAl alloy and Alpha coagulating type TiAl alloys；Beta coagulating type TiAl alloys are：Ti-
(43-45)Al-(2-9)Nb-(0-6)(Mn,Cr,Mo,V)-(0-0.4)(B,C)；Alpha coagulating type TiAl alloys are：Ti-
(45-48)Al-(0-7)Nb-(0-4)(Cr,Mn)-(0-0.4)(B,C)。
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN108856708A (en) * | 2017-05-09 | 2018-11-23 | 中国航空制造技术研究院 | A kind of TiAl based material and its manufacturing method with gradient structure |
| CN111975003A (en) * | 2020-08-14 | 2020-11-24 | 西北工业大学 | Method for regulating and controlling titanium-aluminum alloy full lamellar structure |
| CN112048690A (en) * | 2020-07-30 | 2020-12-08 | 西北工业大学 | Thermomechanical treatment method for controlling TiAl alloy fine grain structure |
| CN115386780A (en) * | 2022-09-13 | 2022-11-25 | 南京工业大学 | Light high-strength high-toughness Gao Shangchao alloy and preparation method thereof |
| CN116590637A (en) * | 2023-04-21 | 2023-08-15 | 武汉理工大学 | Method for improving tissue performance of cast TiAl alloy |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108856708A (en) * | 2017-05-09 | 2018-11-23 | 中国航空制造技术研究院 | A kind of TiAl based material and its manufacturing method with gradient structure |
| CN112048690A (en) * | 2020-07-30 | 2020-12-08 | 西北工业大学 | Thermomechanical treatment method for controlling TiAl alloy fine grain structure |
| CN112048690B (en) * | 2020-07-30 | 2021-12-17 | 西北工业大学 | Thermomechanical treatment method for controlling TiAl alloy fine grain structure |
| CN111975003A (en) * | 2020-08-14 | 2020-11-24 | 西北工业大学 | Method for regulating and controlling titanium-aluminum alloy full lamellar structure |
| CN115386780A (en) * | 2022-09-13 | 2022-11-25 | 南京工业大学 | Light high-strength high-toughness Gao Shangchao alloy and preparation method thereof |
| CN116590637A (en) * | 2023-04-21 | 2023-08-15 | 武汉理工大学 | Method for improving tissue performance of cast TiAl alloy |
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