CN109234656A - A kind of predeformation heat treatment process improving metastable β Titanium-alloy intensity - Google Patents
A kind of predeformation heat treatment process improving metastable β Titanium-alloy intensity 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
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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
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Abstract
The invention discloses a kind of predeformation heat treatment process for improving metastable β Titanium-alloy intensity, are related to titanium alloy material hot-working and technical field of heat treatment.Include: (1) heat treatment in advance: forging state metastable β Titanium-alloy is heated to Tβ0.5~6h of above 0~100 DEG C of heat preservation；(2) predeformation: by above-mentioned metastable β Titanium-alloy in TβBelow~200 DEG C to TβAbove 100 DEG C of 0.2~6h of inside holding, then carry out rolling thermal deformation；(3) direct aging is handled: above-mentioned metastable β Titanium-alloy being heated to 400~600 DEG C, keeps the temperature 4~12h.The present invention passes through rolling thermal deformation and direct aging process of thermal treatment, can in Effective Regulation alloy microstructure α phase precipitation, and Deformation structure is sufficiently replied, to make metastable β Titanium-alloy under the premise of maintaining its excellent plasticity, its intensity is increased substantially, realizes the matched well between intensity and plasticity.
Description
Technical field
The invention discloses a kind of predeformation heat treatment process of metastable β Titanium-alloy, are related to titanium alloy material hot-working
And technical field of heat treatment.
Background technique
Metastable β Titanium-alloy has the characteristics that specific strength height, excellent forming property, deep harden ability, especially with alpha+beta two
Phase titanium alloy is compared, and intensity is higher, can achieve 1200MPa or more after being suitably heat-treated, therefore navigate in aviation
Its field using more and more extensive.
It is single β phase when metastable β Titanium-alloy high temperature, when being cooled to alpha+beta two-phase section, α phase will be precipitated from β matrix.α phase
As main hardening constituent, size, pattern, distribution and volume fraction play the mechanical property of metastable β Titanium-alloy extremely heavy
The effect wanted.Currently, β → α phase transition process of metastable β Titanium-alloy is mainly controlled by heat treatment process, it is heat-treated by regulation
Technique can control the precipitation of α phase, so that obtaining the α phase of different content, size in β matrix, and then can obtain satisfaction and use
It is required that mechanical property.The main heat treatment process of metastable β Titanium-alloy is solid solution+ageing treatment, and general process is first in β
Monophase field keeps the temperature and is quenched to room temperature to obtain full β tissue, then in suitable temperature timeliness (generally at 400 DEG C to 600 DEG C) 4
~12 hours, so that α phase is sufficiently precipitated in β matrix.
However, heat treatment has limitation to the promotion of metastable β Titanium-alloy mechanical property, i.e., heat treatment is adjusted anyway
Technique, mechanical property can not break through a certain maximum value.Therefore, the limiting value of metastable β Titanium-alloy mechanical property how is broken through
The problem intractable as current scientific worker and engineer.Solve this problem, break-through point still with β → α phase transition process,
As long as more α phases are precipitated in β matrix, the mechanical property of metastable β Titanium-alloy will be promoted.Based on solid-state phase changes theory, phase
The driving force of change can not only to there is degree of supercooling to provide, the defects of dislocation, crystal boundary at the energy that stores can also serve as driving
Power, when phase transformation occurs in fault location, the energy that can discharge storage promotes the generation of phase transformation in turn.For metastable β Titanium-alloy, heat
Deformation can effectively promote the defect content of matrix, and then will affect the precipitation of the α phase in follow-up heat treatment process.And then it can
Further to regulate and control the mechanical property of metastable β Titanium-alloy.But by predeformation and heat treatment process in conjunction with regulating and controlling metastable β titanium
The mechanical property difficulty of alloy is larger, and predeformation parameter and solid-solution and aging heat treatment technological parameter can generate final result
Larger impact will be unable to play strengthening effect, or even can alloy property be deteriorated if parameter selection is improper.For example open tiger etc.
People's (Zhang Hu, influence of the heat treatment process to novel high-strength beta-titanium alloy tissue and performance, master thesis, 2013) is to one kind
The predeformation direct aging heat treatment process of novel metastable β Titanium-alloy is studied, but since the deflection of predeformation is inadequate,
β crystal grain is simultaneously not apparent from along rolling to elongation, is also showed the shaft-like such as approximation, so that matrix defect is less, is caused final predeformation straight
The intensity for connecing alloy after aging strengthening model is not above the intensity of alloy after traditional solution aging strengthening model, does not play reinforcing effect
Fruit.Therefore, the best match of predeformation parameter and solid-solution and aging heat treatment technological parameter how is obtained, to improve alloy force
Learning performance is technological difficulties.
Summary of the invention
For the defect for solving strength degree existing for prior art traditional solution+aging thermal treating process, mesh of the invention
Be a kind of predeformation heat treatment process for improving metastable β Titanium-alloy intensity is provided, the present invention can greatly improve metastable β titanium
The intensity of alloy and the available maintenance of its plasticity.
The present invention relates to a kind of predeformation heat treatment process for improving metastable β Titanium-alloy intensity, include the following steps:
(1) heat treatment in advance: after forging state metastable β Titanium-alloy heating and thermal insulation, it is quenched to room temperature, after obtaining heat treatment in advance
Metastable β Titanium-alloy；
(2) predeformation: metastable β Titanium-alloy after above-mentioned heat treatment in advance is subjected to the pre-heat treatment, then using milling train to Asia
Steady beta-titanium alloy carries out rolling thermal deformation, is then quenched to room temperature；
(3) direct aging is heat-treated: the metastable β Titanium-alloy heating and thermal insulation after above-mentioned predeformation then cools to room temperature.
Specifically, the microscopic structure that state metastable β Titanium-alloy is forged described in step (1) is made of β phase matrix and secondaryαphase；
The microscopic structure of metastable β Titanium-alloy is single-phase β phase equiaxed grain structure after the heat treatment in advance.
Preferably, the temperature of heating described in step (1) is in β phase transition temperature TβAbove 0~100 DEG C, soaking time is
0.5~6h.
Preferably, the pre-heat treatment described in step (2) is specially in β phase transition temperature Tβ200 DEG C to T belowβMore than
100 DEG C of 0.2~6h of range inside holding.
Preferably, rolling thermal deformation described in step (2) is multi- pass rolling；The milling train is strip-mill strip or rolled bar
Machine, total rolling deformation amount are controlled 50%~99%.
Preferably, the temperature of heating described in step (3) is 400~600 DEG C, and the time of the heat preservation is 4~12h.
Compared with prior art, the beneficial effects of the present invention are:
(1) heat treatment in advance is in TβRoom temperature is quenched to after 0.5~6h of above 0~100 DEG C of heat preservation to guarantee that it is single that matrix obtains
Phase β phase equiaxed grain structure；
(2) control of rolling heat distortion temperature is in Tβ200 DEG C to T belowβWithin the scope of above 100 DEG C, total deformation control exists
50%~99%, so that single-phase β phase equiaxed grain structure crystal grain in thermal deformation process that (1) step obtains is elongated, in matrix
It forms a large amount of sub boundary and concurrently gives birth to dynamic recrystallization, with single-phase equiaxed grain structure phase transformation, defect volume in β matrix after thermal deformation
Score is greatly improved；
(3) by the metastable β Titanium-alloy after rolling thermal deformation in 400~600 DEG C of progress direct aging processing, aging time is
4~12h, in ag(e)ing process, α phase can the sub boundary and crystal boundary the defects of at direct forming core and grow up, due to defect in matrix
Content is very big, therefore the content for the α phase being precipitated will be much larger than traditional solution+aging strengthening model, so as to greatly improve metastable β
The intensity of titanium alloy, simultaneously as 400~600 DEG C of aging temp are higher than metastable β Titanium-alloy recovery temperature, therefore thermal deformation group
Knitting can sufficiently be replied in ag(e)ing process, thus the available maintenance of its plasticity.
(4) present invention process simple and stable, easy to operate, process cycle is short, low energy consumption, be suitable for industrialized production.
In conclusion compared with traditional solution aging technique, the present invention by comprehensively consider rolling thermal deformation and it is direct when
Imitate the influence of heat treatment process alloy structure and performance, can in Effective Regulation alloy microstructure α phase precipitation, and to become
Shape tissue is sufficiently replied, to make metastable β Titanium-alloy under the premise of maintaining its excellent plasticity, it is strong to increase substantially it
Degree realizes the matched well between intensity and plasticity.
Detailed description of the invention
Fig. 1 is light microscopic micro-organization chart after the heat treatment of 4 predeformation direct aging of the embodiment of the present invention；
Fig. 2 is light microscopic micro-organization chart after 4 predeformation solid-solution and aging heat treatment of comparative example of the present invention.
Specific embodiment
The present invention will be described in further detail with reference to the accompanying drawings and examples.
Embodiment 1
Using the present invention to TB8 metastable β Titanium-alloy (its Tβ=810 DEG C) carry out predeformation direct aging heat treatment process:
(1) TB8 metastable β Titanium-alloy to be heated carries out heat treatment in advance, the heat treatment of heat treatment in advance in β phase monophase field
System is quenched to room temperature after being 900 DEG C of heat preservation 4h；TB8 metastable β Titanium-alloy microscopic structure is that single-phase β phase is isometric after heat treatment in advance
Crystalline substance tissue；
(2) use milling train to TB8 titanium alloy after 860 DEG C of heat preservation 0.5h the TB8 metastable β Titanium-alloy after heat treatment in advance
Multi- pass rolling thermal deformation is carried out, total deformation 20% is then quenched to room temperature, and single-phase β phase deforms smaller, base after hot rolling
This such as also shows at shaft-like；
(3) the TB8 titanium alloy after hot rolling deformation is heated to 540 DEG C of aging temp, is air-cooled to room temperature after keeping the temperature 8h.
In the present embodiment, the room-temperature mechanical property parameter of TB8 metastable β Titanium-alloy after predeformation+direct aging heat treatment
It is shown in Table 1.
Embodiment 2
Using the present invention to TB8 metastable β Titanium-alloy (its Tβ=810 DEG C) carry out predeformation direct aging heat treatment process:
(1) TB8 metastable β Titanium-alloy to be heated carries out heat treatment in advance, the heat treatment of heat treatment in advance in β phase monophase field
System is quenched to room temperature after being 900 DEG C of heat preservation 4h；
(2) use milling train to TB8 titanium alloy after 860 DEG C of heat preservation 0.5h the TB8 metastable β Titanium-alloy after heat treatment in advance
Multi- pass rolling thermal deformation is carried out, total deformation 40% is then quenched to room temperature；
(3) the TB8 titanium alloy after hot rolling deformation is heated to 540 DEG C of aging temp, is air-cooled to room temperature after keeping the temperature 8h.
In the present embodiment, the room-temperature mechanical property parameter of TB8 metastable β Titanium-alloy after predeformation+direct aging heat treatment
It is shown in Table 1.
Embodiment 3
Using the present invention to TB8 metastable β Titanium-alloy (its Tβ=810 DEG C) carry out predeformation direct aging heat treatment process:
(1) TB8 metastable β Titanium-alloy to be heated carries out heat treatment in advance, the heat treatment of heat treatment in advance in β phase monophase field
System is quenched to room temperature after being 900 DEG C of heat preservation 4h；
(2) use milling train to TB8 titanium alloy after 860 DEG C of heat preservation 0.5h the TB8 metastable β Titanium-alloy after heat treatment in advance
Multi- pass rolling thermal deformation is carried out, total deformation 50% is then quenched to room temperature；
(3) the TB8 titanium alloy after hot rolling deformation is heated to 540 DEG C of aging temp, is air-cooled to room temperature after keeping the temperature 8h.
In the present embodiment, the room-temperature mechanical property parameter of TB8 metastable β Titanium-alloy after predeformation+direct aging heat treatment
It is shown in Table 1.
Embodiment 4
Using the present invention to TB8 metastable β Titanium-alloy (its Tβ=810 DEG C) carry out predeformation direct aging heat treatment process:
(1) TB8 metastable β Titanium-alloy to be heated is at β phase monophase field progress heat treatment in advance, the heat of heat treatment in advance
Reason system is quenched to room temperature after being 900 DEG C of heat preservation 4h；
(2) use milling train to TB8 titanium alloy after 860 DEG C of heat preservation 0.5h the TB8 metastable β Titanium-alloy after heat treatment in advance
Multi- pass rolling thermal deformation is carried out, total deformation 75% is then quenched to room temperature；Single-phase β phase equiaxed grain structure after hot rolling
Along rolling to elongation, a large amount of sub boundaries are formed in matrix, and dynamic recrystallization (such as Fig. 1) occurs for part grain boundaries；
(3) the TB8 titanium alloy after hot rolling deformation is heated to 540 DEG C of aging temp, is air-cooled to room temperature after keeping the temperature 8h, it can be with
It was found that a large amount of α hand down, (such as Fig. 1) is precipitated in Grain and sub-grain boundary.
In the present embodiment, the room-temperature mechanical property parameter of TB8 metastable β Titanium-alloy after predeformation+direct aging heat treatment
It is shown in Table 1.
Embodiment 5
Using the present invention to TB8 metastable β Titanium-alloy (its Tβ=810 DEG C) carry out predeformation direct aging heat treatment process:
(1) TB8 metastable β Titanium-alloy to be heated carries out heat treatment in advance, the heat treatment of heat treatment in advance in β phase monophase field
System is quenched to room temperature after being 900 DEG C of heat preservation 4h；
(2) use milling train to TB8 titanium alloy after 860 DEG C of heat preservation 0.5h the TB8 metastable β Titanium-alloy after heat treatment in advance
Multi- pass rolling thermal deformation is carried out, total deformation 85% is then quenched to room temperature；
(3) the TB8 titanium alloy after hot rolling deformation is heated to 540 DEG C of aging temp, is air-cooled to room temperature after keeping the temperature 8h.
In the present embodiment, the room-temperature mechanical property parameter of TB8 metastable β Titanium-alloy after predeformation+direct aging heat treatment
It is shown in Table 1.
Embodiment 6
Using the present invention to TB8 metastable β Titanium-alloy (its Tβ=810 DEG C) carry out predeformation direct aging heat treatment process:
(1) TB8 metastable β Titanium-alloy to be heated carries out heat treatment in advance, the heat treatment of heat treatment in advance in β phase monophase field
System is quenched to room temperature after being 900 DEG C of heat preservation 4h；
(2) use milling train to TB8 titanium alloy after 860 DEG C of heat preservation 0.5h the TB8 metastable β Titanium-alloy after heat treatment in advance
Multi- pass rolling thermal deformation is carried out, total deformation 95% is then quenched to room temperature；
(3) the TB8 titanium alloy after hot rolling deformation is heated to 540 DEG C of aging temp, is air-cooled to room temperature after keeping the temperature 8h.
In the present embodiment, the room-temperature mechanical property parameter of TB8 metastable β Titanium-alloy after predeformation+direct aging heat treatment
It is shown in Table 1.
Comparative example 1
Using the present invention to TB8 metastable β Titanium-alloy (its Tβ=810 DEG C) it carries out carrying out being dissolved+timeliness heat after predeformation again
Treatment process:
(1) TB8 metastable β Titanium-alloy to be heated carries out heat treatment in advance, the heat treatment of heat treatment in advance in β phase monophase field
System is quenched to room temperature after being 900 DEG C of heat preservation 4h；
(2) use milling train to TB8 titanium alloy after 860 DEG C of heat preservation 0.5h the TB8 metastable β Titanium-alloy after heat treatment in advance
Multi- pass rolling thermal deformation is carried out, total deformation 20% is then quenched to room temperature；
(3) the TB8 titanium alloy after hot rolling deformation is carried out to traditional solid solution+aging strengthening model: being dissolved first at 860 DEG C
It is quenched to room temperature after 0.5h, is then heated to 540 DEG C of aging temp, is air-cooled to room temperature after keeping the temperature 8h.
In this comparative example, the room-temperature mechanical property parameter of TB8 metastable β Titanium-alloy is shown in after traditional solution+aging strengthening model
Table 1.
Comparative example 2
Using the present invention to TB8 metastable β Titanium-alloy (its Tβ=810 DEG C) it carries out carrying out being dissolved+timeliness heat after predeformation again
Treatment process:
(1) TB8 metastable β Titanium-alloy to be heated carries out heat treatment in advance, the heat treatment of heat treatment in advance in β phase monophase field
System is quenched to room temperature after being 900 DEG C of heat preservation 4h；
(2) use milling train to TB8 titanium alloy after 860 DEG C of heat preservation 0.5h the TB8 metastable β Titanium-alloy after heat treatment in advance
Multi- pass rolling thermal deformation is carried out, total deformation 40% is then quenched to room temperature；
(3) the TB8 titanium alloy after hot rolling deformation is carried out to traditional solid solution+aging strengthening model: being dissolved first at 860 DEG C
It is quenched to room temperature after 0.5h, is then heated to 540 DEG C of aging temp, is air-cooled to room temperature after keeping the temperature 8h.
In this comparative example, the room-temperature mechanical property parameter of TB8 metastable β Titanium-alloy is shown in after traditional solution+aging strengthening model
Table 1.
Comparative example 3
Using the present invention to TB8 metastable β Titanium-alloy (its Tβ=810 DEG C) it carries out carrying out being dissolved+timeliness heat after predeformation again
Treatment process:
(1) TB8 metastable β Titanium-alloy to be heated carries out heat treatment in advance, the heat treatment of heat treatment in advance in β phase monophase field
System is quenched to room temperature after being 900 DEG C of heat preservation 4h；
(2) use milling train to TB8 titanium alloy after 860 DEG C of heat preservation 0.5h the TB8 metastable β Titanium-alloy after heat treatment in advance
Multi- pass rolling thermal deformation is carried out, total deformation 50% is then quenched to room temperature；
(3) the TB8 titanium alloy after hot rolling deformation is carried out to traditional solid solution+aging strengthening model: being dissolved first at 860 DEG C
It is quenched to room temperature after 0.5h, is then heated to 540 DEG C of aging temp, is air-cooled to room temperature after keeping the temperature 8h.
In this comparative example, the room-temperature mechanical property parameter of TB8 metastable β Titanium-alloy is shown in after traditional solution+aging strengthening model
Table 1.
Comparative example 4
Using the present invention to TB8 metastable β Titanium-alloy (its Tβ=810 DEG C) it carries out carrying out being dissolved+timeliness heat after predeformation again
Treatment process:
(1) TB8 metastable β Titanium-alloy to be heated carries out heat treatment in advance, the heat treatment of heat treatment in advance in β phase monophase field
System is quenched to room temperature after being 900 DEG C of heat preservation 4h；
(2) use milling train to TB8 titanium alloy after 860 DEG C of heat preservation 0.5h the TB8 metastable β Titanium-alloy after heat treatment in advance
Multi- pass rolling thermal deformation is carried out, total deformation 75% is then quenched to room temperature；
(3) the TB8 titanium alloy after hot rolling deformation is carried out to traditional solid solution+aging strengthening model: being dissolved first at 860 DEG C
It is quenched to room temperature after 0.5h, is then heated to 540 DEG C of aging temp, is air-cooled to room temperature after keeping the temperature 8h.
As shown in Fig. 2, acicular α phase is unevenly precipitated in β equiax crystal matrix in TB8 titanium alloy ag(e)ing process, it is precipitated
Amount is less than predeformation direct aging heat treatment process (such as Fig. 1).
In this comparative example, the room-temperature mechanical property parameter of TB8 metastable β Titanium-alloy is shown in after traditional solution+aging strengthening model
Table 1.
Comparative example 5
Using the present invention to TB8 metastable β Titanium-alloy (its Tβ=810 DEG C) it carries out carrying out being dissolved+timeliness heat after predeformation again
Treatment process:
(1) TB8 metastable β Titanium-alloy to be heated carries out heat treatment in advance, the heat treatment of heat treatment in advance in β phase monophase field
System is quenched to room temperature after being 900 DEG C of heat preservation 4h；
(2) use milling train to TB8 titanium alloy after 860 DEG C of heat preservation 0.5h the TB8 metastable β Titanium-alloy after heat treatment in advance
Multi- pass rolling thermal deformation is carried out, total deformation 85% is then quenched to room temperature；
(3) the TB8 titanium alloy after hot rolling deformation is carried out to traditional solid solution+aging strengthening model: being dissolved first at 860 DEG C
It is quenched to room temperature after 0.5h, is then heated to 540 DEG C of aging temp, is air-cooled to room temperature after keeping the temperature 8h.
In this comparative example, the room-temperature mechanical property parameter of TB8 metastable β Titanium-alloy is shown in after traditional solution+aging strengthening model
Table 1.
Comparative example 6
Using the present invention to TB8 metastable β Titanium-alloy (its Tβ=810 DEG C) it carries out carrying out being dissolved+timeliness heat after predeformation again
Treatment process:
(1) TB8 metastable β Titanium-alloy to be heated carries out heat treatment in advance, the heat treatment of heat treatment in advance in β phase monophase field
System is quenched to room temperature after being 900 DEG C of heat preservation 4h；
(2) use milling train to TB8 titanium alloy after 860 DEG C of heat preservation 0.5h the TB8 metastable β Titanium-alloy after heat treatment in advance
Multi- pass rolling thermal deformation is carried out, total deformation 95% is then quenched to room temperature.
(3) the TB8 titanium alloy after hot rolling deformation is carried out to traditional solid solution+aging strengthening model: being dissolved first at 860 DEG C
It is quenched to room temperature after 0.5h, is then heated to 540 DEG C of aging temp, is air-cooled to room temperature after keeping the temperature 8h.
In this comparative example, the room-temperature mechanical property parameter of TB8 metastable β Titanium-alloy is shown in after traditional solution+aging strengthening model
Table 1.
Table 1
(1) by table 1 it can be found that the intensity of TB8 metastable β Titanium-alloy is wanted after direct aging heat treatment after larger predeformation
Than about 50~200MPa high after solid solution+aging strengthening model after traditional predeformation, plasticity is consistent (3~6 He of embodiment substantially
Comparative example 3~6).The above result shows that the predeformation heat treatment process of metastable β Titanium-alloy of the invention will be substantially better than tradition admittedly
Molten+aging thermal treating process can break through metastable β Titanium-alloy strength degree itself.
(2) in addition it can be found that the deflection of predeformation is to the intensity of direct aging treated TB8 metastable β Titanium-alloy
It is affected, the above results show that deflection is bigger, and the intensity of TB8 metastable β Titanium-alloy is bigger (Examples 1 to 6)；Become when pre-
When the deflection of shape only has 20% and 40% (< 50%), direct aging heat treatment after alloy intensity (Examples 1 to 2) not
Higher than the intensity (comparative example 1~2) of alloy after traditional solution+aging strengthening model, this is because after hot rolling single-phase β phase deform compared with
It is small, the shaft-like such as also show substantially, so that matrix defect is less, so that the α phase volume fraction being precipitated in ag(e)ing process is not shown
It writes and increases, the intensity of alloy can not be improved, or even have part reduction, further illustrate predeformation parameter and heat treatment process ginseng
Several matchings is to improve the important factor in order of alloy mechanical property.
The above is only present pre-ferred embodiments, not does any restrictions to the present invention.It is all according to inventive technique
Essence any simple modification, change and equivalence change made to the above embodiment, still fall within technical solution of the present invention
Protection scope in.
Claims (6)
1. a kind of predeformation heat treatment process for improving metastable β Titanium-alloy intensity, it is characterised in that include the following steps:
(1) heat treatment in advance: after forging state metastable β Titanium-alloy heating and thermal insulation, being quenched to room temperature, obtains metastable after heat treatment in advance
Beta-titanium alloy；
(2) predeformation: metastable β Titanium-alloy after above-mentioned heat treatment in advance is subjected to the pre-heat treatment, then using milling train to metastable β titanium
Alloy carries out rolling thermal deformation, is then quenched to room temperature；
(3) direct aging is heat-treated: the metastable β Titanium-alloy heating and thermal insulation after above-mentioned predeformation then cools to room temperature.
2. a kind of predeformation heat treatment process for improving metastable β Titanium-alloy intensity according to claim 1, feature exist
In the microscopic structure for forging state metastable β Titanium-alloy described in step (1) is made of β phase matrix and secondaryαphase；At the preparatory heat
The microscopic structure of metastable β Titanium-alloy is single-phase β phase equiaxed grain structure after reason.
3. a kind of predeformation heat treatment process for improving metastable β Titanium-alloy intensity according to claim 1, feature exist
In the temperature of heating described in step (1) is in β phase transition temperature TβAbove 0~100 DEG C, soaking time is 0.5~6h.
4. a kind of predeformation heat treatment process for improving metastable β Titanium-alloy intensity according to claim 1, feature exist
In the pre-heat treatment described in step (2) is specially in β phase transition temperature Tβ200 DEG C to T belowβIt is protected within the scope of above 100 DEG C
0.2~6h of temperature.
5. a kind of predeformation heat treatment process for improving metastable β Titanium-alloy intensity according to claim 1, feature exist
In rolling thermal deformation described in step (2) is multi- pass rolling；The milling train is strip-mill strip or bar mill, and total rolls
Deformation quantity control processed is 50%~99%.
6. a kind of predeformation heat treatment process for improving metastable β Titanium-alloy intensity according to claim 1, feature exist
In the temperature of heating described in step (3) is 400~600 DEG C, and the time of the heat preservation is 4~12h.
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| CN113278902A (en) * | 2021-05-25 | 2021-08-20 | 西北有色金属研究院 | Performance regulation and control method of large-size TB9 titanium alloy wire |
| CN113385671A (en) * | 2021-06-18 | 2021-09-14 | 湖南大学 | High-toughness low-modulus titanium/beta-titanium alloy multilayer composite material and preparation method thereof |
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| CN115786832B (en) * | 2022-10-31 | 2024-04-26 | 西安交通大学 | Method for improving high Jiang Yawen beta titanium alloy strong plasticity matching and titanium alloy |
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