CN108468007A - Improve the method for beta type gamma-TiAl alloy hot-working character - Google Patents
Improve the method for beta type gamma-TiAl alloy hot-working character Download PDFInfo
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- CN108468007A CN108468007A CN201810262144.2A CN201810262144A CN108468007A CN 108468007 A CN108468007 A CN 108468007A CN 201810262144 A CN201810262144 A CN 201810262144A CN 108468007 A CN108468007 A CN 108468007A
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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
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
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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
- C22F1/008—Using a protective surface layer
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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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Abstract
The invention discloses a kind of methods improving β type γ TiAl alloy hot-working characters, and the content of β type γ TiAl alloy high temperature Plastic phase β phases is improved by hot stressing technology, and low-alloyed specific strength drops in the density without increasing alloy；After alloy sets hydrogen processing, resistance of deformation reduces and ductility improves, and helps to improve die life, and then improve Alloy Forming precision, while energy saving.In turn, then in a vacuum furnace heating and thermal insulation 4~6 hours, can be further reduced the extra β phases introduced by hydrogen in alloy, to improve the creep-resistant property and temperature-room type plasticity of alloy.
Description
Technical field
The present invention relates to a kind of methods improving beta type gamma-TiAl alloy hot-working character.
Background technology
TiAl alloy density is low, specific strength is high, specific stiffness is high, elasticity modulus is high, and has high Properties of High Temperature Creep
And oxidation resistance, therefore be considered as most potential one of high-temperature structural material.Aerospace engine is TiAl alloy
Important application field.It is closed currently, aerospace engine high-temperature structure member mostly uses Ni-based or other highdensity high temperature
Gold, and it is the weight for improving engine thrust-weight ratio, and then improving engine performance to replace these heavy alloys using alloy in lightweight
Want approach.
For TiAl alloy compared with now widely used nickel base superalloy, one of most important advantage is TiAl alloy
Density is low, only the half or so of nickel base superalloy.But TiAl alloy pyroplastic deformability's ability is relatively low, hot-workability
Poor, higher production and processing cost limits the application of TiAl alloy material.
Improving one of the method for plasticity of TiAl alloy at present is, by the way that the members such as Mo, V, Nb, Cr, Ta are added into alloy
Element is to obtain more high-temp plastic phase β phases.But the density of Mo, V, Nb, Cr, Ta metal and the density of high-temperature nickel-base alloy connect
Close even higher, these elements are added in TiAl alloy undoubtedly can increase the density of alloy.And the introducing of β phases will weaken material
The croop property of itself, and the B2 phases that β phase low-temperature stabilizations are mutually ordered into, B2 phases are brittlement phase at low temperature, to temperature-room type plasticity
It can adversely affect.How in the case where not increasing existing TiAl alloy density, reducing creep-resistant property and temperature-room type plasticity,
It is current urgent problem to be solved to improve its hot-working character.
Hot stressing technology can effectively improve the content of β phases in TiAl, to reduce high density β phase stable elements
It is added, and the content of β phases can be efficiently reduced after vacuum dehydrogenation and homogenization heat treatment, so the technology is improving TiAl conjunctions
The density of alloy will not be increased while golden hot-working character again, reduce creep-resistant property and temperature-room type plasticity.
Hot stressing technology provides a good approach to improve TiAl alloy hot-working character.Hot stressing technology exists
It has been applied in the forging and molding of titanium alloy, the β phases in the beta type gamma-TiAl alloy based on hot stressing technology are in high temperature
Under be Plastic phase, help to improve pyroplastic deformability's ability of alloy, the low-alloyed creep-resistant property of drop but β meets, and
And be at low temperature brittlement phase, low-alloyed plasticity can be dropped, therefore, how to reduce the content of β phases, to solution never increase it is existing
TiAl alloy density, the problem of reducing creep-resistant property and improving alloy hot-working character while temperature-room type plasticity, be need into
The direction of one step research.
Invention content
The purpose of the present invention is to provide a kind of methods improving beta type gamma-TiAl alloy hot-working character, to not increase
Under conditions of adding existing beta type gamma-TiAl alloy density, reduction creep-resistant property and temperature-room type plasticity, improve its hot-working character.
Embodiment according to the present invention, provide it is a kind of improve beta type gamma-TiAl alloy hot-working character method, including with
Lower step：
1) beta type gamma-TiAl alloy blank surface oxide layer is removed, workpiece is denoted as；
2) workpiece feeding is set into hydrogen stove；
3) opposed hydrogen stove evacuation, and then it is filled with protection gas, then opposed hydrogen stove heat, 700 are increased in in-furnace temperature
After~800 DEG C, it is flushed with hydrogen gas, hydrogen partial pressure is 0.05~0.15MPa, keeps the temperature 2~4 hours, workpiece obtains hydrogen with room temperature is furnace-cooled to
The beta type gamma-TiAl alloy that weight percent is 0.02~0.05%, is denoted as and sets hydrogen alloy；
4) hydrogen alloy surface spraying antioxidant is being set, then opposed hydrogen alloy is preheated to deformation temperature, and keeps the temperature 1~2
Hour；
5) compression step 4 on a given direction) set hydrogen alloy after preheating, set hydrogen alloy in said direction
Total deformation is 50~63%；
6) the compressed hydrogen alloy of setting obtained by step 5) is cooled to room temperature, and the antioxidant on hydrogen alloy is set in removal, into
And will set in hydrogen alloy merging vacuum drying oven, 700~800 DEG C are heated to, after heat preservation 4~6 hours, with being furnace-cooled to room temperature；
7) the hydrogen alloy of setting that step 6) obtains under 1300~1350 DEG C of temperature condition is subjected to homogenization heat treatment, obtained
Beta type gamma-TiAl alloy to after final improve.
The method of above-mentioned improvement beta type gamma-TiAl alloy hot-working character, optionally, the homogenization heat treatment in step 7)
When need to carry out under protective atmosphere, the soaking time under heat treatment condition and the volume positive correlation for setting hydrogen alloy, and
Soaking time is no less than 10 minutes.
Optionally, the direction in step 5) is vertical.
Optionally, the compression strain rate in step 5) in given directions is 0.01~0.05s-1.
Optionally, it after the completion of the deformation of hydrogen compression of metals is set in step 5), need to be protected in 1100~1250 DEG C of temperature ranges
Furnace cooling after temperature 1~2 hour.
Optionally, it is 0.037% to set hydrogen amount as weight percent of the hydrogen in setting hydrogen alloy.
Optionally, the deformation temperature is 1050~1200 DEG C.
Optionally, the method for beta type gamma-TiAl alloy blank surface oxide layer being removed in step 1) is using mechanical polishing work
Skill disposes oxide layer, and then cleans and dry by acetone.
Optionally, the temperature of homogenization heat treatment is 1335 DEG C in step 7), and 15~20 points are kept the temperature under this temperature condition
Clock.
Optionally, the temperature in step 6) in a vacuum furnace is 700 DEG C.
Embodiment according to the present invention, the method for improving beta type gamma-TiAl alloy hot-working character provided, leads to
The content that hydrogen treatment technology improves beta type gamma-TiAl alloy high temperature Plastic phase β phases is overheated, the density without increasing alloy, drop
Low-alloyed specific strength；After alloy sets hydrogen processing, resistance of deformation reduces and ductility improves, and helps to improve the mold longevity
Life, and then Alloy Forming precision is improved, and meanwhile it is energy saving.In turn, then in a vacuum furnace heating and thermal insulation 4~6 hours, Ke Yijin
One step reduces the extra β phases introduced by hydrogen in alloy, to improve the creep-resistant property and temperature-room type plasticity of alloy.
Description of the drawings
Fig. 1
Specific implementation mode
Embodiment 1：
The present embodiment improves beta type gamma-TiAl alloy hot-working character according to for improvement, using following processing step, with to β
Type gamma-TiAl alloy is handled：
1) surface of beta type gamma-TiAl alloy blank is machined out, to remove the oxide layer of blank surface, so that it is right
The blank for disposing oxide layer is cleaned using acetone, and dry.
2) beta type gamma-TiAl alloy blank is placed on tubular type to set in hydrogen stove, is then vacuumized, vacuum degree reaches 10 in stove- 3Pa ranks, then applying argon gas, as protective gas.
3) tubular type sets hydrogen stove in-furnace temperature and is increased to 700~800 DEG C, is flushed with hydrogen gas, and hydrogen partial pressure 0.05-0.15MPa is protected
Temperature 2~4 hours, blank is furnace-cooled to room temperature, finally obtains the beta type gamma-TiAl alloy that hydrogen weight percent is 0.02~0.05%,
It is denoted as and sets hydrogen alloy.
4) hydrogen Alloy surface spraying high-temperature anti-oxidant is being set, TiAl alloy high-temperature anti-oxidant is using Beijing
It makes every effort to achieve the model SA-35 high-temperature alloy forging glass protecting lubricants of glass Science and Technology Development Co., Ltd. production, this kind
Protecting lubricant can be used as antioxidant.The technological temperature of high temperature adaptation subsequent process steps therein.
5) the hydrogen alloy of setting of the spraying plating of step 4) acquisition high-temperature anti-oxidant is sent into specified preheating furnace, opposed hydrogen
Alloy is preheated, and preheating temperature is 1100~1250 DEG C, after reaching preheating temperature, keeps the temperature 1~2 hour.
6) high temperature (under the conditions of preheating temperature) compression being carried out to the hydrogen alloy of setting after preheating, compression direction is single direction,
Such as it is vertical, compression strain rate is 0.01~0.05s-1, to be 50~63% (after being deformation in short transverse total deformation
The high accounting of shared original).
Wherein, compression strain rate, also known as high temperature compressed strain rate, essence stretching or compression speed divided by mark
Away from this is the conventional conception of this field, and details are not described herein.
7) furnace cooling after 1100~1250 DEG C of temperature range inside holdings 1~2 hour of hydrogen alloy is set after compressive deformation.
8) dehydrogenation step：Remove it is high temperature compressed after the high-temperature anti-oxidant for setting hydrogen alloy surface, then will set hydrogen alloy
It is placed in vacuum drying oven, vacuum drying oven keeps the temperature 4~6 hours after being warming up to 700~800 DEG C, then with being furnace-cooled to room temperature.
9) homogenization heat treatment being carried out in protective atmosphere to the beta type gamma-TiAl alloy after dehydrogenation, temperature is 1300~
1350 DEG C, soaking time is 10~30 minutes (depending on specific soaking time is by workpiece size, workpiece is bigger, and soaking time is longer),
Then with being furnace-cooled to room temperature.
It is mainly provided by inert gas about protective atmosphere, such as argon gas.
Tubular type above-mentioned sets the tubular type that hydrogen stove is Beijing Aviation manufacturing engineering Research Institute and sets hydrogen stove.
Vacuum dehydrogenation processing is carried out to alloy in step 8), makes hydrogen content control in safe range, it is true in vacuum drying oven
Reciprocal of duty cycle is controlled in 1Pa or less.
Setting hydrogen beta type gamma-TiAl alloy has better high-temp plastic and lower high temperature hot deformation resistance, die deformation and abrasion
Degree is small, and the required energy is reduced.
Embodiment 2：
0.037% protium is filled with by beta type gamma-TiAl alloy weight percent in the step 3) of the present embodiment；Step
5) it is 1150 DEG C that hydrogen beta type gamma-TiAl alloy preheating temperature is set in；Strain rate is 0.01s in step 6)-1；In step 9) uniformly
It is 1315 DEG C to change temperature；Other steps are same as Example 1.
Embodiment 3：
0.037% protium is filled with by beta type gamma-TiAl alloy weight percent in the step 3) of the present embodiment；Step
5) it is 1150 DEG C that hydrogen beta type gamma-TiAl alloy preheating temperature is set in；Strain rate is 0.01s in step 6)-1；In step 9) uniformly
It is 1320 DEG C to change temperature；Other steps are same as Example 1.
Embodiment 4：
0.037% protium is filled with by beta type gamma-TiAl alloy weight percent in the step 3) of the present embodiment；Step
5) it is 1150 DEG C that hydrogen beta type gamma-TiAl alloy preheating temperature is set in；Strain rate is 0.01s in step 6)-1；In step 9) uniformly
It is 1330 DEG C to change temperature；Other steps are same as Example 1.
Embodiment 5：
0.037% protium is filled with by beta type gamma-TiAl alloy weight percent in the step 3) of the present embodiment；Step
5) it is 1150 DEG C that hydrogen beta type gamma-TiAl alloy preheating temperature is set in；Strain rate is 0.01s in step 6)-1；In step 9) uniformly
It is 1340 DEG C to change temperature；Other steps are same as Example 1.
Embodiment 6：
0.037% protium is filled with by beta type gamma-TiAl alloy weight percent in the step 3) of the present embodiment；Step
5) it is 1200 DEG C that hydrogen beta type gamma-TiAl alloy preheating temperature is set in；Strain rate is 0.01s in step 6)-1；In step 9) uniformly
It is 1315 DEG C to change temperature；Other steps are same as Example 1.
Embodiment 7：
0.037% protium is filled with by beta type gamma-TiAl alloy weight percent in the step 3) of the present embodiment；Step
5) it is 1200 DEG C that hydrogen beta type gamma-TiAl alloy preheating temperature is set in；Strain rate is 0.01s in step 6)-1；In step 9) uniformly
It is 1320 DEG C to change temperature；Other steps are same as Example 1.
Embodiment 8：
0.037% protium is filled with by beta type gamma-TiAl alloy weight percent in the step 3) of present embodiment；Step
It is rapid 5) in set hydrogen beta type gamma-TiAl alloy preheating temperature be 1200 DEG C；Strain rate is 0.01s in step 5)-1；In step 9)
It is 1330 DEG C to homogenize temperature；Other steps are same as Example 1.
Embodiment 9：
0.037% protium is filled with by beta type gamma-TiAl alloy weight percent in the step 3) of the present embodiment；Step
5) it is 1200 DEG C that hydrogen beta type gamma-TiAl alloy preheating temperature is set in；Strain rate is 0.01s in step 6)-1；In step 9) uniformly
It is 1340 DEG C to change temperature；Other steps are same as Example 1.
Table 1 is the resistance of deformation size comparison for being flushed with hydrogen front and back beta type gamma-TiAl alloy
In addition, Fig. 1 shows alloy hot processing window when not being flushed with hydrogen, visible strain rate (compression strain when not being flushed with hydrogen in figure
Rate) it is even smaller, workpiece still will produce micro-crack.
Alloy hot processing window when being flushed with hydrogen that Fig. 2 is then shown, the process window of workpiece increased.
Claims (10)
1. a kind of method improving beta type gamma-TiAl alloy hot-working character, which is characterized in that include the following steps：
1) beta type gamma-TiAl alloy blank surface oxide layer is removed, workpiece is denoted as；
2) workpiece feeding is set into hydrogen stove；
3) opposed hydrogen stove evacuation, and then it is filled with protection gas, then opposed hydrogen stove heat, 700~800 are increased in in-furnace temperature
After DEG C, it is flushed with hydrogen gas, hydrogen partial pressure is 0.05~0.15MPa, keeps the temperature 2~4 hours, workpiece obtains hydrogen weight with room temperature is furnace-cooled to
The beta type gamma-TiAl alloy that percentage is 0.02~0.05%, is denoted as and sets hydrogen alloy；
4) hydrogen alloy surface spraying antioxidant is being set, then opposed hydrogen alloy is preheated to deformation temperature, and keeps the temperature 1~2 hour；
5) compression step 4 on a given direction) hydrogen alloy is set after preheating, set the total change of hydrogen alloy in said direction
Shape amount is 50~63%；
6) the compressed hydrogen alloy of setting obtained by step 5) is cooled to room temperature, and the antioxidant on hydrogen alloy is set in removal, and then will
It sets in hydrogen alloy merging vacuum drying oven, is heated to 700~800 DEG C, after heat preservation 4~6 hours, with being furnace-cooled to room temperature；
7) the hydrogen alloy of setting that step 6) obtains under 1300~1350 DEG C of temperature condition is subjected to homogenization heat treatment, obtained most
Beta type gamma-TiAl alloy after improving eventually.
2. the method according to claim 1 for improving beta type gamma-TiAl alloy hot-working character, which is characterized in that in step
7) it needs to carry out under protective atmosphere when homogenization heat treatment in, the soaking time under heat treatment condition and sets hydrogen alloy
Volume positive correlation, and soaking time is no less than 10 minutes.
3. the method according to claim 1 for improving beta type gamma-TiAl alloy hot-working character, which is characterized in that step 5)
In direction be vertical.
4. the method according to claim 1 or 3 for improving beta type gamma-TiAl alloy hot-working character, which is characterized in that step
It is rapid 5) in compression strain rate in given directions be 0.01~0.05s-1。
5. the method according to claim 4 for improving beta type gamma-TiAl alloy hot-working character, which is characterized in that in step
It 5), need to be in furnace cooling after 1100~1250 DEG C of temperature range inside holdings 1~2 hour after the completion of setting the deformation of hydrogen compression of metals in.
6. the method according to claim 1 for improving beta type gamma-TiAl alloy hot-working character, which is characterized in that set hydrogen amount
It is 0.037% for weight percent of the hydrogen in setting hydrogen alloy.
7. the method according to claim 1 for improving beta type gamma-TiAl alloy hot-working character, which is characterized in that the change
Shape temperature is 1050~1200 DEG C.
8. the method according to claim 1 for improving beta type gamma-TiAl alloy hot-working character, which is characterized in that step 1)
The middle method for removing beta type gamma-TiAl alloy blank surface oxide layer is to dispose oxide layer, Jin Ertong using mechanical polishing process
Acetone is crossed to clean and dry.
9. the method according to claim 1 for improving beta type gamma-TiAl alloy hot-working character, which is characterized in that step 7)
The temperature of middle homogenization heat treatment is 1335 DEG C, and 15~20 minutes are kept the temperature under this temperature condition.
10. the method according to claim 1 for improving beta type gamma-TiAl alloy hot-working character, which is characterized in that step
6) temperature in a vacuum furnace is 700 DEG C.
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Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0952238A1 (en) * | 1998-04-14 | 1999-10-27 | Hauzer Industries B.V. | Hard multilayer coating |
| CN101648254A (en) * | 2009-08-28 | 2010-02-17 | 哈尔滨工业大学 | Process for forging hydrogenated titanium alloy forging blade |
| CN101817143A (en) * | 2010-01-19 | 2010-09-01 | 哈尔滨工业大学 | Method for improving hot processing performance of TiAl alloy |
| US20130175772A1 (en) * | 2010-09-30 | 2013-07-11 | Technique Surface Lab Inc. | Ice skate blades and method for improving performances thereof |
| CN104308455A (en) * | 2014-08-13 | 2015-01-28 | 哈尔滨工业大学 | Method for improving forging properties of gamma-TiAl alloy through hydrogenation |
| CN104480347A (en) * | 2014-12-17 | 2015-04-01 | 南京理工大学 | TiAl-base alloy and heat treatment technique thereof |
| CN106702211A (en) * | 2016-12-30 | 2017-05-24 | 哈尔滨工业大学 | Method for optimizing beta-gamma TiAl alloy heat processing performance |
-
2018
- 2018-03-28 CN CN201810262144.2A patent/CN108468007A/en active Pending
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0952238A1 (en) * | 1998-04-14 | 1999-10-27 | Hauzer Industries B.V. | Hard multilayer coating |
| CN101648254A (en) * | 2009-08-28 | 2010-02-17 | 哈尔滨工业大学 | Process for forging hydrogenated titanium alloy forging blade |
| CN101817143A (en) * | 2010-01-19 | 2010-09-01 | 哈尔滨工业大学 | Method for improving hot processing performance of TiAl alloy |
| US20130175772A1 (en) * | 2010-09-30 | 2013-07-11 | Technique Surface Lab Inc. | Ice skate blades and method for improving performances thereof |
| CN104308455A (en) * | 2014-08-13 | 2015-01-28 | 哈尔滨工业大学 | Method for improving forging properties of gamma-TiAl alloy through hydrogenation |
| CN104480347A (en) * | 2014-12-17 | 2015-04-01 | 南京理工大学 | TiAl-base alloy and heat treatment technique thereof |
| CN106702211A (en) * | 2016-12-30 | 2017-05-24 | 哈尔滨工业大学 | Method for optimizing beta-gamma TiAl alloy heat processing performance |
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Application publication date: 20180831 |