CN110273118A - A kind of heat treatment process of titanium alloy - Google Patents
A kind of heat treatment process of titanium alloy Download PDFInfo
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- CN110273118A CN110273118A CN201910519014.7A CN201910519014A CN110273118A CN 110273118 A CN110273118 A CN 110273118A CN 201910519014 A CN201910519014 A CN 201910519014A CN 110273118 A CN110273118 A CN 110273118A
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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 heat treatment process of titanium alloy, belong to material science and technology field.Specifically include that first reheat handle heating temperature T be (Tβ‑50)℃≤T≤(Tβ+ 60) DEG C, soaking time t=η1*δmax, δmaxFor the maximum cross-section thickness of titanium alloy forging, η1For heating coefficient, value is 0.6~1.5min/mm, air-cooled, air-cooled, oil cooling or water cooling of coming out of the stove after forging heat preservation to room temperature；Second, which reheats, handles heating temperature T as 780 DEG C of 650 DEG C≤T <, soaking time t=(η2*δmax)/2, δmaxFor the maximum cross-section thickness of titanium alloy forging, η2For heating coefficient, value is 0.3~1.2min/mm, and forging comes out of the stove after keeping the temperature and is air-cooled to room temperature；It is 650 DEG C of 480 DEG C≤T < that third, which reheats and handles heating temperature T, and soaking time is 240min≤t≤600min, and forging comes out of the stove after keeping the temperature and is air-cooled to room temperature.The technique solves the problems, such as that forging edge and core structure performance difference are big after nearly β type, metastable β type and complete steady beta titanium alloy solid solution aging, particularly useful for making going out high intensity, structure property uniformly big section/variable cross-section titanium alloy forging.
Description
Technical field
The invention belongs to material science and technology fields, are related to a kind of heat treatment process of titanium alloy.
Background technique
Titanium or titanium alloy has the good characteristics such as specific strength height, high temperature resistant, corrosion-resistant, solderable, in aerospace, changes
The modern industries such as work, ocean and national defence have a wide range of applications, especially in aviation field, titanium alloy dosage and single-piece
Weight or projected area have become the one of the important signs that for measuring aircraft advance.
To cope with urgent need of the Advanced Aircraft of new generation to loss of weight, intensity and comprehensive performance to titanium alloy material are proposed
Requirement definitely, develops high tough or ultra-high strength and toughness titanium alloy material and application technology has become domestic and international material and grinds
The target that the person of studying carefully makes joint efforts, while being also the important symbol of titanium alloy material science and technology development.It is being point with phase composition
In the titanium alloy of class foundation, nearly β type and metastable beta titanium alloy are because having excellent heat treatment reinforcement effect, high harden ability, good
The characteristics such as good processing performance, optimum are used to develop and develop high tough or ultra-high strength and toughness titanium alloy.In high tough titanium alloy
Research aspect, with the Ti-15-3 (the corresponding trade mark in the country is TB5) of U.S.'s exploitation, Ti-1023 (the corresponding trade mark in the country is TB6), β
21s (the corresponding trade mark in the country is TB8), the BT22 (the corresponding trade mark in the country is TC18) of former Soviet Union's exploitation and its Ti- of Curve guide impeller
5553 and Ti-55531 etc. is that the titanium alloy of representative is most widely used.Such as in aerospace applications field, TB6 titanium alloy forging
The strength level of (thickness≤100mm) under the conditions of solid solution aging is in 1105MPa or more, and fracture toughness level is in 60MPam1/2
More than, strength level of the TC18 titanium alloy forging (thickness≤250mm) under the conditions of double annealing in 1080MPa~1230MPa,
Fracture toughness level is in 60MPam1/2More than.In terms of ultra-high strength and toughness titanium alloy research, the country is achieved considerable in recent years
Development, Beijing Research Inst. of Aeronautic Material develops the nearly β type TB17 titanium alloy with China's independent intellectual property right, the alloy forged piece
After solid-solution and aging heat treatment, there is high intensity-plasticity-toughness matching, can be used as the crucial load-carrying member of aviation, it can also
Space flight, weapons are civilian etc., fields are promoted and applied.
When designing and researching and developing new alloy, [Mo] Equivalent method has become the most generally accepted titanium alloy of science researcher and sets
Count instructional criterion.Current result of study shows when designing and developing high tough or ultra-high strength and toughness titanium alloy material, [Mo] when
Amount is selected near critical value mostly, and alloy has optimal heat treatment reinforcement effect when that is to say nearly β type and metastable β type, simultaneously
Also comprehensively consider influence of the alloying element to α phase and β phase, thus also brings the more of nearly β type and metastable beta titanium alloy phase transformation
Sample and complexity.Consider from strengthening mechanism, the second phase size, quantity and the pattern of β phase Precipitation determine alloy most
Whole intensity.Alloying component, treatment temperature and time, cooling rate etc. are to β phase base to be confirmed to the basic research of beta titanium alloy
Pattern, size, quantity and the distribution that the second phase is precipitated in body have an important influence on.For example, when at lower temperature (350 DEG C or so)
When ageing treatment, to be precipitated based on the ω phase of nanoscale, in the alloy system of Ti-Mo base, ω phase morphology is with ellipse
Based on, and in the alloy system of Ti-Cr base, ω phase morphology is based on rectangular, and even dispersion is distributed among matrix, closes
Gold shows as high-intensitive inductile.In higher temperature ageing treatment, to be precipitated based on the α phase of different scale, at this time α phase with
Matrix keeps Bai Gensi phase relation, and alloy strength reduces but plasticity is obviously improved.Meanwhile thermodynamics and dynamics research knot
Fruit further demonstrates that beta titanium alloy aging response is very fast, and the second phase forming core has reached second grade in β matrix, and grows therewith
Greatly.Just feature once was precipitated according to ω phase in researcher, and proposing with ω phase is α phase forerunner's phase, to obtain the α of micro-nano-scale
Mutually it is evenly distributed on the heat treatment mentality of designing of the microscopic structure on β matrix.The country also has researcher that spy is precipitated according to α phase
Point has devised to obtain multiple (grade) solid solution aging technique for the microscopic structure that there is multiple dimensioned α to mix.
Experience and research confirmation, nearly β type and metastable beta titanium alloy forging border region are constantly present aobvious with center portion region
Micro-assembly robot and mechanical property difference, though forging section thickness lower than the alloy can through hardening thickness it is similarly inevitable, and
This structure property difference becomes apparent with the increase performance of section thickness.The basic reason for causing this phenomenon is due to close
β type and metastable beta titanium alloy are sensitive to heat treatment parameter, and forging is when high-temperature heat treatment is cooling, forging border region and center portion
The temperature field in region and stress field otherness are obvious, influence forging different location transition kinetics therewith, and ultimately cause forging
Border region and the phase composition of center portion region and microstructure morphology's difference.It can be seen that with nearly β type and metastable beta titanium alloy
The strength enhancing of forging, section increase and shape more complicates, and the structure property variability issues of forging different location will further
It highlights, how to guarantee forging structure property uniformity while obtaining high-intensitive, it has also become science researcher's urgent need to resolve
Problem.
Although its leading heat treatment process of the beta titanium alloy of different-alloy type is different, such current related titanium alloy
Heat treatment process can mainly summarize are as follows: common annealing, double annealing, substance solid solution+substance (grade) timeliness, dual solid solution+mono-
Weight (grade) timeliness, substance solid solution+dual (grade) timeliness, dual solid solution+dual (grade) timeliness, after substance solid solution furnace cooling or
Converter cooling+substance (grade) timeliness etc..Current result of study shows, when need to prepare intensity requirement it is high (1200MPa rank and
More than), structure property uniformity good forging when, the above heat treatment process has some limitations.The reason is that, when adopting
When with common annealing heat treatment process, the advantage of beta titanium alloy ageing strengthening is not given full play of, forging intensity is often whole
It is relatively low.And solid-solution and aging heat treatment technique listed above is used, as the increase of forging section thickness or forging shape more become
Complexity, forging border region and the structure property difference in center portion region obviously increase, and are typically easy to cause forging center portion position strong
Spend relatively low, while border region intensity is excessively high, plasticity is extremely low.According to furnace cooling after solid solution or converter cooling+timeliness or
Person reduces the heat treatment process of solid solubility temperature, although forging border region and the structure property otherness in center portion region are changed
It is kind, but often equally cause the integral strength of forging that cannot improve to sacrifice intensity as cost.Therefore, in order to prepare height
The uniform titanium alloy forging of intensity, structure property need to design a kind of new heat treatment process for being suitable for beta titanium alloy.
Summary of the invention
The purpose of the present invention is to present in existing metastable β type, nearly β type and complete steady beta titanium alloy heat treatment process
Limitation and designing a kind of heat treatment process of new titanium alloy is provided, to prepare, high-intensitive, structure property is uniform
The big section of titanium alloy/variable cross-section forging.
The technical solution adopted by the present invention to solve the technical problems is:
(1) first reheats processing.Titanium alloy forging is put into the effective workspace of resistance furnace that arrived setting heating temperature T
It is inside heated, the heating temperature T set is (Tβ-50)℃≤T≤(Tβ+ 60) DEG C, TβFor alloy phase change point temperature, resistance furnace
Start to calculate soaking time, soaking time t=η after arriving again at the heating temperature T of setting1×δmax, δmaxFor titanium alloy forging
Maximum cross-section thickness, unit mm, η1For heating coefficient, value is 0.6~1.5min/mm, and soaking time t unit is min；
(2) titanium alloy forging after step (1) heat preservation is come out of the stove into air-cooled, air-cooled, oil cooling or water cooling to room temperature；
(3) second reheat processing.Titanium alloy forging is put into the effective workspace of resistance furnace that arrived setting heating temperature T
It is inside heated, the heating temperature T set as 780 DEG C of 650 DEG C≤T <, open after arriving again at the heating temperature T of setting by resistance furnace
Begin to calculate soaking time, soaking time t=(η2×δmax)/2, δmaxFor the maximum cross-section thickness of titanium alloy forging, unit mm,
η2For heating coefficient, value is 0.3~1.2min/mm, and soaking time t unit is min；
(4) titanium alloy forging after step (3) heat preservation is come out of the stove and is air-cooled to room temperature；
(5) third is reheated processing.Titanium alloy forging is put into the effective workspace of resistance furnace that arrived setting heating temperature T
It is inside heated, the heating temperature T set as 650 DEG C of 480 DEG C≤T <, open after arriving again at the heating temperature T of setting by resistance furnace
Begin to calculate soaking time, soaking time is 240min≤t≤600min；
(6) titanium alloy forging after step (5) heat preservation is come out of the stove and is air-cooled to room temperature.
The maximum temperature deviation of effective workspace is not more than ± 5 DEG C in the resistance furnace.
The technique is suitable for the heat treatment of nearly β type, metastable β type and complete steady beta titanium alloy.
The present invention have the advantage that and the utility model has the advantages that
(1) the first solid solubility temperature T that reheats when handling is (Tβ-50)℃≤T≤(Tβ+ 60) DEG C, it can be achieved that according to material difference
It designs requirement and obtains suitable organization type, forging is in transformation temperature TβWhen the above processing, damage tolerance can be obtained
The excellent lamellar structure of energy, forging is in transformation temperature TβWhen handling below, the superior duplex structure of fatigue behaviour can get；The
One type of cooling reheated when handling is set as air-cooled, air-cooled, oily cold and water cooling, can according to alloy can full hardening deepness and forging cut
Face thickness is different, by selecting suitable cooling medium, to retain enough metastable β phases, with this come when guaranteeing that forging is subsequent
The intensity in center portion region when effect processing.
(2) second reheat processing be the technique innovation and crucial place, overturn prior heat treatment thinking, herein with forging
Heat penetration is not basic principle, this is mainly based upon following two points: 1. the thermodynamics of quick response when beta titanium alloy timeliness is special
Sign, for Partial controll secondaryαphase forming core, be precipitated and grow up and provide condition；2. passing through in conjunction with numerical simulation of heat treatment technology
Determining and accurate control medium temperature overaging temperature and soaking time, for compensate first reheat processing solid solution it is cooling when forging edge
Region because cooling rate it is too fast caused by thermodynamic losses.Second processing of reheating promotes forging integrally metastable β phase content is consistent, secondary α
Phase size is suitable, to realize the uniformity of forging global tissue performance.
(3) third reheat processing heating temperature T be 650 DEG C of 480 DEG C≤T <, soaking time be 240min≤t≤
600min is kept the temperature by long-time aging, is made the whole secondaryαphase that more small and dispersed is sufficiently precipitated of forging, that is, be ensure that forging
Intensity, tissue is also stabilized, to obtain high-intensitive, even tissue and the stable forging of performance.
The technique is suitable for the heat treatment of nearly β type, metastable β type and complete steady beta titanium alloy, solves the solid solution of such titanium alloy
Forging edge and the big problem of core structure performance difference after timeliness, particularly useful for making going out, high-intensitive, structure property is equal
Even big section/variable cross-section titanium alloy forging.
Detailed description of the invention
Invention is further described in detail with reference to the accompanying drawings and examples.
Fig. 1 is the TB17 titanium alloy forging edge of the embodiment of the present invention 1 and the microstructure picture in center portion region, times magnification
Number is 10000 times, wherein (a) figure is edge microstructure picture；(b) center portion microstructure picture.
Fig. 2 is the TB17 titanium alloy forging edge of the embodiment of the present invention 2 and the microstructure picture in center portion region, times magnification
Number is 50000 times, wherein (a) figure is edge microstructure picture；(b) center portion microstructure picture.
Specific embodiment:
Below by specific example, the present invention is further described in detail:
Embodiment 1
The present embodiment is to be heat-treated a kind of nearly β type TB17 titanium alloy open die forgings, effective thickness 100mm.
Specific heat treatment process is as follows:
(1) first reheats processing.Titanium alloy forging is put into the effective workspace of resistance furnace that arrived setting heating temperature T
It is inside heated, the heating temperature T set is transformation temperature (Tβ) 25 DEG C below, resistance furnace arrives again at the heating temperature T of setting
After start calculate soaking time, soaking time t=120min, after heat preservation, forging, which is come out of the stove, is air-cooled to room temperature.
(2) second reheat processing.Titanium alloy forging is put into the effective workspace of resistance furnace that arrived setting heating temperature T
It is inside heated, as 680 DEG C, resistance furnace starts to calculate heat preservation the heating temperature T set after arriving again at the heating temperature T of setting
Time, soaking time t=30min, after heat preservation, forging, which is come out of the stove, is air-cooled to room temperature.
(3) third is reheated processing.Titanium alloy forging is put into the effective workspace of resistance furnace that arrived setting heating temperature T
It is inside heated, as 500 DEG C, resistance furnace starts to calculate heat preservation the heating temperature T set after arriving again at the heating temperature T of setting
Time, soaking time t=480min, after heat preservation, forging, which is come out of the stove, is air-cooled to room temperature.
Performance detection is carried out to the open die forgings of embodiment 1, and is carried out with the open die forgings of common solid-solution and aging heat treatment
Comparison, the results are shown in Table 1.As can be seen that the intensity of forging edge position is inclined when forging uses common fixation rates
Height, plasticity is relatively low, and has very big difference with the mechanical property of center portion position；And this patent technique is used to carry out hot place to forging
When reason, forging edge and the structure property uniformity of center portion position are obviously improved.
The room-temperature mechanical property of 1 TB17 titanium alloy open die forgings (effective thickness 100mm) of table
Embodiment 2
The present embodiment is to be heat-treated a kind of nearly β type TB17 titanium alloy open die forgings, effective thickness 200mm.
Specific heat treatment process is as follows:
(1) first reheats processing.Titanium alloy forging is put into the effective workspace of resistance furnace that arrived setting heating temperature T
It is inside heated, the heating temperature T set is transformation temperature (Tβ) 20 DEG C below, resistance furnace arrives again at the heating temperature T of setting
After start calculate soaking time, soaking time t=150min, after heat preservation, forging is come out of the stove air-cooled to room temperature.
(2) second reheat processing.Titanium alloy forging is put into the effective workspace of resistance furnace that arrived setting heating temperature T
It is inside heated, as 700 DEG C, resistance furnace starts to calculate heat preservation the heating temperature T set after arriving again at the heating temperature T of setting
Time, soaking time t=55min, after heat preservation, forging, which is come out of the stove, is air-cooled to room temperature.
(3) third is reheated processing.Titanium alloy forging is put into the effective workspace of resistance furnace that arrived setting heating temperature T
It is inside heated, as 510 DEG C, resistance furnace starts to calculate heat preservation the heating temperature T set after arriving again at the heating temperature T of setting
Time, soaking time t=480min, after heat preservation, forging, which is come out of the stove, is air-cooled to room temperature.
Performance detection is carried out to the open die forgings of embodiment 2, and is carried out with the open die forgings of common solid-solution and aging heat treatment
Comparison, the results are shown in Table 2.As can be seen that the tension of forging edge position is strong when forging uses common fixation rates
Degree-elongation percentage is 1393MPa-2.6%, and tensile strength-elongation percentage of forging center portion position is 1285MPa-11.1%, the sense of organization
Energy otherness is very big；And when being heat-treated using this patent technique to forging, tensile strength-elongation percentage of forging edge position
For 1315MPa-8.5%, tensile strength-elongation percentage of forging center portion position is 1283MPa-10.9%, forging edge and center portion
The structure property uniformity of position is obviously improved.
The room-temperature mechanical property of 2 TB17 titanium alloy open die forgings (effective thickness 200mm) of table
Claims (8)
1. a kind of heat treatment process of titanium alloy, which is characterized in that specifically includes the following steps:
(1) first reheats processing；Titanium alloy forging is put into arrived setting heating temperature T the effective workspace of resistance furnace in into
Row heating, the heating temperature T set is (Tβ-50)℃≤T≤(Tβ+ 60) DEG C, TβFor alloy phase change point temperature, resistance furnace is again
Start to calculate soaking time, soaking time t=η after reaching the heating temperature T of setting1×δmax, δmaxMost for titanium alloy forging
Big section thickness, unit mm, η1For heating coefficient, soaking time t unit is min；
(2) titanium alloy forging after step (1) heat preservation is come out and cooled down；
(3) second reheat processing；Titanium alloy forging is put into arrived setting heating temperature T the effective workspace of resistance furnace in into
Row heating, as 780 DEG C of 650 DEG C≤T <, resistance furnace starts to count the heating temperature T set after arriving again at the heating temperature T of setting
Calculate soaking time, soaking time t=(η2×δmax)/2, δmaxFor the maximum cross-section thickness of titanium alloy forging, unit mm, η2For
Heating coefficient, soaking time t unit are min；
(4) titanium alloy forging after step (3) heat preservation is come out and cooled down to room temperature；
(5) third is reheated processing；Titanium alloy forging is put into arrived setting heating temperature T the effective workspace of resistance furnace in into
Row heating；
(6) titanium alloy forging after step (5) heat preservation is come out and cooled down to room temperature.
2. a kind of heat treatment process of titanium alloy according to claim 1, it is characterised in that: the heating furnace is resistance
Furnace.
3. a kind of heat treatment process of titanium alloy according to claim 2, it is characterised in that: the effective workspace temperature difference of furnace temperature
Control is within ± 5 DEG C.
4. a kind of heat treatment process of titanium alloy according to claim 1, it is characterised in that: η in step (1)1Value model
It encloses for 0.6~1.5min/mm.
5. a kind of heat treatment process of titanium alloy according to claim 1, it is characterised in that: titanium alloy is forged in step (2)
The mode that part comes out and cools down is air-cooled, air-cooled, oil cooling or water cooling to room temperature.
6. a kind of heat treatment process of titanium alloy according to claim 1, it is characterised in that: η in step (3)2Value model
It encloses for 0.3~1.2min/mm.
7. a kind of heat treatment process of titanium alloy according to claim 1, it is characterised in that: what is set in step (5) adds
Hot temperature T is 650 DEG C of 480 DEG C≤T <, and resistance furnace starts to calculate soaking time, heat preservation after arriving again at the heating temperature T of setting
Time is 240min≤t≤600min.
8. a kind of heat treatment process of titanium alloy according to claim 1, it is characterised in that: the heat treatment process is applicable in
In the heat treatment of nearly β type, metastable β type and complete steady beta titanium alloy.
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Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111451423A (en) * | 2020-03-19 | 2020-07-28 | 中国船舶重工集团公司第七二五研究所 | Manufacturing process method of titanium alloy ultrahigh-pressure-resistant spherical shell blank |
| CN112662974A (en) * | 2020-12-18 | 2021-04-16 | 陕西宏远航空锻造有限责任公司 | Heat treatment method of TC21 alloy forging |
| CN113523012A (en) * | 2021-07-14 | 2021-10-22 | 山西太钢不锈钢股份有限公司 | Hot processing method of niobium-containing high-alloy austenitic heat-resistant stainless steel bar |
| CN114226616A (en) * | 2021-10-29 | 2022-03-25 | 中国航发北京航空材料研究院 | Isothermal forging method of TB17 titanium alloy |
| CN114959528A (en) * | 2022-05-23 | 2022-08-30 | 中国科学院金属研究所 | Heat treatment process for improving performance stability of thick-section or variable-section TC11 alloy forging |
| CN114959529A (en) * | 2022-05-23 | 2022-08-30 | 中国科学院金属研究所 | Heat treatment process for improving performance stability of thick-section or variable-section Ti6246 alloy forging |
| CN115058673A (en) * | 2022-06-21 | 2022-09-16 | 湖南金天钛业科技有限公司 | Heat treatment method for regulating and controlling mechanical property matching and consistency of TC11 titanium alloy |
| CN115927987A (en) * | 2022-12-29 | 2023-04-07 | 北京钢研高纳科技股份有限公司 | Heat treatment method of high-temperature alloy disc shaft type forge piece and disc shaft type forge piece manufactured by same |
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1403622A (en) * | 2001-09-04 | 2003-03-19 | 北京航空材料研究院 | Titanium alloy quasi-beta forging process |
| CN101353772A (en) * | 2007-07-24 | 2009-01-28 | 北京有色金属研究总院 | Heat treatment process improving two-phase titanium alloy damage tolerance property |
| CN102851627A (en) * | 2012-09-21 | 2013-01-02 | 中国航空工业集团公司北京航空材料研究院 | Novel titanium alloy partitioned beta heat treatment process |
| CN105908112A (en) * | 2016-06-17 | 2016-08-31 | 中国航空工业集团公司北京航空材料研究院 | Repeated solid solution aging thermal treatment process of titanium alloy |
| CN107779801A (en) * | 2017-11-02 | 2018-03-09 | 中国兵器科学研究院宁波分院 | The heat treatment method of armoring titanium alloy TC 4 |
-
2019
- 2019-06-14 CN CN201910519014.7A patent/CN110273118B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1403622A (en) * | 2001-09-04 | 2003-03-19 | 北京航空材料研究院 | Titanium alloy quasi-beta forging process |
| CN101353772A (en) * | 2007-07-24 | 2009-01-28 | 北京有色金属研究总院 | Heat treatment process improving two-phase titanium alloy damage tolerance property |
| CN102851627A (en) * | 2012-09-21 | 2013-01-02 | 中国航空工业集团公司北京航空材料研究院 | Novel titanium alloy partitioned beta heat treatment process |
| CN105908112A (en) * | 2016-06-17 | 2016-08-31 | 中国航空工业集团公司北京航空材料研究院 | Repeated solid solution aging thermal treatment process of titanium alloy |
| CN107779801A (en) * | 2017-11-02 | 2018-03-09 | 中国兵器科学研究院宁波分院 | The heat treatment method of armoring titanium alloy TC 4 |
Non-Patent Citations (1)
| Title |
|---|
| 王新南等: ""热处理工艺对 Ti-6Al-4V ELI 合金厚截面锻件力学性能的影响"", 《钛工业进展》 * |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111451423A (en) * | 2020-03-19 | 2020-07-28 | 中国船舶重工集团公司第七二五研究所 | Manufacturing process method of titanium alloy ultrahigh-pressure-resistant spherical shell blank |
| CN112662974A (en) * | 2020-12-18 | 2021-04-16 | 陕西宏远航空锻造有限责任公司 | Heat treatment method of TC21 alloy forging |
| CN113523012A (en) * | 2021-07-14 | 2021-10-22 | 山西太钢不锈钢股份有限公司 | Hot processing method of niobium-containing high-alloy austenitic heat-resistant stainless steel bar |
| CN114226616A (en) * | 2021-10-29 | 2022-03-25 | 中国航发北京航空材料研究院 | Isothermal forging method of TB17 titanium alloy |
| CN114226616B (en) * | 2021-10-29 | 2023-03-14 | 中国航发北京航空材料研究院 | Isothermal forging method of TB17 titanium alloy |
| CN114959528A (en) * | 2022-05-23 | 2022-08-30 | 中国科学院金属研究所 | Heat treatment process for improving performance stability of thick-section or variable-section TC11 alloy forging |
| CN114959529A (en) * | 2022-05-23 | 2022-08-30 | 中国科学院金属研究所 | Heat treatment process for improving performance stability of thick-section or variable-section Ti6246 alloy forging |
| CN115058673A (en) * | 2022-06-21 | 2022-09-16 | 湖南金天钛业科技有限公司 | Heat treatment method for regulating and controlling mechanical property matching and consistency of TC11 titanium alloy |
| CN115927987A (en) * | 2022-12-29 | 2023-04-07 | 北京钢研高纳科技股份有限公司 | Heat treatment method of high-temperature alloy disc shaft type forge piece and disc shaft type forge piece manufactured by same |
| CN117324522A (en) * | 2023-09-28 | 2024-01-02 | 陕西鼎益科技有限公司 | Forging forming method for improving flaw detection level of titanium alloy bar |
| CN117324522B (en) * | 2023-09-28 | 2024-04-12 | 陕西鼎益科技有限公司 | Forging forming method for improving flaw detection level of titanium alloy bar |
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