CN106048486A - Structure refinement method for Ti2AlNb alloy through (O+B2) two-phase region aging treatment - Google Patents
Structure refinement method for Ti2AlNb alloy through (O+B2) two-phase region aging treatment Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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 high-temperature thermal treatment structure refinement method for a Ti2AlNb alloy. The Ti2AlNb alloy is forged, heated to a (O+B2) two-phase region, and subjected to thermal insulation for 1-5 h. Then, the obtained alloy is quenched with water and cooled to room temperature. Fragmentization of an alpha 2 phase is utilized during a conversion process from the alpha 2 phase to an O phase, and a refined structure is obtained after the aging treatment of thermal insulation for 1-5 h in the (O+B2) two-phase region. The equiaxed grain size and lath grain size in the treated Ti2AlNb alloy structure are obviously refined. With the prolongation of aging time, the equiaxed grain size and lath grain size in the treated Ti2AlNb alloy structure are decreased first and gradually increased. After the aging treatment for 4 hours, the equiaxed grain size and lath grain size are increased, and with the prolongation of the aging time, the equiaxed grain size still undergoes a reduction process, while the lath grain size keeps stable. Through proper (O+B2) two-phase region aging treatment of a Ti-22Al-25Nb alloy, obvious improvement of high-temperature performance of the alloy is ensured.
Description
Technical field
The invention belongs to Ti2AlNb technical field of alloy thermal treatment, particularly to a kind of Ti2AlNb alloy (O+B2) two-phase section
Aging Microstructure thinning method.
Background technology
Ti2AlNb base alloy starts to rise in eighties of last century the nineties, is that the extension as Alpha-2 alloy is ground the earliest
Studying carefully, be subsequently found in conventional Ti 3Al system alloy, add a certain amount of Nb constituent element, will form O phase, O meets and exists at Nb content
One wide in the range of stable existence, thus started the upsurge of the exploitation of Ti2AlNb base alloy and application.Generally Ti2AlNb
The component content of alloy can float in the range of Ti-(18～30) Al-(12.5～30) Nb (at%), and table 1 gives common
The nominal composition scope of Ti2AlNb alloy.
As aforesaid, O phase is the important symbol of Ti2AlNb alloy difference conventional Ti-Al series intermetallic compound.
Ti2AlNb alloy belongs to the on-deformable high-temperature structural material of lightweight, various phase constituents (B2 phase, the α in its tissue2Phase or O
Phase) form, distribution and the performance of content size appreciable impact alloy.For from heat treating regime, Ti2AlNb alloy deformation
After at less than β phase transition temperature 20 DEG C, often carry out solution treatment, now O meets and separates out mutually from matrix than more uniform, so
After cool down with speed faster and can obtain equiaxed structure, generally O phase is by the α of shaft-like such as being wrapped in2The periphery of phase,
The nascent O phase/α of shaft-like distribution such as can obtain when part2Phase granule and the secondary O phase/α of sheet2Phase.Solution treatment obtains
Two-phase structure has become the main Technology for Heating Processing of Ti2AlNb base alloy, it is considered that prolongation over time, lath-shaped and
To gradually be roughened etc. shaft-like tissue, thus deteriorate high-temperature behavior；The most exactly ignore α2Phase → O phase in version process occurs
α2Phase fragmentation is so that structure refinement, and this is also the starting point of the present invention.
Table 1Ti2AlNb alloy routine chemical components (%)
| Component | Content (wt.%) |
| Ti | 51.6～52.6 |
| Al | 21.9～22.7 |
| Nb | 25.4～25.7 |
| N | ≤3.2×10-4 |
| O | ≤0.020 |
| H | ≤0.0017 |
Summary of the invention
The problem of the high-temperature behavior difference that present invention seek to address that Ti2AlNb alloy thick due to tissue and to cause.By having
The fragmentation of α 2 phase that α 2 phases → O phase in version process occurs when effect utilizes high-temperature aging to process, at appropriate (O+B2) two-phase section
Obtain fine and closely woven (O+B2) tissue under aging technique combination (aging time and aging temp), thus carry heavy alloyed high temperatures
Can, and then advance its application in practice.
Technical scheme is as follows:
A kind of Ti2AlNb alloy (O+B2) two-phase section Aging Microstructure thinning method, step is as follows:
(1) by after forged for Ti2AlNb alloy, it be heated to (O+B2) two-phase section and be incubated 1～5 hours, shrend subsequently
And it is cooled to room temperature；
(2) α is utilized2Phase → O phase in version process α2The fragmentation of phase, by (O+B2) two-phase section isothermal 1～5 hours timeliness
Rear acquisition thinning microstructure.
It is described as follows:
(O+B2) two-phase section temperature range of Ti2AlNb alloy can be measured by differential thermal analysis aspect, as Fig. 1 is given
Ti-22Al-25Nb alloy heating process (firing rate is 5 DEG C/min) differential thermal analysis curve, wherein 630 DEG C～961 DEG C are
(O+B2) two-phase section, and choose selected aging temp and aging time in this temperature range.
The Technology for Heating Processing flow process of patent of the present invention is: sample being heated to 900 DEG C and is incubated 30 minutes, stove is cooled to subsequently
740 DEG C～800 DEG C, being incubated 50 minutes, shrend is to room temperature；It is heated to 650 DEG C, is tempered 2 hours, takes Ti-22Al-25Nb alloy and add
Heat is to 630 DEG C～961 DEG C, and is incubated 1～5 hours, and shrend is to room temperature subsequently.
Compared with the typical organization (such as Fig. 2) before Ti-22Al-25Nb alloy (O+B2) two-phase section Ageing Treatment, using should
In Ti2AlNb alloy structure after PROCESS FOR TREATMENT, its isometry particle diameter and lath particle diameter substantially refine, and Fig. 3 gives Ti-22Al-
The 800 DEG C of timeliness of 25Nb alloy (O+B2) two-phase section typical organization after 2 hours.Along with the prolongation of aging time, Ti2AlNb alloy
Isometry particle diameter and lath particle diameter in tissue first reduce and are gradually increased, and timeliness is isometry particle diameter and lath particle diameter after 4 hours
Increasing, along with the prolongation (more than 6 hours) of aging time, isometry particle diameter still experiences a process reduced, and lath particle diameter
Kept stable, when Fig. 4 gives the precipitate size size in 800 DEG C of timeliness Ti-22Al-25Nb alloy structures with timeliness
Between variation relation.The tissue change of alloy aging process is notable on the impact of its high-temperature behavior, and Fig. 5 gives 800 DEG C of timeliness Ti-
650 DEG C of creep rupture strengths of 22Al-25Nb alloy are with the variation relation of aging time, therefrom it is found that Ageing Treatment 6
After hour, the high temperature creep property of alloy significantly deteriorates.As can be seen here, appropriate Ti-22Al-25Nb alloy (O+B2) two-phase section
Ageing Treatment can ensure that being obviously improved of its high-temperature behavior.
Accompanying drawing explanation
Fig. 1 Ti-22Al-25Nb alloy heating process (firing rate is 5 DEG C/min) differential thermal analysis curve, wherein 630 DEG C
～961 DEG C be (O+B2) two-phase section；
Typical organization before Fig. 2 Ti-22Al-25Nb alloy (O+B2) two-phase section Ageing Treatment；
Fig. 3 800 DEG C of timeliness of Ti-22Al-25Nb alloy (O+B2) two-phase section typical organization after 2 hours；
Precipitate size size in 800 DEG C of timeliness Ti-22Al-25Nb alloy structures of Fig. 4 is closed with the change of aging time
System；
Fig. 5 650 DEG C of creep rupture strengths of 800 DEG C of timeliness Ti-22Al-25Nb alloys are with the variation relation of aging time.
Detailed description of the invention
Ti2AlNb alloy used is Ti-22Al-25Nb, and its composition is as shown in table 1.By differential thermal analysis, record this alloy
(O+B2) two-phase section temperature is 630 DEG C～961 DEG C (see Fig. 1).Using four consumables to prepare ingot casting, ingot casting is after cogging is forged
The bar being prepared as a diameter of 150mm is standby.Ingot casting deforms at 1050-1150 DEG C of employing hydraulic press.Mode of texturing is three
Upsetting three is pulled out, and wherein, each upsetting or the deflection pulled out are more than 30%.From the bar forged, sampling carries out aging strengthening model in fact
Testing, 650 DEG C of creep rupture strengths of the bar forged are 183MPa.
The concrete technical scheme embodiment of the present invention is as follows:
Embodiment 1:
Taking Ti-22Al-25Nb alloy and be heated to 800 DEG C, and be incubated 5 hours, shrend is to room temperature subsequently.
Using its isometry particle diameter in the Ti2AlNb alloy structure after this PROCESS FOR TREATMENT is 430 nanometers, and lath particle diameter is 1.32
Micron, its 650 DEG C of creep rupture strengths are 200MPa.
Embodiment 2:
Taking Ti-22Al-25Nb alloy and be heated to 961 DEG C, and be incubated 1 hour, shrend is to room temperature subsequently.
Using its isometry particle diameter in the Ti2AlNb alloy structure after this PROCESS FOR TREATMENT is 452 nanometers, and lath particle diameter is 1.41
Micron, its 650 DEG C of creep rupture strengths are 192MPa.
Embodiment 3:
Taking Ti-22Al-25Nb alloy and be heated to 630 DEG C, and be incubated 5 hours, shrend is to room temperature subsequently.
Using its isometry particle diameter in the Ti2AlNb alloy structure after this PROCESS FOR TREATMENT is 456 nanometers, and lath particle diameter is 1.43
Micron, its 650 DEG C of creep rupture strengths are 194MPa.
Embodiment 4:
Taking Ti-22Al-25Nb alloy and be heated to 820 DEG C, and be incubated 2 hours, shrend is to room temperature subsequently.
Using its isometry particle diameter in the Ti2AlNb alloy structure after this PROCESS FOR TREATMENT is 416 nanometers, and lath particle diameter is 1.23
Micron, its 650 DEG C of creep rupture strengths are 225MPa.
The present invention propose a kind of Ti2AlNb alloy (O+B2) two-phase section Aging Microstructure thinning method and carry heavy alloyed height
The method of temperature creep rupture strength, is different from traditional aging process tissue from principle and is gradually roughened and causes its high-temerature creep to break
Resistance to spalling declines, and is effectively utilized the fragmentation utilizing α 2 phases → O phase in version process α 2 phase, when appropriate (O+B2) two-phase section
Obtain fine and closely woven (O+B2) tissue at effect temperature and aging time combination, thus improve the high-temperature behavior of alloy.Pass through
Embodiment is described, and person skilled substantially can be to this paper institute in without departing from present disclosure, spirit and scope
The manufacture method stated is modified or suitably changes and combine, and realizes the technology of the present invention.Special needs to be pointed out is, all
Similar replacement and change apparent to those skilled in the art, they are considered as being included in present invention essence
In god, scope and content.
Claims (1)
1. Ti2AlNb alloy (O+B2) two-phase section Aging Microstructure thinning method, is characterized in that step is as follows:
(1) by after forged for Ti2AlNb alloy, being heated to (O+B2) two-phase section and be incubated 1～5 hours, shrend subsequently is the coldest
But to room temperature；
(2) α is utilized2Phase → O phase in version process α2The fragmentation of phase, is obtained after timeliness by (O+B2) two-phase section isothermal 1～5 hours
Obtain thinning microstructure.
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Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106637017A (en) * | 2017-01-17 | 2017-05-10 | 哈尔滨工业大学 | Method for self-generation of high-strength wear-resistant layer on surface of Ti-22Al-25Nb alloy |
| CN106868328A (en) * | 2017-01-09 | 2017-06-20 | 天津大学 | One kind obtains β+O duplex structures and improves Ti2The method of AlNb alloy rigidities |
| CN108396174A (en) * | 2018-03-14 | 2018-08-14 | 燕山大学 | Ti-22Al-25Nb/Al2O3The preparation method of composite material |
| CN108465819A (en) * | 2018-03-14 | 2018-08-31 | 燕山大学 | The mechanical alloying preparation method of Ti-22Al-25Nb (at.%) solid solution |
| CN108660399A (en) * | 2018-04-29 | 2018-10-16 | 天津大学 | A kind of predeformation Ti-22Al-25Nb alloys acquisition B2+O/ α2The method of multiform looks stabilizing tissue |
| CN109332693A (en) * | 2018-11-08 | 2019-02-15 | 有研工程技术研究院有限公司 | A kind of three-phase Ti of laser gain material manufacture2The heat treatment process of AlNb based alloy |
| CN112063945A (en) * | 2020-08-28 | 2020-12-11 | 中国科学院金属研究所 | Improve Ti2Heat treatment process for lasting and creep property of AlNb-based alloy |
| CN112247043A (en) * | 2020-08-28 | 2021-01-22 | 中国科学院金属研究所 | Ti2Preparation process of AlNb-based alloy forging |
| CN112281043A (en) * | 2020-12-25 | 2021-01-29 | 北京钢研高纳科技股份有限公司 | High fracture toughness Ti2AlNb-based alloy and preparation method and application thereof |
| CN112410698A (en) * | 2020-11-03 | 2021-02-26 | 中国航发北京航空材料研究院 | Three-phase Ti2AlNb alloy multilayer structure uniformity control method |
| CN113981296A (en) * | 2021-12-24 | 2022-01-28 | 北京钢研高纳科技股份有限公司 | Ti2AlNb-based alloy and preparation method and application thereof |
| CN114262782A (en) * | 2021-12-27 | 2022-04-01 | 广东工业大学 | Thermal ultrasonic surface strengthening method and device for thin-wall part |
| CN116987991A (en) * | 2023-09-26 | 2023-11-03 | 成都先进金属材料产业技术研究院股份有限公司 | Regulating Ti 2 Method for preparing AlNb-based alloy with yield ratio |
-
2016
- 2016-08-02 CN CN201610631527.3A patent/CN106048486A/en active Pending
Non-Patent Citations (1)
| Title |
|---|
| 朱斌等: "《定量分析热处理对Ti2AlNb合金显微组织及硬度的影响》", 《材料热处理学报》 * |
Cited By (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106868328A (en) * | 2017-01-09 | 2017-06-20 | 天津大学 | One kind obtains β+O duplex structures and improves Ti2The method of AlNb alloy rigidities |
| CN106637017A (en) * | 2017-01-17 | 2017-05-10 | 哈尔滨工业大学 | Method for self-generation of high-strength wear-resistant layer on surface of Ti-22Al-25Nb alloy |
| CN108396174A (en) * | 2018-03-14 | 2018-08-14 | 燕山大学 | Ti-22Al-25Nb/Al2O3The preparation method of composite material |
| CN108465819A (en) * | 2018-03-14 | 2018-08-31 | 燕山大学 | The mechanical alloying preparation method of Ti-22Al-25Nb (at.%) solid solution |
| CN108396174B (en) * | 2018-03-14 | 2019-11-05 | 燕山大学 | Ti-22Al-25Nb/Al2O3The preparation method of composite material |
| CN108465819B (en) * | 2018-03-14 | 2020-04-03 | 燕山大学 | Mechanical alloying preparation method of Ti-22Al-25Nb (at.%) solid solution |
| CN108660399A (en) * | 2018-04-29 | 2018-10-16 | 天津大学 | A kind of predeformation Ti-22Al-25Nb alloys acquisition B2+O/ α2The method of multiform looks stabilizing tissue |
| CN109332693A (en) * | 2018-11-08 | 2019-02-15 | 有研工程技术研究院有限公司 | A kind of three-phase Ti of laser gain material manufacture2The heat treatment process of AlNb based alloy |
| CN112063945A (en) * | 2020-08-28 | 2020-12-11 | 中国科学院金属研究所 | Improve Ti2Heat treatment process for lasting and creep property of AlNb-based alloy |
| CN112247043A (en) * | 2020-08-28 | 2021-01-22 | 中国科学院金属研究所 | Ti2Preparation process of AlNb-based alloy forging |
| CN112063945B (en) * | 2020-08-28 | 2021-12-10 | 中国科学院金属研究所 | Improve Ti2Heat treatment process for lasting and creep property of AlNb-based alloy |
| CN112410698A (en) * | 2020-11-03 | 2021-02-26 | 中国航发北京航空材料研究院 | Three-phase Ti2AlNb alloy multilayer structure uniformity control method |
| CN112281043A (en) * | 2020-12-25 | 2021-01-29 | 北京钢研高纳科技股份有限公司 | High fracture toughness Ti2AlNb-based alloy and preparation method and application thereof |
| CN113981296A (en) * | 2021-12-24 | 2022-01-28 | 北京钢研高纳科技股份有限公司 | Ti2AlNb-based alloy and preparation method and application thereof |
| CN114262782A (en) * | 2021-12-27 | 2022-04-01 | 广东工业大学 | Thermal ultrasonic surface strengthening method and device for thin-wall part |
| CN116987991A (en) * | 2023-09-26 | 2023-11-03 | 成都先进金属材料产业技术研究院股份有限公司 | Regulating Ti 2 Method for preparing AlNb-based alloy with yield ratio |
| CN116987991B (en) * | 2023-09-26 | 2024-01-23 | 成都先进金属材料产业技术研究院股份有限公司 | Regulating Ti 2 Method for preparing AlNb-based alloy with yield ratio |
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