CN106134379B - Microstructure and properties control method of near-α-type titanium alloy under isothermal local loading transition zone - Google Patents
Microstructure and properties control method of near-α-type titanium alloy under isothermal local loading transition zoneInfo
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- CN106134379B CN106134379B CN200810076423.6A CN200810076423A CN106134379B CN 106134379 B CN106134379 B CN 106134379B CN 200810076423 A CN200810076423 A CN 200810076423A CN 106134379 B CN106134379 B CN 106134379B
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- 238000011068 loading method Methods 0.000 title claims abstract description 61
- 230000007704 transition Effects 0.000 title claims abstract description 33
- 238000000034 method Methods 0.000 title claims abstract description 20
- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 15
- 238000005242 forging Methods 0.000 claims abstract description 75
- 238000010438 heat treatment Methods 0.000 claims abstract description 15
- 230000008569 process Effects 0.000 claims abstract description 10
- 238000001816 cooling Methods 0.000 claims abstract description 7
- 230000009466 transformation Effects 0.000 claims abstract description 6
- 238000009413 insulation Methods 0.000 claims description 18
- 238000007493 shaping process Methods 0.000 claims description 14
- 229920000742 Cotton Polymers 0.000 claims description 10
- 238000005266 casting Methods 0.000 claims description 10
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 7
- 229910045601 alloy Inorganic materials 0.000 claims description 7
- 239000000956 alloy Substances 0.000 claims description 7
- 238000002360 preparation method Methods 0.000 claims description 7
- 230000008859 change Effects 0.000 claims description 6
- 238000001953 recrystallisation Methods 0.000 claims description 6
- 239000000463 material Substances 0.000 claims description 5
- 238000009659 non-destructive testing Methods 0.000 claims description 5
- 238000003825 pressing Methods 0.000 claims description 4
- 238000007730 finishing process Methods 0.000 claims description 2
- 239000006104 solid solution Substances 0.000 claims description 2
- 230000002159 abnormal effect Effects 0.000 abstract description 2
- 238000005728 strengthening Methods 0.000 abstract 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 6
- 230000000994 depressogenic effect Effects 0.000 description 6
- 238000010275 isothermal forging Methods 0.000 description 4
- 230000009467 reduction Effects 0.000 description 4
- 229910052742 iron Inorganic materials 0.000 description 3
- 239000000155 melt Substances 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 238000000137 annealing Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
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Abstract
本发明是一种近α型钛合金等温局部加载过渡区组织性能控制方法，将过渡区组织性能控制贯穿于整个热加工过程，通过控制毛坯改锻、预成形毛坯制备、局部加载、精整和热处理中的工艺参数，实现对过渡区组织和性能的控制。铸锭在β相区开坯水冷，在相变点以下40～50℃改锻，锻后水冷。局部加载道次不超过2次，加热锻造温度为相变点以下20～30℃，变形速度为0.01～0.02s-1。局部加载后压力机保压10～15min精整锻件。锻后快速水冷，采用强韧化热处理。本发明能有效控制局部加载成形中过渡区的微观组织，获得细小均匀的等轴α相+β转变组织，过渡区组织无晶粒粗化、不均匀化和异常长大，具有组织稳定、力学性能良好的特点。
The invention is a method for controlling the microstructure and properties of the transition zone under isothermal local loading of a near-α-type titanium alloy. The microstructure and properties of the transition zone are controlled throughout the entire thermal processing process. Process parameters in heat treatment to control the structure and properties of the transition zone. The ingot is water-cooled in the β-phase region, and re-forged at 40-50°C below the phase transition point, and water-cooled after forging. The number of partial loading passes is no more than 2, the heating forging temperature is 20-30°C below the phase transition point, and the deformation speed is 0.01-0.02s -1 . After partial loading, press the press for 10 to 15 minutes to finish the forging. Rapid water cooling after forging, using strengthening and toughening heat treatment. The invention can effectively control the microstructure of the transition zone in the local loading forming, and obtain a fine and uniform equiaxed α phase + β transformation structure. The transition zone has no grain coarsening, inhomogeneity and abnormal growth, and has stable structure and mechanical strength. Good performance features.
Description
One, technical field
The present invention relates to hot-working field, specifically a kind of nearly alpha titanium alloy isothermal local loads transition region structure propertyControl method.
Two, technical background
Aero-Space have very high requirement with titanium alloy member to microstructure and mechanical property. For nearly alpha titanium alloy,Forging part requires to have the evenly tiny axle α phase+β that waits to change tissue, to realize the matched well of mechanical property. Adopt etc.When temperature local loading is produced titanium alloy part, forging is the distortion of regional area stand under load at each shaping stage, is being shapedIn journey, on forging, there is load deflection district, not loading zone and transition region. Transition region is subject to loading zone and the not impact of loading zoneAnd deform, unhomogeneity of deformation increases, and adds showing tremendous enthusiasm time and process time also more than common die forging simultaneously. These because ofElement causes forging transition region Microstructural Evolution complexity in process, alligatoring and uneven homogenize easily occurs, transition regionAlso corresponding reduction of mechanical property.
In the patent application that is 200710083701.6 at number of patent application, disclose the complicated entirety of titanium alloy large-sized gusset classThe method of member isothermal local loading and shaping, but do not provide the technical scheme of controlling transition region tissue.
Three, summary of the invention
Organize thick, inhomogeneous and the reduction of transition region mechanical property for overcoming the forging transition region existing in prior artDeficiency, the present invention proposes a kind of nearly alpha titanium alloy isothermal local loading and shaping forging transition region structure property controlling partyMethod.
The present invention by the control of transition region structure property through whole hot procedure, by controlled working process hairBase changes forging, preformed blank preparation, local loading process, finishing process and forges the technological parameter in after-baking,Realize transition region tissue and Properties Control, detailed process is as follows:
The first step, blank change forging
Titan alloy casting ingot is in the above cogging of transformation temperature, and ingot casting is heated to Tβ+ (50～100 DEG C), deflection is greater than 50%,Water-cooled after forging, to improve the metallurgical quality of material, improves the microstructure and composition uniformity of material; Then by the hair obtainingBase is heated to TβThe two-phase section of-(40～50 DEG C) changes forging, and deflection is greater than 50%, and water-cooled after forging is tiny etc. to obtainAxle tissue or bifurcation tissue.
Second step, preformed blank preparation
By the blank appearance parcel adiabatic cotton changing after forging, be heated to Tβ-40 DEG C, adopt open die forging and loose tooling forging to carry out base,Time bases as how fiery in need, and melt down again heating after blank being wrapped up to adiabatic cotton after each fire processing. Can increase like thisEvery fiery deflection, reduces processing fire, suppresses microstructure coarsening.
The 3rd step, isothermal local loading and shaping
In local loading, workpiece is divided into two to three loading zones, mould is divided into corresponding several accordingly. OftenIndividual loading passage is divided into two and loads step, in each loading step, utilizes the mould of piecemeal to enter successively different loading zonesRow local loading, after all loadings complete, proceeds to next and loads passage, repeats the loading side of a loading passageMethod, until arrive total deflection.
The specific implementation process of local loading and shaping is:
First loads work step: blank is heated to Tβ-(30～40 DEG C), mold heated is to Tβ-50 DEG C, with piecemeal mould pairWorkpiece carries out local loading, and pressing speed is 0.2～0.4mm/s, and relative deformation equals total deformation or total deformation55%～65%. As more mold exchange of need, by blank depanning water-cooled.
Second loads work step: blank obtained in the previous step is heated to Tβ-(30～40 DEG C), mold heated is to Tβ-50℃，By other parts of piecemeal die forming workpiece, pressing speed is 0.2～0.4mm/s, and relative deformation equals total deformationOr total deformation 55%～65%.
In local loading, main technological parameter has passage and each pass deformation of loading, heating-up temperature, loading velocity,The type of cooling. For controlling the microstructure of transition region, the selection of main technologic parameters should meet following some: 1. localLoading passage is no more than twice. The preferential a time that adopts loads, and can not be shaped as a time loads, and can select twice timeLoad. While adopting two passages to load, each pass deformation must be greater than the critical strain amount of material generation recrystallization,The first pass deformation is that the 55%～65%, second pass deformation of total deformation is total deformation 45%～35%.2. the heating-up temperature of blank is Tβ-(30～40 DEG C), the heating-up temperature of mould is Tβ-50 DEG C. 3. each loads work step, materialStrain rate 0.01～the 0.02s of material-1, corresponding deformation velocity is 0.2～0.4mm/s. 4. while needing more mold exchange, will forgePart depanning water-cooled.
The 4th step, finishing
Finishing is carried out after last fire that completes local loading and shaping is inferior. Now, each piecemeal mould is depressed simultaneously.Finishing adopts forcing press pressurize to complete, and during due to bulk deformation, required plastic force generally will exceed the equipment scope of forcing press,Its maximum that can provide is provided the tonnage of forcing press pressurize, and the dwell time is 10min～15min. In this conditionUnder, mainly there is superplasticity flow deformation in material, can reduce forming defects.
The 5th step, heat treatment
After forging, take out immediately workpiece water-cooled, then adopt the Technology for Heating Processing of solid solution recrystallization annealing, workpiece is heatedTo Tβ-(20～30 DEG C), insulation 1～2h, water-cooled; Then workpiece is heated to recrystallization temperature, insulation 2～3h, air cooling.
The 6th step, Non-Destructive Testing
Adopt technical scheme of the present invention, can effectively control the microstructure of transition region in local loading and shaping, obtainThe tiny uniform axle α phase+β that waits changes tissue. Transition region macrostructure is fuzzy crystalline substance, and mirco structure does not have blocky α phaseExist. Compared with each loading zone, the axle α phase volume fractions such as transition region and crystallite dimension differ in 5%, mechanicsPerformance is close with each loading zone. Transition region microstructure Evolution is stable, there is no grain coarsening, uneven homogenize and abnormal growthPhenomenon.
Four, brief description of the drawings
Accompanying drawing 1 is the block diagram that nearly alpha titanium alloy isothermal local loads transition region structure property control method.
Five, detailed description of the invention
Embodiment mono-:
The TA15 whole titanium alloy gusset member that the present embodiment Shi Mou iron company produces, adopts by internal mold and external mold structureBecome the isothermal local of patrix to load die forming, internal mold Forming Workpiece mid portion, external mold Forming Workpiece both sides, workpieceThe position that upper internal mold and external mold line of demarcation are corresponding and adjacent area thereof are transition region. This TA15 titan alloy casting ingot adopts threeInferior vacuum consumable arc-melting, transformation temperature TβIt is 990 DEG C. Concrete operations are as follows:
The first step, blank change forging. TA15 titan alloy casting ingot is heated to T in resistance furnaceβ+ 100 DEG C, insulation 2h,Upsetting pull in quick forging machine, deflection 50%～60%, water-cooled after forging; Then blank is heated in resistance furnace to Tβ-40℃，Insulation 1.5h, upsetting pull repeatedly in quick forging machine, total deformation is 50～60%, water-cooled after forging.
Second step, preformed blank preparation. By the blank appearance parcel adiabatic cotton changing after forging, be heated to Tβ-40 DEG C, protectTemperature 2h, adopts open die forging and loose tooling forging to carry out base, after every fire completes, melts down heating at blank surface parcel adiabatic cotton,Heating-up temperature Tβ-40 DEG C, insulation 2h, totally six fire complete base.
The 3rd step, isothermal local load. On 8000 tons of isothermal forging hydraulic presses, carry out isothermal local loading. Adopt togetherInferior local loading, drafts is 28mm, average deformation amount 50%, point two loadings have walked.
First loads in step, blank is heated in chamber type electric resistance furnace to Tβ-30 DEG C, insulation 1h; Mold heated arrives
Tβ-50 DEG C. By the mid portion of internal mold Forming Workpiece, in shaping, internal mold presses down with the speed of 0.2mm/s, depressesAmount is 28mm. After internal mold has loaded, forging is taken out to water-cooled.
Second loads in step, first external mold is installed and is heated to Tβ-50 DEG C. Forging is heated in chamber type electric resistance furnace
Tβ-30 DEG C, be incubated 1 hour, put into subsequently mould and be shaped. External mold loading velocity 0.2mm/s, drafts 28mm.
The 4th step, finishing. On 8000 t hydraulic press, carry out. Interior external mold is depressed simultaneously, and forcing press pressurize tonnage is8000 tons, the time is 15min. After forging, take out fast forging water-cooled.
The 5th step, heat treatment. Forging heat treating regime is 970 DEG C × 1h water-cooled+840 DEG C × 3h air cooling.
The 6th step, Non-Destructive Testing.
Embodiment bis-:
The TA15 whole titanium alloy gusset member that the present embodiment Shi Mou iron company produces, adopts by internal mold and external mold structureBecome the isothermal local of patrix to load die forming, internal mold Forming Workpiece mid portion, external mold Forming Workpiece both sides, workpieceThe position that upper internal mold and external mold line of demarcation are corresponding and adjacent area thereof are transition region. This TA15 titan alloy casting ingot adopts threeInferior vacuum consumable arc-melting, transformation temperature TβIt is 990 DEG C. Concrete operations are as follows:
The first step, blank change forging. TA15 titan alloy casting ingot is heated to T in resistance furnaceβ+ 50 DEG C, insulation 3h, soonUpsetting pull on forging machine, deflection 50%～60%, water-cooled after forging; Then blank is heated in resistance furnace to Tβ-40℃，Insulation 1.5h, upsetting pull repeatedly in quick forging machine, total deformation is 50～60%, water-cooled after forging.
Second step, preformed blank preparation. By the blank appearance parcel adiabatic cotton changing after forging, be heated to Tβ-40 DEG C, protectTemperature 2h, adopts open die forging and loose tooling forging to carry out base, after every fire completes, melts down heating at blank surface parcel adiabatic cotton,Heating-up temperature is Tβ-40 DEG C, insulation 2h, totally four fire complete base.
The 3rd step, isothermal local load. On 8000 tons of isothermal forging hydraulic presses, carry out isothermal local loading. Adopt togetherInferior local loading, drafts is 28mm, average deformation amount 50%, point two loadings have walked.
First loads in step, blank is heated in chamber type electric resistance furnace to Tβ-30 DEG C, insulation 1h; Mold heated arrives
Tβ-50 DEG C. By the mid portion of internal mold Forming Workpiece, in shaping, internal mold presses down with the speed of 0.4mm/s, depressesAmount is 28mm. After internal mold has loaded, forging is taken out to water-cooled.
Second loads in step, first external mold is installed and is heated to Tβ-50 DEG C. Forging is heated in chamber type electric resistance furnace
Tβ-30 DEG C, be incubated 1 hour, put into subsequently mould and be shaped. External mold loading velocity 0.2mm/s, drafts 28mm.
The 4th step, finishing. On 8000 t hydraulic press, carry out. Interior external mold is depressed simultaneously, and forcing press pressurize tonnage is8000 tons, the time is 12min. After forging, take out fast forging water-cooled.
The 5th step, heat treatment. Forging heat treating regime is 960 DEG C × 2h water-cooled+840 DEG C × 2h air cooling.
The 6th step, Non-Destructive Testing.
Embodiment tri-:
The TA15 whole titanium alloy gusset member that the present embodiment Shi Mou iron company produces, adopts by left, center, right threeThe isothermal local that individual piecemeal mould forms patrix loads die forming, intermediate module Forming Workpiece mid portion, left and right mouldPiece motion Forming Workpiece simultaneously both sides, corresponding position and the phase thereof in the line of demarcation of intermediate module and left and right module on workpieceNeighbouring region is transition region. This TA15 titan alloy casting ingot adopts three vacuum consumable arc-meltings, transformation temperature TβIt is 990 DEG C.Concrete operations are as follows:
The first step, blank change forging. Ingot casting is heated to T in resistance furnaceβ+ 50 DEG C, insulation 3h, upsetting pull in quick forging machine,Deflection 50%～60%, water-cooled after forging; Then blank is heated in resistance furnace to Tβ-50 DEG C, insulation 1.5h,Upsetting pull repeatedly in quick forging machine, total deformation 50～60%, water-cooled after forging.
Second step, preformed blank preparation. By the blank appearance parcel adiabatic cotton changing after forging, be heated to Tβ-40 DEG C, protectTemperature 2h, adopts open die forging and loose tooling forging to carry out base, after every fire finishes, melts down heating at blank surface parcel adiabatic cotton,Heating-up temperature Tβ-40 DEG C, insulation 2h, totally four fire complete base.
The 3rd step, isothermal local load. On 8000 tons of isothermal forging hydraulic presses, carry out isothermal local loading. Adopt twiceInferior local loading, overall reduction is 28mm, average deformation amount 50%. The first reduction in pass 18mm, secondInferior drafts 10mm.
The first passage loads point two loadings and has walked. First loads step, first blank is heated in chamber type electric resistance furnaceTo Tβ-40 DEG C, insulation 1h; Mold heated is to Tβ-50 DEG C. By the mid portion of intermediate module Forming Workpiece, be shapedIn, intermediate module presses down with the speed of 0.4mm/s, and drafts is 18mm. After loading completes, forging is taken out to waterCold. Second loads step, first left module and right module is installed and is heated to Tβ-50 DEG C. Forging is added at chamber type electric resistance furnaceHeat is to Tβ-40 DEG C, insulation 1h, puts into subsequently mould and is shaped. Left module and right module are depressed simultaneously, loading velocityFor 0.4mm/s, drafts is 18mm. After the first passage completes, forging is taken out to water-cooled, and pull down external mold.
The second passage loads also divides two loadings to walk. First loads step, first forging is added in chamber type electric resistance furnaceHeat is to Tβ-40 DEG C, insulation 1h; Mold heated is to Tβ-50 DEG C. By the mid portion of intermediate module Forming Workpiece, becomeIn shape, intermediate module presses down with the speed of 0.4mm/s, and drafts is 10mm. After loading completes, forging is taken outWater-cooled. Second loads step, first left module and right module is installed and is heated to Tβ-50 DEG C. By forging at chamber type electric resistance furnaceBe heated to Tβ-40 DEG C, insulation 1h, puts into subsequently mould and is shaped. Left module and right module are depressed simultaneously, load speedDegree is 0.2mm/s, and drafts is 10mm.
The 3rd step, finishing. On 8000 tons of isothermal forging hydraulic presses, carry out. Three of left, center, right module is depressed simultaneously,Forcing press pressurize tonnage is 8000 tons, and the dwell time is 10min. After forging, take out fast forging water-cooled.
The 5th step, heat treatment. Forging heat treating regime is 970 DEG C × 1.5h water-cooled+850 DEG C × 2h air cooling.
The 6th step, Non-Destructive Testing.
Claims (2)
1. a nearly alpha titanium alloy isothermal local loading and shaping forging transition region structure property control method, comprises control blankChange forging, preformed blank preparation and local loading process condition, finishing process condition and forge after-baking, its spyLevy and be the control of transition region structure property through whole hot procedure, by the technique in controlled working processParameter, realizes transition region tissue and Properties Control, and detailed process is as follows:
The first step, blank change forging: titan alloy casting ingot is in the above cogging of transformation temperature, and ingot casting is heated to Tβ+(50～100℃)，Deflection is greater than 50%, water-cooled after forging; The blank obtaining is heated to TβThe two-phase section of-(40～50 DEG C) changes forging, becomesShape amount is greater than 50%, water-cooled after forging;
Second step, preformed blank preparation: by the blank appearance parcel adiabatic cotton changing after forging, be heated to Tβ-40 DEG C, adoptCarry out base with open die forging and loose tooling forging; Fire time bases as many in need, and adiabatic to blank parcel after each fire processingAfter cotton, melt down again heating;
The 3rd step, isothermal local loading and shaping:
A. workpiece is divided into some loading zones, mould is divided into corresponding several accordingly; In each loading passageUtilize the mould of piecemeal to carry out successively local loading to different loading zones; After all loadings complete, proceed to nextLoad passage, repeat the loading method of a loading passage, until arrive total deflection;
B. each loading passage is two work steps:
First loads work step, and blank is heated to Tβ-(30～40 DEG C), mold heated is to Tβ-50 DEG C, with piecemeal mould pairWorkpiece carries out local loading, and pressing speed is 0.2～0.4mm/s, and relative deformation equals total deformation or always becomes55%～65% of shape amount; As more mold exchange of need, by blank depanning water-cooled;
Second loads work step, and blank obtained in the previous step is heated to Tβ-(30～40 DEG C), mold heated is to Tβ-50℃，
By other parts of piecemeal die forming workpiece, pressing speed is 0.2～0.4mm/s, and relative deformation equals total change55%～65% of shape amount or total deformation;
The 4th step, finishing: finishing is carried out after last fire that completes local loading and shaping is inferior, adopts forcing press pressurizeComplete, the dwell time is 10min～15min;
The 5th step, heat treatment: after forging, take out immediately workpiece water-cooled, then adopt the heat treatment work of solid solution recrystallization annealingSkill, is heated to T by workpieceβ-(20～30 DEG C), insulation 1～2h, water-cooled; Workpiece is heated to recrystallization temperature, protectsTemperature 2～3h, air cooling;
The 6th step, Non-Destructive Testing.
2. a kind of nearly alpha titanium alloy isothermal local loading and shaping forging transition region structure property controlling party as claimed in claim 1Method, while it is characterized in that isothermal local loading and shaping adopts two passages to load, each pass deformation is greater than material and sends outThe critical strain amount of raw recrystallization, the 55%～65%, second passage distortion that the first pass deformation is total deformationAmount is 45%～35% of total deformation; The heating-up temperature of blank is Tβ-(30～40 DEG C), the heating-up temperature of mould is
Tβ-50 DEG C; Each loads work step, the strain rate 0.01～0.02s of material-1, corresponding deformation velocity is0.2～0.4mm/s; Need more when mold exchange forging depanning water-cooled.
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| CN200810076423.6A CN106134379B (en) | 2008-08-18 | 2008-08-18 | Microstructure and properties control method of near-α-type titanium alloy under isothermal local loading transition zone |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106734796A (en) * | 2016-12-14 | 2017-05-31 | 西部超导材料科技股份有限公司 | The engine forging method of high temperature resistant titanium alloy large scale rod bar |
| CN106971029A (en) * | 2017-03-10 | 2017-07-21 | 西北工业大学 | A kind of optimization method based on local loading and shaping gusset part prefabricated blank |
| CN108034911A (en) * | 2017-12-05 | 2018-05-15 | 西部超导材料科技股份有限公司 | The preparation method of the high uniformly TC11 alloy bar materials of blade |
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| CN114231791A (en) * | 2021-12-20 | 2022-03-25 | 安徽宝泰特种材料有限公司 | Large-caliber titanium alloy seamless pipe and preparation method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN106734796A (en) * | 2016-12-14 | 2017-05-31 | 西部超导材料科技股份有限公司 | The engine forging method of high temperature resistant titanium alloy large scale rod bar |
| CN106734796B (en) * | 2016-12-14 | 2018-11-06 | 西部超导材料科技股份有限公司 | The forging method of engine high temperature resistant titanium alloy large scale rod bar |
| CN106971029A (en) * | 2017-03-10 | 2017-07-21 | 西北工业大学 | A kind of optimization method based on local loading and shaping gusset part prefabricated blank |
| CN106971029B (en) * | 2017-03-10 | 2020-06-16 | 西北工业大学 | Method for optimizing pre-formed blank of forming rib plate based on local loading |
| CN108034911A (en) * | 2017-12-05 | 2018-05-15 | 西部超导材料科技股份有限公司 | The preparation method of the high uniformly TC11 alloy bar materials of blade |
| CN109822028A (en) * | 2019-03-05 | 2019-05-31 | 中国第二重型机械集团德阳万航模锻有限责任公司 | Press forges titanium alloy forging anti-deformation control method |
| CN114231791A (en) * | 2021-12-20 | 2022-03-25 | 安徽宝泰特种材料有限公司 | Large-caliber titanium alloy seamless pipe and preparation method thereof |
| CN114231791B (en) * | 2021-12-20 | 2022-06-21 | 安徽宝泰特种材料有限公司 | Water flushing tank for large-diameter titanium alloy seamless pipe |
| CN114959525A (en) * | 2022-04-29 | 2022-08-30 | 中国科学院金属研究所 | High-temperature titanium alloy hot processing preparation method with mixed structure and high-strength characteristics |
| CN114959525B (en) * | 2022-04-29 | 2023-11-10 | 中国科学院金属研究所 | High-temperature titanium alloy hot working preparation method with mixed structure and high strength characteristics |
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