CN101629273B - Method for realizing near alpha titanium alloy dual-property employing local loading process - Google Patents
Method for realizing near alpha titanium alloy dual-property employing local loading process Download PDFInfo
- Publication number
- CN101629273B CN101629273B CN2009100235877A CN200910023587A CN101629273B CN 101629273 B CN101629273 B CN 101629273B CN 2009100235877 A CN2009100235877 A CN 2009100235877A CN 200910023587 A CN200910023587 A CN 200910023587A CN 101629273 B CN101629273 B CN 101629273B
- Authority
- CN
- China
- Prior art keywords
- district
- loading
- loads
- zone
- workpiece
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
Images
Landscapes
- Forging (AREA)
Abstract
The invention discloses a method for realizing near alpha titanium alloy dual-property employing local loading process, which divides a workpiece into an A loading zone and a B loading zone, and a C zone is the transition zone between the A loading zone and the B loading zone, wherein the A loading zone is a large deformation zone while the B loading zone is a small deformation zone, and the method is realized through the isothermal local loading with two passes and two loading steps in each pass. The specific shaping process comprises blank forging, preparation of preforming billet, isothermal local loading, finishing, thermal treatment and nondestructive testing. The shaped workpiece can obtain the tri-modal microstructure with high room temperature plasticity, high strength and long fatigue life and 20% equiaxial alpha phase content in the A loading zone, the lamellar microstructure with high tensile strength at high temperature, high fracture toughness and strong creep deformation resistance in the B loading zone, and the bimodal microstructure with higher equiaxial alpha phase content in the C transition zone than in the A loading zone so as to further realize the dual-property of the integral component; therefore, the method is a simple and efficient shaping method for the integral dual-property component.
Description
One, technical field
The present invention relates to the hot-work field, specifically is a kind of method that adopts local loading process to realize near alpha titanium alloy dual-property.
Two, background technology
For the comparatively complicated member of some Service Environment, the force-bearing situation of same member different sites is different often with Service Environment.What particularly this type of situation showed in the aerospace member is particularly outstanding.Some girder constructions in the aircraft for example, hot operation end temperature is higher, and the inboardend working temperature is relatively low but need the big stress of carrying.In order to satisfy high-performance and high reliability, objectively require should have high high temperature tensile strength, fracture toughness property and creep resisting ability at the hot operation end of beam, inboardend should have high room temperature tensile intensity, plasticity and fatigue strength simultaneously.The and for example compressor disc in the jet engine and the turbine disk, working order exists big thermograde and stress gradient, disk body (core is to the integral part that coils spoke) links to each other with axle, bear and be fixed on the centrifugal tensile stress that the blade high speed rotating on the dish edge tenon tooth produces, and owing to the inhomogeneous thermal stresses that produces of being heated along wheel disc radius and thickness direction, stress is big but temperature is lower; Dish edge (fir shape tenon part) links to each other with blade and is subjected to the stress of centrifugal tensile stress, thermal stress and blade vibration generation that blade rotation produces, and is stressed less but temperature is higher.Therefore require disk body that high room temperature tensile intensity, plasticity and low cycle fatigue intensity are arranged, and the dish edge require to have high high temperature tensile strength, fracture toughness property and creep creep rupture strength.Even integrated member has different mechanical properties at different sites, realize dual-property, better adapt to service condition, increase the service life.At present, the Technology of making whole dual-property mainly contains powder metallurgy, the shaping of combination base isothermal forging, thermomechanical treatment, gradient thermal treatment etc.Yet these methods exist mostly that the technical process complexity is wayward, production efficiency is low, and powder metallurgy is shaped with combination base isothermal forging and also has interface problems such as " the weak connections ".
Three, summary of the invention
The technical process complexity that exists in the prior art is wayward, production efficiency is low and interface problems such as " weak connections " in order to overcome, and the present invention proposes a kind of method that adopts local loading process to realize near alpha titanium alloy dual-property.
Concrete forming process of the present invention is:
The first step, blank changes forging
Titanium alloy bar is heated to T
β+ (40～50 ℃), insulation 1～2h carries out jumping-up, pulling, and deflection 50%～70% is forged the back water-cooled to room temperature, to improve the metallurgical quality of material, improves the tissue and the homogeneity of ingredients of material; The blank that obtains is heated to T
βThe two-phase region of-(40～50 ℃) changes forging, repeatedly jumping-up, pull out to deflection be 50%～70%; Forge the back water-cooled to room temperature, to obtain tiny equiaxed structure.
Second step, the precast billet preparation
To change blank heating after the forging to T
β-40 ℃, insulation 1～2h adopts flat-die forging to carry out base, obtains to satisfy the precast billet of original shape requirement, forges the back water-cooled; Again precast billet is heated to T
β+ (20～30 ℃), insulation 1～2h, water-cooled is to room temperature.Thereby obtain to have the precast billet of martensite α ' tissue.Blank surface car light, the defective detail sanding.
According to actual needs, workpiece is divided into two loading zones in A district and B district, the C district is the zone of transition between A and B.Wherein the A district is gross distortion zone (becoming the inboardend of ellbeam and the disk body of wheel disc), and deflection is 50%～60%, and B district is a deflection in 20%～30% small deformation zone (the hot operation end of one-tenth ellbeam and the dish edge of wheel disc).
In the 3rd step, isothermal local loads
Local loading is finished two passages, and each passage loads to go on foot by two to be formed.Concrete steps are as follows:
First passage first loads the step, and blank heating is arrived T
β-(40～50 ℃), mold heated is to T
β-60 ℃, workpiece A district is carried out local loading; The speed of depressing that loads is 0.2～0.4mm/s; The control draught makes the material deformation amount between 50%～60%.
First passage second loads the step, and blank heating is arrived T
β-(40～50 ℃), mold heated is to T
β-60 ℃, workpiece B district is carried out local loading; The speed of depressing that loads is 0.2～0.4mm/s; The control draught makes the material deformation amount between 20%～30%, and first loads passage finishes, and takes out workpiece water and is chilled to room temperature.
Second passage first loads the step, and blank heating is arrived T
β-(15～20 ℃), mold heated is to T
β-30 ℃, workpiece A district is carried out local loading; The speed of depressing that loads is 0.2～0.4mm/s; The control draught makes the material deformation amount between 20%～30%.
Second passage second loads the step, and blank heating is arrived T
β-(15～20 ℃), mold heated is to T
β-30 ℃, workpiece B district is carried out local loading; The speed of depressing that loads is 0.2～0.4mm/s; The control draught makes the material deformation amount between 20%～30%.
The 4th step, finishing
After the second passage local loading was finished, directly A, the B district to workpiece loaded simultaneously, depresses speed 0.05～0.1mm/s, and control A, B district draught make the material deformation amount in 10%.After reaching the predetermined deformation amount, whole pressurize 10min～15min.
The 5th step, thermal treatment
Forge the back workpiece water and be chilled to room temperature, adopt the thermal treatment process of recrystallization annealing, workpiece is heated to recrystallization temperature, insulation 1～2h, air cooling is to room temperature.
The 6th step, nondestructive testing.
The workpiece that adopts heat processing technique of the present invention to be shaped axle α phase content such as can obtain in A district and be about 20% three-state tissue, obtains the basket tissue in the B district, and a α phase content such as zone of transition C district is high than the A district, is the bifurcation tissue.So drip molding has high temperature-room type plasticity, intensity and long fatigue lifetime in the A district, the B district has high hot strength, creep rupture strength, fracture toughness property and creep strength, even integrated member obtains dual-property.
The present invention proposes the whole dual-property component forming of a kind of advantages of simplicity and high efficiency method, promptly under specified temp, method by local loading is accurately controlled local deformaton, thereby obtain different predetermined tissues at different loading zones, obtain having high room temperature tensile intensity in the gross distortion district, plasticity, fatigue strength and comprehensive mechanical property etc. the axle three-state tissue of α phase content about 20%, obtain having high high temperature tensile strength in the small deformation district, the basket tissue of fracture toughness property and creep resisting ability, zone of transition is the bifurcation tissue, thereby realizes the dual-property of integrated member.
Four, description of drawings
Accompanying drawing 1 is a process flow sheet;
Accompanying drawing 2 is that dual-property rectangular beam isothermal local loads synoptic diagram;
Accompanying drawing 3 is three-state tissues that embodiment one dual-property rectangular beam drip molding A district obtains;
Accompanying drawing 4 is basket tissues that embodiment one dual-property rectangular beam drip molding B district obtains;
Accompanying drawing 5 is bifurcation tissues that embodiment one dual-property rectangular beam drip molding C district obtains;
Accompanying drawing 6 is three-state tissues that embodiment two dual-property rectangular beam drip molding A districts obtain;
Accompanying drawing 7 is basket tissues that embodiment two dual-property rectangular beam drip molding B districts obtain;
Accompanying drawing 8 is bifurcation tissues that embodiment two dual-property rectangular beam drip molding C districts obtain;
Accompanying drawing 9 is that dual-property wheel disc isothermal local loads synoptic diagram;
Accompanying drawing 10 is three-state tissues that dual-property wheel disc drip molding A district obtains;
Accompanying drawing 11 is basket tissues that dual-property wheel disc drip molding B district obtains;
Accompanying drawing 12 is bifurcation tissues that dual-property wheel disc drip molding C district obtains.
Five, specific embodiments
Embodiment one
Present embodiment is a kind of method that adopts local loading process to realize near rectangular beam dual-property.
The starting material of present embodiment adopt the TA15 titanium alloy rod bar of Φ 300mm, and nominal composition is Ti-6Al-2Zr-1Mo-1V, transformation temperature T
βBe 990 ℃, 830 ℃ of recrystallization temperatures.Detailed process is as follows:
The first step, blank changes forging
Bar is heated to T in chamber type electric resistance furnace
β+ 40 ℃, insulation 2h carries out jumping-up, pulling on the forging machine soon, and deflection 50%～70% is forged back water-cooled to 25 ℃; Then the blank that obtains is heated to T
β-50 ℃, insulation 2h is changing forging on fast forging machine, jumping-up, pulling repeatedly, and deflection 50%～70% is forged back water-cooled to 25 ℃.
Second step, the precast billet preparation
To change blank heating after the forging in the chamber type electric resistance furnace to T
β-40 ℃, insulation 1h adopts flat-die forging to carry out base, obtains step-like precast billet, forges back water-cooled to 25 ℃; Again precast billet is heated to T
β+ 20 ℃, insulation 1h, water-cooled.Blank surface car light, the defective detail sanding obtains as shown in Figure 2 that A district thickness is 80mm, and B district thickness is the precast billet of 50mm.Wherein A district and B district are two loading zones, and the C district is the zone of transition between A and B.The A district is the gross distortion zone, and deflection is 50%～60%, becomes the inboardend of ellbeam, B district be deflection in 20%～30% small deformation zone, the hot operation end of one-tenth ellbeam.
In the 3rd step, isothermal local loads
Blank heats in chamber type electric resistance furnace, carries out isothermal local and load on 800 tons of isothermal hydropress, divides two passages to finish, and every time loads to go on foot by two forms.Concrete steps are as follows:
First passage first loads the step, and blank heating is arrived T
β-40 ℃, mold heated is to T
β-60 ℃, workpiece A district is carried out local loading; The speed of the depressing 0.2mm/s that loads, draught 40mm, the material deformation amount is 50%.
First passage second loads the step, and blank heating is arrived T
β-40 ℃, mold heated is to T
β-60 ℃, workpiece B district is carried out local loading; The speed of the depressing 0.2mm/s that loads, draught 10mm, the material deformation amount is that the loading of 20%, the first passage is finished, and takes out the workpiece water-cooled.
Second passage first loads the step, and blank heating is arrived T
β-15 ℃, mold heated is to T
β-30 ℃, workpiece A district is carried out local loading; The speed of the depressing 0.2mm/s that loads, draught 8mm, the material deformation amount is 20%.
Second passage second loads the step, and blank heating is arrived T
β-15 ℃, mold heated is to T
β-30 ℃, workpiece B district is carried out local loading; The speed of the depressing 0.2mm/s that loads, draught 8mm, the material deformation amount is 20%.
The 4th step, finishing
After the second passage local loading was finished, directly A, the B district to workpiece loaded simultaneously, depresses speed 0.1mm/s.A, B district draught are 1mm, and the material deformation amount is 3%.Whole pressurize 10min.
The 5th step, thermal treatment
Forge the back workpiece water and be chilled to 25 ℃, again workpiece is heated to 830 ℃ in chamber type electric resistance furnace, insulation 1h, air cooling to 25 ℃.
The 6th step, nondestructive testing.
Embodiment two
Present embodiment is a kind of method that adopts local loading process to realize near rectangular beam dual-property.
The starting material of present embodiment adopt the TA15 titanium alloy rod bar of Φ 500mm, and nominal composition is Ti-6Al-2Zr-1Mo-1V, transformation temperature T
βBe 990 ℃, 830 ℃ of recrystallization temperatures.Detailed process is as follows:
The first step, blank changes forging
Bar is heated to T in chamber type electric resistance furnace
β+ 50 ℃, insulation 1h carries out jumping-up, pulling on the forging machine soon, and deflection 50%～70% is forged back water-cooled to 25 ℃; Then the blank that obtains is heated to T
β-40 ℃, insulation 1h is changing forging on fast forging machine, jumping-up, pulling repeatedly, and deflection 50%～70% is forged back water-cooled to 25 ℃.
Second step, the precast billet preparation
To change blank heating after the forging in the chamber type electric resistance furnace to T
β-40 ℃, insulation 2h adopts flat-die forging to carry out base, obtains step-like precast billet, forges back water-cooled to 25 ℃; Again precast billet is heated to T
β+ 30 ℃, insulation 2h, water-cooled.Blank surface car light, the defective detail sanding obtains as shown in Figure 2 that A district thickness is 150mm, and B district thickness is the precast billet of 90mm.Wherein A district and B district are two loading zones, and the C district is the zone of transition between A and B.The A district is the gross distortion zone, and deflection is 50%～60%, becomes the inboardend of ellbeam, B district be deflection in 20%～30% small deformation zone, the hot operation end of one-tenth ellbeam.
In the 3rd step, isothermal local loads
Blank heats in chamber type electric resistance furnace, carries out isothermal local and load on 800 tons of isothermal hydropress, divides two passages to finish, and every time loads to go on foot by two forms.Concrete steps are as follows:
First passage first loads the step, and blank heating is arrived T
β-50 ℃, mold heated is to T
β-60 ℃, workpiece A district is carried out local loading; The speed of the depressing 0.4mm/s that loads, draught 90mm, the material deformation amount is 60%.
First passage second loads the step, and blank heating is arrived T
β-50 ℃, mold heated is to T
β-60 ℃, workpiece B district is carried out local loading; The speed of the depressing 0.4mm/s that loads, draught 27mm, the material deformation amount is that the loading of 30%, the first passage is finished, and takes out the workpiece water-cooled.
Second passage first loads the step, and blank heating is arrived T
β-20 ℃, mold heated is to T
β-30 ℃, workpiece A district is carried out local loading; The speed of the depressing 0.4mm/s that loads, draught 18mm, the material deformation amount is 30%.
Second passage second loads the step, and blank heating is arrived T
β-20 ℃, mold heated is to T
β-30 ℃, workpiece B district is carried out local loading; The speed of the depressing 0.4mm/s that loads, draught 19mm, the material deformation amount is 30%.
The 4th step, finishing
After the second passage local loading was finished, directly A, the B district to workpiece loaded simultaneously, depresses speed 0.05mm/s.A district draught 1mm, the material deformation amount is 2%, B district draught 3mm, the material deformation amount is 7%.Whole pressurize 15min.
The 5th step, thermal treatment
Forge the back workpiece water and be chilled to 25 ℃, again workpiece is heated to 830 ℃ in chamber type electric resistance furnace, insulation 2h, air cooling to 25 ℃.
The 6th step, nondestructive testing.
Embodiment three
Present embodiment is a kind of method that adopts local loading process to realize near wheel disc dual-property.
The starting material of present embodiment adopt the TA15 titanium alloy rod bar of Φ 400mm, nominal composition Ti-6Al-2Zr-1Mo-1V, transformation temperature T
βBe 990 ℃, 830 ℃ of recrystallization temperatures.Concrete operations are as follows:
The first step, blank changes forging
Bar is heated to T in chamber type electric resistance furnace
β+ 40 ℃, insulation 2h carries out jumping-up, pulling on the forging machine soon, and deflection 50%～70% is forged back water-cooled to 20 ℃; Then the blank that obtains is heated to T
β-40 ℃, insulation 2h is changing forging on fast forging machine, jumping-up, pulling repeatedly, and deflection 50%～70% is forged back water-cooled to 20 ℃.
Second step, the precast billet preparation
To change blank heating after the forging in the chamber type electric resistance furnace to T
β-40 ℃, insulation 2h adopts flat-die forging to carry out base, obtains the round pie precast billet, forges back water-cooled to 20 ℃; Again precast billet is heated to T
β+ 20 ℃, insulation 2h, water-cooled to 20 ℃.Blank surface car light, the defective detail sanding obtains the precast billet of Φ 200mm * 55mm as shown in Figure 6.Blank is divided into two loading zones in A district and B district, and the C district is the zone of transition between A and B.Wherein the A district is the gross distortion zone, the disk body part of shaping wheel disc, deflection is 50%～60%, the B district be deflection in 20%～30% small deformation zone, the dish edge part of shaping wheel disc.
In the 3rd step, isothermal local loads
Blank heats in chamber type electric resistance furnace, carries out isothermal local and load on 800 tons of isothermal hydropress, divides two passages to finish, and every time loads to go on foot by two forms.Concrete steps are as follows:
First passage first loads the step, and blank heating is arrived T
β-40 ℃, mold heated is to T
β-60 ℃, workpiece A district is carried out local loading; The speed of the depressing 0.3mm/s that loads, draught 30mm, the material deformation amount is 55%.
First passage second loads the step, and blank heating is arrived T
β-40 ℃, mold heated is to T
β-60 ℃, workpiece B district is carried out local loading; The speed of the depressing 0.3mm/s that loads, draught 14mm, the material deformation amount is 25%.First passage loads and finishes, and takes out workpiece water and is chilled to 20 ℃.
Second passage first loads the step, and blank heating is arrived T
β-15 ℃, mold heated is to T
β-30 ℃, workpiece A district is carried out local loading; The speed of the depressing 0.3mm/s that loads, draught 6mm, the material deformation amount is 25%.
Second passage second loads the step, and blank heating is arrived T
β-15 ℃, mold heated is to T
β-30 ℃, workpiece B district is carried out local loading; Load, depress speed 0.3mm/s, draught 7.5mm, the material deformation amount is 25%.
The 4th step, finishing
After the second passage local loading was finished, directly A, the B district to workpiece loaded simultaneously, depresses speed 0.1mm/s, and A, B district draught are 0.5mm, and the material deformation amount is 1%.Whole pressurize 10min.
The 5th step, thermal treatment
Forge the back workpiece water and be chilled to 20 ℃, again workpiece is heated to 830 ℃ in chamber type electric resistance furnace, insulation 1.5h, air cooling to 20 ℃.
The 6th step, nondestructive testing.
Claims (1)
1. a method that adopts local loading process to realize near alpha titanium alloy dual-property is divided into two loading zones in A district and B district with workpiece, and the C district is the zone of transition between A and B; Wherein the A district is the gross distortion zone, and deflection is 50%～60%, and the B district is a deflection in 20%～30% small deformation zone; The isothermal local that loads the step by two passages, two of each passages loads the realization shaping; It is characterized in that concrete forming process is:
The first step, blank changes forging;
Titanium alloy bar is heated to T
β+ (40～50 ℃), insulation 1～2h carries out jumping-up, pulling, and deflection is 50%～70%, forges the back water-cooled to room temperature; The blank that obtains is heated to T
βThe two-phase region of-(40～50 ℃) changes forging, repeatedly jumping-up, pull out to deflection be 50%～70%, forge the back water-cooled to room temperature;
Second step, the precast billet preparation;
To change blank heating after the forging to T
β-40 ℃, insulation 1～2h adopts flat-die forging to carry out base, forges the back water-cooled to room temperature; Precast billet is heated to T
β+ (20～30 ℃), insulation 1～2h, water-cooled is to room temperature; Blank surface car light, the defective detail sanding;
In the 3rd step, isothermal local loads; Comprise,
A. first passage first loads the step, and blank heating is arrived T
β-(40～50 ℃), mold heated is to T
β-60 ℃, workpiece A district is carried out local loading; The speed of the depressing 0.2～0.4mm/s that loads; It is 50%～60% that the control draught makes the material deformation amount;
B. first passage second loads the step, and blank heating is arrived T
β-(40～50 ℃), mold heated is to T
β-60 ℃, workpiece B district is carried out local loading; The speed of the depressing 0.2～0.4mm/s that loads; It is that 20%～30%, the first loading passage is finished that the control draught makes the material deformation amount, takes out workpiece water and is chilled to room temperature;
C. second passage first loads the step, and blank heating is arrived T
β-(15～20 ℃), mold heated is to T
β-30 ℃, workpiece A district is carried out local loading; The speed of the depressing 0.2～0.4mm/s that loads; It is 20%～30% that the control draught makes the material deformation amount;
D. second passage second loads the step, and blank heating is arrived T
β-(15～20 ℃), mold heated is to T
β-30 ℃, workpiece B district is carried out local loading; The speed of the depressing 0.2～0.4mm/s that loads; It is 20%～30% that the control draught makes the material deformation amount;
The 4th step, finishing;
After the second passage local loading was finished, directly A, the B district to workpiece loaded simultaneously, depresses speed 0.05～0.1mm/s, and control A, B district draught make the material deformation amount in 10%; After reaching the predetermined deformation amount, whole pressurize 10min～15min;
The 5th step, thermal treatment;
Forge the back workpiece water and be chilled to room temperature, workpiece is heated to recrystallization temperature, insulation 1～2h, air cooling is to room temperature;
The 6th step, nondestructive testing.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2009100235877A CN101629273B (en) | 2009-08-14 | 2009-08-14 | Method for realizing near alpha titanium alloy dual-property employing local loading process |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2009100235877A CN101629273B (en) | 2009-08-14 | 2009-08-14 | Method for realizing near alpha titanium alloy dual-property employing local loading process |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101629273A CN101629273A (en) | 2010-01-20 |
| CN101629273B true CN101629273B (en) | 2010-12-08 |
Family
ID=41574549
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2009100235877A Expired - Fee Related CN101629273B (en) | 2009-08-14 | 2009-08-14 | Method for realizing near alpha titanium alloy dual-property employing local loading process |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101629273B (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102212765B (en) * | 2011-04-14 | 2012-11-28 | 西北工业大学 | Method for obtaining tri-state structure during titanium alloy local loading formation |
| CN102367563B (en) * | 2011-10-13 | 2013-06-26 | 北京航空航天大学 | Titanium alloy thin-wall part hot-stretch creep deformation composite molding method |
| CN102500675B (en) * | 2011-10-13 | 2013-12-04 | 北京航空航天大学 | Hot forming tool of titanium alloy thin-wall part and machining method of hot forming tool |
| CN102758158B (en) * | 2012-08-02 | 2013-12-04 | 西北工业大学 | Method for obtaining tri-state tissue from near alpha titanium alloy in alpha+beta two-phase region |
| CN108188659A (en) * | 2017-12-21 | 2018-06-22 | 中国原子能科学研究院 | A kind of manufacturing process of steel billet |
| CN112760583B (en) * | 2020-12-23 | 2022-02-18 | 宁波江丰电子材料股份有限公司 | Heat treatment process of titanium material |
-
2009
- 2009-08-14 CN CN2009100235877A patent/CN101629273B/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| CN101629273A (en) | 2010-01-20 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101629273B (en) | Method for realizing near alpha titanium alloy dual-property employing local loading process | |
| CN109454188B (en) | Free forging method of Ti55531 titanium alloy large-size bar | |
| US11021780B2 (en) | Method for manufacturing nickel-based alloy high-temperature component | |
| CN102896267B (en) | Isothermal forging method of TC17 titanium alloy disc-shaped forge piece | |
| JP5669451B2 (en) | Method for producing forged pieces from γ titanium-aluminum-mother alloy | |
| CN112296602B (en) | Manufacturing method of double-alloy double-structure titanium alloy blisk | |
| CN109482796B (en) | Beta forging and heat treatment method of TC4 titanium alloy disc forging | |
| CN103173694B (en) | The preparation method of high temperature resistant securing member | |
| CN107427896A (en) | The manufacture method of Ni base superalloy | |
| CN102581188B (en) | Method for machining TC4-DT titanium alloy large-specification slab forged piece | |
| CN111906225B (en) | Forging method of oversized Ti80 titanium alloy forging stock | |
| CN105506525A (en) | Preparation method of Ti2AlNb-based alloy large-size uniform fine-grain bar | |
| CN102873166B (en) | Aircraft spherical shell isothermal forming method and device | |
| CN105734473A (en) | Isothermal forging structure control method of TC17 titanium alloy | |
| CN102758161B (en) | Method for obtaining tri-state tissue from titanium alloy | |
| CN106435404A (en) | Low wind speed wind power unit low-carbon alloy steel wind power main shaft manufacturing method | |
| KR101330641B1 (en) | A Manufacturing method for profiled ring of Ni-base superalloy for obtaining a uniform microstructure | |
| Behrens et al. | Thermomechanical processing for creating bi-metal bearing bushings | |
| CN105603347A (en) | Method for obtaining tri-state texture in titanium alloy near-isothermal local loading forming process | |
| CN102758159A (en) | Method for acquiring titanium alloy tristate structure by forging and heat treatment | |
| CN112376005B (en) | Method for manufacturing TA11 titanium alloy bar | |
| Gupta et al. | Effect of variants of thermomechanical working and annealing treatment on titanium alloy Ti6Al4V closed die forgings | |
| CN113957360A (en) | Heat treatment method for preventing austenitic stainless steel cast piece from cracking | |
| RU209367U1 (en) | MONOBLOCK BLANK BLISK | |
| CN102259182B (en) | Method for preparing high-performance molybdenum cake material by using smelting method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20101208 Termination date: 20170814 |