CN102665946A - Method for producing a high-strength and highly ductile titanium alloy - Google Patents
Method for producing a high-strength and highly ductile titanium alloy Download PDFInfo
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- CN102665946A CN102665946A CN2010800535482A CN201080053548A CN102665946A CN 102665946 A CN102665946 A CN 102665946A CN 2010800535482 A CN2010800535482 A CN 2010800535482A CN 201080053548 A CN201080053548 A CN 201080053548A CN 102665946 A CN102665946 A CN 102665946A
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- titanium alloy
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- microscopic structure
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- 229910001069 Ti alloy Inorganic materials 0.000 title claims abstract description 45
- 238000004519 manufacturing process Methods 0.000 title abstract 3
- 238000005096 rolling process Methods 0.000 claims abstract description 30
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 17
- 238000011282 treatment Methods 0.000 claims abstract description 11
- 238000002360 preparation method Methods 0.000 claims description 12
- 238000000034 method Methods 0.000 abstract description 27
- 238000010438 heat treatment Methods 0.000 abstract description 7
- 229910045601 alloy Inorganic materials 0.000 description 8
- 239000000956 alloy Substances 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 7
- 229910000883 Ti6Al4V Inorganic materials 0.000 description 6
- 238000001816 cooling Methods 0.000 description 6
- 238000002474 experimental method Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- 230000009977 dual effect Effects 0.000 description 2
- 239000010936 titanium Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 238000005275 alloying Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 239000002159 nanocrystal Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 239000010955 niobium Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- 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
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Metal Rolling (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
Disclosed is a method for producing a high-strength and highly ductile titanium alloy. The method for producing a high-strength and highly ductile titanium alloy comprises the following steps: providing a titanium alloy having a martensitic structure; and partially and dynamically spheroidizing a microstructure of said titanium alloy having a martensitic structure through heat and mechanical treatments. The method of the present invention produces a titanium alloy having a partially and dynamically spheroidized microstructure, and provides the titanium alloy with superior yield strength (YS) and uniform elongation (U.EL). The method of the present invention involves adjusting a rolling direction and deformation with respect to a layered microstructure, and thus enables the microstructure to have a micro-equiaxial structure and a layered structure coexisting therein. The method of the present invention can produce a titanium alloy having an improved product of yield strength and uniform elongation (YS*U.EL) as compared to conventional heat treatment methods.
Description
Technical field
The present invention relates to a kind of titanium alloy, relate more specifically to a kind of partial dynamic nodularization of passing through, have a kind of preparation method of titanium alloy of microscopic structure, said microscopic structure is mixed and is had small equiaxed structure and lamellar tissue.
Background technology
Like titanium alloy, in the employed metal material, yield strength and uniform elongation are very important mechanical properties in extreme environment.When applying than the bigger intensity of its yield strength from the outside to the titanium alloy that is mainly used in structural material, material can produce permanent deformation, and it is extremely important therefore to obtain high-yield strength.
And when producing than the bigger distortion of uniform elongation, the fragile part of material possibly produce constriction and rupture, and therefore in order to improve the reliability of structural material, it also is essential obtaining high uniform elongation.
Yet when preparing titanium alloy with general heat treatment, yield strength and uniform elongation have the tendency of mutual inverse ratio, therefore propose the multiple method that overcomes this tendency.Disclose in Korea S's publication number 2009-0069647 number (2009.07.01) recently and a kind ofly compared with pure titanium, improved the method for intensity and toughness through being prepared in the alloy that adds niobium in the titanium.
But the method is about the alloyage process before heat/mechanical treatment, with this method that intensity that makes the alloy of having developed through heat/mechanical treatment after the alloying and toughness increase, its category difference.
In addition, in first to file korean application number 10-2009-0083931 number (2009.09.07), disclosing of the applicant is a kind of to having the titanium alloy of stratiform microscopic structure, through implementing the method that tandem rolling makes grain ultrafining in warm zone.
More specifically; Initial microscopic structure is induced to behind the martensite of being made up of small layer structure; Through observing the influence to the variation generation of microscopic structure such as deflection, rate of deformation, deformation temperature; Make the state-variable optimization, thus the titanium alloy that preparation has the equiaxed structure of nanocrystal under low deflection.
Though but said method has the advantage that has improved yield strength greatly; But have and compare the significantly reduced shortcoming of uniform elongation with general heat treatment method; Therefore compare with general microscopic structure, have the shortcoming that the product of yield strength and uniform elongation does not improve or diminishes on the contrary.
Therefore reliability and the application in order to enlarge titanium alloy needs a kind of heat/mechanical treatment that passes through, and makes yield strength and the uniform elongation technology of balance more.
Summary of the invention
The object of the present invention is to provide a kind of preparation method of titanium alloy; This method is in order to keep the balance of yield strength and uniform elongation; Through heat and mechanical treatment titanium alloy, make the nodularization of microscopic structure partial dynamic, make to mix in the titanium alloy to have equiaxed structure and lamellar tissue.
High strength according to a preferred embodiment of the invention, the preparation method of high-tenacity titanium alloy may further comprise the steps: the titanium alloy with martensitic structure is provided; Reach titanium alloy, make the nodularization of microstructure partial dynamic through heat and the said martensitic structure of mechanical treatment.
The microscopic structure of the said titanium alloy that is provided comprises the martensitic structure of stratiform.
The invention is characterized in that said heat and mechanical treatment are at 775 ℃～875 ℃ deformation temperature, 0.07s
-1～0.13s
-1Rate of deformation ,-0.2～-1.6 deflection scope in rolling.
In addition, the invention is characterized in that said heat and mechanical treatment are at 800 ℃ deformation temperature, 0.1s
-1Rate of deformation ,-0.2～-1.6 deflection scope in rolling.
The invention is characterized in, said rolling through unidirection rolling (uni-directional rolling) realization.
The invention is characterized in,, have small equiaxed structure and lamellar tissue simultaneously in the microscopic structure of said titanium alloy through said partial dynamic nodularization.
Utilize the present invention can produce a kind of the have outstanding yield strength and the titanium alloy of uniform elongation, in environment for use, can improve reliability, also can enlarge its range of application.
Description of drawings
Fig. 1 is the optical microscope photograph with Ti-6Al-4V alloy of initial equiaxed structure.
Fig. 2 for show with titanium alloy 1040 ℃ keep 1 hour after, the photo of the martensitic structure that obtains through water-cooled.
Fig. 3 for show with titanium alloy 1040 ℃ keep 4 hours after, carry out air cooling, again in 730 ℃ keep 4 hours after, the photo of the thick lamellar tissue that obtains through air cooling.
Fig. 4 for show with titanium alloy 950 ℃ keep 4 hours after, carry out water-cooled, again in 540 ℃ keep 6 hours after, the photo of the dual tissue that obtains through air cooling.
The Ti-6Al-4V alloy of Fig. 5 for having martensitic structure is with 800 ℃ of deformation temperatures, rate of deformation 0.1s
-1And deflection-0.2 is when carrying out unidirection rolling, the EBSD photo of microscopic structure.
Fig. 6 is with 800 ℃ of deformation temperatures, rate of deformation 0.1s
-1And during deflection-0.8 unidirection rolling, the EBSD photo of microscopic structure.
Fig. 7 is with 800 ℃ of deformation temperatures, rate of deformation 0.1s
-1And during deflection-1.2 unidirection rolling, the EBSD photo of microscopic structure.
Fig. 8 is with 800 ℃ of deformation temperatures, rate of deformation 0.1s
-1And during deflection-1.6 unidirection rolling, the EBSD photo of microscopic structure.
EBSD photo when Fig. 9 is the Ti-6Al-4V alloy tandem rolling that will have martensitic structure, this moment, process conditions were 800 ℃ of deformation temperatures, rate of deformation 0.1s
-1And deflection-1.6.
Figure 10 to Figure 12 is for showing the normal temperature stretching experiment result of the titanium alloy with each microscopic structure, and Figure 10 is an average yield strength, and Figure 11 is average uniform elongation, and Figure 12 is the product of average yield strength and average uniform elongation.
The specific embodiment
Below, describe the present invention in detail.
For the microscopic structure (being the small simultaneous microscopic structure of equiaxed structure and lamellar tissue) that obtains the partial dynamic nodularization; Initial microscopic structure is induced to behind the martensite of being made up of small layer structure the influence that observation deflection, rate of deformation, deformation temperature etc. cause the variation of microscopic structure.
Fig. 1 to Fig. 4 is the photo that utilizes observation by light microscope to arrive, and is the representative microscopic structure that can obtain through known heat treatment method.Fig. 1 is the initial microscopic structure of Ti-6Al-4V alloy, is a kind of equiaxed structure with 10 μ m left and right sides grain sizes.
Fig. 2 is a kind of martensitic structure with small layer structure, this small layer structure be with the microscopic structure of Fig. 1 1040 ℃ β transformation temperature (～1000 ℃) more than keep 1 hour after, through the water-cooled acquisition.
Fig. 3 is a kind of lamellar tissue with thick layer structure, this lamellar tissue be with the microscopic structure of Fig. 1 1040 ℃ keep 4 hours after, carry out air cooling, again in 730 ℃ keep 4 hours after, obtain through air cooling.
The dual tissue of Fig. 4 for constituting by thick equiaxed structure and lamellar tissue, equiaxed structure that this is thick and lamellar tissue be with the microscopic structure of Fig. 1 950 ℃ keep 4 hours after, carry out water-cooled, again in 540 ℃ keep 6 hours after, through the air cooling acquisition.
Fig. 5 to Fig. 8 is to the Ti-6Al-4V alloy with martensitic structure like Fig. 2; After changing process conditions and unidirection rolling (uni-directional rolling); The inverse pole figure of observing with EBSD (electron backs cattered diffraction) device (inverse pole figure, IPF).
The process conditions of Fig. 5 are 800 ℃ of deformation temperatures, rate of deformation 0.1s
-1, deflection-0.4.
The process conditions of Fig. 6 are 800 ℃ of deformation temperatures, rate of deformation 0.1s
-1, deflection-0.8.
The process conditions of Fig. 7 are 800 ℃ of deformation temperatures, rate of deformation 0.1s
-1, deflection-1.2.
The process conditions of Fig. 8 are 800 ℃ of deformation temperatures, rate of deformation 0.1s
-1, deflection-1.6.
Extremely shown in Figure 8 like Fig. 5; When unidirection rolling along with the increase of deflection; Though the variation that has branch rate that the martensitic structure of Fig. 2 is cut apart the small equiaxed structure of formation to increase, the microscopic structure of Fig. 5 to Fig. 8 all exists small equiaxed structure and lamellar tissue (shown in red part) simultaneously.
The difference of the tissue of Fig. 4 and the microscopic structure of Fig. 5 to Fig. 8 does, thick equiaxed structure is mixed with the lamellar tissue that forms group (colony) and existed in Fig. 4, and in Fig. 5 to Fig. 8, small equiaxed structure is mixed existence with the lamellar tissue that does not form group on the contrary.On the other hand, along with the increase of deflection, the branch rate increase of small equiaxed structure is to become the crystal grain with high dip angle border effectively because be formed at the inner subgrain of each layer structure.
The result is that the microscopic structure of Fig. 5 to Fig. 8 and process conditions thereof are cores of this method.
Fig. 9 is for the Ti-6Al-4V alloy with martensitic structure with Fig. 2, at 800 ℃ of deformation temperatures, rate of deformation 0.1s
-1, deflection-1.6 condition under, carry out tandem rolling (cross-rolling) after, the inverse pole figure of observing with the EBSD device.
Titanium alloy shown in Figure 9 produces fully dynamically nodularization, is made up of small equiaxed structure.Comparison diagram 9 and Fig. 8, though process conditions such as deformation temperature, rate of deformation and deflection are identical, rolling direction is different.
That is, titanium alloy shown in Figure 8 obtains through unidirection rolling, and titanium alloy shown in Figure 9 obtains through tandem rolling.Different ground with unidirection rolling; When carrying out tandem rolling, in the rolling step of odd number, fail the lamellar tissue of merogenesis in the rolling step of even number, to cut apart effectively, the result will obtain the fully dynamically microscopic structure of nodularization; Yet this is in the titanium alloy of preparation partial dynamic nodularization, the condition that need avoid.
On the other hand, to the mechanical property under above its normal temperature of all microstructure observations of mentioning.For this reason, with respect to rolling direction, after 0 °, 45 °, 90 ° these three directions were extracted the test piece of the gauge length with 25mm, (extensometer) was installed in test piece with extensometer, adopted 8801 pairs of all directions of INSTRON to implement 3 stretching experiments.
That is, each microscopic structure 9 experiments have altogether been carried out repeatedly.Figure 10 to Figure 12 shows stretching experiment result's mean value, the microscopic structure of table 1 expression comparative example and embodiment etc., heat treatment method etc.
Table 1
Figure 10 is the average yield strength to each microscopic structure, and Figure 11 is the average uniform elongation to each microscopic structure, and Figure 12 is to the average yield strength of each microscopic structure and the product of average uniform elongation.
When the tissue behind the general heat treatment methods of enforcement such as comparative example 2,3,4 and comparative example 5 was compared with the initial microscopic structure of comparative example 1, though average yield strength increases, average uniform elongation reduced.
On the contrary, embodiment 1 prepared in accordance with the present invention, when the initial microscopic structure with comparative example 1 compared, though average yield strength is similar, average uniform elongation increased.When the initial microscopic structure with embodiment 2,3 and comparative example 1 compared, average yield strength all had increase with average uniform elongation.When the initial microscopic structure with embodiment 4 and comparative example 1 compared, average yield strength increased, and demonstrated similarly average uniform elongation.
Conclusion is that the embodiment 1,2,3,4 through method of the present invention prepares compares with the titanium alloy through other heat treatment methods, demonstrates the product of the average yield strength of raising more than 25～100% and average percentage elongation.
More than embodiments of the invention are illustrated; Yet claim scope of the present invention is not limited to this; In claims and specification and the disclosed scope of accompanying drawing, can be out of shape enforcement in a variety of forms, it naturally also belongs to scope of the present invention.
Claims (6)
1. the preparation method of a high strength, high-tenacity titanium alloy may further comprise the steps:
Titanium alloy with martensitic structure is provided; And
Through the titanium alloy of heat and the said martensitic structure of mechanical treatment, make the nodularization of microscopic structure partial dynamic.
2. the preparation method of high strength according to claim 1, high-tenacity titanium alloy,
The microscopic structure of the said titanium alloy that is provided comprises the martensitic structure of stratiform.
3. the preparation method of high strength according to claim 1, high-tenacity titanium alloy,
Said heat and mechanical treatment do, at 775 ℃～875 ℃ deformation temperature, 0.07s
-1～0.13s
-1Rate of deformation ,-0.2～-1.6 deflection scope in rolling.
4. the preparation method of high strength according to claim 3, high-tenacity titanium alloy,
Said heat and mechanical treatment do, at 800 ℃ deformation temperatures, 0.1s
-1Rate of deformation ,-0.2～-1.6 deflection scope in rolling.
5. according to the preparation method of each described high strength, high-tenacity titanium alloy in the claim 1 to 4,
Said rolling through unidirection rolling (uni-directional rolling) realization.
6. the preparation method of high strength according to claim 5, high-tenacity titanium alloy,
Through said partial dynamic nodularization, the microscopic structure of said titanium alloy exists small equiaxed structure and lamellar tissue simultaneously.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020090130762A KR101158477B1 (en) | 2009-12-24 | 2009-12-24 | Method for producing high strength and high ductility titanium alloy |
| KR10-2009-0130762 | 2009-12-24 | ||
| PCT/KR2010/009272 WO2011078600A2 (en) | 2009-12-24 | 2010-12-23 | Method for producing a high-strength and highly ductile titanium alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN102665946A true CN102665946A (en) | 2012-09-12 |
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Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2010800535482A Pending CN102665946A (en) | 2009-12-24 | 2010-12-23 | Method for producing a high-strength and highly ductile titanium alloy |
Country Status (6)
| Country | Link |
|---|---|
| US (1) | US20130019999A1 (en) |
| JP (1) | JP2013513731A (en) |
| KR (1) | KR101158477B1 (en) |
| CN (1) | CN102665946A (en) |
| DE (1) | DE112010005003T5 (en) |
| WO (1) | WO2011078600A2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112143936A (en) * | 2020-09-29 | 2020-12-29 | 中国科学院金属研究所 | High-thermal-stability equiaxial nanocrystalline Ti-Cr alloy and preparation method thereof |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2014113740A1 (en) * | 2013-01-18 | 2014-07-24 | University Of Pittsburgh - Of The Commonwealth System Of Higher Education | Removal of carbon dioxide via dialysis |
| CN113600616B (en) * | 2021-08-09 | 2023-05-30 | 成都先进金属材料产业技术研究院股份有限公司 | Thermal processing method for improving high-speed impact resistance of two-phase titanium alloy |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR910003876B1 (en) * | 1988-12-29 | 1991-06-15 | 포항종합제철 주식회사 | Making process for pare ti-material having a good bending property |
| JPH05295502A (en) * | 1992-04-21 | 1993-11-09 | Nkk Corp | Production of alpha plus beta titanium alloy sheet for superplastic working |
| CN1292038A (en) * | 1998-02-02 | 2001-04-18 | 菲利普莫里斯生产公司 | Two phase titanium aluminide alloy |
| KR20090121934A (en) * | 2008-05-23 | 2009-11-26 | 포항공과대학교 산학협력단 | Manufacturing method of titanium alloy for superplastic forming |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR960007428B1 (en) * | 1993-12-28 | 1996-05-31 | 포항종합제철주식회사 | Making method of titanium alloy |
| US8058201B2 (en) | 2006-11-16 | 2011-11-15 | Multisorb Technologies, Inc. | Clean, compressed sorbent tablets |
| KR100977801B1 (en) | 2007-12-26 | 2010-08-25 | 주식회사 포스코 | Titanium alloy with exellent hardness and ductility and method thereof |
| KR101048124B1 (en) | 2008-06-16 | 2011-07-08 | 기아자동차주식회사 | Spark Plug Tube Unit for Engine |
-
2009
- 2009-12-24 KR KR1020090130762A patent/KR101158477B1/en not_active IP Right Cessation
-
2010
- 2010-12-23 WO PCT/KR2010/009272 patent/WO2011078600A2/en active Application Filing
- 2010-12-23 JP JP2012544404A patent/JP2013513731A/en active Pending
- 2010-12-23 DE DE112010005003T patent/DE112010005003T5/en not_active Ceased
- 2010-12-23 US US13/511,419 patent/US20130019999A1/en not_active Abandoned
- 2010-12-23 CN CN2010800535482A patent/CN102665946A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR910003876B1 (en) * | 1988-12-29 | 1991-06-15 | 포항종합제철 주식회사 | Making process for pare ti-material having a good bending property |
| JPH05295502A (en) * | 1992-04-21 | 1993-11-09 | Nkk Corp | Production of alpha plus beta titanium alloy sheet for superplastic working |
| CN1292038A (en) * | 1998-02-02 | 2001-04-18 | 菲利普莫里斯生产公司 | Two phase titanium aluminide alloy |
| KR20090121934A (en) * | 2008-05-23 | 2009-11-26 | 포항공과대학교 산학협력단 | Manufacturing method of titanium alloy for superplastic forming |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112143936A (en) * | 2020-09-29 | 2020-12-29 | 中国科学院金属研究所 | High-thermal-stability equiaxial nanocrystalline Ti-Cr alloy and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| WO2011078600A3 (en) | 2011-11-17 |
| JP2013513731A (en) | 2013-04-22 |
| US20130019999A1 (en) | 2013-01-24 |
| KR101158477B1 (en) | 2012-06-20 |
| WO2011078600A2 (en) | 2011-06-30 |
| KR20110073950A (en) | 2011-06-30 |
| DE112010005003T5 (en) | 2012-11-15 |
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Application publication date: 20120912 |