CA2597248A1 - Method for casting titanium alloy - Google Patents
Method for casting titanium alloy Download PDFInfo
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- CA2597248A1 CA2597248A1 CA002597248A CA2597248A CA2597248A1 CA 2597248 A1 CA2597248 A1 CA 2597248A1 CA 002597248 A CA002597248 A CA 002597248A CA 2597248 A CA2597248 A CA 2597248A CA 2597248 A1 CA2597248 A1 CA 2597248A1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/002—Castings of light metals
- B22D21/005—Castings of light metals with high melting point, e.g. Be 1280 degrees C, Ti 1725 degrees C
-
- 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
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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- Chemical & Material Sciences (AREA)
- Mechanical Engineering (AREA)
- Engineering & Computer Science (AREA)
- Organic Chemistry (AREA)
- Metallurgy (AREA)
- Materials Engineering (AREA)
- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Forging (AREA)
- Powder Metallurgy (AREA)
- Materials For Medical Uses (AREA)
- Continuous Casting (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
The invention relates to a method for casting objects from a ~-titanium alloy containing titanium molybdenum with a molybdenum content of 7.5 to 25 %.
According to the invention: a melting of the alloy is carried out at a temperature of higher than 1770 ~C; the molten alloy is precision cast into a mold corresponding to the object to be produced, and this cast object is subjected to a hot-isostatic pressing, solution annealing and subsequent quenching. An efficient production of objects made from ~-titanium alloys in the precision casting process is achieved using the inventive method. The invention thus creates the possibility of combining the advantageous properties of ~-titanium alloys, particularly their excellent mechanical properties, with the advantages of a production of objects in the precision casting process. Even objects having complex shapes, which could not or could not be sensibly produced by conventional forging methods, can be produced from a ~-titanium alloy thanks to the invention.
According to the invention: a melting of the alloy is carried out at a temperature of higher than 1770 ~C; the molten alloy is precision cast into a mold corresponding to the object to be produced, and this cast object is subjected to a hot-isostatic pressing, solution annealing and subsequent quenching. An efficient production of objects made from ~-titanium alloys in the precision casting process is achieved using the inventive method. The invention thus creates the possibility of combining the advantageous properties of ~-titanium alloys, particularly their excellent mechanical properties, with the advantages of a production of objects in the precision casting process. Even objects having complex shapes, which could not or could not be sensibly produced by conventional forging methods, can be produced from a ~-titanium alloy thanks to the invention.
Description
Method for casting titanium alloy The invention relates to a process for casting objects from a R-titanium alloy, more specifically a titanium-molybdenum alloy.
Titanium alloys are becoming more and more popular on account of their numerous advantageous properties.
Titanium alloys are used in all fields in which high demands are imposed on the material, in particular on account of their good chemical stability, even at high temperature, and their low weight combined with excellent mechanical properties. On account of their excellent biocompatibility, titanium alloys are also preferentially used in the medical sector, in particular for implants and prostheses.
Various methods for shaping titanium alloys are known.
In addition to cutting processes, these primarily include casting and forging processes. In principle, titanium alloys are forging alloys, for which reason forging processes are generally used, since it has been found that titanium alloys are difficult to cast. This approach is generally taken for complicated shapes but leads to restrictions in terms of the choice of suitable alloys. In particular, it has been found that only unsatisfactory results are achieved when casting R-titanium alloys (US-A 2004/0136859).
The invention is based on the object of providing an improved casting process for R-titanium alloys which allows even complex shapes to be produced with good material properties.
Titanium alloys are becoming more and more popular on account of their numerous advantageous properties.
Titanium alloys are used in all fields in which high demands are imposed on the material, in particular on account of their good chemical stability, even at high temperature, and their low weight combined with excellent mechanical properties. On account of their excellent biocompatibility, titanium alloys are also preferentially used in the medical sector, in particular for implants and prostheses.
Various methods for shaping titanium alloys are known.
In addition to cutting processes, these primarily include casting and forging processes. In principle, titanium alloys are forging alloys, for which reason forging processes are generally used, since it has been found that titanium alloys are difficult to cast. This approach is generally taken for complicated shapes but leads to restrictions in terms of the choice of suitable alloys. In particular, it has been found that only unsatisfactory results are achieved when casting R-titanium alloys (US-A 2004/0136859).
The invention is based on the object of providing an improved casting process for R-titanium alloys which allows even complex shapes to be produced with good material properties.
The solution according to the invention resides in a process having the features of the main claim.
Advantageous refinements form the subject matter of the subclaims.
According to the invention, in a process for casting objects from a(3-titanium alloy comprising titanium-molybdenum with a molybdenum content of from 7.5 to 25%, it is provided that the alloy is melted at a temperature of over 1770 C, the molten alloy is investment-cast into a casting mold corresponding to the object to be produced, is hot-isostatically pressed, solution-annealed and then quenched.
In the present context, an object is to be understood as meaning a product which has been shaped for final use. The object may, for example in the aeronautical industry, be parts used for jet engines, rotor bearings, wing boxes or other supporting structure parts, or in the field of medicine may be endoprostheses, such as hip prostheses, or implants, such as plates or pins or dental implants. The term object in the context of the present application does not encompass billets which are intended for further processing by shaping processes, i.e. in particular does not include ingots produced by permanent mold casting for further processing by forging.
The process according to the invention achieves economical production of objects made from (3-titanium alloys using the investment-casting process. The invention therefore provides the possibility of combining the advantageous properties of (3-titanium alloys, in particular their excellent mechanical properties, with the advantages of production of objects using the investment-casting process. The invention allows even objects of complex shapes, which it has been impossible to produce (economically) using conventional forging processes, to be produced from a (3-titanium alloy. Therefore, the invention also opens up the application area of complex-shaped objects to 5(3-titanium alloys, which are known to have favorable mechanical properties and biocompatibility.
The molybdenum content in the alloy or its molybdenum equivalent is in the range from 7.5 to 25%. The result of this is that, in particular for a molybdenum content of at least 10%, the (3-phase is sufficiently stabilized even as far as the room temperature range. It is preferable for the content to be between 12 and 16%.
This allows a meta-stable P-phase to be achieved by rapid cooling following the investment casting. There is generally no need to add further alloy-forming elements. In particular, there is no need to add vanadium or aluminum. Dispensing with these has the advantage mentioned above that the toxicity resulting from these alloy-forming elements can be avoided. The same correspondingly applies to bismuth, which also does not have the same biocompatibility as titanium.
It has been found that the invention, using the (3-titanium alloys which have hitherto been almost impossible to use for investment casting, allows the production of even more complex shapes than the a/p-titanium alloys which have hitherto been used for investment casting, such as for example TiA16V4. The process according to the invention achieves improved mold filling properties. This means that as a result of the invention, in particular sharp edges can be produced with a higher quality during investment casting. The susceptibility to the formation of voids in investment casting is also reduced as a result of the improved mold filling properties.
Advantageous refinements form the subject matter of the subclaims.
According to the invention, in a process for casting objects from a(3-titanium alloy comprising titanium-molybdenum with a molybdenum content of from 7.5 to 25%, it is provided that the alloy is melted at a temperature of over 1770 C, the molten alloy is investment-cast into a casting mold corresponding to the object to be produced, is hot-isostatically pressed, solution-annealed and then quenched.
In the present context, an object is to be understood as meaning a product which has been shaped for final use. The object may, for example in the aeronautical industry, be parts used for jet engines, rotor bearings, wing boxes or other supporting structure parts, or in the field of medicine may be endoprostheses, such as hip prostheses, or implants, such as plates or pins or dental implants. The term object in the context of the present application does not encompass billets which are intended for further processing by shaping processes, i.e. in particular does not include ingots produced by permanent mold casting for further processing by forging.
The process according to the invention achieves economical production of objects made from (3-titanium alloys using the investment-casting process. The invention therefore provides the possibility of combining the advantageous properties of (3-titanium alloys, in particular their excellent mechanical properties, with the advantages of production of objects using the investment-casting process. The invention allows even objects of complex shapes, which it has been impossible to produce (economically) using conventional forging processes, to be produced from a (3-titanium alloy. Therefore, the invention also opens up the application area of complex-shaped objects to 5(3-titanium alloys, which are known to have favorable mechanical properties and biocompatibility.
The molybdenum content in the alloy or its molybdenum equivalent is in the range from 7.5 to 25%. The result of this is that, in particular for a molybdenum content of at least 10%, the (3-phase is sufficiently stabilized even as far as the room temperature range. It is preferable for the content to be between 12 and 16%.
This allows a meta-stable P-phase to be achieved by rapid cooling following the investment casting. There is generally no need to add further alloy-forming elements. In particular, there is no need to add vanadium or aluminum. Dispensing with these has the advantage mentioned above that the toxicity resulting from these alloy-forming elements can be avoided. The same correspondingly applies to bismuth, which also does not have the same biocompatibility as titanium.
It has been found that the invention, using the (3-titanium alloys which have hitherto been almost impossible to use for investment casting, allows the production of even more complex shapes than the a/p-titanium alloys which have hitherto been used for investment casting, such as for example TiA16V4. The process according to the invention achieves improved mold filling properties. This means that as a result of the invention, in particular sharp edges can be produced with a higher quality during investment casting. The susceptibility to the formation of voids in investment casting is also reduced as a result of the improved mold filling properties.
It is expedient for a cold-wall crucible vacuum induction installation to be used to melt the R-titanium alloy. An installation of this type makes it possible to reach the high temperatures which are required for reliable melting of titanium-molybdenum alloys for investment casting. For example, the melting point of TiMo15 is 1770 C. A supplement of approx. 60 C
should expediently be added to this to effect reliable investment casting. In particular, therefore, a temperature of 1830 C has to be reached for TiMo15.
It is preferable for the hot isostatic pressing to take place at a temperature which is at most equal to a beta transus temperature of the titanium-molybdenum alloy and is no more than 100 C below the beta transus temperature.
The hot isostatic pressing counteracts undesirable effects of concentrating the molybdenum in dendrites while depleting the remaining melts by dissolving inter-dendritic precipitations. A temperature below the beta-transus temperature, specifically at most 100 C
below it, is favorable. Temperatures in the range from 710 C to 760 C, preferably of approx. 740 C, at an argon pressure of approximately 1100 to 1200 bar have proven suitable for a titanium-molybdenum alloy with a molybdenum content of 15%.
Temperatures of at least 700 C to 880 , preferably in the range from 800 C to 860 C, have proven suitable for solution annealing. Argon is preferably used to produce a shielding gas atmosphere. This improves the ductility of the alloy.
It is expedient for quenching of the object by water to be carried out after the solution annealing. It is preferable to use cold water. In this context, the term "cold" is to be understood as meaning the temperature of unheated tap water. It has been found that the quenching has a considerable influence on the mechanical properties of the object which are ultimately achieved. Alternatively, quenching may also take place in shielding gas, for example by argon cooling. The results achieved, however, are not as good as those achieved with cold water.
It may be expedient for the object finally also to be hardened. This may allow the modulus of elasticity to be increased slightly, if required. For this purpose, it is preferable for the hardening to be carried out in a temperature range from approx. 600 C to approx.
700 C.
The invention is explained in more detail below with reference to the drawing, which illustrates an advantageous exemplary embodiment. In the drawing:
Fig. 1 shows a table which gives mechanical properties of the investment-cast titanium alloy according to the invention;
Fig. 2 shows an image of the microstructure in a cast state immediately after casting;
Fig. 3 shows an image of the microstructure after hot isostatic pressing;
Fig. 4 shows an image of the microstructure after solution annealing with a subsequent quench;
and Fig. 5 illustrates liquidus and solidus temperatures for a titanium-molybdenum alloy.
should expediently be added to this to effect reliable investment casting. In particular, therefore, a temperature of 1830 C has to be reached for TiMo15.
It is preferable for the hot isostatic pressing to take place at a temperature which is at most equal to a beta transus temperature of the titanium-molybdenum alloy and is no more than 100 C below the beta transus temperature.
The hot isostatic pressing counteracts undesirable effects of concentrating the molybdenum in dendrites while depleting the remaining melts by dissolving inter-dendritic precipitations. A temperature below the beta-transus temperature, specifically at most 100 C
below it, is favorable. Temperatures in the range from 710 C to 760 C, preferably of approx. 740 C, at an argon pressure of approximately 1100 to 1200 bar have proven suitable for a titanium-molybdenum alloy with a molybdenum content of 15%.
Temperatures of at least 700 C to 880 , preferably in the range from 800 C to 860 C, have proven suitable for solution annealing. Argon is preferably used to produce a shielding gas atmosphere. This improves the ductility of the alloy.
It is expedient for quenching of the object by water to be carried out after the solution annealing. It is preferable to use cold water. In this context, the term "cold" is to be understood as meaning the temperature of unheated tap water. It has been found that the quenching has a considerable influence on the mechanical properties of the object which are ultimately achieved. Alternatively, quenching may also take place in shielding gas, for example by argon cooling. The results achieved, however, are not as good as those achieved with cold water.
It may be expedient for the object finally also to be hardened. This may allow the modulus of elasticity to be increased slightly, if required. For this purpose, it is preferable for the hardening to be carried out in a temperature range from approx. 600 C to approx.
700 C.
The invention is explained in more detail below with reference to the drawing, which illustrates an advantageous exemplary embodiment. In the drawing:
Fig. 1 shows a table which gives mechanical properties of the investment-cast titanium alloy according to the invention;
Fig. 2 shows an image of the microstructure in a cast state immediately after casting;
Fig. 3 shows an image of the microstructure after hot isostatic pressing;
Fig. 4 shows an image of the microstructure after solution annealing with a subsequent quench;
and Fig. 5 illustrates liquidus and solidus temperatures for a titanium-molybdenum alloy.
The text which follows describes a way of carrying out the method according to the invention.
The starting material is aP-titanium alloy with a molybdenum content of 15% (TiMol5). This alloy can be obtained commercially in the form of small billets (ingots).
A first step involves investment casting of the objects that are to be cast. A casting installation is provided for melting and casting the TiMol5. This is preferably a cold-wall crucible vacuum induction melting and casting installation. An installation of this type can reach the high temperatures which are required for reliable melting of TiMol5 for investment casting. The melting point of TiMol5 is 1770 C, plus a supplement of approx. 60 C for reliable investment casting. Overall, therefore, a temperature of 1830 C has to be reached.
The investment casting of the melt then takes place using processes which are known per se, for example, with wax cores and ceramic molds as lost molds.
Investment casting techniques of this type are known for the investment casting of TiA16V4.
As can be seen from the figure (1000 times magnification) in Fig. 2, dendrites are formed, and considerable precipitations are evident in inter-dendritic zones. This is a consequence of what is known as the negative segregation of titanium-molybdenum alloys. This effect is based on the specific profile of the liquidus and solidus temperatures of titanium-molybdenum alloys, as illustrated in Fig. 5. On account of the profile of the melting temperatures of the liquid phase (TL) and the solid phase (TS) illustrated, it is firstly the regions with a high molybdenum content which solidify in the melt, during which process the dendrites that can be seen in the figure are formed. This leads to depletion of the residual melt, i.e. its molybdenum content drops. The inter-dendritic zones in the cast microstructure have a molybdenum content of less than 15%, and it is even possible for the molybdenum content to drop to approx.
10%. As a result of the molybdenum depletion, the inter-dendritic zones lack a sufficient quantity of 0-stabilizers. The result of this is that an increased a/(3 transformation temperature is locally established, resulting in the formation of the precipitations shown in Fig. 2.
It is expedient for a surface zone which may form during casting as a hard, brittle layer, known as the a-case, to be removed by pickling. The thickness of this layer is usually approx. 0.03 mm.
To counteract the unfavorable effect of the negative segregation with the precipitations in the inter-dendritic zones, according to the invention the castings, after the casting molds have been removed following the investment casting, are subjected to a heat treatment. This involves hot isostatic pressing (HIP) specifically at a temperature just below the (3-transus temperature. It may be in the range from 710 C to 760 C and is preferably approximately 740 C.
This causes the undesirable precipitations in the inter-dendritic zones to be dissolved again. There is no need for any preliminary age-hardening before or after the hot isostatic pressing. However, fine secondary phases precipitate again during the cooling following hot isostatic pressing, preferentially in the original inter-dendritic zones (cf. Fig. 3, 1000 times magnification). This leads to undesirable embrittlement of the material.
The starting material is aP-titanium alloy with a molybdenum content of 15% (TiMol5). This alloy can be obtained commercially in the form of small billets (ingots).
A first step involves investment casting of the objects that are to be cast. A casting installation is provided for melting and casting the TiMol5. This is preferably a cold-wall crucible vacuum induction melting and casting installation. An installation of this type can reach the high temperatures which are required for reliable melting of TiMol5 for investment casting. The melting point of TiMol5 is 1770 C, plus a supplement of approx. 60 C for reliable investment casting. Overall, therefore, a temperature of 1830 C has to be reached.
The investment casting of the melt then takes place using processes which are known per se, for example, with wax cores and ceramic molds as lost molds.
Investment casting techniques of this type are known for the investment casting of TiA16V4.
As can be seen from the figure (1000 times magnification) in Fig. 2, dendrites are formed, and considerable precipitations are evident in inter-dendritic zones. This is a consequence of what is known as the negative segregation of titanium-molybdenum alloys. This effect is based on the specific profile of the liquidus and solidus temperatures of titanium-molybdenum alloys, as illustrated in Fig. 5. On account of the profile of the melting temperatures of the liquid phase (TL) and the solid phase (TS) illustrated, it is firstly the regions with a high molybdenum content which solidify in the melt, during which process the dendrites that can be seen in the figure are formed. This leads to depletion of the residual melt, i.e. its molybdenum content drops. The inter-dendritic zones in the cast microstructure have a molybdenum content of less than 15%, and it is even possible for the molybdenum content to drop to approx.
10%. As a result of the molybdenum depletion, the inter-dendritic zones lack a sufficient quantity of 0-stabilizers. The result of this is that an increased a/(3 transformation temperature is locally established, resulting in the formation of the precipitations shown in Fig. 2.
It is expedient for a surface zone which may form during casting as a hard, brittle layer, known as the a-case, to be removed by pickling. The thickness of this layer is usually approx. 0.03 mm.
To counteract the unfavorable effect of the negative segregation with the precipitations in the inter-dendritic zones, according to the invention the castings, after the casting molds have been removed following the investment casting, are subjected to a heat treatment. This involves hot isostatic pressing (HIP) specifically at a temperature just below the (3-transus temperature. It may be in the range from 710 C to 760 C and is preferably approximately 740 C.
This causes the undesirable precipitations in the inter-dendritic zones to be dissolved again. There is no need for any preliminary age-hardening before or after the hot isostatic pressing. However, fine secondary phases precipitate again during the cooling following hot isostatic pressing, preferentially in the original inter-dendritic zones (cf. Fig. 3, 1000 times magnification). This leads to undesirable embrittlement of the material.
The objects have only a low ductility following the hot isostatic pressing.
To eliminate the disruptive precipitations, the castings are annealed in a chamber furnace under a shielding gas atmosphere (e.g. argon). A temperature range from approx. 700 C to 860 C with a duration of several hours, generally two hours, is selected for this purpose. In this context, there is a reciprocal relationship between the temperature and duration; at higher temperature, a shorter time is sufficient, and vice versa. Following the solution annealing, the castings are quenched with cold water. Fig. 4 (1000 times magnification) illustrates the microstructure following the solution annealing. Primary R-grains and, within the grains, very fine inter-dendritic precipitations (cf. cloud-like accumulation in the top left of the figure) can be seen. The objects which have been investment-cast using the process according to the invention have R-grains with a mean size of more than 0.3 mm in their crystal structure. This size is typical of the crystal structure achieved by the process according to the invention.
The mechanical properties achieved following the solution annealing are given in the table in Fig. 1.
It can be seen that the modulus of elasticity drops with an increasing temperature during the solution annealing, specifically as far as levels of 60,000 N/mm2. The ductility values improve with decreasing strength and hardness. For example, after solution annealing for two hours at 800 C, a modulus of elasticity of 60,000 N/mm2 combined with an elongation at break of approx. 40% and a fracture strength Rm of approx. 730 N/mm2 are achieved.
To eliminate the disruptive precipitations, the castings are annealed in a chamber furnace under a shielding gas atmosphere (e.g. argon). A temperature range from approx. 700 C to 860 C with a duration of several hours, generally two hours, is selected for this purpose. In this context, there is a reciprocal relationship between the temperature and duration; at higher temperature, a shorter time is sufficient, and vice versa. Following the solution annealing, the castings are quenched with cold water. Fig. 4 (1000 times magnification) illustrates the microstructure following the solution annealing. Primary R-grains and, within the grains, very fine inter-dendritic precipitations (cf. cloud-like accumulation in the top left of the figure) can be seen. The objects which have been investment-cast using the process according to the invention have R-grains with a mean size of more than 0.3 mm in their crystal structure. This size is typical of the crystal structure achieved by the process according to the invention.
The mechanical properties achieved following the solution annealing are given in the table in Fig. 1.
It can be seen that the modulus of elasticity drops with an increasing temperature during the solution annealing, specifically as far as levels of 60,000 N/mm2. The ductility values improve with decreasing strength and hardness. For example, after solution annealing for two hours at 800 C, a modulus of elasticity of 60,000 N/mm2 combined with an elongation at break of approx. 40% and a fracture strength Rm of approx. 730 N/mm2 are achieved.
Claims (8)
1. A process for casting objects from a .beta.-titanium alloy comprising titanium-molybdenum with a molybdenum content of from 7.5 to 25%, characterized by melting the alloy at a temperature of over 1770°C, investment-casting the molten alloy into a casting mold corresponding to the object to be produced, hot isostatic pressing, solution annealing and subsequent quenching.
2. The process as claimed in claim 1, characterized by using a cold-wall crucible vacuum induction installation for melting the .beta.-titanium alloy.
3. The process as claimed in claim 1 or 2, characterized by carrying out the hot isostatic pressing at a temperature which is at most equal to a beta transus temperature of the titanium-molybdenum alloy and is no more than 100°C below the beta transus temperature.
4. The process as claimed in either of claims 1 and 2, characterized by carrying out the solution annealing at a temperature of from approx. 700°C to approx.
900°C.
900°C.
5. The process as claimed in claim 4, characterized by carrying out the solution annealing at a temperature of from 800°C to 860°C.
6. The process as claimed in one of the preceding claims, characterized by quenching with preferably cold water following the solution annealing.
7. The process as claimed in one of the preceding claims, characterized by final hardening of the object.
8. The process as claimed in claim 7, characterized by carrying out the hardening at a temperature of from 600°C to 700°C.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP05004173A EP1696043A1 (en) | 2005-02-25 | 2005-02-25 | Process for casting a Titanium-alloy |
| EP05004173.0 | 2005-02-25 | ||
| PCT/EP2006/001790 WO2006089790A1 (en) | 2005-02-25 | 2006-02-27 | Method for casting titanium alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2597248A1 true CA2597248A1 (en) | 2006-08-31 |
| CA2597248C CA2597248C (en) | 2016-04-19 |
Family
ID=34933944
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA2597248A Expired - Fee Related CA2597248C (en) | 2005-02-25 | 2006-02-27 | Method for casting titanium alloy |
Country Status (18)
| Country | Link |
|---|---|
| EP (2) | EP1696043A1 (en) |
| JP (1) | JP5155668B2 (en) |
| KR (1) | KR101341298B1 (en) |
| CN (1) | CN100594248C (en) |
| AR (1) | AR052391A1 (en) |
| AT (1) | ATE438746T1 (en) |
| AU (1) | AU2006218029B2 (en) |
| BR (1) | BRPI0607832A2 (en) |
| CA (1) | CA2597248C (en) |
| DE (1) | DE502006004443D1 (en) |
| DK (1) | DK1851350T3 (en) |
| ES (1) | ES2328955T3 (en) |
| MX (1) | MX2007010366A (en) |
| PL (1) | PL1851350T3 (en) |
| RU (1) | RU2402626C2 (en) |
| TW (1) | TWI395821B (en) |
| WO (1) | WO2006089790A1 (en) |
| ZA (1) | ZA200707586B (en) |
Families Citing this family (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102019401B (en) * | 2010-12-30 | 2012-05-23 | 哈尔滨工业大学 | Cast forming method of small titanium alloy or titanium-aluminum alloy complicated casting |
| US9827605B2 (en) * | 2011-02-23 | 2017-11-28 | National Institute For Materials Science | Ti—Mo alloy and method for producing the same |
| CN102294436B (en) * | 2011-09-19 | 2013-01-02 | 哈尔滨实钛新材料科技发展有限公司 | Method for precisely casting titanium alloy and titanium aluminum alloy with low cost |
| RU2492275C1 (en) * | 2012-01-11 | 2013-09-10 | Открытое Акционерное Общество "Корпорация Всмпо-Ависма" | Method of producing plates from two-phase titanium alloys |
| CN102978554A (en) * | 2012-11-13 | 2013-03-20 | 安徽春辉仪表线缆集团有限公司 | Titanium alloy valve rod preparation method of plug valve |
| CN104550949A (en) * | 2013-10-24 | 2015-04-29 | 中国科学院金属研究所 | Method for rapidly forming Ti-6Al-4V three-dimensional metal parts by electron beams |
| CN105817608B (en) * | 2016-04-29 | 2019-01-18 | 南京宝泰特种材料股份有限公司 | A kind of titanium alloy smelting casting method |
| CN111850346A (en) * | 2020-08-06 | 2020-10-30 | 西部金属材料股份有限公司 | High-strength titanium alloy without solid solution aging treatment and preparation method thereof |
| KR20220122374A (en) | 2021-02-26 | 2022-09-02 | 창원대학교 산학협력단 | Method for vacuum centrifugal casting of titanium |
Family Cites Families (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4852614A (en) * | 1971-11-04 | 1973-07-24 | ||
| JPS5217307A (en) * | 1975-07-31 | 1977-02-09 | Kobe Steel Ltd | Process for heat treatment of beta-type titanium alloy |
| JPH0686638B2 (en) * | 1985-06-27 | 1994-11-02 | 三菱マテリアル株式会社 | High-strength Ti alloy material with excellent workability and method for producing the same |
| US4612066A (en) * | 1985-07-25 | 1986-09-16 | Lev Levin | Method for refining microstructures of titanium alloy castings |
| US4857269A (en) * | 1988-09-09 | 1989-08-15 | Pfizer Hospital Products Group Inc. | High strength, low modulus, ductile, biopcompatible titanium alloy |
| JP2541341B2 (en) * | 1990-05-15 | 1996-10-09 | 大同特殊鋼株式会社 | Precision casting method and precision casting apparatus for Ti and Ti alloy |
| JP3041080B2 (en) * | 1991-04-19 | 2000-05-15 | 電気興業株式会社 | Precision casting equipment |
| US5226982A (en) * | 1992-05-15 | 1993-07-13 | The United States Of America As Represented By The Secretary Of The Air Force | Method to produce hollow titanium alloy articles |
| US5947723A (en) * | 1993-04-28 | 1999-09-07 | Gac International, Inc. | Titanium orthodontic appliances |
| JPH0841565A (en) * | 1994-07-29 | 1996-02-13 | Mitsubishi Materials Corp | Titanium alloy casting having high strength and high toughness |
| JPH10130757A (en) * | 1996-10-25 | 1998-05-19 | Daido Steel Co Ltd | Inplant made of ti alloy |
| US20040136859A1 (en) * | 2000-04-12 | 2004-07-15 | Cana Lab Corporation | Titanium alloys having improved castability |
| AU2003280458A1 (en) * | 2002-06-27 | 2004-01-19 | Memry Corporation | ss TITANIUM COMPOSITIONS AND METHODS OF MANUFACTURE THEREOF |
| US20040168751A1 (en) * | 2002-06-27 | 2004-09-02 | Wu Ming H. | Beta titanium compositions and methods of manufacture thereof |
| DE102004022458B4 (en) * | 2004-04-29 | 2006-01-19 | Leibniz-Institut Für Festkörper- Und Werkstoffforschung Dresden E.V. | Cold-formable titanium-based alloy bodies and process for their production |
| EP1695676A1 (en) * | 2005-02-25 | 2006-08-30 | WALDEMAR LINK GmbH & Co. KG | Method of producing a medical implant made of a beta-Titanium-Molybdenum-alloy and according implant |
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2005
- 2005-02-25 EP EP05004173A patent/EP1696043A1/en not_active Withdrawn
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- 2006-02-24 TW TW095106325A patent/TWI395821B/en not_active IP Right Cessation
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- 2006-02-27 WO PCT/EP2006/001790 patent/WO2006089790A1/en active Application Filing
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- 2006-02-27 DK DK06707301T patent/DK1851350T3/en active
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- 2006-02-27 KR KR1020077021726A patent/KR101341298B1/en active IP Right Grant
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| RU2007135062A (en) | 2009-03-27 |
| PL1851350T3 (en) | 2010-01-29 |
| CN100594248C (en) | 2010-03-17 |
| KR20070105379A (en) | 2007-10-30 |
| DK1851350T3 (en) | 2009-10-19 |
| DE502006004443D1 (en) | 2009-09-17 |
| AU2006218029A1 (en) | 2006-08-31 |
| EP1851350A1 (en) | 2007-11-07 |
| WO2006089790A1 (en) | 2006-08-31 |
| TW200643182A (en) | 2006-12-16 |
| EP1851350B1 (en) | 2009-08-05 |
| ATE438746T1 (en) | 2009-08-15 |
| TWI395821B (en) | 2013-05-11 |
| AR052391A1 (en) | 2007-03-14 |
| CN101128609A (en) | 2008-02-20 |
| BRPI0607832A2 (en) | 2009-06-13 |
| AU2006218029B2 (en) | 2011-07-21 |
| ZA200707586B (en) | 2008-10-29 |
| JP5155668B2 (en) | 2013-03-06 |
| ES2328955T3 (en) | 2009-11-19 |
| CA2597248C (en) | 2016-04-19 |
| RU2402626C2 (en) | 2010-10-27 |
| KR101341298B1 (en) | 2013-12-12 |
| JP2008531288A (en) | 2008-08-14 |
| MX2007010366A (en) | 2007-10-17 |
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