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WO2006089790A1 - Procede de moulage d'un alliage de titane - Google Patents

Procede de moulage d'un alliage de titane Download PDF

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Publication number
WO2006089790A1
WO2006089790A1 PCT/EP2006/001790 EP2006001790W WO2006089790A1 WO 2006089790 A1 WO2006089790 A1 WO 2006089790A1 EP 2006001790 W EP2006001790 W EP 2006001790W WO 2006089790 A1 WO2006089790 A1 WO 2006089790A1
Authority
WO
WIPO (PCT)
Prior art keywords
temperature
titanium
alloy
marked
molybdenum
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.)
Ceased
Application number
PCT/EP2006/001790
Other languages
German (de)
English (en)
Inventor
Sevki Baliktay
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Waldemar Link GmbH and Co KG
Original Assignee
Waldemar Link GmbH and Co KG
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Waldemar Link GmbH and Co KG filed Critical Waldemar Link GmbH and Co KG
Priority to BRPI0607832-0A priority Critical patent/BRPI0607832A2/pt
Priority to DE502006004443T priority patent/DE502006004443D1/de
Priority to PL06707301T priority patent/PL1851350T3/pl
Priority to AU2006218029A priority patent/AU2006218029B2/en
Priority to AT06707301T priority patent/ATE438746T1/de
Priority to MX2007010366A priority patent/MX2007010366A/es
Priority to DK06707301T priority patent/DK1851350T3/da
Priority to CN200680005976A priority patent/CN100594248C/zh
Priority to KR1020077021726A priority patent/KR101341298B1/ko
Priority to CA2597248A priority patent/CA2597248C/fr
Priority to EP06707301A priority patent/EP1851350B1/fr
Priority to JP2007556567A priority patent/JP5155668B2/ja
Publication of WO2006089790A1 publication Critical patent/WO2006089790A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Classifications

    • 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
    • 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

Definitions

  • the invention relates to a method for casting objects from a ß-titanium alloy, more specifically a titanium-molybdenum alloy.
  • Titanium alloys are becoming increasingly popular because of their many beneficial properties. In particular, because of their good chemical resistance, even at high temperature, and their low weight with excellent mechanical properties titanium alloys are used in all areas where high demands are placed on the material. Because of their excellent biocompatibility, titanium alloys are also preferably used in the medical field, in particular for implants and prostheses.
  • titanium alloys are forgings, so forging processes are mostly used. Because it has been shown that titanium alloys are difficult to pour. Usually this way will label with complicated shapes, however this way leads to restrictions in the selection of suitable alloys. In particular, it was found that only unsatisfactory results are achieved when casting ⁇ -titanium alloys (US-A-2004/0136859).
  • the invention has for its object to provide an improved casting process for ß-titanium alloys, which allows a production of complex shapes with good Materialeigen- shafts.
  • the alloy in a method for casting articles of a ⁇ -titanium alloy comprising titanium molybdenum having a molybdenum content of 7.5 to 25%, the alloy is melted at a temperature above 1770 ° C., the molten alloy is poured into a is mold-molded appropriate hot mold, hot isostatically pressed, solution-annealed and then quenched.
  • parts for engines, rotor bearings, wing boxes or other support structure parts or in the field of medicine can be endoprostheses, such as hip prostheses, or implants, such as plates and pins or dental implants.
  • endoprostheses such as hip prostheses
  • implants such as plates and pins or dental implants.
  • article for the purposes of the present application does not include ingots intended for further processing by forming processes, ie in particular ingots not produced by knock casting for further processing by forging.
  • the invention With the method according to the invention, a rational production of objects made of .beta.-titanium alloys in precision casting is achieved. achieved.
  • the invention thus makes it possible to combine the advantageous properties of ⁇ -titanium alloys, in particular its outstanding mechanical properties, with the advantages of producing objects in a fine casting process. Even objects with complex shapes, which could not be made or not made meaningful by conventional forging methods, can be made thanks to the invention of a ß-titanium alloy. In this way, the invention also opens up the field of application of the complex shaped articles to the titanium alloys known for their excellent mechanical properties and biocompatibility.
  • the proportion of molybdenum in the alloy or its molybdenum equivalent is in the range of 7.5 to 25%. This results in a sufficient stabilization of the ß-phase up to the range of room temperature, in particular with a molybdenum content of at least 10%. Preferably, the content is between 12 and 16%. This can be achieved by fast cooling after the investment casting a metastable ß-phase.
  • the addition of other alloying agents is usually unnecessary. In particular, it is not necessary that vanadium or aluminum be added. The omission of this has the already mentioned advantage that the toxicity emanating from these alloy formers can be avoided.
  • bismuth which in terms of its biocompatibility likewise does not equal titanium.
  • a cold wall crucible vacuum induction plant is used to melt the beta titanium alloy.
  • the high temperatures required for a safe melting of titanium-molybdenum alloys for investment casting can be achieved.
  • the melting point of TiMol ⁇ is 1770 0 C to this is still a surcharge of about 60 0 C appropriate to achieve a safe investment casting.
  • a temperature of 1830 0 C for TiMol5 ER has enough.
  • the hot isostatic pressing takes place at a temperature having a beta transus temperature of the titanium-molybdenum alloy and a minimum of 100 0 C is at most as high as below the beta transus temperature.
  • Hot isostatic pressing counteracts the unfavorable effects of an accumulation of molybdenum in dendrites while depleting the residual melt by dissolving interdendritic precipitates.
  • Favorable is a temperature below the ⁇ -transus temperature, up to 100 0 C below.
  • For Titanmolybdänlegie- tion with 15% molybdenum content have temperatures ranging from 710 0 C to 760 0 C, proven preferably from about 740 0 C, at an argon pressure of about 1100 to 1200 bar.
  • temperatures of at least 700 ° C. up to 880 ° C. have proven useful, preferably in the region of 800 ° ° C to 860 ° C.
  • Argon is preferably used to generate a protective gas atmosphere. This achieves an improvement in the ductility of the alloy.
  • quenching of the article by water occurs after solution heat treatment.
  • cold water is used.
  • cold is meant the temperature of unheated tap water. Quenching has been shown to exert a strong influence on the ultimate mechanical properties of the article. Alternatively, it can also be quenched in inert gas, for example by argon cooling. However, the results achieved remain behind those achieved with cold water.
  • the curing in a temperature range of about 600 ° C to about 700 ° C is done.
  • Fig. 1 is a table with mechanical properties of the finely cast titanium alloy according to the invention
  • FIG. 2 is an illustration of the microstructure in a cast condition immediately after casting
  • Fig. 3 is an illustration of the microstructure after hipping; 4 shows a picture of the microstructure after solution annealing with subsequent quenching; and
  • FIG. 5 shows a representation of liquidus and solidus temperatures for a titanium-molybdenum alloy.
  • Starting material is a ß-titanium alloy with a molybdenum content of 15% (TiMoI5). This alloy can be purchased commercially in the form of small ingots.
  • an investment casting of the objects to be cast takes place.
  • For melting and casting of TiMol5 is a
  • Caster provided.
  • it is a cold wall crucible vacuum induction melting and casting equipment.
  • the melting point of TiMol ⁇ is 1770 0 C plus a surcharge of about 60 0 C for a safe investment casting. Overall, therefore, a temperature of 1830 0 C must be reached.
  • the fine casting of the melt is then carried out by means of per se known methods, for example with wax cores and ceramic forms as a lost form.
  • Such investment casting techniques are known for investment casting of TiA16V4.
  • the interdendritic zones have a molybdenum content of less than 15% in the cast structure, whereby the molybdenum content can decrease to values of about 10%.
  • a sufficient amount of ⁇ -stabilizers is missing in the interdendritic zones. This has the consequence that an increased a / ß conversion temperature is established locally, as a result of which the precipitates to be recognized in FIG. 2 are formed.
  • this layer has a thickness of about 0.03 mm.
  • the castings freed from the casting molds after the investment casting are subjected to a heat treatment according to the invention.
  • a hot isostatic pressing is provided, namely at a temperature just below the ß-transus temperature. It may be in the range 710 0 C to 760 0 C, preferably it is about 740 0 C.
  • the unwanted precipitates in the interdendritic zones go back into solution.
  • An advance storage before or after the hipping is not required.
  • fine secondary phases separate again from, preferably in the original interdendritic zones (see Fig. 3, lOOOX magnification). This results in unwanted embrittlement of the material.
  • the articles have a low ductility after being tipped.
  • the castings are annealed in a chamber furnace under a protective gas atmosphere (eg argon).
  • a protective gas atmosphere eg argon
  • a temperature range of about 700 0 C to 860 0 C is selected, with a duration of several, usually two hours. There is an opposite relationship between the temperature and the duration, at higher temperature is sufficient for a shorter time and vice versa.
  • the castings are quenched with cold water.
  • Fig. 4 1,000X magnification
  • the microstructure after solution annealing is shown.
  • the objects finely cast with the method according to the invention have ⁇ -grains with an average size of more than 0.3 mm in their crystal structure. This size is typical of the crystal structure achieved by the process of the invention.
  • the modulus of elasticity decreases with increasing temperature during solution annealing, to values of up to 60,000 N / mm 2 .
  • the toughness values improve with decreasing strength and hardness. So you reach after two hours solution annealing at 800 0 C, a modulus of elasticity of 60,000 N / mm 2 at an elongation at break of about 40% and a breaking strength Rm of about 730 N / mm 2 .

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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)
  • Forging (AREA)
  • Powder Metallurgy (AREA)
  • Materials For Medical Uses (AREA)
  • Continuous Casting (AREA)
  • Manufacture And Refinement Of Metals (AREA)

Abstract

L'invention concerne un procédé de moulage d'objets à partir d'un alliage de ß-titane à base de titane-molybdène, la teneur en molybdène étant comprise entre 7,5 et 25 %. Ce procédé se caractérise en ce qu'il consiste à fondre l'alliage à une température supérieure à 1770 °C, à effectuer un moulage de précision de l'alliage fondu dans un moule correspondant à l'objet à produire, à effectuer ensuite une compression isostatique à température élevée, puis un recuit de mise en solution et une trempe. Le procédé selon l'invention permet de produire de façon rationnelle des objets en alliages de ß-titane par un procédé de moulage de précision. L'invention permet ainsi d'associer les propriétés avantageuses des alliages de ß-titane, en particulier leurs excellentes propriétés mécaniques, aux avantages d'une production d'objets par un procédé de moulage de précision. L'invention permet également de produire à partir d'un alliage de ß-titane des objets de forme complexe qui ne pourraient pas être produits par des procédés de forgeage classiques, ou pas de façon rationnelle.
PCT/EP2006/001790 2005-02-25 2006-02-27 Procede de moulage d'un alliage de titane Ceased WO2006089790A1 (fr)

Priority Applications (12)

Application Number Priority Date Filing Date Title
BRPI0607832-0A BRPI0607832A2 (pt) 2005-02-25 2006-02-27 método para lingotamento de liga de titánio
DE502006004443T DE502006004443D1 (de) 2005-02-25 2006-02-27 Verfahren zum giessen einer titanlegierung
PL06707301T PL1851350T3 (pl) 2005-02-25 2006-02-27 Sposób odlewania stopu tytanowego
AU2006218029A AU2006218029B2 (en) 2005-02-25 2006-02-27 Method for casting titanium alloy
AT06707301T ATE438746T1 (de) 2005-02-25 2006-02-27 Verfahren zum giessen einer titanlegierung
MX2007010366A MX2007010366A (es) 2005-02-25 2006-02-27 Metodo de fundicion para una aleacion de titanio.
DK06707301T DK1851350T3 (da) 2005-02-25 2006-02-27 Fremgangsmåde til stöbning af en titaniumlegering
CN200680005976A CN100594248C (zh) 2005-02-25 2006-02-27 铸造钛合金的方法
KR1020077021726A KR101341298B1 (ko) 2005-02-25 2006-02-27 티타늄 합금 주조 방법
CA2597248A CA2597248C (fr) 2005-02-25 2006-02-27 Procede de moulage d'un alliage de titane
EP06707301A EP1851350B1 (fr) 2005-02-25 2006-02-27 Procede de moulage d'un alliage de titane
JP2007556567A JP5155668B2 (ja) 2005-02-25 2006-02-27 チタン合金の鋳造方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP05004173A EP1696043A1 (fr) 2005-02-25 2005-02-25 Procédé de couler un alliage a base de titan
EP05004173.0 2005-02-25

Publications (1)

Publication Number Publication Date
WO2006089790A1 true WO2006089790A1 (fr) 2006-08-31

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Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/EP2006/001790 Ceased WO2006089790A1 (fr) 2005-02-25 2006-02-27 Procede de moulage d'un alliage de titane

Country Status (18)

Country Link
EP (2) EP1696043A1 (fr)
JP (1) JP5155668B2 (fr)
KR (1) KR101341298B1 (fr)
CN (1) CN100594248C (fr)
AR (1) AR052391A1 (fr)
AT (1) ATE438746T1 (fr)
AU (1) AU2006218029B2 (fr)
BR (1) BRPI0607832A2 (fr)
CA (1) CA2597248C (fr)
DE (1) DE502006004443D1 (fr)
DK (1) DK1851350T3 (fr)
ES (1) ES2328955T3 (fr)
MX (1) MX2007010366A (fr)
PL (1) PL1851350T3 (fr)
RU (1) RU2402626C2 (fr)
TW (1) TWI395821B (fr)
WO (1) WO2006089790A1 (fr)
ZA (1) ZA200707586B (fr)

Families Citing this family (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102019401B (zh) * 2010-12-30 2012-05-23 哈尔滨工业大学 一种小型钛合金或钛铝合金复杂铸件的铸造成形方法
WO2012115187A1 (fr) * 2011-02-23 2012-08-30 独立行政法人物質・材料研究機構 Alliage de ti-mo et son procédé de production
CN102294436B (zh) * 2011-09-19 2013-01-02 哈尔滨实钛新材料科技发展有限公司 一种钛合金及钛铝合金的低成本精密铸造方法
RU2492275C1 (ru) * 2012-01-11 2013-09-10 Открытое Акционерное Общество "Корпорация Всмпо-Ависма" Способ изготовления плит из двухфазных титановых сплавов
CN102978554A (zh) * 2012-11-13 2013-03-20 安徽春辉仪表线缆集团有限公司 一种旋塞阀的钛合金阀杆制备方法
CN104550949A (zh) * 2013-10-24 2015-04-29 中国科学院金属研究所 一种电子束快速成形Ti-6Al-4V三维金属零件的方法
CN105817608B (zh) * 2016-04-29 2019-01-18 南京宝泰特种材料股份有限公司 一种钛合金熔炼浇铸方法
CN111850346A (zh) * 2020-08-06 2020-10-30 西部金属材料股份有限公司 一种无需固溶时效处理的高强钛合金及其制备方法
KR20220122374A (ko) 2021-02-26 2022-09-02 창원대학교 산학협력단 티타늄 진공원심주조방법

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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
US20040136859A1 (en) * 2000-04-12 2004-07-15 Cana Lab Corporation Titanium alloys having improved castability
US20040168751A1 (en) * 2002-06-27 2004-09-02 Wu Ming H. Beta titanium compositions and methods of manufacture thereof

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Also Published As

Publication number Publication date
JP2008531288A (ja) 2008-08-14
AR052391A1 (es) 2007-03-14
RU2402626C2 (ru) 2010-10-27
EP1851350B1 (fr) 2009-08-05
DK1851350T3 (da) 2009-10-19
EP1696043A1 (fr) 2006-08-30
MX2007010366A (es) 2007-10-17
TW200643182A (en) 2006-12-16
EP1851350A1 (fr) 2007-11-07
BRPI0607832A2 (pt) 2009-06-13
KR101341298B1 (ko) 2013-12-12
PL1851350T3 (pl) 2010-01-29
KR20070105379A (ko) 2007-10-30
CA2597248C (fr) 2016-04-19
ATE438746T1 (de) 2009-08-15
CN100594248C (zh) 2010-03-17
RU2007135062A (ru) 2009-03-27
TWI395821B (zh) 2013-05-11
DE502006004443D1 (de) 2009-09-17
CN101128609A (zh) 2008-02-20
ES2328955T3 (es) 2009-11-19
CA2597248A1 (fr) 2006-08-31
AU2006218029B2 (en) 2011-07-21
AU2006218029A1 (en) 2006-08-31
JP5155668B2 (ja) 2013-03-06
ZA200707586B (en) 2008-10-29

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