EP1778885A1 - High strength, oxidation and wear resistant titanium-silicon based alloy - Google Patents

High strength, oxidation and wear resistant titanium-silicon based alloy

Info

Publication number
EP1778885A1
EP1778885A1 EP05767947A EP05767947A EP1778885A1 EP 1778885 A1 EP1778885 A1 EP 1778885A1 EP 05767947 A EP05767947 A EP 05767947A EP 05767947 A EP05767947 A EP 05767947A EP 1778885 A1 EP1778885 A1 EP 1778885A1
Authority
EP
European Patent Office
Prior art keywords
alloy
mpa
oxidation
rare earth
high strength
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.)
Granted
Application number
EP05767947A
Other languages
German (de)
French (fr)
Other versions
EP1778885B1 (en
EP1778885A4 (en
Inventor
Karl Forwald
Georg Frommeyer
Gunnar Halvorsen
Kai Johansen
Øyvind MIKKELSEN
Gunnar Schüssler
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.)
Elkem ASA
Original Assignee
Elkem ASA
Elkem Materials AS
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
Priority claimed from NO20042959A external-priority patent/NO20042959D0/en
Application filed by Elkem ASA, Elkem Materials AS filed Critical Elkem ASA
Publication of EP1778885A1 publication Critical patent/EP1778885A1/en
Publication of EP1778885A4 publication Critical patent/EP1778885A4/en
Application granted granted Critical
Publication of EP1778885B1 publication Critical patent/EP1778885B1/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • 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
    • C22C—ALLOYS
    • C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
    • C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
    • C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
    • C22C32/0031—Matrix based on refractory metals, W, Mo, Nb, Hf, Ta, Zr, Ti, V or alloys thereof

Definitions

  • the present invention concerns high strength silicon-containing titanium-based alloys with optionally additives of aluminium, boron, chromium, scandium and rare earth metals (Y, Er, and Ce and La containing misch metal).
  • T ⁇ -6AI-4V A variety of two phase ⁇ / ⁇ -titanium and near ⁇ -titanium alloys, such as T ⁇ -6AI-4V, IMI 834 (Ti- ⁇ .8-AMSn-3Zr-0JNb-0. ⁇ Mo-0.3 ⁇ Si-0.06C) and TIMET 1100 (Ti-6AI- 2.7Sn-4Zr-0.4Mo-0.45Si) show great potential application in the air plane and space industry.
  • Ti-6AI-4V exhibits the broadest application due to an optimum combination of high strength and fracture toughness and excellent fatigue properties at room and elevated temperature.
  • These alloys have, however, some disadvantages such as a poor oxidation resistance above 475°C ( ⁇ -case formation), insufficient creep strength at 600°C and higher temperatures and a poor wear resistance at room and elevated temperatures.
  • the ⁇ -case causes crevice formation on the oxidised surface and has a detrimental effect on the fatigue properties.
  • the arc melting process of these relatively high melting point alloy of about 1660 0 C) and the necessary melt overheating to about 1750 to 1770 0 C is a very energy consuming procedure for the manufacture of investment castings for the air plane and automotive industry, and engineering purposes in general.
  • JP 2002060871 A describes a titanium alloy containing 0.2 - 2.3 wt % Si, 0.1 - 0.7 wt
  • % O total content oxygen
  • These are e.g. golf club heads, fishing tackles and medical components such as tooth root, implants, bone plates, joints and crowns.
  • the low silicon-containing titanium-based alloy does, however, suffer from a disadvantage, by forming small needle like Ti 3 Si precipates along grain boundaries, which decrease the fracture toughness and ductility of this material.
  • the alloys described by Frommeyer et. al. have excellent hardness and flow strength.
  • the warm strength of the Ti-Si-Al alloys is, however, moderate and there is no indication of the oxidation resistance at high temperature.
  • Ti-Si alloys with relatively high silicon contents which exhibit a relatively low melting point due to their eutectic constitution, good casting properties and high strength at higher temperatures as well as a very high resistance to oxidation and creep deformation at high temperatures.
  • the present invention thus relates to a Ti-Si alloy comprising 2.5 - 12 wt % Si, 0 - 5 wt % Al, 0 -5 wt % Cr, 0 - 0.5 wt % B, 0 - 1 wt % rare earth metals and/or yttrium and/or Sc, the remaining except for impurities being Ti.
  • the alloy contains 0.3 - 3 wt % Al.
  • the Ti-Si alloy contains 3 - 6 wt % Si and 1.2 - 2.5 wt % Al.
  • the alloy contains 0.001 to 0.15 wt % rare earth metals and/or scandium.
  • the rare earths yttriym and scandium additions form a fine dispersion of thermo- dynamically stable oxides, such as Er 2 ⁇ 3 , Y 2 O 3 etc. in the Ti-Si alloy.
  • the alloy preferably contains 0.1 to 1.5 wt % Cr.
  • the addition of Cr enhances solid solution hardening and therefore increases the strength and increase the oxidation resistance of the alloy.
  • the Ti-Si alloy In the as cast state, the Ti-Si alloy possesses fine-grained hypoeutectic, eutectic or slightly hypereutectic microstructures depending upon the silicon content.
  • the microstructure of the eutectic Ti-Si alloy consists of finely dispersed Ti 5 Si 3 suicide particles of discontinuous rod like shape within the hexagonal close-packed ⁇ - Ti(Si) solid solution matrix.
  • the hypoeutectic microstructure consists of primary solidified ⁇ -Ti(Si) crystals and the surrounding eutectic.
  • the Ti-Si alloy according to the invention has with a yield stress of at least 800 MPa, a Brinell hardness of 350-400 HB and sufficient ductility and fracture toughness -stress intensity factor Kic . of more than 23 MPa Vm at room temperature and up to 500 0 C.
  • the Ti-Si alloy according to the invention further exhibits excellent oxidation resistance up to 65O 0 C and above depending upon the Si content and improved wear resistance both at room and elevated temperature.
  • the hypereutectic microstructures consist of primary solidified TJsSi 3 crystals of hexagonal shape within the fine-grained eutectic microstructure.
  • hypoeutectic Ti-Si alloys exhibit at room temperature fractures toughness -K
  • the eutectic alloy shows a fracture toughness of K
  • C of 15 - 18 MPa Vm and the yield stress exceeds 850 MPa at room temperature. At 600 0 C and above the fracture toughness is increased to 30 MPa Vm and the strength is of the order of at least Rm 450 MPa.
  • Oxidation tests with exposure to air at 600 0 C have resulted in an increase in mass of less than 5 mg/cm 2 after 500 hours.
  • the conventional Ti-AI6- V4 alloy exhibits alpha case formation at 475 0 C during long term exposure on air.
  • the Ti-AI6-V4 alloy with potential application in the air plane and space industry exhibits a creep stress of about 150 MPa at 450 0 C.
  • the Ti-Si alloy according to the invention has a low melting point of between about 1330 and about 138O 0 C.
  • the alloy according to the invention has further excellent casting properties making it possible to cast virtually any size and shape.
  • the Ti-Si alloy according to this invention are advantageously suitable for the manufacture of diverse components, subjected to high temperature, such as:
  • the Ti-Si alloy according to the invention is particularly suitable for as cast components because of their relatively low melting temperatures of about 1330 to 138O 0 C and excellent castability.
  • the Ti-Si alloy according to the invention can be produced in conventional way, such as by arc melting in a water cooled copper hearth. Detailed description of invention
  • a hypoeutectic Ti-6Si-2AI alloy according to the invention was produced by arc melting using a non consumable tungsten electrode. Titanium sponge with a purity of more than 99.8 wt %, metallurgical grade silicon and aluminium granules with a purity of more than 99.8 wt % were used as starting materials. The alloy was kept during arc melting in a water cooled copper hearth by forming a thin solid skull on the copper hearth and was then cast into a copper mould in order to achieve rod like ingots. These were machined by turning and grinding to cylindrical compression and tensile test samples exhibiting a smooth surface finish.
  • the Brinell hardness was determined to be about 336 + 3 HB 187.5/2.5 applying a testing load of 187.5 kp.
  • the flow stress was determined at room temperature in compression test to be about Rp 0 2 « 725 to 750 MPa and the plastic strain exceeds - ⁇ p ⁇ 10 %.
  • the fracture toughness was measured in a four point bend test.
  • the stress intensity factor Kic varies between 19 ⁇ Kic ⁇ 21 MPa Vm. At higher temperature of 65O 0 C the flow stress is still 260 Rp 0 2 275 MPa and the fracture toughness is about 32 ⁇ K
  • the weight gain in an oxidation test on air at 600 0 C was 4.5 mg/cm 2 after 525 hrs.
  • a hypereutectic Ti-IOSi alloy containing 0.2 wt % Al was also produced by arc melting technique as described above in Example 1.
  • the macrohardness -Brinell- of this alloy was determined to be about 365 HB 187.5/2.5 and the yield stress at room temperature ranges between 930 ⁇ Rp ⁇ 965 MPa depending upon the grain size of the alloy.
  • the plastic strain in compression is about 6 to 8 % and the fracture toughness is in between K
  • C 16 and 19 MPa Vm.
  • the yield stress is about 330 to 360 MPa.
  • the fracture toughness is in between 25 and 28 MPa Vm.
  • the creep strength was determined at 600 0 C and exhibits values of 215 to 230 MPa in the coarse-grained state.
  • the oxidation on air at 65O 0 C leads to a weight gain of about 3.8 mg/cm 3 at 500 hrs exposure time.
  • a hypoeutectic (near eutectic) oxide dispersion strengthened Ti-7Si-2Al alloy with addition of 0.07 mass-% Y was also produced by the arc melting technique described in example 1.
  • Metallic Yttrium was added to the melt and formed Y 2 O 3 with the dissolved oxygen of about 1200 ppm.
  • the Brinell hardness was determined to be 347 ⁇ 2 HB 187.5/2.5.
  • the measured yield strength was about 960 to 990 MPa.
  • First creep experiments at 600°C with the creep rate of ⁇ 10 " V 1 showed a creep strength in between 235 and 255 MPa.
  • Example 4 A hypoeutectic oxide dispersion strengthened Ti-5.5Si-3.5AI.-1.5Cr-0.1 Y alloy was produced by the melting method technique described in Example 1. Metallic yttrium was added to the melt and formed Y 2 O 3 with oxygen dissolved in the melt.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
  • Heat Treatments In General, Especially Conveying And Cooling (AREA)

Abstract

The present invention relates to high strength, oxidation and wear resistant silicon base alloy containing: 2.5-12wt % Si; 0 - 5 wt % Al; 0-0.5 % B; 0-5 % Cr; 0 - 1 wt % rare earth metals and/or yttrium and/or scandium balance Ti with unavoidable impurities.

Description

Title of invention
High strength, oxidation and wear resistant titanium-silicon alloy
Field of invention
The present invention concerns high strength silicon-containing titanium-based alloys with optionally additives of aluminium, boron, chromium, scandium and rare earth metals (Y, Er, and Ce and La containing misch metal).
Background art
A variety of two phase α/β-titanium and near α-titanium alloys, such as TΪ-6AI-4V, IMI 834 (Ti-δ.8-AMSn-3Zr-0JNb-0.δMo-0.3δSi-0.06C) and TIMET 1100 (Ti-6AI- 2.7Sn-4Zr-0.4Mo-0.45Si) show great potential application in the air plane and space industry.
Among them Ti-6AI-4V exhibits the broadest application due to an optimum combination of high strength and fracture toughness and excellent fatigue properties at room and elevated temperature. These alloys have, however, some disadvantages such as a poor oxidation resistance above 475°C (α-case formation), insufficient creep strength at 600°C and higher temperatures and a poor wear resistance at room and elevated temperatures. The α-case causes crevice formation on the oxidised surface and has a detrimental effect on the fatigue properties. The arc melting process of these relatively high melting point alloy of about 16600C) and the necessary melt overheating to about 1750 to 17700C is a very energy consuming procedure for the manufacture of investment castings for the air plane and automotive industry, and engineering purposes in general.
Low silicon-containing titanium-based alloys are well known. Thus JP 2002060871 A describes a titanium alloy containing 0.2 - 2.3 wt % Si, 0.1 - 0.7 wt
% O (total content oxygen), and 0.16 - 1.12 wt % N and 0.001 - 0.3 wt % B and remainder of titanium including unavoidable impurities, used for as cast products. These are e.g. golf club heads, fishing tackles and medical components such as tooth root, implants, bone plates, joints and crowns. The low silicon-containing titanium-based alloy does, however, suffer from a disadvantage, by forming small needle like Ti3Si precipates along grain boundaries, which decrease the fracture toughness and ductility of this material.
From the paper "Structures and properties of the refractory suicides, Ti5Si3 and TiS2 and Ti-Si-(AI) eutectic alloys", by Frommeyer et. al. published in May 2004, it is on page 301 described a hypereutectic Ti-Si7.5-AI1 alloy. It is further stated that with increasing silicon content up to about 9% by weight, the microstructure of the cast samples consists of fine dispersion of Ti5Si3 suicide particles within the α- Ti(Si) solid solution matrix.
The alloys described by Frommeyer et. al. have excellent hardness and flow strength. The warm strength of the Ti-Si-Al alloys is, however, moderate and there is no indication of the oxidation resistance at high temperature.
There is thus a need for an alloy that has a high strength at high temperatures, has a lower melting point than the Ti-Al-V alloys and has good casting properties.
Description of invention
By the present invention it is provided Ti-Si alloys with relatively high silicon contents which exhibit a relatively low melting point due to their eutectic constitution, good casting properties and high strength at higher temperatures as well as a very high resistance to oxidation and creep deformation at high temperatures.
The present invention thus relates to a Ti-Si alloy comprising 2.5 - 12 wt % Si, 0 - 5 wt % Al, 0 -5 wt % Cr, 0 - 0.5 wt % B, 0 - 1 wt % rare earth metals and/or yttrium and/or Sc, the remaining except for impurities being Ti.
According to a preferred embodiment the alloy contains 0.3 - 3 wt % Al. According to another preferred embodiment the Ti-Si alloy contains 3 - 6 wt % Si and 1.2 - 2.5 wt % Al.
According to yet another preferred embodiment the alloy contains 0.001 to 0.15 wt % rare earth metals and/or scandium.
It has been found that the addition of rare earth metals and/or yttrium and/or scandium improves the warm strength and creep strength of the Ti-Si alloy up to at least 675°C,
The rare earths yttriym and scandium additions form a fine dispersion of thermo- dynamically stable oxides, such as Er2θ3, Y2O3 etc. in the Ti-Si alloy.
The alloy preferably contains 0.1 to 1.5 wt % Cr. The addition of Cr enhances solid solution hardening and therefore increases the strength and increase the oxidation resistance of the alloy.
In the as cast state, the Ti-Si alloy possesses fine-grained hypoeutectic, eutectic or slightly hypereutectic microstructures depending upon the silicon content. The microstructure of the eutectic Ti-Si alloy consists of finely dispersed Ti5Si3 suicide particles of discontinuous rod like shape within the hexagonal close-packed α- Ti(Si) solid solution matrix. The hypoeutectic microstructure consists of primary solidified α-Ti(Si) crystals and the surrounding eutectic.
The Ti-Si alloy according to the invention has with a yield stress of at least 800 MPa, a Brinell hardness of 350-400 HB and sufficient ductility and fracture toughness -stress intensity factor Kic . of more than 23 MPa Vm at room temperature and up to 5000C.
The Ti-Si alloy according to the invention further exhibits excellent oxidation resistance up to 65O0C and above depending upon the Si content and improved wear resistance both at room and elevated temperature. The yield strength at 65O0C will be of at least Rp0 2 >250 MPa and the tensile strength exceeds Rm =
450 MPa.
The hypereutectic microstructures consist of primary solidified TJsSi3 crystals of hexagonal shape within the fine-grained eutectic microstructure.
In the as cast state the hypoeutectic Ti-Si alloys exhibit at room temperature fractures toughness -K|C-values- of more than 23 MPa Vm , yield stress of more than 500 MPa with a plastic strain of more than 1.5 to 3 %.
The eutectic alloy shows a fracture toughness of K|C of 15 - 18 MPa Vm and the yield stress exceeds 850 MPa at room temperature. At 6000C and above the fracture toughness is increased to 30 MPa Vm and the strength is of the order of at least Rm = 450 MPa.
Oxidation tests with exposure to air at 6000C have resulted in an increase in mass of less than 5 mg/cm2 after 500 hours. In comparison the conventional Ti-AI6- V4 alloy exhibits alpha case formation at 4750C during long term exposure on air.
The creep stress (applied stress at given temperature where the creep rate is έ = 107S"1) of the eutectic Ti-Si alloy according to the invention is higher than 200 MPa at 6000C. In contrast the Ti-AI6-V4 alloy with potential application in the air plane and space industry exhibits a creep stress of about 150 MPa at 4500C.
The Ti-Si alloy according to the invention has a low melting point of between about 1330 and about 138O0C. The alloy according to the invention has further excellent casting properties making it possible to cast virtually any size and shape. As a result of its spectrum of characteristics properties presented above, the Ti-Si alloy according to this invention are advantageously suitable for the manufacture of diverse components, subjected to high temperature, such as:
connecting rods, piston crowns, piston pins, inlet and outlet valves and manifolds of exhaust gas mains in internal combustion engines and diesel engines;
static blades in axial flow compressors and fan blades in jet engines;
wear resistant parts in textile machines -weaving looms- like shuttles and connecting shafts;
surgical implants, bone plates, joints;
hard facings and surface alloys used as coatings in surface engineering for improving wear resistance and to avoid fretting;
watch cases;
pump cases and impellers for the chemical and oil industry.
The Ti-Si alloy according to the invention is particularly suitable for as cast components because of their relatively low melting temperatures of about 1330 to 138O0C and excellent castability.
The Ti-Si alloy according to the invention can be produced in conventional way, such as by arc melting in a water cooled copper hearth. Detailed description of invention
Example 1
A hypoeutectic Ti-6Si-2AI alloy according to the invention was produced by arc melting using a non consumable tungsten electrode. Titanium sponge with a purity of more than 99.8 wt %, metallurgical grade silicon and aluminium granules with a purity of more than 99.8 wt % were used as starting materials. The alloy was kept during arc melting in a water cooled copper hearth by forming a thin solid skull on the copper hearth and was then cast into a copper mould in order to achieve rod like ingots. These were machined by turning and grinding to cylindrical compression and tensile test samples exhibiting a smooth surface finish.
The Brinell hardness was determined to be about 336 + 3 HB 187.5/2.5 applying a testing load of 187.5 kp. The flow stress was determined at room temperature in compression test to be about Rp0 2 « 725 to 750 MPa and the plastic strain exceeds -εpι 10 %. The fracture toughness was measured in a four point bend test. The stress intensity factor Kic varies between 19 < Kic ≤ 21 MPa Vm. At higher temperature of 65O0C the flow stress is still 260 Rp0 2 275 MPa and the fracture toughness is about 32< K|C < 34 MPa Vm. The weight gain in an oxidation test on air at 6000C was 4.5 mg/cm2 after 525 hrs.
Example 2
A hypereutectic Ti-IOSi alloy containing 0.2 wt % Al was also produced by arc melting technique as described above in Example 1.
The macrohardness -Brinell- of this alloy was determined to be about 365 HB 187.5/2.5 and the yield stress at room temperature ranges between 930 < Rp <965 MPa depending upon the grain size of the alloy. The plastic strain in compression is about 6 to 8 % and the fracture toughness is in between K|C = 16 and 19 MPa Vm.
At higher temperature of 65O0C the yield stress is about 330 to 360 MPa. The fracture toughness is in between 25 and 28 MPa Vm. The creep strength was determined at 6000C and exhibits values of 215 to 230 MPa in the coarse-grained state.
The oxidation on air at 65O0C leads to a weight gain of about 3.8 mg/cm3 at 500 hrs exposure time.
Example 3
A hypoeutectic (near eutectic) oxide dispersion strengthened Ti-7Si-2Al alloy with addition of 0.07 mass-% Y was also produced by the arc melting technique described in example 1. Metallic Yttrium was added to the melt and formed Y2O3 with the dissolved oxygen of about 1200 ppm. The Brinell hardness was determined to be 347 ± 2 HB 187.5/2.5. The measured yield strength was about 960 to 990 MPa. First creep experiments at 600°C with the creep rate of έ =10"V1 showed a creep strength in between 235 and 255 MPa.
Example 4 A hypoeutectic oxide dispersion strengthened Ti-5.5Si-3.5AI.-1.5Cr-0.1 Y alloy was produced by the melting method technique described in Example 1. Metallic yttrium was added to the melt and formed Y2O3 with oxygen dissolved in the melt.
The Brinell hardness was measured to 373±2 HB at a load of 187.5 Kp at room temperature and the fracture toughness stress intensity was measured to Kic = 21
MPa Vm . At 650°C the tensile strength was measured to about Rm = 360 MPa, the fracture toughness was between 35 and 40 MPa Vϊn and the creep strength at the strain rate of έ =10'V1 excelled 270 MPa. Oxidation tests at 6000C in air exhibits a mass gain of less than 8 mg/cm3 after an exposure time of 500 hours. For comparison, the oxidation tests of the c coommmmeerrcciiaall T TΪΪ--66AAII--44VV a allllooyy s shhoo^ws a mass gain of more than 20 mg/cm3 after 500 hours exposure in air at 600°C.
These examples show that the Ti-Si alloys of the present invention have a surprisingly high warm strength and very good oxidation resistance at high temperatures.

Claims

Claims
1. High strength, oxidation and wear resistant titanium-silicon base alloy characterized in that the alloy contains: 2.5 - 12 wt % Si
0- 5wt%AI 0 - 0.5 % B 0 - 5 % Cr
0 - 1 wt % rare earth metals and/or yttrium and/or scandium balance Ti with unavoidable impurities.
2. Alloy according to claim 1, characterized in that the alloy contains 0.001 - 1 wt % rare earth metals and/or yttrium and/or scandium.
3. Alloy according to claim 1 and 2, characterized in that the alloy contains 0.3 to 3 wt % Al.
4. Alloy according to claim 2, characterized in that the alloy contains 0.001 - 0.15 wt % rare earth metal and/or scandium.
5. Alloy according to claims 1 -4, c h a ra ct e ri zed in that the alloy contains 0.1 to 1.5 wt % Cr.
6. Alloy according to claim 1 -5, characterized in that the alloy contains 0.01 to 0.03 wt % B.
7. Alloy according to claims 1-6, cha racterized i n that the alloy contains 3-6 wt % Si and 1.2-2.5 wt % al.
8. Alloy according to claim 1, with near eutectic composition and related microstructure, characterized in that the alloy contains 6 - 9 wt % Si 1.2 - 2.5 wt % Al
0.001 - 0.15 wt % rare earth metals with yield strength of more than 700 Mpa at room temperature, fracture toughness of more than K|C = 15 MPa Vm , and improved wear and oxidation resistance.
EP05767947.4A 2004-07-13 2005-07-01 High strength, oxidation and wear resistant titanium-silicon based alloy Active EP1778885B1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
NO20042959A NO20042959D0 (en) 2004-07-13 2004-07-13 High strength, oxidation and wear resistant titanium-silicon base alloys and the use thereof
NO20045664A NO322348B1 (en) 2004-07-13 2004-12-27 High strength titanium silicon alloys, oxidation and abrasion resistance
PCT/NO2005/000246 WO2006006869A1 (en) 2004-07-13 2005-07-01 High strength, oxidation and wear resistant titanium-silicon based alloy

Publications (3)

Publication Number Publication Date
EP1778885A1 true EP1778885A1 (en) 2007-05-02
EP1778885A4 EP1778885A4 (en) 2012-12-26
EP1778885B1 EP1778885B1 (en) 2014-12-10

Family

ID=35209717

Family Applications (1)

Application Number Title Priority Date Filing Date
EP05767947.4A Active EP1778885B1 (en) 2004-07-13 2005-07-01 High strength, oxidation and wear resistant titanium-silicon based alloy

Country Status (12)

Country Link
EP (1) EP1778885B1 (en)
JP (1) JP4599402B2 (en)
KR (1) KR20070049157A (en)
AU (1) AU2005263030B2 (en)
BR (1) BRPI0513282B1 (en)
CA (1) CA2571761C (en)
DK (1) DK1778885T3 (en)
EA (1) EA010770B1 (en)
ES (1) ES2530635T3 (en)
NO (1) NO322348B1 (en)
UA (1) UA82165C2 (en)
WO (1) WO2006006869A1 (en)

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103555999A (en) * 2013-11-06 2014-02-05 北京科技大学 High-strength cast Ti-Si-Al-B-Zr base alloy
CN103556000A (en) * 2013-11-11 2014-02-05 北京科技大学 Ti-Si-Al-based alloy containing RE (rare earth) and intermetallic compound reinforcing phase

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1995009932A1 (en) * 1993-10-06 1995-04-13 The University Of Birmingham Titanium alloy products and methods for their production

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH043459A (en) * 1990-04-19 1992-01-08 Mitsubishi Electric Corp Manufacture of laminated semiconductor device
JPH04105659A (en) * 1990-08-27 1992-04-07 Shinya Iwamoto Biological titanium alloy and manufacture thereof
US5366570A (en) * 1993-03-02 1994-11-22 Cermics Venture International Titanium matrix composites
JP2001089821A (en) * 1999-09-22 2001-04-03 Sumitomo Metal Ind Ltd Titanium alloy having high strength and high ductility and excellent in high temperature atmospheric oxidation resistance
JP2002088407A (en) * 2000-09-12 2002-03-27 Matsumoto Shika Univ Particle mainly consisting of metal, elecrode member and method for producing the elecrode member
JP3765475B2 (en) * 2000-11-16 2006-04-12 日立金属株式会社 Ti-Si alloy-based target material, method for producing the same, and film coating method
JP3793813B2 (en) * 2002-09-13 2006-07-05 独立行政法人産業技術総合研究所 High strength titanium alloy and method for producing the same

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1995009932A1 (en) * 1993-10-06 1995-04-13 The University Of Birmingham Titanium alloy products and methods for their production

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
See also references of WO2006006869A1 *
YU PORYADCHENKO N ET AL: "High-Temperature Strength of Titanium Alloys Alloyed with Silicon, Aluminum, and Zirconium in Air", MATERIALS SCIENCE, KLUWER ACADEMIC PUBLISHERS-CONSULTANTS BUREAU, NE, vol. 41, no. 2, 1 March 2005 (2005-03-01), pages 230-236, XP019222284, ISSN: 1573-885X, DOI: 10.1007/S11003-005-0155-1 *

Also Published As

Publication number Publication date
WO2006006869A1 (en) 2006-01-19
KR20070049157A (en) 2007-05-10
BRPI0513282B1 (en) 2014-09-16
EA200700126A1 (en) 2007-04-27
NO20045664L (en) 2006-01-16
NO20045664D0 (en) 2004-12-27
JP2008506838A (en) 2008-03-06
CA2571761C (en) 2010-06-01
JP4599402B2 (en) 2010-12-15
BRPI0513282A (en) 2008-05-06
EP1778885B1 (en) 2014-12-10
UA82165C2 (en) 2008-03-11
CA2571761A1 (en) 2006-01-19
AU2005263030A1 (en) 2006-01-19
EP1778885A4 (en) 2012-12-26
ES2530635T3 (en) 2015-03-04
NO322348B1 (en) 2006-09-18
DK1778885T3 (en) 2015-02-23
AU2005263030B2 (en) 2009-07-02
EA010770B1 (en) 2008-10-30

Similar Documents

Publication Publication Date Title
US9388481B2 (en) High strength, oxidation and wear resistant titanium-silicon based alloy
JP5270123B2 (en) Nitride reinforced cobalt-chromium-iron-nickel alloy
JP3388411B2 (en) High strength notched ductile precipitation hardened stainless steel alloy
JP4800864B2 (en) compressor
WO2008036760A2 (en) High strength, high stress corrosion cracking resistant and castable al-zn-mg-cu zr alloy for shape cast products
MXPA05001576A (en) Casting of an aluminium alloy.
RU2150528C1 (en) Titanium-based alloy
JPH0730419B2 (en) Chromium and silicon modified .GAMMA.-titanium-aluminum alloys and methods for their production
JP6028546B2 (en) Aluminum alloy
EP0327557A1 (en) Rapid solidification route aluminium alloys containing chromium.
AU2005263030B2 (en) High strength, oxidation and wear resistant titanium-silicon based alloy
JP4288821B2 (en) Low thermal expansion Fe-based heat-resistant alloy with excellent high-temperature strength
WO2017123186A1 (en) Tial-based alloys having improved creep strength by strengthening of gamma phase
JP2000345259A (en) CREEP RESISTANT gamma TYPE TITANIUM ALUMINIDE
JP3216837B2 (en) Iron-based super heat-resistant alloy for heat-resistant bolts
JPH05209249A (en) Low thermal expansion superalloy
JPH08134615A (en) Production of high strength titanium alloy excellent in characteristic of balance of mechanical property
JP2002235133A (en) beta TYPE TITANIUM ALLOY
JP4102224B2 (en) High strength, high ductility β-type titanium alloy
RU2228966C1 (en) Titanium-based alloy
JP3331625B2 (en) Method for producing Ti-Al-based intermetallic compound-based alloy
WO2023162540A1 (en) Aluminum alloy material and method for producing same
JP2022045612A (en) Titanium alloy, and manufacturing method of the same, and engine component using the same
CN114941087A (en) TiAlMoMn titanium alloy with high elasticity modulus and high strength and preparation method thereof
JP2004263260A (en) Ni-BASED, BORIDE-DISPERSED, ANTICORROSIVE WEAR-RESISTANT ALLOY

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20070212

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LI LT LU LV MC NL PL PT RO SE SI SK TR

DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20121122

RIC1 Information provided on ipc code assigned before grant

Ipc: C22F 1/18 20060101ALI20121116BHEP

Ipc: C22C 14/00 20060101AFI20121116BHEP

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20140422

GRAJ Information related to disapproval of communication of intention to grant by the applicant or resumption of examination proceedings by the epo deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR1

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

INTG Intention to grant announced

Effective date: 20140709

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IS IT LI LT LU LV MC NL PL PT RO SE SI SK TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602005045417

Country of ref document: DE

Effective date: 20150115

Ref country code: AT

Ref legal event code: REF

Ref document number: 700710

Country of ref document: AT

Kind code of ref document: T

Effective date: 20150115

REG Reference to a national code

Ref country code: DK

Ref legal event code: T3

Effective date: 20150216

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2530635

Country of ref document: ES

Kind code of ref document: T3

Effective date: 20150304

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 700710

Country of ref document: AT

Kind code of ref document: T

Effective date: 20141210

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20141210

REG Reference to a national code

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20141210

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG4D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150311

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150410

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150410

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602005045417

Country of ref document: DE

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed

Effective date: 20150911

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20150701

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20150731

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20150731

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20160331

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20150731

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20150701

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: CZ

Payment date: 20160610

Year of fee payment: 12

Ref country code: ES

Payment date: 20160613

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: TR

Payment date: 20160620

Year of fee payment: 12

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DK

Payment date: 20160712

Year of fee payment: 12

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20050701

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20141210

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CZ

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170701

REG Reference to a national code

Ref country code: DK

Ref legal event code: EBP

Effective date: 20170731

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170731

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20181107

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: ES

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170702

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170701

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: SE

Payment date: 20230613

Year of fee payment: 19

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20230607

Year of fee payment: 19

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20240606

Year of fee payment: 20