Indian Patents. 255271:HIGH STRENGTH, OXIDATION AND WEAR RESISTANT TITANIUM SILICON BASED ALLOY

Title of Invention	HIGH STRENGTH, OXIDATION AND WEAR RESISTANT TITANIUM SILICON BASED ALLOY
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.

Full Text	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 a/p-titanium and near cc-titanium alloys, such as Ti-6AI-4V, [Mi 834 (TI-5.8-AI-4Sn-3Zr-0.7Nb-0.5Mo-0.35Si-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 a>mbination of high strength and fracture toughness and excellent fatigue properties at room and elevated temperature. These alloys have, however, some isadvantages such as a poor oxidation resistance above 475°C (a-case Kxntation), insufficient creep strength at 600°C and higher temperatures and a poor wear resistance at room and elevated temperatures. The a-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 1660cC) and the necessary melt overheating to about 1750 to 177O°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 Low saicon-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 (totai 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 silicides, 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 silicide particles within the oc-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-AI 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 tower melting point than the Ti-AI-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 iBrnoeratures. Tne 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 % Bf 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 and1.2-2.5wt%AI. According to yet another preferred embodiment the alloy contains 0.001 to 0.15 wt % rare earth metafs 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 Er2O3, 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 3»tefion resistance of the alloy. in the as cast state, the Ti-Si alloy possesses fine-grained hypoeutectic, eutectic or sfightty hypereutectic microstructures depending upon the silicon content The mioDstructune of the eutectic Ti-Si alloy consists of finely dispersed T15S13 silicide particles of discontinuous rod like shape within the hexagonal close-packed ~hs Ti-Si aDoy according to the invention has with a yield stress of at least 800 M?s. a 3rinell hardness of 350-400 HB and sufficient ductility and fracture :oughness -stress intensity factor Kic > of more than 23 MPa^ at room temperature and up to 500°C. The ThSi aJloy according to the invention further exhibits excellent oxidation resistance up to 650°C and above depending upon the Si content and improved wear resistance both at room and elevated temperature. The yield strength at 650°C will be of at least RPQ2 >250 MPa and the tensile strength exceeds Rm = 450 MPa. The hypereutectic microstructures consist of primary solidified Ti5Si3 crystals of hexagonal shape within the fine-grained eutectic microstructure. in the as cast state the hypoeuteetic Ti-Si alloys exhibit at room temperature fractures toughness -Kic-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 KiC of 15 - 18 MPa Vm and the yield stress exceeds 850 MPa at room temperature. At 600°C and above the fracture toughness is increased to 30 MPa Vm and the strength is of the order of a4 least Rm = 450 MPa. Oxidation tests wfth exposure to air at 600°C have resulted in an increase in mass of tess than 5 mg/cm2 after 500 hours. In comparison the conventional TI-AI6-V4 afloy exhibits alpha case formation at 475°C during long term exposure on air. The creep stress (applied stress at given temperature where the creep rate is e = 1 oV1) of the eutectic Ti-Si alloy according to the invention is higher than 200 MPa at 50C5C. 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 450°C. The Ti-Si alloy according to the invention has a low melting point of between aoaut 1330 and about 1380°C. 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 oi! industry. e ThS\ alloy according to the invention is particularly suitable for as cast toonents because of their relatively low melting temperatures of about 1330 to 38O°C and excellent castabiiity. -~r ~H-S\ alloy according to the invention can be produced in conventional way, ucr as by arc meiting 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 bad of 187.5 kp. The flow stress was determined at room temperature in compression test to be about RP « 725 to 750 MPa and the plastic strain exceeds -spj 10 %. The fracture toughness was measured in a four point bend tsst The stress intensity factor KjC varies between 19 £ Kic ^ 21 MPa Vm. At -uqher temperature of 650°C the flow stress is still 260 RPft, 275 MPa and the fracture toughness is about 32^ K\|C A hypereutectic TMOSi 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 137.5/2.5 and the yield stress at room temperature ranges between 930 RPo 2 ^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 19MPaVm. At higher temperature of 650°C 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°C and exhibits values of 215 to 230 MPa in the coarse-grained state. The oxidation on air at 650°C 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-2AI 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 oeermined to be 347 ±2 HB 187.5/2.5. The measured yield strength was about 960 to 990 MPa. Rrst creep experiments at 600°C with the creep rate of e =10'V1 shewed 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 "he Brinell hardness was measured to 373±2 HB at a load of 187.5 Kp at room s and the fracture toughness stress intensity was measured to Kic = 21 . At 650°C the tensile strength was measured to about Rm = 360 MPa, the fracture toughness was between 35 and 40 MPa Jm and the creep strength at the strain rate of s =10"7s1 excelled 270 MPa. Oxidation tests at 600°C 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 commercial TI-6AI-4V alloy shows 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 1. High strength, oxidation and wear resistant titanium-silicon base alloy characterized in that the alloy contains: 2.5-12wt%Si 0- 5wt%AI 0 - 0.5 % B 0-5%Cr 0.001 -1 wt % rare earth metals and/or yttrium and/or scandium balance Ti with unavoidable impurities. 2. Alloy according to claim ^characterized in that the alloy contains 0.3 to 3 wt % Ai. 3. Alloy according to claim 1 or 2, characterized in that the attoy contains 0.001 - 0.15 wt % rare earth metal and/or scandium. 4. Alloy according to claims 1-3, characterized in that the alloy contains 0.1 to 1.5 wt % Cr. 5. Alloy according to claim 1-4, characterized in that the anion contains 0.01 to 0.03 wt % B. z Alloy according to claims 1-5, characterized in that the alley contains 3-6 wt % Si and 1.2*2.5 wt % AI. Alloy according to claim 1, with near eutectic composition and •3a=t5c "Icrostructure, characterized in that the alloy contains 6 - 9 wt % Si -.2-2.5wt%Ai 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 MPaVm, and improved wear and oxidation resistance.

Full Text

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 a/p-titanium and near cc-titanium alloys, such as Ti-6AI-4V, [Mi 834 (TI-5.8-AI-4Sn-3Zr-0.7Nb-0.5Mo-0.35Si-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 a>mbination of high strength and fracture toughness and excellent fatigue properties at room and elevated temperature. These alloys have, however, some isadvantages such as a poor oxidation resistance above 475°C (a-case Kxntation), insufficient creep strength at 600°C and higher temperatures and a poor wear resistance at room and elevated temperatures. The a-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 1660cC) and the necessary melt overheating to about 1750 to 177O°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
Low saicon-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 (totai 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 silicides, 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 silicide particles within the oc-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-AI 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 tower melting point than the Ti-AI-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 iBrnoeratures.
Tne 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 % Bf 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 and1.2-2.5wt%AI.
According to yet another preferred embodiment the alloy contains 0.001 to 0.15 wt % rare earth metafs 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 Er2O3, 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 3»tefion resistance of the alloy.
in the as cast state, the Ti-Si alloy possesses fine-grained hypoeutectic, eutectic or sfightty hypereutectic microstructures depending upon the silicon content The mioDstructune of the eutectic Ti-Si alloy consists of finely dispersed T15S13 silicide particles of discontinuous rod like shape within the hexagonal close-packed ~hs Ti-Si aDoy according to the invention has with a yield stress of at least 800 M?s. a 3rinell hardness of 350-400 HB and sufficient ductility and fracture
:oughness -stress intensity factor Kic > of more than 23 MPa^ at room temperature and up to 500°C.
The ThSi aJloy according to the invention further exhibits excellent oxidation resistance up to 650°C and above depending upon the Si content and improved

wear resistance both at room and elevated temperature. The yield strength at 650°C will be of at least RPQ2 >250 MPa and the tensile strength exceeds Rm =
450 MPa.
The hypereutectic microstructures consist of primary solidified Ti5Si3 crystals of hexagonal shape within the fine-grained eutectic microstructure.
in the as cast state the hypoeuteetic Ti-Si alloys exhibit at room temperature
fractures toughness -Kic-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 KiC of 15 - 18 MPa Vm and the yield stress exceeds 850 MPa at room temperature. At 600°C and above the
fracture toughness is increased to 30 MPa Vm and the strength is of the order of a4 least Rm = 450 MPa.
Oxidation tests wfth exposure to air at 600°C have resulted in an increase in mass of tess than 5 mg/cm2 after 500 hours. In comparison the conventional TI-AI6-V4 afloy exhibits alpha case formation at 475°C during long term exposure on air.
The creep stress (applied stress at given temperature where the creep rate is e = 1 oV1) of the eutectic Ti-Si alloy according to the invention is higher than 200 MPa at 50C5C. 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 450°C.
The Ti-Si alloy according to the invention has a low melting point of between aoaut 1330 and about 1380°C. 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 oi! industry.
e ThS\ alloy according to the invention is particularly suitable for as cast toonents because of their relatively low melting temperatures of about 1330 to
38O°C and excellent castabiiity.
-~r ~H-S\ alloy according to the invention can be produced in conventional way, ucr as by arc meiting 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 bad of 187.5 kp. The flow stress was determined at room temperature in compression test to be about RP « 725 to 750 MPa and the plastic strain
exceeds -spj 10 %. The fracture toughness was measured in a four point bend tsst The stress intensity factor KjC varies between 19 £ Kic ^ 21 MPa Vm. At -uqher temperature of 650°C the flow stress is still 260 RPft, 275 MPa and the
fracture toughness is about 32^ K|C A hypereutectic TMOSi 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 137.5/2.5 and the yield stress at room temperature ranges between 930
RPo 2 ^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 19MPaVm.
At higher temperature of 650°C 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°C and exhibits values of 215 to 230 MPa in the coarse-grained
state.
The oxidation on air at 650°C 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-2AI 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 oeermined to be 347 ±2 HB 187.5/2.5. The measured yield strength was about 960 to 990 MPa. Rrst creep experiments at 600°C with the creep rate of e =10'V1 shewed 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
"he Brinell hardness was measured to 373±2 HB at a load of 187.5 Kp at room s and the fracture toughness stress intensity was measured to Kic = 21
. At 650°C the tensile strength was measured to about Rm = 360 MPa,
the fracture toughness was between 35 and 40 MPa *Jm and the creep strength at the strain rate of s =10"7s*1 excelled 270 MPa.

Oxidation tests at 600°C 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 commercial TI-6AI-4V alloy shows 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
1. High strength, oxidation and wear resistant titanium-silicon base
alloy characterized in that the alloy contains:
2.5-12wt%Si 0- 5wt%AI 0 - 0.5 % B 0-5%Cr
0.001 -1 wt % rare earth metals and/or yttrium and/or scandium balance Ti with unavoidable impurities.
2. Alloy according to claim ^characterized in that the
alloy contains 0.3 to 3 wt % Ai.
3. Alloy according to claim 1 or 2, characterized in that the
attoy contains 0.001 - 0.15 wt % rare earth metal and/or scandium.
4. Alloy according to claims 1-3, characterized in that the
alloy contains 0.1 to 1.5 wt % Cr.
5. Alloy according to claim 1-4, characterized in that the
anion contains 0.01 to 0.03 wt % B.
z Alloy according to claims 1-5, characterized in that the
alley contains 3-6 wt % Si and 1.2*2.5 wt % AI.
Alloy according to claim 1, with near eutectic composition and •3a=t5c "Icrostructure, characterized in that the alloy contains
6 - 9 wt % Si
-.2-2.5wt%Ai
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 MPaVm, and improved wear and oxidation resistance.

Documents:

0125-chenp-2007-abstract.pdf

0125-chenp-2007-claims.pdf

0125-chenp-2007-correspondnece-others.pdf

0125-chenp-2007-description(complete).pdf

0125-chenp-2007-form 1.pdf

0125-chenp-2007-form 26.pdf

0125-chenp-2007-form 3.pdf

0125-chenp-2007-form 5.pdf

0125-chenp-2007-others.pdf

0125-chenp-2007-pct.pdf

125-CHENP-2007 AMENDED CLAIMS 17-01-2013.pdf

125-CHENP-2007 AMENDED PAGES OF SPECIFICATION 17-01-2013.pdf

125-CHENP-2007 CORRESPONDENCE OTHERS 01-02-2012.pdf

125-CHENP-2007 EXAMINATION REPORT REPLY RECEIVED 17-01-2013.pdf

125-CHENP-2007 PRIORITY DOCUMENT 17-01-2013.pdf

125-CHENP-2007 CORRESPONDENCE OTHERS 05-06-2012.pdf

125-CHENP-2007 FORM-3 17-01-2013.pdf

125-CHENP-2007 OTHER PATENT DOCUMENT 17-01-2013.pdf

125-CHENP-2007 POWER OF ATTORNEY 17-01-2013.pdf

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Patent Number

255271

Indian Patent Application Number

125/CHENP/2007

PG Journal Number

06/2013

Publication Date

08-Feb-2013

Grant Date

08-Feb-2013

Date of Filing

11-Jan-2007

Name of Patentee

ELKEM ASA

Applicant Address

HOFFSVEIEN 65B, 0377 OSLO,

Inventors:

#	Inventor's Name	Inventor's Address
1	FROMMEYER, GEORG	CARL-ZUCKMAYER-STRASSE 38, 40699 EKRATH, GERMANY;
2	HALVORSEN, GUNNAR,	ASVEIEN 18, N-4620 KRISTIANSAND S, NORWAY;
3	JOHANSEN, KAI	LINERLEBAKKEN 20, N-4621 KRISTIANSALAND S NORWAY;
4	MIKKELSEN, OYVIND	SOLLIVEIEN 5, N-4621 KRISTIANSAND S, NORWAY;
5	SCHUSSLER, GUNNAR	BARLINV. 10, N-4621 KRISTIANSLAND S, NORWAY;
6	FORWALD, KARL	SELJEVEIEN 16, N-4622 KRISTINSAND,

PCT International Classification Number

C22C14/00

PCT International Application Number

PCT/NO05/00246

PCT International Filing date

2005-07-01

PCT Conventions:

#	PCT Application Number	Date of Convention	Priority Country
1	20045664	2004-12-27	U.S.A.
2	20042959	2004-07-13	U.S.A.