US20030185701A1 - Process for the production of Al-Fe-V-Si alloys - Google Patents
Process for the production of Al-Fe-V-Si alloys Download PDFInfo
- Publication number
- US20030185701A1 US20030185701A1 US10/112,052 US11205202A US2003185701A1 US 20030185701 A1 US20030185701 A1 US 20030185701A1 US 11205202 A US11205202 A US 11205202A US 2003185701 A1 US2003185701 A1 US 2003185701A1
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- Prior art keywords
- magnesium
- alloys
- melt
- master alloys
- alloy
- 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.)
- Abandoned
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- 238000000034 method Methods 0.000 title claims abstract description 29
- 230000008569 process Effects 0.000 title claims abstract description 24
- 229910000676 Si alloy Inorganic materials 0.000 title claims abstract description 12
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 11
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 45
- 239000011777 magnesium Substances 0.000 claims abstract description 45
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 41
- 239000000956 alloy Substances 0.000 claims abstract description 41
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical group [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims abstract description 29
- 239000000155 melt Substances 0.000 claims abstract description 10
- 238000005266 casting Methods 0.000 claims description 10
- 229910052782 aluminium Inorganic materials 0.000 claims description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 8
- 229910052720 vanadium Inorganic materials 0.000 claims description 8
- 230000008018 melting Effects 0.000 claims description 7
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 6
- 238000007872 degassing Methods 0.000 claims description 6
- 238000002844 melting Methods 0.000 claims description 6
- 238000001816 cooling Methods 0.000 claims description 5
- 239000007789 gas Substances 0.000 claims description 5
- 239000000203 mixture Substances 0.000 claims description 5
- 229910052710 silicon Inorganic materials 0.000 claims description 5
- 239000004411 aluminium Substances 0.000 claims description 4
- 229910052786 argon Inorganic materials 0.000 claims description 3
- 238000001125 extrusion Methods 0.000 claims description 3
- 229910018134 Al-Mg Inorganic materials 0.000 claims description 2
- 229910018125 Al-Si Inorganic materials 0.000 claims description 2
- 229910018467 Al—Mg Inorganic materials 0.000 claims description 2
- 229910018520 Al—Si Inorganic materials 0.000 claims description 2
- 229910018505 Ni—Mg Inorganic materials 0.000 claims description 2
- 229910007981 Si-Mg Inorganic materials 0.000 claims description 2
- 229910008316 Si—Mg Inorganic materials 0.000 claims description 2
- 230000004907 flux Effects 0.000 claims description 2
- 238000010438 heat treatment Methods 0.000 claims description 2
- 238000005098 hot rolling Methods 0.000 claims description 2
- 238000009827 uniform distribution Methods 0.000 abstract description 7
- 229910000838 Al alloy Inorganic materials 0.000 abstract description 3
- 229910021332 silicide Inorganic materials 0.000 abstract description 3
- 230000008859 change Effects 0.000 abstract description 2
- 210000001787 dendrite Anatomy 0.000 abstract description 2
- 239000010419 fine particle Substances 0.000 abstract description 2
- 239000011164 primary particle Substances 0.000 abstract description 2
- FVBUAEGBCNSCDD-UHFFFAOYSA-N silicide(4-) Chemical compound [Si-4] FVBUAEGBCNSCDD-UHFFFAOYSA-N 0.000 abstract description 2
- 230000000903 blocking effect Effects 0.000 abstract 1
- 239000000843 powder Substances 0.000 description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 239000000463 material Substances 0.000 description 7
- 238000007712 rapid solidification Methods 0.000 description 7
- 239000002245 particle Substances 0.000 description 5
- 238000009826 distribution Methods 0.000 description 4
- 229910052742 iron Inorganic materials 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 238000000889 atomisation Methods 0.000 description 3
- 239000004927 clay Substances 0.000 description 3
- 229910002804 graphite Inorganic materials 0.000 description 3
- 239000010439 graphite Substances 0.000 description 3
- 230000004048 modification Effects 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
- 229910000628 Ferrovanadium Inorganic materials 0.000 description 2
- 238000007596 consolidation process Methods 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- PNXOJQQRXBVKEX-UHFFFAOYSA-N iron vanadium Chemical compound [V].[Fe] PNXOJQQRXBVKEX-UHFFFAOYSA-N 0.000 description 2
- 238000002074 melt spinning Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000012552 review Methods 0.000 description 2
- 229910001203 Alloy 20 Inorganic materials 0.000 description 1
- 206010010144 Completed suicide Diseases 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000002939 deleterious effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000004512 die casting Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 229910001338 liquidmetal Inorganic materials 0.000 description 1
- ATTFYOXEMHAYAX-UHFFFAOYSA-N magnesium nickel Chemical compound [Mg].[Ni] ATTFYOXEMHAYAX-UHFFFAOYSA-N 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000010309 melting process Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- XUIMIQQOPSSXEZ-NJFSPNSNSA-N silicon-30 atom Chemical compound [30Si] XUIMIQQOPSSXEZ-NJFSPNSNSA-N 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
Definitions
- the present invention relates to an improved process for the production of high strength and high wear resistant Al—Fe—V—Si alloys.
- the present invention will be useful for the industries engaged in production of high strength wear resistant aluminium alloys which are widely used in aerospace, transport and other engineering sectors.
- U.S. Pat. No. 2,963,780 discloses a method for obtaining improved tensile strength at 350° C. in aluminium based alloys (see also: U.S. Pat. No. 2,967,351; U.S. Pat. No. 3,462,248).
- the alloys are formed by atomization of the liquid metals into finely divided droplets by high velocity gas streams. The droplets are then rapidly cooled to obtain the desired alloys. In atomization process the molten alloy is impacted by a high energy fluid for obtaining powders. The powders are cold pressed, degassed followed by hot consolidation (E. J. Lavernia, J. D Ayers, T. S. Srivatsan, International Materials Review, vol.
- the product capacity is limited to a small size only because the ribbon or powder so obtained are compacted or sintered to a small for obtaining homogeneous structure.
- the main object of the present invention is to establish melting treatment process for the production of cast and mechanically worked high strength and high wear resistant Al-fe-V—Si alloys leading to superior properties.
- the present invention provides a process for the production of high strength and high wear resistant Al—Fe—V—Si alloy which comprises
- the degassing of the melt is effected by adding flux or argon gas.
- the magnesium used is pure magnesium of 99.8% purity.
- the pure aluminium used is of 99.6% purity.
- the magnesium used is magnesium bearing master alloys selected from the group consisting of Al—Mg, F 3 —Si—Mg and Ni—Mg master alloys.
- the magnesium bearing master alloys used is selected from Al-10-20% Mg, Fe—Si-9-20% Mg and Ni-10-20% Mg.
- the process of present invention makes use of melting and alloying in a furnace. Casting are made in die casting or in permanent mould for ensuring a cooling rate 10-50° C./s, which is common in foundry practices.
- the microstructure of the cast materials reveals ten-armed star shaped particles with composition similar to Al 3 F 3 with some amount of V and Si along with other interdendritic Al—Fe-silicide phases. These star shaped particles act as notches, which are deleterious to the toughness of the materials.
- the chunky star shaped particles prevent proper feeding of the casting which results in microporosity in castings. Thus, the mechanical properties of the samples deteriorate to a greater extent.
- the present invention aims to modify/block primary intermetallic phases as well as interdendritic silicide phases by treating the melt with elemental magnesium or magnesium bearing master alloys to get a structure containing uniform distribution of intermetallic phases.
- the uniform distribution of primary and interdendritic phases are obtained with addition of magnesium or magnesium bearing master alloys because morphology of the interface changes, thus resulting in the creation of more nuclei. It also breaks dendrite of the primary particles leading to structural change and fine particles.
- Cooling rate required is much lesser than the existing of rapid solidification.
- the process of present invention has achieved distribution of refined primary intermetallic and interdendritic suicide phases.
- the cast and mechanically worked products produced by the present invention exhibit comparable mechanical properties to those produced by rapid solidification processing route.
Abstract
The present invention relates to an improved process for the production of high strength and high wear resistant Al—Fe—V—Si alloys. The present invention comprises modifying/blocking primary intermetallic phases as well as interdendritic silicide phases by treating the melt with elemental magnesium or magnesium bearing master alloys to get a structure containing uniform distribution of intermetallic phases. The uniform distribution of primary and interdendritic phases are obtained with addition of magnesium or magnesium bearing master alloys because morphology of the interface changes resulting in the creation of more nuclei. It also breaks dendrite of the primary particles leading to structural change and fine particles. The present invention is useful for the industries engaged in production of high strength wear resistant aluminium alloys which are widely used in aerospace, transport and other engineering sectors.
Description
- The present invention relates to an improved process for the production of high strength and high wear resistant Al—Fe—V—Si alloys. The present invention will be useful for the industries engaged in production of high strength wear resistant aluminium alloys which are widely used in aerospace, transport and other engineering sectors.
- In the general melting and casting process, the wide differences of densities and melting point of Al, Fe, V and Si couple with low diffusivity of Fe, V in Al pose problems in producing cast homogeneous structure. Al—Fe—V—Si alloys are generally produced and shaped through a costly technique or rapid solidification—powder compacting—extrusion/rolling route. In the prior art rapid solidification processes, such as atomization and melt spinning are used to obtain rapidly solidified alloy powders or ribbons respectively.
- U.S. Pat. No. 2,963,780 discloses a method for obtaining improved tensile strength at 350° C. in aluminium based alloys (see also: U.S. Pat. No. 2,967,351; U.S. Pat. No. 3,462,248). The alloys are formed by atomization of the liquid metals into finely divided droplets by high velocity gas streams. The droplets are then rapidly cooled to obtain the desired alloys. In atomization process the molten alloy is impacted by a high energy fluid for obtaining powders. The powders are cold pressed, degassed followed by hot consolidation (E. J. Lavernia, J. D Ayers, T. S. Srivatsan, International Materials Review, vol. 37, No. 1 (1992), 1-44). Then it is hot worked for obtaining final product. The melt spinning process employed a high pressure shock wave of gas to propel a small droplet of melt against a clean rotating metal wheel to produce a brittle ribbon or thin sheet. The ribbons are pulverized to obtain powder. The powders may be cold pressed and sintered or consolidated and heat treated (E. J. Lavernia, J. D. Ayers, T. S. Srivatsan, International Materials Review, vol. 37, No. 1 (1992), 1-44). Then it is extruded or rolled to make material for final product. U.S. Pat. No. 4,347,076 discloses formation of high strength aluminum alloys at temperatures of about 350° C. obtained by rapid solidification techniques. However, alloys obtained herein have low engineering ductility at room temperature and thus cannot be used in structural applications where a minimum tensile elongation of about 3% is required, for example in gas turbines.
- Rapid solidification techniques are however, capital intensive and require high skill of operation because:
- (i) the cooling rate is very high (10 to 10) which is difficult to achieve unless huge capital cost equipment is used
- (ii) the powders/ribbons so obtained are not of uniform size leading to deterioration of mechanical properties
- (iii) the steps of consolidation of the rapidly solidified alloy powders/melt spin ribbons and process to shape give additional cost to the technique
- (iv) the product capacity is limited to a small size only because the ribbon or powder so obtained are compacted or sintered to a small for obtaining homogeneous structure.
- It is therefore important to produce alloys which overcome the above problems associated with the art and at the same time where the manufacturing processes are not capital intensive.
- The main object of the present invention is to establish melting treatment process for the production of cast and mechanically worked high strength and high wear resistant Al-fe-V—Si alloys leading to superior properties.
- It is an object of the invention to provide a process for the production of Al—Fe—V—Si alloy in cast route whose mechanical properties are comparable with those of identical alloy made by the known process as mentioned above.
- Accordingly, the present invention provides a process for the production of high strength and high wear resistant Al—Fe—V—Si alloy which comprises
- (i) melting pure aluminum, Al—Fe—V, Al—Si master alloys at a temperature in the range of 800 to 1000° C. to obtain a melt of Al—Fe—V—Si in the following composition ranges.
- Fe=8 to 10 wt %, V=0.8 to 1.0 wt %, Si=0.8 to 1.7 wt % and balance Al,
- (ii) degassing the said melt
- (iii) adding magnesium or magnesium bearing master alloys in the range of 0.05-1.0 wt % to the degassed melt.
- (iv) pouring the resultant melt in a die to obtain a casting followed by cooling
- (v) heating the casting obtained to a temperature in the range of 350 to 500° C.
- (vi) hot rolling/extrusion of the homogenized casting in the temperature range of 250 to 500° C.
- In another embodiment of the invention the degassing of the melt is effected by adding flux or argon gas.
- In still another embodiment of the invention the magnesium used is pure magnesium of 99.8% purity.
- In an embodiment of the invention the pure aluminium used is of 99.6% purity.
- In yet another embodiment of the invention the magnesium used is magnesium bearing master alloys selected from the group consisting of Al—Mg, F3—Si—Mg and Ni—Mg master alloys.
- In another embodiment of the invention the magnesium bearing master alloys used is selected from Al-10-20% Mg, Fe—Si-9-20% Mg and Ni-10-20% Mg.
- The process of present invention makes use of melting and alloying in a furnace. Casting are made in die casting or in permanent mould for ensuring a cooling rate 10-50° C./s, which is common in foundry practices. The microstructure of the cast materials reveals ten-armed star shaped particles with composition similar to Al3F3 with some amount of V and Si along with other interdendritic Al—Fe-silicide phases. These star shaped particles act as notches, which are deleterious to the toughness of the materials. Moreover, the chunky star shaped particles prevent proper feeding of the casting which results in microporosity in castings. Thus, the mechanical properties of the samples deteriorate to a greater extent.
- The present invention aims to modify/block primary intermetallic phases as well as interdendritic silicide phases by treating the melt with elemental magnesium or magnesium bearing master alloys to get a structure containing uniform distribution of intermetallic phases. The uniform distribution of primary and interdendritic phases are obtained with addition of magnesium or magnesium bearing master alloys because morphology of the interface changes, thus resulting in the creation of more nuclei. It also breaks dendrite of the primary particles leading to structural change and fine particles.
- The following examples are given by way of illustration and should not be construed to limit the scope of invention.
- 2 kg of Al-8.0% Fe-0.8% V=0.9% Si alloy was melted in a clay bonded graphite crucible in electric resistance furnace. The alloy was modified with 0.5% pure magnesium. The materials taken were metallic silicon 18 gm, ferro-vanadium 25 gm, aluminium—30%, iron master alloy 510 gm. 0.5% pure magnesium (10 gm) was used to modify the alloy. After melting the melt was kept at a temperature of 860° C. for complete dissolution of solute elements. Degassing treatment was done by pure argon followed by magnesium treatment at temperature of 850° C. The melt was poured in metallic mould of 30 nun diameter. The specimen so obtained was evaluated for microstructure and mechanical properties. The microstructure was uniform distribution of primary and interdendritic phases in aluminium matrix. The mechanical properties were reported in Table-1.
TABLE 1 Mechanical properties of unmodified and modified alloys 0.2% proof strength Strength Elongation Alloy composition Condition of the alloy (kg/mm2) (kg/mm2) % Al-8.3Fe-0.8 V-0.9 Si As cast, untreated 12.5 13 2.5 Al-8.3Fe-O.8 V-0.9 Si 0.5% Mg treated 18 20 5 Al-8.3Fe-0.8 V-O.9 Si 1.0% Mg treated 19 22 6.5 Al-8.3Fe-0.5 V-0.9 Si 1.0% of Al-20% Mg treated 21 25 7 Al-8.3Fe-0.8 V-0.9 Si 1.5% of Al-20% Mg treated 23 26 8 Al-8.3Fe-0.8 V-0.9 Si 0.5% of Ni-20% Mg treated 25 29 9 Al-8.3Fe-0.8 V-0.9 Si 1.0% of Ni-20% Mg treated 27 32 9.5 - 2 k.g of Al-8.0% Fe-0.8% V-0.9% Si alloy was melted in clay bonded graphite crucible in electric resistance furnace. The melt was modified with 1.0% of aluminum 20% magnesium master alloy 20 gm of master alloy was taken. The microstructure obtained by this modification was more uniform distribution of primary and interdendritic phase. The particle size distribution was liner than pure magnesium treatment. The mechanical properties were shown in Table-1. The alloys were further hot rolled at a temperature of 350° C. and deformation was 75%. The mechanical properties was shown in Table-2
TABLE 2 Mechanical Properties of hot worked alloys, hot rolled at 350° C., reduction 75% 0.2% proof strength Strength Elongation Alloy composition Condition of the alloy (kg/mm2) (kg/mm2) % Al-8.3Fe-0.8 V-0.9 Si 1.0% of Al-20% Mg 26 32 8.5 Al-8.3Fe-0.8 V-0.9 Si 1.5% of Al029% Mg treated 29 35 9.0 Al-8.3Fe-0.8 V-0.9 Si 0.5% of Ni-20% Mg treated 29.5 35 12 Al-8.3Fe-0.8 V-0.9 Si 1.0% of Ni-20% Mg treated 32 38 11.5 - 3 kg of aluminum 08.3% iron-0.8% vanadium-0.9% silicon alloy was melted in a clay bonded graphite crucible in electric resistance furnace. The alloy was modified with 1.0% of nickel—20% magnesium The materials taken were silicon 30 gm, ferro-vanadium 38 gm, aluminium—30% iron master alloy 780 gm, nickel magnesium 30 gm. After degassing the melt the alloy was modified. Prior to modification the master alloy was preheated to 250° C. The microstructure obtained by modification was more uniform distribution or primary and interdentic phase. The particle size distribution was finer than pure magnesium treatment. The mechanical properties were shown in Table-1. The alloys were further hot rolled at a temperature of 350° C. and deformation was 75%. The mechanical properties are shown in Table-2.
- By the process of present invention a cast high strength and high wear resistant Al—Fe—V—Si alloy having uniforms distribution of primary phases in the form of cuboidal, hexagonal, rectangular shape and refined interdendritic phase has been achieved. The properties of the alloy produced by the process of present invention are comparable to those obtained known process. The mechanical properties also improved considerably after hot working as shown in Table 1 and 2 above.
- The Main Advantages of Present Invention Are:
- 1. The steps involved for making the alloy are simple economic and takes much shorter time than the existing process of rapid solidification route.
- 2. Costly equipment for making powders/ribbons are avoided in the process of present invention.
- 3. Cooling rate required is much lesser than the existing of rapid solidification.
- 4. The process of present invention has achieved distribution of refined primary intermetallic and interdendritic suicide phases.
- 5. The cast and mechanically worked products produced by the present invention exhibit comparable mechanical properties to those produced by rapid solidification processing route.
- 6. The cost of production of the present invention is much cheaper than the existing process of rapid solidification route.
Claims (6)
1. A process for the production of high strength and high wear resistant Al—Fe—V—Si alloy which comprises
(i) melting pure aluminum, Al—Fe—V, Al—Si master alloys at a temperature in the range of 800 to 1000° C. to obtain a melt of Al—Fe—V—Si in the following composition ranges.
Fe=8 to 10 wt %, V=0.8 to 1.0 wt %, Si=0.8 to 1.7 wt % and balance Al,
(ii) degassing the said melt
(iii) adding magnesium or magnesium bearing master alloys in the range of 0.05-1.0 wt % to the degassed melt.
(iv) pouring the resultant melt in a die to obtain a casting followed by cooling
(v) heating the casting obtained to a temperature in the range of 350 to 500° C.
(vi) hot rolling/extrusion of the homogenized casting in the temperature range of 250 to 500° C.
2. A process as claimed in claim 1 wherein the pure aluminium used is of 99.6% purity.
3. A process as claimed in claim 1 wherein the degassing of the melt is effected by adding flux or argon gas.
4. A process as claimed in claim 1 wherein the magnesium used is pure magnesium of 99.8% purity.
5. A process as claimed in claim 1 wherein the magnesium used is magnesium bearing master alloys selected from the group consisting of Al—Mg, F3—Si—Mg and Ni—Mg master alloys.
6. A process as claimed in claim 5 wherein the magnesium bearing master alloys used is selected from Al-10-20% Mg, Fe—Si-9-20% Mg and Ni-10-20% Mg.
Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PCT/IN2002/000071 WO2003080881A1 (en) | 2002-03-26 | 2002-03-26 | Process for the production of al-fe-v-si alloys |
US10/112,052 US20030185701A1 (en) | 2002-03-26 | 2002-04-01 | Process for the production of Al-Fe-V-Si alloys |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PCT/IN2002/000071 WO2003080881A1 (en) | 2002-03-26 | 2002-03-26 | Process for the production of al-fe-v-si alloys |
US10/112,052 US20030185701A1 (en) | 2002-03-26 | 2002-04-01 | Process for the production of Al-Fe-V-Si alloys |
Publications (1)
Publication Number | Publication Date |
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US20030185701A1 true US20030185701A1 (en) | 2003-10-02 |
Family
ID=30002056
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
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US10/112,052 Abandoned US20030185701A1 (en) | 2002-03-26 | 2002-04-01 | Process for the production of Al-Fe-V-Si alloys |
Country Status (2)
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US (1) | US20030185701A1 (en) |
WO (1) | WO2003080881A1 (en) |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR2880086A1 (en) * | 2004-12-23 | 2006-06-30 | Renault Sas | Mechanical friction component, for use as brake or clutch discs or drums, notably for motor vehicles, incorporates a friction zone of an alloy of aluminium and iron and other chosen elements |
WO2007039340A1 (en) * | 2005-09-30 | 2007-04-12 | BAM Bundesanstalt für Materialforschung und -prüfung | Method for producing a wear-resistant aluminum alloy, an aluminum alloy obtained according to the method, and use thereof |
DE102011004133A1 (en) | 2011-02-15 | 2012-08-16 | Federal-Mogul Wiesbaden Gmbh | Method for producing a lead-free, plated aluminum plain bearing |
US9945018B2 (en) | 2014-11-26 | 2018-04-17 | Honeywell International Inc. | Aluminum iron based alloys and methods of producing the same |
RU2725498C1 (en) * | 2019-09-18 | 2020-07-02 | Федеральное государственное бюджетное образовательное учреждение высшего образования "Московский государственный технологический университет "СТАНКИН" (ФГБОУ ВО "МГТУ "СТАНКИН") | Sintered ligature from powder materials for alloying aluminum alloys |
CN112779442A (en) * | 2020-12-28 | 2021-05-11 | 北京康普锡威科技有限公司 | High-strength heat-resistant aluminum alloy powder for 3D printing and preparation method thereof |
NL2032205B1 (en) * | 2021-12-13 | 2023-06-27 | Univ Guilin Technology | Wrought aluminium-ferro alloy and preparation method thereof |
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RU2395610C2 (en) * | 2008-07-17 | 2010-07-27 | Олег Владимирович Анисимов | Procedure for generation of additives and addition alloys for production of alloys |
-
2002
- 2002-03-26 WO PCT/IN2002/000071 patent/WO2003080881A1/en not_active Application Discontinuation
- 2002-04-01 US US10/112,052 patent/US20030185701A1/en not_active Abandoned
Cited By (11)
Publication number | Priority date | Publication date | Assignee | Title |
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FR2880086A1 (en) * | 2004-12-23 | 2006-06-30 | Renault Sas | Mechanical friction component, for use as brake or clutch discs or drums, notably for motor vehicles, incorporates a friction zone of an alloy of aluminium and iron and other chosen elements |
WO2007039340A1 (en) * | 2005-09-30 | 2007-04-12 | BAM Bundesanstalt für Materialforschung und -prüfung | Method for producing a wear-resistant aluminum alloy, an aluminum alloy obtained according to the method, and use thereof |
US20080219882A1 (en) * | 2005-09-30 | 2008-09-11 | Mathias Woydt | Method for Producing a Wear-Resistant Aluminum Alloy,An Aluminum Alloy Obtained According to the Method, and Ues Thereof |
DE102011004133A1 (en) | 2011-02-15 | 2012-08-16 | Federal-Mogul Wiesbaden Gmbh | Method for producing a lead-free, plated aluminum plain bearing |
WO2012110115A1 (en) | 2011-02-15 | 2012-08-23 | Federal-Mogul Wiesbaden Gmbh | Method for producing a lead-free, plated aluminium plain bearing |
DE102011004133B4 (en) * | 2011-02-15 | 2015-11-19 | Federal-Mogul Wiesbaden Gmbh | Method for producing a lead-free, plated aluminum plain bearing |
US9193017B2 (en) | 2011-02-15 | 2015-11-24 | Federal-Mogul Wiesbaden Gmbh | Method for producing a lead-free, plated aluminium plain bearing |
US9945018B2 (en) | 2014-11-26 | 2018-04-17 | Honeywell International Inc. | Aluminum iron based alloys and methods of producing the same |
RU2725498C1 (en) * | 2019-09-18 | 2020-07-02 | Федеральное государственное бюджетное образовательное учреждение высшего образования "Московский государственный технологический университет "СТАНКИН" (ФГБОУ ВО "МГТУ "СТАНКИН") | Sintered ligature from powder materials for alloying aluminum alloys |
CN112779442A (en) * | 2020-12-28 | 2021-05-11 | 北京康普锡威科技有限公司 | High-strength heat-resistant aluminum alloy powder for 3D printing and preparation method thereof |
NL2032205B1 (en) * | 2021-12-13 | 2023-06-27 | Univ Guilin Technology | Wrought aluminium-ferro alloy and preparation method thereof |
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