CA1336364C - High damping capacity, two-phase fe-mn-al-c alloy - Google Patents
High damping capacity, two-phase fe-mn-al-c alloyInfo
- Publication number
- CA1336364C CA1336364C CA000605033A CA605033A CA1336364C CA 1336364 C CA1336364 C CA 1336364C CA 000605033 A CA000605033 A CA 000605033A CA 605033 A CA605033 A CA 605033A CA 1336364 C CA1336364 C CA 1336364C
- Authority
- CA
- Canada
- Prior art keywords
- alloy
- cast iron
- phase
- alloys
- damping capacity
- 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.)
- Expired - Fee Related
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 38
- 239000000956 alloy Substances 0.000 title claims abstract description 38
- 238000013016 damping Methods 0.000 title claims abstract description 18
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 14
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 12
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 12
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910001141 Ductile iron Inorganic materials 0.000 claims abstract description 6
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims abstract description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 3
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 3
- 239000011651 chromium Substances 0.000 claims abstract description 3
- 230000002596 correlated effect Effects 0.000 claims abstract description 3
- 239000011572 manganese Substances 0.000 claims description 8
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 7
- 229910001566 austenite Inorganic materials 0.000 claims description 7
- 229910052748 manganese Inorganic materials 0.000 claims description 7
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 6
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 4
- 229910017052 cobalt Inorganic materials 0.000 claims description 4
- 239000010941 cobalt Substances 0.000 claims description 4
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 239000011733 molybdenum Substances 0.000 claims description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 3
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 3
- 229910052796 boron Inorganic materials 0.000 claims description 3
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 239000010949 copper Substances 0.000 claims description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 229910052758 niobium Inorganic materials 0.000 claims description 3
- 239000010955 niobium Substances 0.000 claims description 3
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 3
- 229910052757 nitrogen Inorganic materials 0.000 claims description 3
- 229910052710 silicon Inorganic materials 0.000 claims description 3
- 239000010703 silicon Substances 0.000 claims description 3
- 239000010936 titanium Substances 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 3
- 229910052721 tungsten Inorganic materials 0.000 claims description 3
- 239000010937 tungsten Substances 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 3
- 229910052726 zirconium Inorganic materials 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 235000000396 iron Nutrition 0.000 abstract description 5
- 230000007797 corrosion Effects 0.000 abstract description 2
- 238000005260 corrosion Methods 0.000 abstract description 2
- 229910002804 graphite Inorganic materials 0.000 abstract description 2
- 239000010439 graphite Substances 0.000 abstract description 2
- 229910001018 Cast iron Inorganic materials 0.000 abstract 2
- 229910000851 Alloy steel Inorganic materials 0.000 abstract 1
- 241000352333 Amegilla alpha Species 0.000 abstract 1
- 229910000975 Carbon steel Inorganic materials 0.000 abstract 1
- 229910000640 Fe alloy Inorganic materials 0.000 abstract 1
- 229910001060 Gray iron Inorganic materials 0.000 abstract 1
- 229910001296 Malleable iron Inorganic materials 0.000 abstract 1
- 230000001276 controlling effect Effects 0.000 abstract 1
- 229910001339 C alloy Inorganic materials 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910018487 Ni—Cr Inorganic materials 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000003381 stabilizer Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Laminated Bodies (AREA)
Abstract
Carbon steels and other hot-and cold-workable ferrous alloys generally have poor damping capacity as compared to that cast iron(gray cast iron, malleable cast iron and ductile cast iron). This is because the graphite in cast irons helps to absorb the damping force and depresses the damping wave. But cast iron can not be rolled into strip or sheet. By controlling the correlated concentrations of manganese, aluminum and carbon, Fe-Mn-Al-C based alloys are made to be a .alpha.+.gamma. two-phase alloy steel with different .alpha. and .gamma. volume fractions. With particular ferrite volumes, workable Fe-Mn-Al-C based alloys have equivalent and better damping capacity than that of cast irons especially in the high frequency side. Such alloys suppress the vibration noise that comes from machine rooms, motors, air conditioners, and etc.
Chromium and other minor amount of elements can be added to this alloy system to improve the corrosion resistance.
Chromium and other minor amount of elements can be added to this alloy system to improve the corrosion resistance.
Description
1 ~36364 HIGH DAMPING CAPACITY, TWO-PHASE Fe-Mn-Al-C ALLOY
BACKGROUND:
For the past years alpha-gamma two-phase alloys have been developed by adding molybdenum and cobalt to the Fe-Ni-Cr alloy syætem for the purpose of making alloys having both better stress corrosion and hydrogen embrittlement resistance.
But none of these alloys was designed for the purpose of higher damping capacity. The iron-base materials that have been used for high damping capacity are the cast irons. The graphite in gray cast irons is the most important factor for absorbing the high frequency vibration wave. But cast irons generally are not workable, making them of limited value in highdamping applications.
DESCRIPTION OF THE DRAWING
In the drawing:
Figure 1 depicts the damping capacity curve for an alloy of the invention; and Figure 2 depicts the damping capacity curve for ductile iron.
DETAILED DESCRIPTION OF THE INVENTION:
In Fe-Mn-Al-C alloys, manganese and carbon are gamma-phase formers and aluminum is an alpha-phase former. By suitable compositonal arrangement, Fe-Mn-~l-C alloys can be designed to be fully gamma phase, such as Fe-29Mn-7~1-lC.
Reduction of the manganese or carbon or both of them and the ~_ increase of aluminum can promote the appearance of alpha phase, and make the alloy an alpha+gamma two-phase ~teel. The volume fraction of alpha phase can be controlled by changing the amount of manganese or aluminum or carbon or other ferrite-forming elements.
la 60538-1062 The invention provides a ferrite-austenite two-phase alloy characterized by high damping capa~ity having a composition consisting essentially of about 10 to 45 wt%
manganese, about 4 to 15 wt% aluminum, 0 to about 12 wt%
chromium, about 0.01 to 0.7 wt% carbon and at least one of 0 to 4.0 wt% molybdenum, 0 to 4.0 wt% copper, 0 to 2.0 wt%
nickel, 0 to 3.5 wt% niobium, 0 to 500 ppm boron, 0 to 0.2 wt%
nitrogen, 0 to 3.5 wt% titanium, 0 to 2.0 wt% cobalt, 0 to 3.5 wt% vanadium, 0 to 3.5 wt% tungsten, 0 to 2.0 wt%
zirconium, and 0 to 2.5 wt% silicon and the balance essentially iron, said manganese and carbon as austenite formers being correlated relative to aluminum as a ferrite former such as to provide a two-phase alloy containing by volume about 25~ to 75~
ferrite and the balance essentially austenite, said alloy being characterized by a damping capa~ity substantially equivalent to that of ductile iron.
B
E~ample 1. -2- 1 3 3 6 3 6 4 This example illustrates the effect of the element compositions on the change of oc volume fraction in the E`e-Mn-Al-C based alloys. Manganese and car~on are austenite phase stabilizers and aluminum is a ferrite phase former. The effect of the carbon content on the fe~Tite fraction of the Fe-Mn-Al-C based alloys is shown in Table I. in which the chemical composition of aIuminum and manganese are essentially constant and the carbon content decreases from 0.6 wt% to 0.11 wt~o.With the decreasing of carbon content, the ferrite phase volume fractions of the alloys increases from 0% to 36%. With the change of manganese, carbon and alt~minum contents, the volume fractions of ferrite phase and balanced y phase is controlled to be from 25% to 76%. Within this ferrite fraction range, excellent damping capacity is always found in the Fe-Mn-Al-C based alloy.
Table I
\ composition Mn Al C ferrite vol%
alloy ~ t%) (wt%) (wt%) 1 26.0 7.4 0.5 0 2 26.3 7.6 0.34 11.9 3 25.8 7.4 0.11 36.0 E Y~rnPIe 2.
This example illustrates the good damping capacity of the said a+~ two-phase Fe-Mn-Al-C based alloys which have been measured and determined with comparison to ductile cast iron. The test sample of the invention contained 19.7Mn-5.84Al-5.74Cr-0.19C. The ferrite volume fraction is about 6~to balanced with y phase. The damping capacity curves of the d~rnping capacity tests of the Fe-~In-Al-C
based alloy and ductile cast iron are shown in Fig. 1 and Fig. 2. It is seen that the damping capacities of the two alloys are almost equivalent.
-3- 1 3:36364 ~E~ample 3.
-- This e~ample illustrates the good workability of a+y two-phase Fe-Mn-Al-C based alloys. The alloys listed in Table II were cast into ingot; homogenized at 1200C; cut and hot forged at 1200C; further ~nne~led at 1150C and descaled. The alloys were cold rolled into 2.0 mm thick strip and annealed. The fernte v~lume percentages of these strips were measured and are listed in Table III. The mechanical properties of these annealed strips are also listed in Table III. It is seen that the alloys of the invention have good workablility and excellent mechanical propertIes.
Table ll.
alloyno. I Mn ~ Al I C I Cr I Other #109 25.1 6.7 0.287 5.6 200ppmN2 #108 30.3 6.3 0.244 5.8 #320 21.6 6.8 0.11 0 ----#317 20.0 6.1 0.4 5.5 0.92Mo #129 33.4 10.3 0.47 2.1 0.2Ti #116 29.5 10.2 0.4 0 0.1Nb Table lll Isample no. 0.2% proof ultimate tensile % elongation hardness ferrite stress(ksi) stress (ksi) (Rb) %
~108 39 94 44 80 28 7r320 41 98 43 82 67 tr317 44 101 41 83 75 .t 129 61 112 38 86 65 tr 116 59 109 37 85 73
BACKGROUND:
For the past years alpha-gamma two-phase alloys have been developed by adding molybdenum and cobalt to the Fe-Ni-Cr alloy syætem for the purpose of making alloys having both better stress corrosion and hydrogen embrittlement resistance.
But none of these alloys was designed for the purpose of higher damping capacity. The iron-base materials that have been used for high damping capacity are the cast irons. The graphite in gray cast irons is the most important factor for absorbing the high frequency vibration wave. But cast irons generally are not workable, making them of limited value in highdamping applications.
DESCRIPTION OF THE DRAWING
In the drawing:
Figure 1 depicts the damping capacity curve for an alloy of the invention; and Figure 2 depicts the damping capacity curve for ductile iron.
DETAILED DESCRIPTION OF THE INVENTION:
In Fe-Mn-Al-C alloys, manganese and carbon are gamma-phase formers and aluminum is an alpha-phase former. By suitable compositonal arrangement, Fe-Mn-~l-C alloys can be designed to be fully gamma phase, such as Fe-29Mn-7~1-lC.
Reduction of the manganese or carbon or both of them and the ~_ increase of aluminum can promote the appearance of alpha phase, and make the alloy an alpha+gamma two-phase ~teel. The volume fraction of alpha phase can be controlled by changing the amount of manganese or aluminum or carbon or other ferrite-forming elements.
la 60538-1062 The invention provides a ferrite-austenite two-phase alloy characterized by high damping capa~ity having a composition consisting essentially of about 10 to 45 wt%
manganese, about 4 to 15 wt% aluminum, 0 to about 12 wt%
chromium, about 0.01 to 0.7 wt% carbon and at least one of 0 to 4.0 wt% molybdenum, 0 to 4.0 wt% copper, 0 to 2.0 wt%
nickel, 0 to 3.5 wt% niobium, 0 to 500 ppm boron, 0 to 0.2 wt%
nitrogen, 0 to 3.5 wt% titanium, 0 to 2.0 wt% cobalt, 0 to 3.5 wt% vanadium, 0 to 3.5 wt% tungsten, 0 to 2.0 wt%
zirconium, and 0 to 2.5 wt% silicon and the balance essentially iron, said manganese and carbon as austenite formers being correlated relative to aluminum as a ferrite former such as to provide a two-phase alloy containing by volume about 25~ to 75~
ferrite and the balance essentially austenite, said alloy being characterized by a damping capa~ity substantially equivalent to that of ductile iron.
B
E~ample 1. -2- 1 3 3 6 3 6 4 This example illustrates the effect of the element compositions on the change of oc volume fraction in the E`e-Mn-Al-C based alloys. Manganese and car~on are austenite phase stabilizers and aluminum is a ferrite phase former. The effect of the carbon content on the fe~Tite fraction of the Fe-Mn-Al-C based alloys is shown in Table I. in which the chemical composition of aIuminum and manganese are essentially constant and the carbon content decreases from 0.6 wt% to 0.11 wt~o.With the decreasing of carbon content, the ferrite phase volume fractions of the alloys increases from 0% to 36%. With the change of manganese, carbon and alt~minum contents, the volume fractions of ferrite phase and balanced y phase is controlled to be from 25% to 76%. Within this ferrite fraction range, excellent damping capacity is always found in the Fe-Mn-Al-C based alloy.
Table I
\ composition Mn Al C ferrite vol%
alloy ~ t%) (wt%) (wt%) 1 26.0 7.4 0.5 0 2 26.3 7.6 0.34 11.9 3 25.8 7.4 0.11 36.0 E Y~rnPIe 2.
This example illustrates the good damping capacity of the said a+~ two-phase Fe-Mn-Al-C based alloys which have been measured and determined with comparison to ductile cast iron. The test sample of the invention contained 19.7Mn-5.84Al-5.74Cr-0.19C. The ferrite volume fraction is about 6~to balanced with y phase. The damping capacity curves of the d~rnping capacity tests of the Fe-~In-Al-C
based alloy and ductile cast iron are shown in Fig. 1 and Fig. 2. It is seen that the damping capacities of the two alloys are almost equivalent.
-3- 1 3:36364 ~E~ample 3.
-- This e~ample illustrates the good workability of a+y two-phase Fe-Mn-Al-C based alloys. The alloys listed in Table II were cast into ingot; homogenized at 1200C; cut and hot forged at 1200C; further ~nne~led at 1150C and descaled. The alloys were cold rolled into 2.0 mm thick strip and annealed. The fernte v~lume percentages of these strips were measured and are listed in Table III. The mechanical properties of these annealed strips are also listed in Table III. It is seen that the alloys of the invention have good workablility and excellent mechanical propertIes.
Table ll.
alloyno. I Mn ~ Al I C I Cr I Other #109 25.1 6.7 0.287 5.6 200ppmN2 #108 30.3 6.3 0.244 5.8 #320 21.6 6.8 0.11 0 ----#317 20.0 6.1 0.4 5.5 0.92Mo #129 33.4 10.3 0.47 2.1 0.2Ti #116 29.5 10.2 0.4 0 0.1Nb Table lll Isample no. 0.2% proof ultimate tensile % elongation hardness ferrite stress(ksi) stress (ksi) (Rb) %
~108 39 94 44 80 28 7r320 41 98 43 82 67 tr317 44 101 41 83 75 .t 129 61 112 38 86 65 tr 116 59 109 37 85 73
Claims (13)
1. A ferrite-austenite two-phase alloy characterized by high damping capacity having a composition consisting essentially of about 10 to 45 wt% manganese, about 4 to 15 wt%
aluminum, 0 to about 12 wt% chromium, about 0.01 to 0.7 wt%
carbon and at least one of 0 to 4.0 wt% molybdenum, 0 to 4.0 wt% copper, 0 to 2.0 wt% nickel, 0 to 3.5 wt% niobium, 0 to 500 ppm boron, 0 to 0.2 wt% nitrogen, 0 to 3.5 wt%
titanium, 0 to 2.0 wt% cobalt, 0 to 3.5 wt% vanadium, 0 to 3.5 wt% tungsten, 0 to 2.0 wt% zirconium, and 0 to 2.5 wt%
silicon and the balance essentially iron, said manganese and carbon as austenite formers being correlated relative to aluminum as a ferrite former such as to provide a two-phase alloy containing by volume about 25% to 75% ferrite and the balance essentially austenite, said alloy being characterized by a damping capacity substantially equivalent to that of ductile iron.
aluminum, 0 to about 12 wt% chromium, about 0.01 to 0.7 wt%
carbon and at least one of 0 to 4.0 wt% molybdenum, 0 to 4.0 wt% copper, 0 to 2.0 wt% nickel, 0 to 3.5 wt% niobium, 0 to 500 ppm boron, 0 to 0.2 wt% nitrogen, 0 to 3.5 wt%
titanium, 0 to 2.0 wt% cobalt, 0 to 3.5 wt% vanadium, 0 to 3.5 wt% tungsten, 0 to 2.0 wt% zirconium, and 0 to 2.5 wt%
silicon and the balance essentially iron, said manganese and carbon as austenite formers being correlated relative to aluminum as a ferrite former such as to provide a two-phase alloy containing by volume about 25% to 75% ferrite and the balance essentially austenite, said alloy being characterized by a damping capacity substantially equivalent to that of ductile iron.
2. The alloy of claim 1 containing 0 to 4.0 wt%
molybdenum.
molybdenum.
3. The alloy of claim 1 containing 0 to 4.0 wt% copper.
4. The alloy of claim 1 containing 0 to 2.0 wt% nickel.
5. The alloy of claim 1 containing 0 to 3.5 wt% niobium.
6. The alloy of claim 1 containing 0 to 500 ppm boron.
7. The alloy of claim 1 containing 0 to 0.2 wt%
nitrogen.
nitrogen.
8. The alloy of claim 1 containing 0 to 3.5 wt%
titanium.
titanium.
9. The alloy of claim 1 containing 0 to 2.0 wt% cobalt.
10. The alloy of claim 1 containing 0 to 3.5 wt% vanadium
11. The alloy of claim 1 containing 0 to 3.5 wt%
tungsten.
tungsten.
12. The alloy of claim 1 containing 0 to 2.0 wt%
zirconium.
zirconium.
13. The alloy of claim 1 containing 0 to 2.5 wt% silicon.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US07/218,695 US4875933A (en) | 1988-07-08 | 1988-07-08 | Melting method for producing low chromium corrosion resistant and high damping capacity Fe-Mn-Al-C based alloys |
| US218,695 | 1988-07-08 | ||
| US341,117 | 1989-04-20 | ||
| US07/341,117 US4966636A (en) | 1988-07-08 | 1989-04-20 | Two-phase high damping capacity F3-Mn-Al-C based alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1336364C true CA1336364C (en) | 1995-07-25 |
Family
ID=26913151
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000605033A Expired - Fee Related CA1336364C (en) | 1988-07-08 | 1989-07-07 | High damping capacity, two-phase fe-mn-al-c alloy |
Country Status (7)
| Country | Link |
|---|---|
| EP (1) | EP0380630B1 (en) |
| JP (1) | JPH03500305A (en) |
| AT (1) | ATE114736T1 (en) |
| AU (1) | AU610429B2 (en) |
| CA (1) | CA1336364C (en) |
| DE (1) | DE68919672T2 (en) |
| WO (1) | WO1990000629A1 (en) |
Families Citing this family (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR960006453B1 (en) * | 1993-10-22 | 1996-05-16 | 최종술 | Fe-Mn vibration damping alloy steel and its manufacturing method |
| CN1043253C (en) * | 1995-08-18 | 1999-05-05 | 赵学胜 | Al-Mn-Si-N series austenitic stainless acid-resisting steel |
| DE10259230B4 (en) * | 2002-12-17 | 2005-04-14 | Thyssenkrupp Stahl Ag | Method for producing a steel product |
| US20090165897A1 (en) * | 2005-02-02 | 2009-07-02 | Corus Staal Bv | Austenitic steel having high strength and formability, method of producing said steel and use thereof |
| EP2008971A4 (en) | 2006-04-20 | 2010-08-04 | Asahi Glass Co Ltd | CORE SILICA-ENVELOPE AND METHOD FOR MANUFACTURING SAME |
| WO2013064202A1 (en) * | 2011-11-03 | 2013-05-10 | Tata Steel Nederland Technology B.V. | Method of manufacturing a duplex steel sheet having enhanced formability |
| WO2013178887A1 (en) * | 2012-05-31 | 2013-12-05 | Arcelormittal Investigación Desarrollo Sl | Low-density hot- or cold-rolled steel, method for implementing same and use thereof |
| DK3265102T3 (en) | 2015-03-06 | 2025-10-13 | Atea Pharmaceuticals Inc | BETA-D-2'-DEOXY-2'ALPHA-FLUORO-2'-BETA-C-SUBSTITUTED-2-MODIFIED-N6-SUBSTITUTED PURIN NUCLEOTIDES FOR HCV TREATMENT |
| CN104674109B (en) * | 2015-03-11 | 2017-01-18 | 北京科技大学 | Low-density Fe-Mn-Al-C system cold-rolled automobile steel plate and preparation method |
| KR101910744B1 (en) * | 2017-07-26 | 2018-10-22 | 포항공과대학교 산학협력단 | Medium-entropy alloys with excellent cryogenic properties |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CA655825A (en) * | 1963-01-15 | Ciba Limited | Unsaturated aliphatic amino-diols and process for their manufacture | |
| DE1239857B (en) * | 1959-06-23 | 1967-05-03 | United States Steel Corp | Use of an austenitic steel alloy for forgeable components |
| AU8261182A (en) * | 1981-04-22 | 1982-10-28 | Unisearch Limited | Oxidation and corrosion-resistant febase-al-mn alloys |
| JPS60248866A (en) * | 1984-05-24 | 1985-12-09 | Yamato Metal Kogyo Kk | Stainless steel for cryogenic service having excellent sea water resistance |
-
1989
- 1989-07-06 EP EP89908610A patent/EP0380630B1/en not_active Expired - Lifetime
- 1989-07-06 AT AT89908610T patent/ATE114736T1/en not_active IP Right Cessation
- 1989-07-06 AU AU39815/89A patent/AU610429B2/en not_active Ceased
- 1989-07-06 JP JP1508050A patent/JPH03500305A/en active Pending
- 1989-07-06 DE DE68919672T patent/DE68919672T2/en not_active Expired - Fee Related
- 1989-07-06 WO PCT/US1989/002950 patent/WO1990000629A1/en not_active Ceased
- 1989-07-07 CA CA000605033A patent/CA1336364C/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| AU3981589A (en) | 1990-02-05 |
| ATE114736T1 (en) | 1994-12-15 |
| EP0380630A1 (en) | 1990-08-08 |
| EP0380630A4 (en) | 1990-12-27 |
| AU610429B2 (en) | 1991-05-16 |
| DE68919672T2 (en) | 1995-04-06 |
| DE68919672D1 (en) | 1995-01-12 |
| WO1990000629A1 (en) | 1990-01-25 |
| EP0380630B1 (en) | 1994-11-30 |
| JPH03500305A (en) | 1991-01-24 |
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