EP0380630B1 - Use of a high damping capacity, two-phase fe-mn-al-c alloy - Google Patents
Use of a high damping capacity, two-phase fe-mn-al-c alloy Download PDFInfo
- Publication number
- EP0380630B1 EP0380630B1 EP89908610A EP89908610A EP0380630B1 EP 0380630 B1 EP0380630 B1 EP 0380630B1 EP 89908610 A EP89908610 A EP 89908610A EP 89908610 A EP89908610 A EP 89908610A EP 0380630 B1 EP0380630 B1 EP 0380630B1
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- EP
- European Patent Office
- Prior art keywords
- alloy
- cast iron
- phase
- damping capacity
- alloys
- 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.)
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- 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
Definitions
- This invention relates to a high damping capacity, two-phase Fe-Mn-Al-C alloy.
- alpha-gamma two-phase alloys have been developed by adding molybdenum and cobalt to the Fe-Ni-Cr alloy system for the purpose of making alloys having both better stress corrosion and hydrogen embrittlement resistance.
- the iron-based 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 high damping applications.
- a ferrite-austenite two-phase alloy for high damping capacity applications, said alloy having a composition comprising of 10 to 45 wt% manganese, 4 to 15 wt% aluminum, up to 12 wt% chromium, 0.01 to 0.7 wt% carbon and optionally containing 0 to 4.0 wt% molybdenum, 0 to 4.0 wt% copper, 0 to 2.0 wt% nickel, 0 to 3.5 wt% niobium, up to 500 ppm boron, up 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, up to 2.5 wt% silicon, the balance iron and impurities, the composition being such that the ferrite phase of said alloy comprises 25% to 75%
- Fe-Mn-Al-C alloys manganese and carbon are gamma-phase formers and aluminum is an alpha-phase former.
- Fe-Mn-Al-C alloys can be designed to be fully gamma phase, such as Fe-29Mn-7A1-1C. 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 steel.
- the volume fraction of alpha phase can be controlled by changing the amount of manganese or aluminum or carbon or other ferrite-forming elements.
- This example illustrates the effect of the element compositions on the change of a volume fraction in the Fe-Mn-Al-C based alloys.
- Manganese and carbon are austenite phase stabilizers and aluminum is a ferrite phase former.
- the effect of the carbon content on the ferrite fraction of the Fe-Mn-Al-C based alloys is shown in Table I, in which the chemical composition of aluminum and manganese are essentially constant and the carbon content decreases from 0.5 wt% to 0.11 wt%. 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 aluminum contents, the volume fractions of ferrite phase and balanced ⁇ phase is controlled to be from 25% to 75%.
- This example illustrates the good damping capacity of the said ⁇ + ⁇ 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 65% balanced with ⁇ phase.
- the damping capacity curves of the damping capacity tests of the Fe-Mn-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.
- This example illustrates the good workability of ⁇ + ⁇ two-phase Fe-Mn-Al-C based alloys.
- the alloys listed in Table II were cast into ingot; homogenized at 1200°C; cut and hot forged at 1200°C; further annealed at 1150°C and descaled.
- the alloys were cold rolled into 2.0 mm thick strip and annealed.
- the ferrite volume 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 workability and excellent mechanical properties. Table II alloy no.
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- 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
Description
- This invention relates to a high damping capacity, two-phase Fe-Mn-Al-C alloy.
- Previously, alpha-gamma two-phase alloys have been developed by adding molybdenum and cobalt to the Fe-Ni-Cr alloy system for the purpose of making alloys having both better stress corrosion and hydrogen embrittlement resistance. However, none of these alloys was designed for the purpose of higher damping capacity. The iron-based 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 high damping applications.
- According to the present invention, there is provided use of a ferrite-austenite two-phase alloy for high damping capacity applications, said alloy having a composition comprising of 10 to 45 wt% manganese, 4 to 15 wt% aluminum, up to 12 wt% chromium, 0.01 to 0.7 wt% carbon and optionally containing 0 to 4.0 wt% molybdenum, 0 to 4.0 wt% copper, 0 to 2.0 wt% nickel, 0 to 3.5 wt% niobium, up to 500 ppm boron, up 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, up to 2.5 wt% silicon, the balance iron and impurities, the composition being such that the ferrite phase of said alloy comprises 25% to 75% by volume of the alloy, the remainder being essentially austenite, said alloy having a damping capacity of about the same level as that of ductile iron.
- For a better understanding of the invention, and to show how the same may be carried into effect, reference will now be made, by way of example only, to the accompanying drawings, in which:-
- Figure 1 depicts the damping capacity curve for an alloy in accordance with the present invention; and
- Figure 2 depicts the damping capacity curve for ductile iron.
- In Fe-Mn-Al-C alloys, manganese and carbon are gamma-phase formers and aluminum is an alpha-phase former. By suitable compositional arrangement, Fe-Mn-Al-C alloys can be designed to be fully gamma phase, such as Fe-29Mn-7A1-1C. 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 steel. The volume fraction of alpha phase can be controlled by changing the amount of manganese or aluminum or carbon or other ferrite-forming elements.
- This example illustrates the effect of the element compositions on the change of a volume fraction in the Fe-Mn-Al-C based alloys. Manganese and carbon are austenite phase stabilizers and aluminum is a ferrite phase former. The effect of the carbon content on the ferrite fraction of the Fe-Mn-Al-C based alloys is shown in Table I, in which the chemical composition of aluminum and manganese are essentially constant and the carbon content decreases from 0.5 wt% to 0.11 wt%. 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 aluminum contents, the volume fractions of ferrite phase and balanced γ phase is controlled to be from 25% to 75%. Within this ferrite fraction range, excellent damping capacity is always found in the Fe-Mn-Al-C based alloy.
Table I composition alloy No. Mn (wt%) Al (wt%) C (wt%) ferrite vol% 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 - This example illustrates the good damping capacity of the said α + γ 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 65% balanced with γ phase. The damping capacity curves of the damping capacity tests of the Fe-Mn-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.
- This example illustrates the good workability of α+γ two-phase Fe-Mn-Al-C based alloys. The alloys listed in Table II were cast into ingot; homogenized at 1200°C; cut and hot forged at 1200°C; further annealed at 1150°C and descaled. The alloys were cold rolled into 2.0 mm thick strip and annealed. The ferrite volume 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 workability and excellent mechanical properties.
Table II alloy no. Mn Al C Cr 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 III sample no. 0.2% proof stress (ksi) ultimate tensile stress (ksi) % elongation hardness (Rb) ferrite % #109 45 103 42 84 45 #108 39 94 44 80 28 #320 41 98 43 82 67 #317 44 101 41 83 75 #129 61 112 38 86 65 #116 59 109 37 85 73 1 ksi = 6.895 MPa
Claims (1)
- Use of a ferrite-austenite two-phase alloy for high damping capacity applications, said alloy having a composition comprising of 10 to 45 wt% manganese, 4 to 15 wt% aluminum, up to 12 wt% chromium, 0.01 to 0.7 wt% carbon and optionally containing 0 to 4.0 wt% molybdenum, 0 to 4.0 wt% copper, 0 to 2.0 wt% nickel, 0 to 3.5 wt% niobium, up to 500 ppm boron, up 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, up to 2.5 wt% silicon, the balance iron and impurities, the composition being such that the ferrite phase of said alloy comprises 25% to 75% by volume of the alloy, the remainder being essentially austenite, said alloy having a damping capacity of about the same level as that of ductile iron.
Applications Claiming Priority (5)
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 |
US218695 | 1988-07-08 | ||
US07/341,117 US4966636A (en) | 1988-07-08 | 1989-04-20 | Two-phase high damping capacity F3-Mn-Al-C based alloy |
US341117 | 1989-04-20 | ||
PCT/US1989/002950 WO1990000629A1 (en) | 1988-07-08 | 1989-07-06 | High damping capacity, two-phase fe-mn-al-c alloy |
Publications (3)
Publication Number | Publication Date |
---|---|
EP0380630A1 EP0380630A1 (en) | 1990-08-08 |
EP0380630A4 EP0380630A4 (en) | 1990-12-27 |
EP0380630B1 true EP0380630B1 (en) | 1994-11-30 |
Family
ID=26913151
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP89908610A Expired - Lifetime EP0380630B1 (en) | 1988-07-08 | 1989-07-06 | Use of a 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 (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR960006453B1 (en) * | 1993-10-22 | 1996-05-16 | 최종술 | Making method of vibration decrease alloy steel & the manufacturing process |
DE10259230B4 (en) * | 2002-12-17 | 2005-04-14 | Thyssenkrupp Stahl Ag | Method for producing a steel product |
CN101111622B (en) * | 2005-02-02 | 2011-09-07 | 塔塔钢铁艾默伊登有限责任公司 | Austenitic steel having high strenght and formability method of producing said steel and use thereof |
WO2007122930A1 (en) | 2006-04-20 | 2007-11-01 | Asahi Glass Company, Limited | Core-shell silica and method for producing 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 |
AU2016229966B2 (en) | 2015-03-06 | 2018-09-27 | Atea Pharmaceuticals, Inc. | Beta-D-2'-deoxy-2'alpha-fluoro-2'-beta-C-substituted-2-modified-N6-substituted purine 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 DE DE68919672T patent/DE68919672T2/en not_active Expired - Fee Related
- 1989-07-06 AT AT89908610T patent/ATE114736T1/en not_active IP Right Cessation
- 1989-07-06 WO PCT/US1989/002950 patent/WO1990000629A1/en active IP Right Grant
- 1989-07-06 JP JP1508050A patent/JPH03500305A/en active Pending
- 1989-07-06 EP EP89908610A patent/EP0380630B1/en not_active Expired - Lifetime
- 1989-07-06 AU AU39815/89A patent/AU610429B2/en not_active Ceased
- 1989-07-07 CA CA000605033A patent/CA1336364C/en not_active Expired - Fee Related
Also Published As
Publication number | Publication date |
---|---|
WO1990000629A1 (en) | 1990-01-25 |
AU3981589A (en) | 1990-02-05 |
ATE114736T1 (en) | 1994-12-15 |
CA1336364C (en) | 1995-07-25 |
EP0380630A1 (en) | 1990-08-08 |
EP0380630A4 (en) | 1990-12-27 |
JPH03500305A (en) | 1991-01-24 |
DE68919672D1 (en) | 1995-01-12 |
AU610429B2 (en) | 1991-05-16 |
DE68919672T2 (en) | 1995-04-06 |
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