EP0649914B1 - An Fe-Mn vibration damping alloy steel and a method for making the same - Google Patents

An Fe-Mn vibration damping alloy steel and a method for making the same Download PDF

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Publication number
EP0649914B1
EP0649914B1 EP94401992A EP94401992A EP0649914B1 EP 0649914 B1 EP0649914 B1 EP 0649914B1 EP 94401992 A EP94401992 A EP 94401992A EP 94401992 A EP94401992 A EP 94401992A EP 0649914 B1 EP0649914 B1 EP 0649914B1
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EP
European Patent Office
Prior art keywords
alloy
alloy steel
vibration damping
ingot
cold rolling
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 - Lifetime
Application number
EP94401992A
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German (de)
English (en)
French (fr)
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EP0649914A2 (en
EP0649914A3 (en
Inventor
Chong-Sool Choi
Joong-Hwan Jun
Young-Sam Ko
Man-Eob Lee
Seung-Han Baek
Yong-Chul Son
Jeong-Cheol Kim
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Woojin Osk Corp
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Woojin Osk Corp
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Publication of EP0649914A2 publication Critical patent/EP0649914A2/en
Publication of EP0649914A3 publication Critical patent/EP0649914A3/en
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Publication of EP0649914B1 publication Critical patent/EP0649914B1/en
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a method for making an Fe-Mn vibration damping alloy steel at a low production cost.
  • vibration damping alloy In line with a trend for high-grade and high precision aircraft, ships, automotive vehicles and various machinery, vibration damping alloy is widely used in the many kinds of machine parts that are sources of vibration and noise. Study of vibration damping alloys has been lively because of the increase in demand for such alloys.
  • Vibration damping alloys developed and used so far are classified into following types: Fe-C-Si and Al-Zn which are of the composite type; Fe-Cr, Fe-Cr-Al and Co-Ni which are of the ferromagnetic type; Mg-Zr, Mg and Mg 2 Ni which are of the dislocation type;- and Mn-Cu, Cu-Al-Ni and Ni-Ti which are of the twin type.
  • the above vibration damping alloys have excellent vibration damping capacities but have poor mechanical properties. Thus, the alloys cannot be used widely; and since they contain a lot of expensive elements, the production costs are high, limiting the industrial use of the alloys.
  • an amount of electrolytic iron and an electrolytic manganese is weighed to contain 10 to 24% manganese by weight and the remainder iron.
  • the iron is melted first by heating in a melting furnace at more than 1500°C; and then the manganese is charged and melted.
  • the melted mixture is cast into a mold to produce an ingot.
  • the cast ingot is homogenized at 1000°C to 1300°C for 12 to 40 hours and then the homogenized ingot is hot-rolled to produce a rolled metal of a predetermined dimension.
  • the rolled metal is subjected to a solid solution treatment at 900°C to 1100°C for 30 to 60 minutes and cooled by air or water. Finally the rolled metal is again cold rolled around room temperature (25°C ⁇ 50°C) so as to have a reduction rate of 5-25%, thereby obtaining Fe-Mn alloy steels having high vibration damping capacities.
  • the reason why the above condition is determined in the present invention is as follows.
  • the homogenizing condition is defined to be at 1000°C to 1300°C for 12 to 40 hours so that the manganese, the main element, may be segregated during the period of time the ingot is cast.
  • the ingot is heated at a high temperature of 1000°C to 1300°C, the high concentrated manganese is diffused into a low concentration region which homogenizes the composition of the manganese.
  • the homogenization time may be reduced to be within 12 hours, but a local melting phenomenon may occur at the grain boundary where the manganese is segregated during casting. Accordingly, the homogenization is preferably performed at 1000°C to 1300°C for 12 to 40 hours.
  • the solid solution treatment is performed at 900°C to 1100°C for 30 to 60 minutes. If the treatment is carried out at higher than 1100°C, the grains of the alloys are coarsened which deteriorates the tensile strength. If the temperature is too low, such as less than 900°C, the grains become so small that raising the tensile strength decreases the martensite start temperature(Ms). Thus, a small amount of epsilon martensite is produced and the damping capacity is lowered. Accordingly, the optimum condition to have both excellent tensile strength and damping capacity is at 900°C to 1100°C for 30 to 60 minutes.
  • the alloy of the present invention contains manganese of 10 to 24% by weight, see, FIG. 1 of the binary phase diagram.
  • the alloys which contain up to 10% manganese create ⁇ ' martensite, the alloys which contain from 10 to 15% manganese create a 3-phase mixture structure of ⁇ + ⁇ ' + ⁇ , and the alloys which contain from 15 to 28% manganese create a 2-phase mixture structure of ⁇ + ⁇ .
  • the Fe-Mn vibration damping mechanism absorbs vibration energy by movement of the ⁇ / ⁇ interface under external vibration stress. If the manganese alloy is less than 10% Mn only one phase, ⁇ ' martensite is created and the vibration damping effect hardly occurs. Since ⁇ and ⁇ martensites are extensive in the 10 to 28% Mn alloys, a lot of ⁇ / ⁇ interfaces exist which yields high vibration damping effects.
  • the damping capacity cannot be improved by cold rolling when the alloy has more than 24% Mn by weight. Accordingly, the composition of Mn is defined to the range of 10 to 24% because ⁇ martensite is produced preferentially by cold rolling at around room temperature without slip dislocation.
  • the cold rolling is performed at a reduction of less than 30% at around the room temperature, more fine and thin ⁇ plates are produced inside by the cold rolling which increases the total interface area of the ⁇ / ⁇ interface, and higher vibration damping capacity is obtained than before the cold rolling. If the amount of cold rolling is increased to more than 30%, coalescence of ⁇ martensite plates occurs, and hence the ⁇ / ⁇ interface area is reduced. The martensite produced in this way restrains the movement of the ⁇ / ⁇ interface, and a lot of dislocations are produced inside the ⁇ and ⁇ martensites which interact with the ⁇ / ⁇ interface disturbing the movement of the ⁇ / ⁇ interface and thereby degrading the vibration damping capacity.
  • the alloy of the present invention may contain carbon of up to 0.2% by weight, silicon of up to 0.4% by weight, sulfur of up to 0.05% by weight, and phosphorus of up to 0.05% by weight as impurities.
  • the impurity elements are diffused to the ⁇ / ⁇ interfaces which locks the interface, and movement of the ⁇ / ⁇ interfaces is difficult, thereby degrading the vibration damping capacities.
  • Table 1 shows the comparison of results of the vibration damping capacities in the alloy of the present invention and the conventional alloy according to the cold rolling process.
  • the alloy of the present invention that has undergone cold rolling has a superior vibration damping effect compared to the alloy that is not cold rolled.
  • SDC Alloy Specific Damping Capacity
  • Fe-10% Mn 10 10 14 14 9 Alloy steel with composition according to the present invention Fe-13% Mn 12 12 16 16 11 Fe-15% Mn 15 15 20 20 14 Fe-17% Mn 25 25 30 30 23 Fe-20% Mn 25 25 30 30 23 Fe-23% Mn 22 22 27 27 21 Fe-24% Mn 15 15 20 20 14 Fe-26% Mn 9 9 10 10 9
  • FIG. 1 shows the Fe-rich side of Fe-Mn binary phase diagram which is the basis of this invention. Transformation temperatures of each phase are determined using a dilatometer by cooling at a rate of 3°C/min.
  • ⁇ ' martensite is formed in the case of up to 10% Mn by weight.
  • ⁇ + ⁇ ' + ⁇ is formed in the case of 10 to 15% Mn by weight.
  • ⁇ + ⁇ is formed in the case of 15 to 28% Mn by weight and a single phase structure of ⁇ in the case of more than 28% Mn by weight.
  • FIG. 2 shows a volume fraction of each phase by an X-ray diffraction analysis method after each alloy is subjected to solid solution treatment at 1000°C and air-cooled to the room temperature.
  • the Mn percentages by weight corresponding to ⁇ ' martensitic alloy have a poor vibration damping capacity and the alloy of ⁇ + ⁇ ' + ⁇ mixture structure has excellent vibration damping capacity as well as tensile strength.
  • Table 2 shows a comparison of vibration damping capacities according to martensitic structure in case of 10% reduction by cold rolling.
  • SDC Alloy Structure Specific Damping Capacity
  • Kg/mm2 Tensile Strength (Kg/mm2) Fe - 4% Mn ⁇ ' martensite 5 66 Fe - 17% Mn ⁇ + ⁇ '+ ⁇ martensite 30 70 Low Carbon Steel Tempered martensite 5 49
  • the alloy having the ⁇ + ⁇ ' + ⁇ mixture structure has a greater vibration damping capacity than that of ⁇ ' martensitic alloy, because the sub-structure of the ⁇ ' martensite consists of dislocations and absorbs vibration energy by movement of the dislocations.
  • the alloy of the ⁇ + ⁇ ' + ⁇ mixture structure if the alloy receives vibrational stress, the ⁇ / ⁇ interface moves and absorbs vibration energy yielding an excellent vibration damping capacity.
  • FIG. 3 shows the variation of a specific damping capacities according to the amount of cold rolling in case of the Fe-17% Mn alloy.
  • the specific damping capacity (SDC) is increased in accordance with the increase in the amount of cold rolling, and maximum vibration damping capacity is presented at the reduction rate from 10 to 20%. If the amount of cold rolling is more than about 20%, the SDC is decreased. If the amount of cold rolling is more than about 30%, the vibration damping capacity is less than the vibration damping capacity without cold rolling.
  • the method according to the present invention stipulates 5-25% cold rolling reduction rate.
  • the comparative alloy Fe-4%Mn
  • Fe-17%Mn alloy has a remarkable vibrational amplitude decay after water quenching for high temperature rolling (FIG. 4C).
  • FIG. 4D shows free vibration damping curves of a comparative alloy and the alloy of this invention before and after the cold rolling.
  • the alloys of this invention have vibration damping capacities and mechanical properties which are superior to conventional alloys.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Soundproofing, Sound Blocking, And Sound Damping (AREA)
EP94401992A 1993-10-22 1994-09-07 An Fe-Mn vibration damping alloy steel and a method for making the same Expired - Lifetime EP0649914B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR1019930021973A KR960006453B1 (ko) 1993-10-22 1993-10-22 Fe-Mn계 진동 감쇠 합금강과 그 제조 방법
KR9321973 1993-10-22

Publications (3)

Publication Number Publication Date
EP0649914A2 EP0649914A2 (en) 1995-04-26
EP0649914A3 EP0649914A3 (en) 1995-10-25
EP0649914B1 true EP0649914B1 (en) 1998-03-04

Family

ID=19366339

Family Applications (1)

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EP94401992A Expired - Lifetime EP0649914B1 (en) 1993-10-22 1994-09-07 An Fe-Mn vibration damping alloy steel and a method for making the same

Country Status (5)

Country Link
EP (1) EP0649914B1 (ko)
JP (1) JP2637371B2 (ko)
KR (1) KR960006453B1 (ko)
AT (1) ATE163687T1 (ko)
DE (1) DE69408773T2 (ko)

Families Citing this family (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20000033105A (ko) * 1998-11-19 2000-06-15 구자홍 칼라브라운관용 러그의 조성물 및 제조방법
JP4631228B2 (ja) * 2001-07-31 2011-02-16 株式会社豊田自動織機 ピストン式圧縮機における防振構造
US6979182B2 (en) 2001-07-31 2005-12-27 Kabushiki Kaisha Toyota Jidoshokki Vibration damping mechanism for piston type compressor
WO2006109919A1 (en) * 2005-04-11 2006-10-19 Korea Institute Of Science And Technology High-strength damping alloys and low-noise diamond saw using the same
DE102006059884B4 (de) * 2006-12-19 2020-08-06 Volkswagen Ag Austenitischer Schweißzusatzwerkstoff auf Eisen-Basis für das Schweißen eines austenitischen Werkstoffs mit einem weiteren Werkstoff
KR100840287B1 (ko) * 2006-12-26 2008-06-20 주식회사 포스코 잔류 오스테나이트와 ｈｃｐ 마르텐사이트 조직이 혼합된복합조직강 및 그의 열처리 방법
JP5200243B2 (ja) * 2007-02-14 2013-06-05 国立大学法人 名古屋工業大学 Ｆｅ−Ｍｎ系合金の制振特性向上方法
JP4984272B2 (ja) * 2009-08-26 2012-07-25 有限会社Ｔｋテクノコンサルティング 制振性に優れた鋼その製造方法及び該鋼を含んで構成される制振体
RU2443795C2 (ru) * 2010-04-16 2012-02-27 Тамара Федоровна Волынова МНОГОФУНКЦИОНАЛЬНЫЕ АНТИФРИКЦИОННЫЕ НАНОСТРУКТУРИРОВАННЫЕ ИЗНОСОСТОЙКИЕ ДЕМПФИРУЮЩИЕ С ЭФФЕКТОМ ПАМЯТИ ФОРМЫ СПЛАВЫ НА МЕТАСТАБИЛЬНОЙ ОСНОВЕ ЖЕЛЕЗА СО СТРУКТУРОЙ ГЕКСАГОНАЛЬНОГО ε-МАРТЕНСИТА И ИЗДЕЛИЯ С ИСПОЛЬЗОВАНИЕМ ЭТИХ СПЛАВОВ С ЭФФЕКТОМ САМООРГАНИЗАЦИИ НАНОСТРУКТУРНЫХ КОМПОЗИЦИЙ, САМОУПРОЧНЕНИЯ И САМОСМАЗЫВАНИЯ ПОВЕРХНОСТЕЙ ТРЕНИЯ, С ЭФФЕКТОМ САМОГАШЕНИЯ ВИБРАЦИЙ И ШУМОВ
JP2013221191A (ja) * 2012-04-18 2013-10-28 Nagoya Institute Of Technology 制振合金の処理方法
US9612141B2 (en) * 2013-04-25 2017-04-04 Woojin Inc. Ultrasonic flow measurement system
KR101518599B1 (ko) 2013-10-23 2015-05-07 주식회사 포스코 방진성이 우수한 고강도 고망간 강판 및 그 제조방법
KR101543898B1 (ko) * 2013-12-24 2015-08-11 주식회사 포스코 용접성 및 용접부 충격인성이 우수한 강재
KR101736636B1 (ko) * 2015-12-23 2017-05-17 주식회사 포스코 방진특성이 우수한 고Mn강판 및 그 제조방법
CN114807726A (zh) * 2022-05-06 2022-07-29 成都大学 一种快速制备Fe-Mn阻尼合金的方法

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE2434330A1 (de) * 1974-07-17 1976-01-29 Stephan & Soehne Teigmisch- und knetmaschine
JPS62142722A (ja) * 1985-12-18 1987-06-26 Nippon Steel Corp 溶接性に優れた高張力鋼の製造方法
EP0380630B1 (en) * 1988-07-08 1994-11-30 Famcy Steel Corporation Use of a high damping capacity, two-phase fe-mn-al-c alloy
JPH05255813A (ja) * 1991-12-24 1993-10-05 Nippon Steel Corp 加工性と制振性能に優れた高強度合金

Also Published As

Publication number Publication date
JP2637371B2 (ja) 1997-08-06
EP0649914A2 (en) 1995-04-26
KR960006453B1 (ko) 1996-05-16
ATE163687T1 (de) 1998-03-15
DE69408773D1 (de) 1998-04-09
JPH07150300A (ja) 1995-06-13
DE69408773T2 (de) 1998-08-13
KR950011633A (ko) 1995-05-15
EP0649914A3 (en) 1995-10-25

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