WO2009145039A1 - 高剛性高減衰能鋳鉄 - Google Patents

高剛性高減衰能鋳鉄 Download PDF

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Publication number
WO2009145039A1
WO2009145039A1 PCT/JP2009/058705 JP2009058705W WO2009145039A1 WO 2009145039 A1 WO2009145039 A1 WO 2009145039A1 JP 2009058705 W JP2009058705 W JP 2009058705W WO 2009145039 A1 WO2009145039 A1 WO 2009145039A1
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Prior art keywords
cast iron
modulus
young
vibration damping
damping
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PCT/JP2009/058705
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English (en)
French (fr)
Japanese (ja)
Inventor
高橋　栄
藤本　亮輔
坂本　直樹
Original Assignee
東芝機械株式会社
Priority date (The priority date 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 date listed.)
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Publication date
Application filed by 東芝機械株式会社 filed Critical 東芝機械株式会社
Priority to KR1020137001618A priority Critical patent/KR101423892B1/ko
Priority to DE112009001294T priority patent/DE112009001294B4/de
Publication of WO2009145039A1 publication Critical patent/WO2009145039A1/ja
Priority to US12/940,140 priority patent/US20110041960A1/en
Priority to US14/015,760 priority patent/US20140000832A1/en

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/10—Cast-iron alloys containing aluminium or silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D25/00—Special casting characterised by the nature of the product
    • B22D25/06—Special casting characterised by the nature of the product by its physical properties
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D27/00—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting
    • B22D27/20—Measures not previously mentioned for influencing the grain structure or texture; Selection of compositions therefor
    • 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
    • C21D5/00—Heat treatments of cast-iron
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/08—Making cast-iron alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys

Definitions

  • This invention relates to a cast iron with high rigidity and high damping ability which is excellent in Young's modulus and vibration damping properties.
  • the cast iron of the present invention is used, for example, as a structural material for machine tools and high-precision machine tools that require rigidity, or precision measuring instruments in which Young's modulus and vibration are problems. Thereby, those processing efficiency, the precision of a processed product, and precision precision can be improved.
  • flake graphite lead cast iron having relatively excellent vibration damping ability has been mainly used as a structural material for machine tools. Since flake graphite cast iron has a complex type vibration isolation mechanism by containing a large amount of flake graphite, it has a high damping capacity compared to steel, etc., and also has formability and cost for manufacturing large structural materials. This has advantageous features.
  • materials having excellent damping ability such as concrete materials, natural granite, and CFRP.
  • flake graphite cast iron is widely used in structural materials such as machine tool beds, tables, and columns because of its excellent damping properties, castability, and cost.
  • a machine tool that processes difficult-to-work materials with severe work hardening requires high rigidity for stably maintaining a large depth of cut and high vibration damping ability for suppressing generation of harmful vibrations.
  • the current flake graphite cast iron may not be able to obtain sufficient processing efficiency and accuracy of the processed product due to the influence of vibration.
  • flake graphite cast iron such as FC300 used for machine tools or the like contains a large amount of flake graphite that exhibits a composite damping mechanism. Therefore, it is a structural material that is excellent in vibration damping ability among conventional materials. In order to improve the vibration damping capacity of the flake graphite cast iron, the amount of flake graphite may be increased. However, there is a problem that the dynamic Young's modulus (hereinafter simply referred to as Young's modulus) decreases as the amount of flake graphite cast iron increases. Adjustment of the graphite amount of flake graphite cast iron can be controlled by the amount of C and Si. As a structural material of a machine tool, when the Young's modulus decreases, it becomes necessary to increase the thickness of the structural material in order to maintain rigidity. Therefore, not only a problem in structural design occurs, but also the cost increases, which is not preferable.
  • Young's modulus As a structural material of a machine tool, when the Young's modulus decreases, it
  • Patent Documents 1 to 3 show measurement results of vibration damping ability. However, since there is no description regarding the Young's modulus, the value is unknown. Specifically, since Patent Documents 1 and 2 relate to brake materials, it is presumed that Young's modulus is not indispensable but rather strength is emphasized. In particular, Patent Document 1 describes that it is an object of the present invention to provide a brake material having excellent strength comparable to that of gray cast iron and having a damping capacity superior to that of gray cast iron. Patent Document 3 describes that an aluminum-containing vibration-damping cast iron was invented in order to improve the vibration-damping performance from the viewpoint of improving the vibration-damping performance of machine tools and precision machining equipment. However, in order to maintain the mechanical accuracy, it is indispensable to maintain the rigidity of the structural material, but this is not shown.
  • Patent Document 1 a cast iron with the addition of aluminum was heated at A 1 transformation point or above (910 ⁇ 1000 °C), and perlite to 70% in the subsequent cooling rate and adjust the area ratio vibrations Brake material with excellent damping capacity and strength has been obtained.
  • Patent Document 2 have been achieved improvements in the vibration damping capacity by in the effects and hypereutectic compositions of A 1 added to form a bulking and fine pores of the graphite, the method Young's modulus is significantly reduced Is done.
  • Patent Document 3 is an example in which aluminum is added to improve vibration damping performance. However, it does not touch on Young's modulus. That is, in the methods described in Patent Documents 1 to 3, the Young's modulus and the vibration damping ability cannot always be achieved, so it is necessary to further improve the vibration damping ability.
  • the present invention has been made in consideration of such circumstances, and has both a Young's modulus and a vibration damping capability, both of which have been problems of the prior art, while being able to further improve the vibration damping capability and excellent in a high Young's modulus and vibration damping capability.
  • An object is to provide cast iron with high rigidity and high damping capacity.
  • the present invention provides a high-rigidity and high-damping capacity cast iron having a Young's modulus comparable to that of conventionally used flake graphite cast iron having an excellent vibration-damping capacity and significantly superior vibration-damping capacity. The purpose is to do.
  • the high rigidity and high damping capacity cast iron according to this invention is cast iron containing Al: 3 to 7%, and is obtained by heating at 280 to 630 ° C. after casting and further cooling treatment.
  • the first invention includes Al: 3 to 7%, Mn: 0.25 to 1.0%, P: 0.04% or less, S: 0.03% or less, It is cast iron comprising the balance Fe and inevitable impurities, and is characterized by being obtained by heating at 280 to 630 ° C. after casting and further cooling.
  • the high rigidity and high damping capacity cast iron according to the present invention is cast iron containing Al: 3 to 7% and Sn: 0.03 to 0.20%, and 280 to 630 after casting. It is obtained by heating at 0 ° C. and further cooling treatment. More specifically, the second invention relates to Al: 3-7%, Mn: 0.25-1.0%, P: 0.04% or less, S: 0.03% or less, Sn: 0.03 to 0.20%, cast iron composed of the balance Fe and inevitable impurities, characterized by being obtained by heating at 280 to 630 ° C. after casting and further cooling.
  • Cast iron composed of ⁇ 1.0%, P: 0.04% or less, S: 0.03% or less, Sn: 0.03 ⁇ 0.20%, balance Fe and inevitable impurities, It is characterized by being obtained by heating at 280 to 630 ° C. and further cooling.
  • the present invention it is possible to obtain a high-rigidity, high-damping capacity cast iron excellent in Young's modulus and vibration damping ability that can further improve the vibration damping capacity while achieving both Young's modulus and vibration damping capacity. Specifically, it is possible to obtain a high-rigidity, high-damping capacity cast iron having a Young's modulus comparable to that of conventionally used flake graphite cast iron having excellent vibration-damping capacity and significantly superior vibration-damping capacity.
  • FIG. 1 is a characteristic diagram showing the relationship between the heat treatment temperature and the improvement rate of the damping performance.
  • FIG. 2 is a characteristic diagram showing the relationship between the Young's modulus and logarithmic decay rate of Al-added flake graphite cast iron.
  • FIG. 3 is a characteristic diagram showing the relationship between the Young's modulus and the logarithmic decay rate of Al, Sn-added flake graphite cast iron.
  • the present inventors have made further improvements to find out the present invention.
  • the vibration damping capacity is improved with the addition amount of Al (aluminum), but the limit appears.
  • the addition amount of Al is sequentially increased and the vibration damping ability and Young's modulus are measured, the improvement is seen from the addition of 3% Al, but when it exceeds 7%, the vibration damping ability is rather lowered.
  • Young's modulus and vibration damping ability are improved by adding an appropriate amount of tin (Sn) to flake graphite cast iron to which Al is added.
  • the present inventors greatly change the vibration damping capacity and Young's modulus by adjusting the carbon equivalent (CE), (C / Si) weight ratio of flake graphite cast iron, and the addition amounts of Al and Sn. I also made it clear.
  • C.I. E. carbon equivalent
  • (C / Si) weight ratio, Al, and Sn need to be adjusted appropriately.
  • Al: 3-7% is specified for the following reason. That is, in flake graphite cast iron to which Al and Sn are added, the addition amount of Al has a favorable effect on the vibration damping capacity from 3%, and when it is less than 3%, almost no improvement effect is recognized. Moreover, when it becomes 6% or more, the vibration damping capacity gradually decreases, and when it exceeds 7%, the vibration damping capacity further decreases. And if the addition amount of Al exceeds 7%, the iron Al carbide formed by the addition of Al becomes hard and brittle, so that it becomes easy to crack and the workability deteriorates. For this reason, the appropriate addition amount of Al is set to 3 to 7%.
  • Sn is defined as 0.03 to 0.2% for the following reason. That is, if the amount of Sn added is too small, the effect of improving the Young's modulus and vibration damping ability is not recognized. The effect is shown to improve the Young's modulus and vibration damping capacity from about 0.03%, and the most remarkable effect is shown at around 0.08%. When the amount of Sn added is increased, the effect is gradually reduced, and when it is 0.2% or more, the effect is greatly reduced, and the improvement effect cannot be obtained. Therefore, the appropriate amount of Sn added is 0.03 to 0.2%. Sn is an important additive element because it improves not only the Young's modulus and vibration damping capacity but also the tensile strength.
  • the high-rigidity and high-damping capacity cast iron of the present invention contains C, Si, Mn, P, S and the like in addition to the above Al and Sn.
  • C and Si are as described in detail later.
  • Mn is 0.25 to 1.0% as in the case of ordinary flake graphite cast iron. The reason is that if Mn is 0.25% or more, the strength and hardness of cast iron increase, but if it exceeds 1.0%, cast iron is chilled and hardened and brittle.
  • P is set to 0.04% or less as in the case of ordinary flake graphite cast iron.
  • P exceeds 0.04%, it reacts with iron to form a steadite, which is a hard compound, and makes cast iron brittle.
  • S is 0.03% or less as in the case of ordinary flake graphite cast iron. The reason for this is that if S exceeds 0.03%, the fluidity of the molten metal is deteriorated and the cast iron is chilled to be hard and brittle.
  • the carbon equivalent shown in the above formula (1) is 3.30 to 3.95% as described above.
  • the carbon equivalent is increased, the vibration damping ability is improved and the Young's modulus is lowered.
  • the increase or decrease of the carbon equivalent cannot achieve both, but the influence on vibration damping capacity and Young's modulus is large, so an appropriate value is required.
  • Al is added, the eutectic composition at which the eutectic reaction between austenite and graphite changes as compared with conventional flake graphite cast iron.
  • Conventional flake graphite cast iron causes a eutectic reaction when the carbon equivalent represented by the above formula 1 is 4.3%.
  • Al is added, the eutectic reaction occurs at a value smaller than this value. .
  • a carbon equivalent larger than the eutectic composition is not preferable because it becomes hypereutectic and the Young's modulus is greatly reduced.
  • the carbon equivalent (CE) exceeds 3.95%, the vibration damping ability is greatly improved, but the Young's modulus is greatly reduced. This is thought to be because the carbon equivalent exceeds the eutectic composition and becomes hypereutectic. On the other hand, when the carbon equivalent is small, the Young's modulus is improved because the amount of graphite formed decreases. However, since the vibration damping ability is reduced, a carbon equivalent of 3.3% or more is necessary. Therefore, the carbon equivalent was 3.30 to 3.90.
  • the heat treatment temperature after casting is 280 to 630 ° C. The performance improvement by the heating / cooling process varies greatly depending on the heating temperature. The effect of this heat treatment is shown in FIG. In addition, although FIG.
  • the improvement rate of the damping performance is 5% or more.
  • the temperature range in which the effect is improved to 20% or more is 360 to 580 ° C. Although a high effect appears in these temperature ranges, the most effective case is when heated to 500 ° C. and cooled.
  • the cooling method may be either furnace cooling or air cooling. The reason why the damping performance is improved by the heat treatment is unknown.
  • the process of heat treatment varies depending on the process after casting the cast product according to the present invention. For example, when using as it is after casting, it heat-processes after casting. Further, for example, when used after being machined after casting and finished to a predetermined size, it is most preferable to perform heat treatment after machining. However, if there is a reason why heat treatment cannot be performed after machining, heat treatment may be performed before machining.
  • Examples 1 to 8 and Comparative Examples 1 to 8) First, the composition of cast iron was adjusted using a high-frequency melting furnace. Next, cast iron ingot made of FC300, carburized material, ferromanganese, and silicon carbide are put into a graphite crucible and dissolved, and then the amount of carbon and silicon are adjusted with ferrosilicon and the carburized material, and the dissolved amount is about 20 kg. It was. However, the Al amount of the obtained casting was adjusted by adding ferroaluminum and the tin amount by adding pure tin. The dissolution temperature was about 1450 ° C. A Ca—Si—Ba inoculum was added before pouring, and then cast into a furan self-hardening mold of ⁇ 30 ⁇ 300 mm.
  • the obtained casting was processed to 4 ⁇ 20 ⁇ 200 mm, and the logarithmic damping factor and dynamic Young's modulus were obtained as evaluation values of vibration damping ability.
  • a comparison was made with one that was not heat-treated. That is, in Examples 1 to 8, Al-added cast iron was heat-treated, and in Comparative Examples 1 to 8, Al-added cast iron was not heat-treated.
  • the test method was based on JISG0602. That is, the test piece was hung at two points to give a strain amplitude of 1 ⁇ 10 ⁇ 4 with an electromagnetic vibrator, and thereafter, the vibration was stopped and free damping was performed to obtain a logarithmic damping factor and a dynamic Young's modulus.
  • FIG. 2 a graph showing the relationship between the Young's modulus and the logarithmic decay rate of each sample is shown in FIG.
  • the values of Young's modulus and logarithmic decay rate of each sample vary, but the average value is represented by a straight line.
  • a line a represents data of Examples 1 to 8
  • a line b represents data of Comparative Examples 1 to 8.
  • the Young's modulus of the above data is in the range of 115 to 130 GPa because the Young's modulus is about 120 GPa when vibration damping performance is emphasized in FC250 and FC300 of current cast iron. The data of the range was published in.
  • the performance of the present invention with the heat treatment improved by about 40% with respect to the Young's modulus-logarithmic decay characteristics of Comparative Examples 1 to 8 (without heat treatment).
  • This value shows a performance of about 2.5 to 3.0 times or more as compared with the characteristics of the cast irons FC250 and FC300 (the logarithmic decay rate when the Young's modulus is 120 PGa is about 100 ⁇ 10 ⁇ 4 ).
  • Example 9 to 16 and Comparative Examples 9 to 16 The same operation as in Examples 1 to 8 and Comparative Examples 1 to 8 was carried out, and cast into a furan self-hardening mold of ⁇ 30 ⁇ 300 mm. The obtained casting was processed to 4 ⁇ 20 ⁇ 200 mm, and the logarithmic damping factor and dynamic Young's modulus were obtained as evaluation values of vibration damping ability. At this time, a comparison was made with one that was not heat-treated. That is, in Examples 9 to 16, Al and Sn-added cast iron was heat-treated, and in Comparative Examples 9 to 16, Al and Sn-added cast iron were not heat-treated. The test method was based on JISG0602.
  • the test piece was hung at two points to give a strain amplitude of 1 ⁇ 10 ⁇ 4 with an electromagnetic vibrator, and thereafter, the vibration was stopped and free damping was performed to obtain a logarithmic damping factor and a dynamic Young's modulus.
  • the properties of the cast product thus obtained are shown in Table 2 below.
  • the logarithmic attenuation rate showed a value when the strain amplitude of vibration was 1 ⁇ 10 ⁇ 4 .
  • P and S were not shown in Table 2, both P ⁇ 0.025 and S ⁇ 0.020.
  • dissolution is the same and a cast sample differs.
  • FIG. 3 a graph showing the relationship between the Young's modulus and the logarithmic decay rate of each sample is shown in FIG.
  • the values of Young's modulus and logarithmic decay rate of each sample vary, but the average value is represented by a straight line.
  • line a represents data of Examples 9 to 16
  • line b represents data of Comparative Examples 8 to 16.
  • the Young's modulus of the above data is in the range of 115 to 130 GPa because the Young's modulus is about 120 GPa when vibration damping performance is emphasized in FC250 and FC300 of current cast iron. The data of the range was published in.
  • the heat-treated present invention has a performance improvement of about 30% with respect to the Young's modulus-logarithmic decay characteristics of Comparative Examples 9 to 16 (without heat treatment). This value shows about 3.5 times the performance compared with the characteristics of the cast irons FC250 and FC300 (the logarithmic decay rate when the Young's modulus is 120 PGa is about 100 ⁇ 10 ⁇ 4 ).
  • the present invention is not limited to the above-described embodiment as it is, and is embodied by appropriately changing the composition of Al, Sn, C, Si, Mn, P, S, etc. within the scope not departing from the gist of the invention. it can. Moreover, various inventions can be formed by appropriately combining a plurality of compositions disclosed in the embodiment.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
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  • Vibration Prevention Devices (AREA)
PCT/JP2009/058705 2008-05-30 2009-05-08 高剛性高減衰能鋳鉄 WO2009145039A1 (ja)

Priority Applications (4)

Application Number Priority Date Filing Date Title
KR1020137001618A KR101423892B1 (ko) 2008-05-30 2009-05-08 고강성 고감쇠능 주철
DE112009001294T DE112009001294B4 (de) 2008-05-30 2009-05-08 Gusseisen mit hoher Festigkeit und hohem Dämpfungsvermögen
US12/940,140 US20110041960A1 (en) 2008-05-30 2010-11-05 High rigidity, high damping capacity cast iron
US14/015,760 US20140000832A1 (en) 2008-05-30 2013-08-30 High rigidity, high damping capcity cast iron

Applications Claiming Priority (2)

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JP2008-142932 2008-05-30
JP2008142932A JP5618466B2 (ja) 2008-05-30 2008-05-30 高剛性高減衰能鋳鉄

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JP5618500B2 (ja) * 2009-07-03 2014-11-05 東芝機械株式会社 高剛性高減衰能鋳鉄の機械部材及びその製造方法
DE102012100990B3 (de) * 2012-02-07 2013-06-27 Ford-Werke Gmbh Gußeisenwerkstoff
DE112014002442B4 (de) 2013-05-14 2019-07-11 Toshiba Kikai Kabushiki Kaisha Gusseisen hoher Stärke und hoher Dämpfungsfähigkeit
KR102240112B1 (ko) * 2014-02-21 2021-04-14 두산공작기계 주식회사 편상 흑연 주철 및 이의 제조 방법
KR102657327B1 (ko) * 2018-12-11 2024-04-12 현대자동차주식회사 탈탄층 및 질화층을 포함하는 브레이크 디스크 및 이의 제조방법

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS63140064A (ja) * 1986-12-03 1988-06-11 Nissan Motor Co Ltd ブレ−キ材料
JPH01283341A (ja) * 1987-08-31 1989-11-14 Shimazu Kinzoku Seiko Kk ニッケル−銅系防振鋳鉄
JPH0978179A (ja) * 1995-09-14 1997-03-25 Toshiba Corp 防振鋳鉄およびその製造方法
JP2001200330A (ja) * 1999-11-08 2001-07-24 Aisin Takaoka Ltd 振動減衰能に優れた鋳鉄材料及びその製造方法
JP2002348634A (ja) * 2001-05-18 2002-12-04 National Institute For Materials Science アルミニウム含有制振鋳鉄

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2885285A (en) * 1957-08-22 1959-05-05 Allis Chalmers Mfg Co Alloyed nodular iron
GB1558621A (en) * 1975-07-05 1980-01-09 Zaidan Hojin Denki Jiki Zairyo High dumping capacity alloy
JPS5565349A (en) * 1978-11-06 1980-05-16 Hiroshi Kimura Magnetic alloy
US4548643A (en) * 1983-12-20 1985-10-22 Trw Inc. Corrosion resistant gray cast iron graphite flake alloys
KR20010054925A (ko) * 1999-12-08 2001-07-02 이계안 자동차용 리테이너 베어링
US6973954B2 (en) * 2001-12-20 2005-12-13 International Engine Intellectual Property Company, Llc Method for manufacture of gray cast iron for crankcases and cylinder heads
RU2318883C2 (ru) * 2002-05-08 2008-03-10 Эй-Кей СТИЛ ПРОПЕРТИЗ ИНК Способ непрерывного литья полосы неориентированной электротехнической стали
JP4926423B2 (ja) * 2005-07-27 2012-05-09 アンリツ株式会社 光変調器
JP5268344B2 (ja) * 2007-02-14 2013-08-21 東芝機械株式会社 高剛性高減衰能鋳鉄

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS63140064A (ja) * 1986-12-03 1988-06-11 Nissan Motor Co Ltd ブレ−キ材料
JPH01283341A (ja) * 1987-08-31 1989-11-14 Shimazu Kinzoku Seiko Kk ニッケル−銅系防振鋳鉄
JPH0978179A (ja) * 1995-09-14 1997-03-25 Toshiba Corp 防振鋳鉄およびその製造方法
JP2001200330A (ja) * 1999-11-08 2001-07-24 Aisin Takaoka Ltd 振動減衰能に優れた鋳鉄材料及びその製造方法
JP2002348634A (ja) * 2001-05-18 2002-12-04 National Institute For Materials Science アルミニウム含有制振鋳鉄

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
NAOKI SAKAMOTO ET AL.: "Al o Tenka shita Henjo Kokuen Chutetsu no Young-ritsu to Taisu Gensuiritsu no Henka", DAI 150 KAI ZENKOKU KOEN TAIKAI KOEN GAIYOSHU, 1 May 2007 (2007-05-01), pages 46 *
RYOSUKE FUJIMOTO ET AL.: "Al o Tenka shita Henjo Kokuen Chutetsu no Soshiki to Shindo Gensui Kiko", DAI 150 KAI ZENKOKU KOEN TAIKAI KOEN GAIYOSHU, 1 May 2007 (2007-05-01), pages 47 *

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DE112009001294B4 (de) 2013-10-31
US20140000832A1 (en) 2014-01-02
DE112009001294T5 (de) 2011-04-14
US20110041960A1 (en) 2011-02-24
KR20100139117A (ko) 2010-12-31
KR20130019002A (ko) 2013-02-25
JP2009287103A (ja) 2009-12-10
KR101268160B1 (ko) 2013-05-27
JP5618466B2 (ja) 2014-11-05
KR101423892B1 (ko) 2014-07-28

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