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WO2007066555A1 - ALLIAGE A BASE DE Co ET SON PROCEDE DE FABRICATION - Google Patents

ALLIAGE A BASE DE Co ET SON PROCEDE DE FABRICATION Download PDF

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Publication number
WO2007066555A1
WO2007066555A1 PCT/JP2006/323877 JP2006323877W WO2007066555A1 WO 2007066555 A1 WO2007066555 A1 WO 2007066555A1 JP 2006323877 W JP2006323877 W JP 2006323877W WO 2007066555 A1 WO2007066555 A1 WO 2007066555A1
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WO
WIPO (PCT)
Prior art keywords
phase
strength
amount
alloy
magnetization
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.)
Ceased
Application number
PCT/JP2006/323877
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English (en)
Japanese (ja)
Inventor
Kiyohito Ishida
Ryosuke Kainuma
Katsunari Oikawa
Yuji Sutou
Toshihiro Omori
Keisuke Ando
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Japan Science and Technology Agency
Original Assignee
Japan Science and Technology Agency
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.)
Filing date
Publication date
Application filed by Japan Science and Technology Agency filed Critical Japan Science and Technology Agency
Priority to EP06833680A priority Critical patent/EP1959024A4/fr
Priority to JP2007549087A priority patent/JPWO2007066555A1/ja
Publication of WO2007066555A1 publication Critical patent/WO2007066555A1/fr
Priority to US12/112,513 priority patent/US20080289730A1/en
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/07—Alloys based on nickel or cobalt based on cobalt

Definitions

  • Ferromagnetic Co that has high elasticity and can control displacement by magnetic field, and its manufacturing method.
  • Titanium gold is drawing attention as a material showing a high Young's modulus and is used in frames and the like.
  • Reference 2 introduces that titanium gold containing the elements 4A and 5A can be used as a material with a low Young's modulus.
  • Shaped gold is known for displacement control based on degree, and a level change has been obtained. , It is a phenomenon in which the original shape is recovered by utilizing the rutensite state that occurs when the deformed material is heated above a certain temperature.
  • Magnetic gold is also attracting attention as an actuator. With magnetic gold, numerization that exceeds conventional charges has been obtained externally, and even with respect to dynamic gold, it has been eliminated.
  • a magnetic type gold for example, there is a Ga system, and a material that induces a magnetic field is introduced in Ref. CoN-based gold is introduced in sentence 45, and Co-based gold is also introduced in 6.
  • Ga-based materials have poor ductility and it is difficult to provide the complicated and dense shapes required for mechanical products.
  • the Co phase is used as the second phase to improve the properties, but the magnetization is small.
  • Co-based and relatively ductile a dynamic result can be obtained, but the ductility is insufficient. I don't get sex.
  • the purpose of the present invention is to provide good Co gold having the following by controlling the growth of the e phase in the component in which two or more kinds of e are added.
  • Bright Co, mass e 00 to 00 to 300 0 ⁇ 0 to 25 Contains two or more kinds. When three kinds of e are added, the total content is preferably set in the range of 002 to 50. ⁇ Simply describe the ratio.
  • the proposed Co is at least ferromagnetic, and the c-structure E phase generated at the origin is distributed. It is higher than the E phase and can be controlled by the component.
  • c ⁇ A metal in which the E phase is distributed, and Co gold with a predetermined composition is 900-400.
  • FIG. 6 is a graph showing the effect of volumeification conditions on the volume fraction of the e phase in the Co e gold weave.
  • 0 is the volume fraction of the E phase in the Co weave.
  • Co is a ferromagnetic element with high chirality, but Co is poor in processing.
  • Co is a cc-structured phase at high temperature, and becomes lutensite in the E-phase of -c-structured at a temperature close to 440C when cooled.
  • the v phase is good because of the irregularity of c and c.
  • the E phase is a phase that has the effect of increasing elasticity, it easily decomposes and causes defects such as. Therefore, even if an element that stabilizes and stabilizes the phase is added, the phase remains and the improvement of Co gold can be expected.
  • Fe with magnetism is effective not only for improving processing but also for improving Co gold. is there.
  • the upper limit of the E phase is preferably set to 99 in order to cancel the improvement effect of the excessive residual phase of the E phase.
  • E of c-structure and the rest are Co gold having a composite of phases of c-structure, but the existence of different phases is allowed as long as it does not adversely affect.
  • the phases include metallic compounds (b, c, c, etc.) generated by the third addition.
  • Co gold added with e shows particularly excellent properties. Although it is preferable to show a large degree of change in a relatively low field on the way as a displacement control by, the Co gold line is measured, and the magnetization strength of 30 eg above the field of 0.2T Tesla is measured.
  • a promising material as a displacement controller has the effect of weakening the magnetization, but since the level of magnetization still reaches the level, it is given the property as a displacement controller.
  • the applied metals such as e and Co are at 0.3 degree, and when applied, the deformation is suppressed, and the yield increases as the hardness and tensile strength increase.
  • this Co for example
  • Young's modulus is low because the force required for deformation is high and displacement due to the field is difficult to obtain.
  • Young's modulus is a physical property related to atoms and is considered to be difficult to control by thermomechanical processing. In this study, the Young's modulus is achieved by controlling the martensitic rutensite variant.
  • the lattice In Co, the lattice is in the rutensite state.
  • the hysteresis is 50C, and the hysteresis further spreads during processing, so a wide Young's modulus is achieved.
  • Co 45 has a phase structure and uses the rutensite / state for shaping, but the phase does not transform into the E phase.
  • the existence of two phases with poor properties is also a factor under processing, but Ming Co can be regarded as a material with excellent properties also in the absence of phases.
  • Co-gold which is ferromagnetic but has a low degree of oxidization, the amount of bright Co is extremely large, and therefore displacement control by magnetic field distribution is extremely effective.
  • e has the effect of lowering the degree of rutensite, contributing to the improvement of ductility, and increasing the magnetization. Such an effect becomes remarkable with the addition of e on 0.0. However, it lowers the excess lutensite temperature variation and causes the deterioration of the E-phase activity. Therefore, the upper limit of e 0 30 25 was set.
  • e The content of each is preferably set in the range of -8 to 25 to 20 and more preferably 2 to 65 to 20 5 to 5.
  • a C V o z W Ta S C B P Missing metal can be added to the Co e system as needed with two or more species selected. When adding several parts, select the total amount within the range of 0.002 to 50, 0.005 to 30).
  • V is a component that reduces the degree of rutensite. However, it stabilizes the phase and lowers the volume fraction of the e-phase. Therefore, when adding, the value of V T should be determined within the range of 00-0 V 00-20 T 00-5.
  • Co is an effective component for corrosion resistance, it causes excessive ductility.
  • ZW Ta It is an effective ingredient for chemicals, but it causes less ductility, so when adding it, select a large amount in the range of 00 to 0 z 00 to 3 W 00 to 30 Ta 00 to 00 to 5 To do.
  • S is a component that increases the degree of rutensite, it causes excessive ductility, so when adding it, select a large amount within the range of S00-8.
  • C B P Si-metal is an effective component for crystallization, but it causes excessive ductility. Therefore, when adding C B P missy metal, select a large amount in the range of C 000-3 B 000-3 P 000-3 Missy metal 0.00-3. After solving the Co gold that has been adjusted to the desired size, it is subjected to inter-cast rolling and punching to obtain the target size.
  • the strain that has been introduced up to the processing is removed and the material is qualitatively refined. Since it has to be solidified and has a degree of recrystallization sufficiently, it has a melting point of over 900C, which is 400. C is required, preferably from 000.
  • phase of c ⁇ c ⁇ structure is transformed into the phase of ⁇ c ⁇ structure. Even if the lutensite s is higher than room temperature, the phase is stabilized by e and the cooling texture does not become a single phase.
  • the materialized Co gold is processed by rolling, etc.
  • the degree of processing is set to 700C below 0.6Tm. Since it will be significant depending on the increase in the E phase induction rate, set the machining rate to 0 or higher. Although the work rate is limited according to the power of the equipment, it is preferable to set the upper limit to 90 because excess equipment will increase the burden of equipment.
  • the upper E-phase upper limit is preferably set to 99% because it reduces the excessive Young's decrease of the E-phase and relatively increases the volume fraction of the phase effective for improvement.
  • Embodying 70 at 900-400C Embodying 70 at 900-400C.
  • aging may be done at 300 to 800C, preferably 400 to 700C.
  • the crystal can increase or decrease the strength. Strength increases when Cottrell occurs and decreases when recovery or recrystallization occurs. Because at least the atomic distance is necessary for the reason.
  • F to F8 are Co e type 2 to 8 are Co type 3 to 8 are Co type based alloy meters.
  • 3 to 3 also include the results of investigating the volume fraction of the E phase at the temperature of Co gold. Therefore, the characteristics like Co e S S3 6 are shown in Table 4. Also, the volume fraction of the e phase of e The impact of this is shown in Fig.8.
  • the fraction X of the phase was calculated by substituting 200) 00 of (200) (00) by X-folding into.
  • the field was marked by using a vibration force meter, and it was set as the level at 0.2T.
  • Table 9 shows the relationship between conditions and physical properties.
  • the volume ratio of the E phase (fixed between processing rate 40 processing conditions 700) of the processing conditions Graphs 6 to 4 show the physical conditions of the fixed processing conditions of 70 CX2, 20 C 5 processing rate 40 fixed at 80).
  • the machining rate aging condition was fixed and the volume fraction was changed, but there was no significant change in the volume fraction, recovery, or magnetization of the E phase. This is the same in the test o 23 o 9 20 and can be understood from 6 92.
  • test o 95, where the work rate is 80, the recovery is high due to aging.
  • test o23 the recovery by the later aging was similar to that of the previous one shown in Table 3, and no remarkable aging was obtained.
  • Co 205 e Co 0 Co 5 was used as the basic composition of Co e Co Co e Co, and the third component was added to prepare Co gold.
  • sheet 05 was rolled and subjected to rolling treatment through interrolling in the same manner.
  • Table 0 (Co e system Co system 2Co system) shows the results of measuring the volume fraction of E phase of the obtained Co gold.
  • No. 2 gold was selected, and it was cast, hot-rolled, rolled to plate 033, further solidified at 200C for 5 minutes, and then pressure-rolled at 20. 50 for the Co e-based money created. . .
  • the volume fraction of the E phase at every 00C was calculated. After giving a degree test, the shape was set to return when. Regarding the integration of E, the same method was used each time.
  • the volume fraction of E phase is 50.
  • Co-based Co-based alloys also have a metallic weave occupying most of the phases, and showed a large value for recovery.
  • Co-gold added with can be obtained. Utilizing the properties of Co gold thus provided provides functional materials that are useful as a heater sensor that can control the displacement by a magnetic field.

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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)
  • Hard Magnetic Materials (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L’invention concerne un alliage à base de Co comprenant au moins un élément choisi parmi de 0,01 à 10 % de Fe, de 0,01 à 30 % de Ni et de 0,01 à 25 % de Mn, ledit alliage à base de Co ayant une structure métallique dans laquelle une phase ϵ de structure de copolyméres séquencés générée par une transformation induite thermiquement ou par une contrainte est formée en un rapport supérieur ou égal à 10 % en volume. Le cas échéant, il est possible d’ajouter au moins un élément choisi parmi de 0,01 à 10 % de Al, de 0,01 à 35 % de Cr, de 0,01 à 20 % de V, de 0,01 à 15 % de Ti, de 0,01 à 30 % de Mo, de 0,01 à 10 % de Nb, de 0,01 à 3 % de Zr, de 0,01 à 30 % de W, de 0,01 à 10 % de Ta, de 0,01 à 5 % de Hf, de 0,01 à 8 % de Si, de 0,001 à 3 % de C, de 0,001 à 3 % de B, de 0,001 à 3 % de P et de 0,001 à 3 % de misch métal. Cet alliage à base de Co présente une grande capacité de déformation élastique, ainsi qu'une bonne ductilité et une bonne maniabilité. Cet alliage à base de Co est utilisé en tant que matériau fonctionnel, par exemple pour un capteur ou un actionneur capable de moduler un déplacement par application d’un champ magnétique.
PCT/JP2006/323877 2005-12-05 2006-11-22 ALLIAGE A BASE DE Co ET SON PROCEDE DE FABRICATION Ceased WO2007066555A1 (fr)

Priority Applications (3)

Application Number Priority Date Filing Date Title
EP06833680A EP1959024A4 (fr) 2005-12-05 2006-11-22 ALLIAGE A BASE DE Co ET SON PROCEDE DE FABRICATION
JP2007549087A JPWO2007066555A1 (ja) 2005-12-05 2006-11-22 Ｃｏ基合金及びその製造方法
US12/112,513 US20080289730A1 (en) 2005-12-05 2008-04-30 Material having a high elastic deformation and process for producing the same

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2005-350431 2005-12-05
JP2005350431 2005-12-05

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US12/112,513 Continuation US20080289730A1 (en) 2005-12-05 2008-04-30 Material having a high elastic deformation and process for producing the same

Publications (1)

Publication Number Publication Date
WO2007066555A1 true WO2007066555A1 (fr) 2007-06-14

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US (1) US20080289730A1 (fr)
EP (1) EP1959024A4 (fr)
JP (1) JPWO2007066555A1 (fr)
WO (1) WO2007066555A1 (fr)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2426809C1 (ru) * 2010-10-01 2011-08-20 Юлия Алексеевна Щепочкина Сплав
US9157136B2 (en) 2012-12-05 2015-10-13 Industrial Technology Research Institute Multi-element alloy material and method of manufacturing the same
KR20190109008A (ko) * 2018-03-16 2019-09-25 서울대학교산학협력단 자가 치유 특성을 가지는 변태 유기 소성 초합금 및 그 제조 방법

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* Cited by examiner, † Cited by third party
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KR20090038016A (ko) * 2006-08-23 2009-04-17 도꾸리쯔교세이호징 가가꾸 기쥬쯔 신꼬 기꼬 Ｆｅ기 합금 및 그 제조 방법
CN104080933B (zh) * 2011-11-18 2016-03-30 土耳其科学技术研究理事会 高温工具用合金
WO2014081491A2 (fr) * 2012-08-28 2014-05-30 Questek Innovations Llc Alliages de cobalt
US10844465B2 (en) 2017-08-09 2020-11-24 Garrett Transportation I Inc. Stainless steel alloys and turbocharger kinematic components formed from stainless steel alloys
WO2019099719A1 (fr) * 2017-11-16 2019-05-23 Arconic Inc. Alliages de cobalt-chrome-aluminium et leurs procédés de production
DE102018208737A1 (de) * 2018-06-04 2019-12-05 Siemens Aktiengesellschaft Y, Y` gehärtete Kobalt-Nickel-Basislegierung, Pulver, Komponente und Verfahren
DE102018208736A1 (de) * 2018-06-04 2019-12-05 Siemens Aktiengesellschaft Y, Y' gehärtete Kobalt-Nickel-Basislegierung, Pulver, Komponente und Verfahren
CN110592432B (zh) * 2019-09-25 2020-09-04 北京北冶功能材料有限公司 一种钴基变形高温合金及其制备方法
CN115679233A (zh) * 2022-09-21 2023-02-03 北京航空材料研究院股份有限公司 一种物理场固态处理铸造钛合金的方法及得到的钛合金
CN116790956A (zh) * 2023-07-06 2023-09-22 沈阳航空航天大学 低温环境下具有超高力学性能的高熵合金及其制备方法

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JPH0251839A (ja) * 1988-06-11 1990-02-21 Degussa Ag マグネトロン陰極スパツタ装置用ターゲツト
US5958154A (en) 1996-08-19 1999-09-28 Massachusetts Institute Of Technology High-strain, magnetic field-controlled actuator materials
JP2002129273A (ja) 2000-08-14 2002-05-09 Kiyohito Ishida 強磁性形状記憶合金およびそれを用いたアクチュエーター
JP2002249836A (ja) 2000-12-20 2002-09-06 Toyota Central Res & Dev Lab Inc 高弾性変形能を有するチタン合金およびその製造方法
JP2002332531A (ja) 1999-06-11 2002-11-22 Toyota Central Res & Dev Lab Inc チタン合金およびその製造方法
JP2004238720A (ja) 2003-02-10 2004-08-26 Kiyohito Ishida 形状記憶合金
JP2004277865A (ja) 2003-03-18 2004-10-07 Honda Motor Co Ltd 形状記憶合金及びその製造方法

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JPS6314864A (ja) * 1986-07-08 1988-01-22 Ulvac Corp Ｃｏ基合金スパツタタ−ゲツトおよびその製造法
JPH0251839A (ja) * 1988-06-11 1990-02-21 Degussa Ag マグネトロン陰極スパツタ装置用ターゲツト
US5958154A (en) 1996-08-19 1999-09-28 Massachusetts Institute Of Technology High-strain, magnetic field-controlled actuator materials
JP2002332531A (ja) 1999-06-11 2002-11-22 Toyota Central Res & Dev Lab Inc チタン合金およびその製造方法
JP2002129273A (ja) 2000-08-14 2002-05-09 Kiyohito Ishida 強磁性形状記憶合金およびそれを用いたアクチュエーター
JP2002249836A (ja) 2000-12-20 2002-09-06 Toyota Central Res & Dev Lab Inc 高弾性変形能を有するチタン合金およびその製造方法
JP2004238720A (ja) 2003-02-10 2004-08-26 Kiyohito Ishida 形状記憶合金
JP2004277865A (ja) 2003-03-18 2004-10-07 Honda Motor Co Ltd 形状記憶合金及びその製造方法

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See also references of EP1959024A4 *

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2426809C1 (ru) * 2010-10-01 2011-08-20 Юлия Алексеевна Щепочкина Сплав
US9157136B2 (en) 2012-12-05 2015-10-13 Industrial Technology Research Institute Multi-element alloy material and method of manufacturing the same
TWI555856B (zh) * 2012-12-05 2016-11-01 財團法人工業技術研究院 多元合金塊材及其製作方法
KR20190109008A (ko) * 2018-03-16 2019-09-25 서울대학교산학협력단 자가 치유 특성을 가지는 변태 유기 소성 초합금 및 그 제조 방법
KR102136455B1 (ko) 2018-03-16 2020-07-21 서울대학교산학협력단 자가 치유 특성을 가지는 변태 유기 소성 초합금 및 그 제조 방법

Also Published As

Publication number Publication date
EP1959024A1 (fr) 2008-08-20
JPWO2007066555A1 (ja) 2009-05-14
EP1959024A4 (fr) 2009-12-23
US20080289730A1 (en) 2008-11-27

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