WO2007066555A1 - ALLIAGE A BASE DE Co ET SON PROCEDE DE FABRICATION - Google Patents
ALLIAGE A BASE DE Co ET SON PROCEDE DE FABRICATION Download PDFInfo
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- 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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- WIPO (PCT)
- Prior art keywords
- phase
- strength
- amount
- alloy
- magnetization
- Prior art date
Links
- 239000000956 alloy Substances 0.000 title claims abstract description 65
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 63
- 238000000034 method Methods 0.000 title description 4
- 230000008569 process Effects 0.000 title description 3
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 23
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 22
- 229910052751 metal Inorganic materials 0.000 claims abstract description 8
- 239000002184 metal Substances 0.000 claims abstract description 8
- 229910001122 Mischmetal Inorganic materials 0.000 claims abstract description 6
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 6
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 6
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 5
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 5
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 4
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 4
- 238000012545 processing Methods 0.000 claims description 23
- 230000032683 aging Effects 0.000 claims description 22
- 230000035882 stress Effects 0.000 claims description 20
- 238000004519 manufacturing process Methods 0.000 claims description 8
- 239000000203 mixture Substances 0.000 claims description 7
- 238000005452 bending Methods 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims 1
- 230000005291 magnetic effect Effects 0.000 abstract description 42
- 239000000463 material Substances 0.000 abstract description 35
- 230000009466 transformation Effects 0.000 abstract description 30
- 229910052742 iron Inorganic materials 0.000 abstract description 19
- 238000006073 displacement reaction Methods 0.000 abstract description 14
- 230000005489 elastic deformation Effects 0.000 abstract description 4
- 229910052782 aluminium Inorganic materials 0.000 abstract description 3
- 239000012071 phase Substances 0.000 description 99
- 230000005415 magnetization Effects 0.000 description 51
- 238000011084 recovery Methods 0.000 description 47
- 229910000734 martensite Inorganic materials 0.000 description 29
- 239000000243 solution Substances 0.000 description 26
- 230000000694 effects Effects 0.000 description 24
- 238000012360 testing method Methods 0.000 description 19
- 229910020598 Co Fe Inorganic materials 0.000 description 15
- 229910002519 Co-Fe Inorganic materials 0.000 description 15
- 238000005482 strain hardening Methods 0.000 description 15
- 229910020630 Co Ni Inorganic materials 0.000 description 14
- 229910002440 Co–Ni Inorganic materials 0.000 description 13
- 229910002056 binary alloy Inorganic materials 0.000 description 12
- 230000007423 decrease Effects 0.000 description 12
- 229910020632 Co Mn Inorganic materials 0.000 description 11
- 229910020678 Co—Mn Inorganic materials 0.000 description 11
- 230000005294 ferromagnetic effect Effects 0.000 description 10
- 238000005097 cold rolling Methods 0.000 description 8
- 229910001285 shape-memory alloy Inorganic materials 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 6
- 230000003446 memory effect Effects 0.000 description 6
- 230000000704 physical effect Effects 0.000 description 6
- 230000002441 reversible effect Effects 0.000 description 6
- 229910000640 Fe alloy Inorganic materials 0.000 description 5
- 230000008859 change Effects 0.000 description 5
- 238000001816 cooling Methods 0.000 description 5
- 238000002844 melting Methods 0.000 description 5
- 230000008018 melting Effects 0.000 description 5
- 229910003310 Ni-Al Inorganic materials 0.000 description 4
- 230000006866 deterioration Effects 0.000 description 4
- 238000010586 diagram Methods 0.000 description 4
- 238000001953 recrystallisation Methods 0.000 description 4
- 239000010936 titanium Substances 0.000 description 4
- 229910000531 Co alloy Inorganic materials 0.000 description 3
- 229910001069 Ti alloy Inorganic materials 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 230000003679 aging effect Effects 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000003247 decreasing effect Effects 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 230000004044 response Effects 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000807 Ga alloy Inorganic materials 0.000 description 1
- 229910000914 Mn alloy Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 229910004337 Ti-Ni Inorganic materials 0.000 description 1
- 229910011209 Ti—Ni Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000006399 behavior Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 210000000988 bone and bone Anatomy 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000006355 external stress Effects 0.000 description 1
- 210000000744 eyelid Anatomy 0.000 description 1
- 239000003302 ferromagnetic material Substances 0.000 description 1
- 230000005307 ferromagnetism Effects 0.000 description 1
- 230000006870 function Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- KHYBPSFKEHXSLX-UHFFFAOYSA-N iminotitanium Chemical compound [Ti]=N KHYBPSFKEHXSLX-UHFFFAOYSA-N 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 239000008204 material by function Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002907 paramagnetic material Substances 0.000 description 1
- 230000036961 partial effect Effects 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000002243 precursor Substances 0.000 description 1
- 230000008707 rearrangement Effects 0.000 description 1
- 230000003938 response to stress Effects 0.000 description 1
- 230000004043 responsiveness Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000003313 weakening effect Effects 0.000 description 1
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.
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 |
Family
ID=38122702
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2006/323877 WO2007066555A1 (fr) | 2005-12-05 | 2006-11-22 | ALLIAGE A BASE DE Co ET SON PROCEDE DE FABRICATION |
Country Status (4)
Country | Link |
---|---|
US (1) | US20080289730A1 (fr) |
EP (1) | EP1959024A4 (fr) |
JP (1) | JPWO2007066555A1 (fr) |
WO (1) | WO2007066555A1 (fr) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
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 |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP2055797A4 (fr) * | 2006-08-23 | 2014-12-17 | Japan Science & Tech Agency | Alliage à base de fer et son procédé de fabrication |
WO2013072899A1 (fr) * | 2011-11-18 | 2013-05-23 | Tubitak | Alliage pour applications de formage d'acier à haute température |
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 |
DE102018208736A1 (de) * | 2018-06-04 | 2019-12-05 | Siemens Aktiengesellschaft | Y, Y' gehärtete Kobalt-Nickel-Basislegierung, Pulver, Komponente und Verfahren |
DE102018208737A1 (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 |
Citations (8)
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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 |
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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 |
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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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US3356542A (en) * | 1967-04-10 | 1967-12-05 | Du Pont | Cobalt-nickel base alloys containing chromium and molybdenum |
CA892488A (en) * | 1968-11-15 | 1972-02-08 | W. Kushnir Bud | Two-phase cobalt-iron alloys prepared by powder metallurgy |
BE756652A (fr) * | 1969-09-26 | 1971-03-01 | United Aircraft Corp | Superalliages contenant des phases precipitees topologiquement d'assemblage serre |
US3767385A (en) * | 1971-08-24 | 1973-10-23 | Standard Pressed Steel Co | Cobalt-base alloys |
JP2004269994A (ja) * | 2003-03-11 | 2004-09-30 | Japan Science & Technology Agency | 生体適合性Co基合金及びその製造方法 |
-
2006
- 2006-11-22 EP EP06833680A patent/EP1959024A4/fr not_active Withdrawn
- 2006-11-22 WO PCT/JP2006/323877 patent/WO2007066555A1/fr active Application Filing
- 2006-11-22 JP JP2007549087A patent/JPWO2007066555A1/ja active Pending
-
2008
- 2008-04-30 US US12/112,513 patent/US20080289730A1/en not_active Abandoned
Patent Citations (8)
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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 |
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Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
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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 |
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EP1959024A4 (fr) | 2009-12-23 |
US20080289730A1 (en) | 2008-11-27 |
JPWO2007066555A1 (ja) | 2009-05-14 |
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