EP3511432B1 - Alliage de cuivre résistant à l'adoucissement, procédé de préparation et application correspondante - Google Patents

Alliage de cuivre résistant à l'adoucissement, procédé de préparation et application correspondante Download PDF

Info

Publication number
EP3511432B1
EP3511432B1 EP17847871.5A EP17847871A EP3511432B1 EP 3511432 B1 EP3511432 B1 EP 3511432B1 EP 17847871 A EP17847871 A EP 17847871A EP 3511432 B1 EP3511432 B1 EP 3511432B1
Authority
EP
European Patent Office
Prior art keywords
phase
copper alloy
temperature
softening
copper
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.)
Active
Application number
EP17847871.5A
Other languages
German (de)
English (en)
Other versions
EP3511432A4 (fr
EP3511432A1 (fr
Inventor
Yongjun PEI
Jijun Wang
Er ZHANG
Yubo SONG
Renchang Hu
Juan Li
Weiwei Li
Mengtao TIAN
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Ningbo Powerway Alloy Plate & Strip Co Ltd
Ningbo Powerway Alloy Material Co Ltd
Original Assignee
Ningbo Powerway Alloy Plate & Strip Co Ltd
Ningbo Powerway Alloy Material Co Ltd
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 Ningbo Powerway Alloy Plate & Strip Co Ltd, Ningbo Powerway Alloy Material Co Ltd filed Critical Ningbo Powerway Alloy Plate & Strip Co Ltd
Publication of EP3511432A4 publication Critical patent/EP3511432A4/fr
Publication of EP3511432A1 publication Critical patent/EP3511432A1/fr
Application granted granted Critical
Publication of EP3511432B1 publication Critical patent/EP3511432B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • 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
    • C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2202/00—Physical properties

Definitions

  • the present invention relates to the field of copper alloy manufacturing, and in particular to a softening-resistant copper alloy, a preparation method thereof and applications thereof, belonging to the technical field of novel alloy materials.
  • Welding is a manufacturing technology that joins metals or other materials by heating, at high-temperature or under high-pressure.
  • fusion welding there are mainly three methods for joining materials: fusion welding, pressure welding and braze welding.
  • a workpiece and the solder are molten to form a molten area, and the molten pool is cooled and solidified to form a connection between the materials.
  • sources of energy for welding including gas flame, electric arc, laser, electron beams, friction, ultrasonic waves and the like.
  • the only welding process was metal forging already used by the blacksmith for hundreds of years. The earliest modern welding techniques appeared at the end of the 19 th century, first arc welding and oxygen-fuel welding and then resistance welding.
  • the actually popularized products such as conductive nozzles for welding equipment, electrode caps and electrified railway contact lines, mostly use conventional copper chromium zirconium alloy (e.g., American Standard C18150) which has been widely applied in the above fields due to its excellent strength and electrical conductivity.
  • conventional copper chromium zirconium alloy e.g., American Standard C18150
  • This change will present new requirements on the raw material performances of parts, among which high-temperature softening resistance comes first. This is because the wear of the parts will be less if the high-temperature softening resistance is better. Accordingly, the service life of the parts is prolonged and the precision during the welding process is also improved.
  • the conventional copper chromium zirconium alloy e.g., American Standard C18150
  • the Chinese patent application CN102534291 A discloses a Cu alloy containing Cr and Zr that offers improved strength and electrical conductivity and is intended for use in applications such as resistance sleeves for welding electrodes, overhead poweline wires and electrical contact materials.
  • An objective of the present invention is to provide a copper alloy with better high-temperature softening resistance, in order to solve the problem that the high-temperature softening resistance of the existing copper chromium zirconium alloy is to be improved.
  • the softening-resistant copper alloy comprises: 0.1%-1.0 wt% Cr, 0.01% -0.2 wt% Zr, 0.01%-0.10 wt% Si, and ⁇ 0.10 wt% Fe, 0.0001-0.10 wt.% Mg, 0.01-2.5 wt.% of at least one of Co, Zn, Mn, Sn and Nb, with their total amount not exceeding 3.5 wt.% and with the remaining of copper and inevitable impurities, characterized in that, the microstructure of the copper alloy comprises: an elemental Cr phase, a Cu 5 Zr phase, and a Cr 3 Si phase and wherein the elemental Cr phase and the Cr 3 Si phase satisfy the following relationship; if the weight of the elemental Cr phase is X and the weight of the Cr 3 Si phase is Y, then the ratio X/Y is greater than zero and msaller than twenty (0 ⁇ X/Y ⁇ 20).
  • the high-temperature softening resistance effect of the material is improved by adding a proper amount of Si to form a compound Cr 3 Si, and the strength and the high-temperature softening resistance of the material are further improved by strengthening the copper alloy matrix by the elemental Cr phase and the Cu 5 Zr phase, using the synergistic effect of the Cr 3 Si phase and the elemental Cr phase and by controlling the content of the impurity Fe.
  • the solid solubility of chromium in copper at the normal temperature is very small (less than 0.5%), but the solid solubility of chromium in copper at a high temperature is relatively high (up to 0.65%). Therefore, chromium is able to realize precipitation strengthening and used as a main strengthening element in the copper alloy of the present invention.
  • dispersion strengthening phase particles of the elemental Cr can be obtained by heat treatment, so the copper matrix is strengthened. While strengthening the copper matrix, Cr will also form a compound Cr 3 Si with Si solid-dissolved in the copper matrix.
  • the compound Cr 3 Si is a compound phase that is stable at a high temperature and will not be dissolved even at a high temperature of 800 °C, so that the high-temperature softening resistance is very high.
  • the content of chromium in the copper alloy of the present invention is 0.1% to 1.0%. If the content of chromium is less than this range, Cr and Si are difficult to form Cr 3 Si or can form a small amount of Cr 3 Si so that the desired effect cannot be achieved; however, if the content of chromium is greater than this range, chromium will be largely precipitated to form a strengthening phase, so that the chromium will be largely accumulated at the crystal boundary and the plasticity of the material is damaged.
  • Zirconium has a certain solubility in the copper alloy. By adding zirconium, the recrystallization temperature of the copper matrix can be increased and the high-temperature softening resistance of the copper alloy can be thus improved. Moreover, zirconium and copper will form an intermediate compound Cu 5 Zr, strengthening the copper matrix and also improving the electrical performance of the copper alloy.
  • the content of zirconium in the copper alloy of the present invention is 0.01% to 0.2%. If the content of zirconium is less than this range, the desired effect cannot be achieved; however, if the content of zirconium is greater than this range, although the alloy can be strengthened, the electrical conductivity of the alloy will be greatly reduced and the overall performance of the alloy will be influenced.
  • Silicon has a certain solid solubility in copper. Silicon can strengthen the copper alloy matrix, but will greatly influence the electrical conductivity of copper and will greatly reduce the electrical conductivity of the copper alloy. However, when there is a proper amount of chromium in the copper alloy, silicon and chromium can form a Cr 3 Si phase compound. Since Cr 3 Si is a precipitated phase, the electrical conductivity of the material can be greatly improved after Cr 3 Si is precipitated, so that the overall performance of the copper alloy is positively influenced.
  • the content of silicon in the copper alloy of the present invention is 0.01% to 0.1%.
  • the content of silicon is less than this range, the Cr 3 Si phase formed in the copper alloy is not enough to achieve the desired effect; however, if the content of silicon is greater than this range, although sufficient Cr 3 Si phase can be formed, the precipitation of Cr will be greatly reduced and the overall performance of the alloy will thus be influenced.
  • Fe is controlled as an impurity element.
  • a small amount of Fe facilitates the improvement of strength, but a too high content of Fe will affect the electrical conductivity. Therefore, in the present invention, the content of Fe is controlled below 0.1 wt.%.
  • the elemental Cr phase, the Cu 5 Zr phase and the Cr 3 Si phase in the microstructure of the copper alloy of the present invention have the following effects.
  • the Cr 3 Si phase is generated during the liquid state and crystallization process of the alloy, is stable in both structure and performance at a high temperature, and will not be dissolved at 800 °C while still maintaining its original structure. Accordingly, the high-temperature softening resistance of the alloy can be greatly improved.
  • the Cu 5 Zr phase is completely dissolved in the copper matrix to form a supersaturated solid solution after solid solution treatment on the alloy, then precipitated out of the copper matrix during the subsequent aging process and dispersedly distributed in the alloy. After the Cu 5 Zr phase is precipitated, a pinning effect on the dislocation is achieved, so that the strength and hardness of the copper matrix are improved.
  • Another strengthening phase in the copper alloy of the present invention is the elemental Cr phase.
  • the elemental Cr phase is also generated during the heat treatment of the alloy.
  • the elemental Cr phase is completely dissolved in the copper matrix to form a supersaturated solid solution after the solid solution treatment, then precipitated out of the copper matrix during the subsequent aging process and dispersedly distributed in the alloy.
  • the elemental Cr phase plays a crucial role in the improvement of the strength of the alloy.
  • the three main strengthening phases in the alloy of the present invention exist independently and have a certain dependence.
  • the addition of a suitable proportion of alloy elements to form a rational proportion of phases is very important for the performance of the alloy.
  • the elemental Cr phase as the main strengthening phase in the alloy, plays a leading role in the strengthening of the alloy
  • the Cr 3 Si phase as a high-temperature phase, plays a leading role in the high-temperature softening resistance of the alloy
  • the Cu 5 Zr phase as another moderate strengthening phase, can strengthen the alloy and can also increase nucleating particles, refine the elemental Cr phase and the Cr 3 Si phase and allow the elemental Cr phase and the Cr 3 Si phase to be dispersedly distributed, so that both the strength and the high-temperature softening resistance are further improved.
  • the elemental Cr phase and the Cr 3 Si phase satisfy the following relationship: if the weight of the elemental Cr phase is X and the weight of the Cr 3 Si phase is Y, then 0 ⁇ X/Y ⁇ 20.
  • both the high-temperature softening resistance and the strength of the copper alloy will be greatly improved.
  • the ratio of the strengthening phases is greater than 20, the amount of the Cr 3 Si phase in the alloy is very small. As a result, the high-temperature softening resistance of the alloy cannot satisfy the requirements.
  • the copper alloy further comprises: 0.0001 % - 0.10 wt% Mg.
  • the copper alloy further comprises: 0.01% to 2.5 wt% of any one or more of Co, Zn, Mn, Sn and Nb, and their total amount does not exceed 3.5 wt% of the copper alloy.
  • the softening temperature of the copper alloy is greater than or equal to 580°C.
  • the softening temperature of the copper alloy is greater than or equal to 580°C, the demands for various welding processes by the material can be greatly increased, and the service life of the welding material is prolonged.
  • the softening temperature of the copper alloy is determined by tests. Generally, when the material is kept at a certain temperature for 2 hours and then cooled in water, the hardness of the treated material is tested. If the hardness loss of the treated material is within 15%, it is considered that the material is not softened at this temperature; or otherwise, it is considered that the material is softened.
  • the softening temperature of the conventional copper chromium zirconium alloy is about 550°C.
  • the hardness loss of the treated material is about 13% to 15%; and, if the conventional copper chromium zirconium alloy is kept at 580°C, the hardness loss is far greater than 15%.
  • the softening temperature of the conventional copper chromium zirconium alloy is 550 °C .
  • the hardness loss of the material at 550°C is 4% to 8%, and the hardness loss of the material at 550°C does not exceed 10%. Therefore, the softening temperature of the copper alloy of the present invention is greater than or equal to 580°C.
  • the present invention further discloses a method for preparing copper alloy, the method comprising: alloying and refining-casting into an ingot-ingot sawing, heating and extruding-solid solution heat treatment-stretching and drawing-aging heat treatment-straightening and finalizing;
  • the casting temperature for the alloying treatment and the covered refining is 1150°C to 1350°C; the temperature for the hot extrusion is 850°C to 950°C; the temperature for the solid solution treatment is 850°C to 1000°C; the cooling medium is water, and the cooling rate is 10°C/min to 150°C/s; the machining rate of the cold stretching and drawing is 20% to 60%; the temperature for the aging heat treatment is 420 °C to 520 °C; and the copper alloy is insulated for 2h to 4h.
  • the elemental Cr phase, the Cu 5 Zr phase and the Cr 3 Si phase are rational in size and more dispersive in distribution, so that various performances of the copper alloy of the present invention are improved.
  • the present invention discloses a method of using the copper alloy, the method comprising using the softening-resistant copper alloy in contact lines and welding materials..
  • the present invention has the following advantages:
  • the high-temperature softening resistance effect of the material is improved by adding a proper amount of Si to form a compound Cr 3 Si, and the strength and the high-temperature softening resistance of the material are further improved by strengthening the copper alloy matrix by the elemental Cr phase and the Cu 5 Zr phase, using the synergistic effect of the Cr 3 Si phase and the elemental Cr phase and by controlling the content of the impurity Fe.
  • the softening temperature of the copper alloy of the present invention is greater than or equal to 580°C, the requirements on various performances of the copper alloy in the fields of welding and contact lines are better satisfied.
  • %IACS used for representing the electrical conductivity of a metal or alloy (reference to the standard annealed pure copper).
  • the electrical conductivity of the standard annealed pure copper is generally defined as 100%IACS, i.e., 5.80F+7(1/ ⁇ m ) or 58(m/ ⁇ mm 2 ).
  • the value is the ratio of the resistivity (in volume or mass) specified by the International Annealed Copper Standard to the resistivity of the sample in the same unit multiplied by 100.
  • Embodiments 1-20 (embodiments 1-17 and all further embodiments produced using these compositions are not part of the invention)
  • the finished softening-resistant copper alloy products in Embodiments 21-40 of the present invention were obtained by preparing materials according to the components and their mass percentages of the softening-resistant copper alloy in Embodiments 1-20 in Table 1, then smelting, casting into an ingot, processing and molding, heating to 450°C to 520°C at an average heating rate of 1 °C/min to 30°C/min and holding this temperature for 2h to 4h (Embodiments 21-40 where the finished products were obtained, corresponding to the components and their mass percentages of the softening-resistant copper alloy in Embodiments 1-20, respectively).
  • the materials were prepared according to the components and their mass percentages of the softening-resistant copper alloy in Embodiments 1-20 in Table 1, and then treated under the following conditions: the casting temperature for the alloying treatment and the covered refining was 1150°C to 1350°C, the temperature for hot extrusion was 850°C to 950°C, the temperature for solid solution treatment was 850°C to 1000°C, the cooling medium was water, the cooling rate was 10°C/min to 150°C/s, the machining rate of cold drawing was 20% to 60%, the temperature for aging heat treatment was 420°C to 520°C, and the temperature holding time was 2 h to 4 h. Finally, the finished softening-resistant copper alloy bar products in ⁇ 8 in Embodiments 41-60, corresponding to the components and their mass percentages of the softening-resistant copper alloy in Embodiments 1-20, were obtained by finishing.
  • the tensile strength, hardness, electrical conductivity and softening temperature of the softening-resistant copper alloy bars in Embodiments 58-60 of the present invention were tested by methods specified by the related national and industrial Embodiments 41-57 fall outside the scope of the invention.
  • the test results are shown in Table 3.
  • the room-temperature tensile tests were carried out by an electronic universal mechanical property testing machine according to GB/T228.1-2010 Metal Material Tensile Test Section 1: Test at Room Temperature.
  • the samples were circular cross-section proportional samples having a proportional coefficient of 5.65.
  • the electrical conductivity tests were carried out according to GB/T228.1-2010 Test Methods for Electrical Performance of Electric Wires and Cables Section 2: Metal Material Resistivity Test.
  • test instrument a ZFD microcomputer bridge DC resistance tester was used, and the samples were 1000 mm in length.
  • the electrical conductivity was represented by %IACS.
  • the hardness tests were carried out by a hardometer according to GB/T 230.1-2009 Metal Material: Rockwell Hardness Test.
  • the tensile strength is higher than or equal to 470MPa, the Rockwell hardness is above 75, and the electrical conductivity is above 75%IACS.
  • Embodiments 61-80 The components and their mass percentages of the softening-resistant copper alloys in Embodiments 61-80 are the same as those in Embodiments 41-60. That is, the materials were prepared according to the components and their mass percentages of the softening-resistant copper alloy in Embodiments 1-20 in Table 1, and then treated under the following conditions: the casting temperature for the alloying treatment and the covered refining was 1150°C to 1350°C, the temperature for hot extrusion was 850°C to 950°C, the temperature for solid solution treatment was 850°C to 1000°C, the cooling medium was water, the cooling rate was 10°C/min to 150°C/s, the machining rate of cold drawing was 20% to 60%, the temperature for aging heat treatment was 420 °C to 520 °C, and the temperature holding time was 2h to 4h. Finally, the finished softening-resistant copper alloy bar products in ⁇ 8 were obtained by finishing.
  • the softening temperature tests were carried out by methods specified by HB5420-89 Copper and Copper Alloys for Resistance Welding Electrodes and Auxiliary Devices.
  • the test temperature was 580°C.
  • the test results are shown in Table 4. Embodiments 61-77 fall outside of the scope of the invention.
  • the hardness loss of the copper alloy of the present invention at 580°C is below 8%, while the hardness loss of the conventional copper chromium zirconium alloy in the comparison embodiment is greater than 18%. It is indicated that the high-temperature softening resistance of the copper alloy of the present invention is greatly improved.
  • the softening-resistant copper alloy bars in anyone of Embodiments 41-60 are machined into appliances for welding.
  • the softening-resistant copper alloy bars in anyone of Embodiments 41-60 are machined into contact lines for electrified railways.
  • the softening-resistant copper alloy of the present invention has high strength, good electrical performance and excellent high-temperature softening resistance, and is particularly applied in industrial fields such as welding appliances and contact lines for electrified railways.

Landscapes

  • 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)
  • Conductive Materials (AREA)

Claims (3)

  1. Alliage de cuivre résistant au ramollissement, comprenant :
    0,1 - 1,0 % en poids de Cr,
    0,01 - 0,2 % en poids de Zr,
    0,01 - 0,10 % en poids de Si,
    ≤ 0,10 % en poids de Fe,
    0,0001 - 0,10 % en poids de Mg, et
    0,01 - 2,5 % en poids d'au moins un élément parmi Co, Zn, Mn, Sn et Nb, leur quantité totale ne dépassant pas 3,5 % en poids de l'alliage de cuivre,
    le reste étant du cuivre et des impuretés inévitables,
    dans lequel la microstructure de l'alliage de cuivre comprend :
    une phase de Cr élémentaire,
    une phase Cu5Zr, et
    une phase Cr3Si, et
    dans laquelle la phase de Cr élémentaire et la phase de Cr3Si satisfont à la relation suivante :
    si le poids de la phase Cr élémentaire est X et le poids de la phase Cr3Si est Y, alors le rapport X/Y est supérieur à zéro et inférieur à vingt (0< X/Y <20).
  2. Procédé de préparation de l'alliage de cuivre selon la revendication 1, le procédé comprenant les étapes de : alliage et affinage-coulée en un lingot-sciage, chauffage et extrusion du lingot-traitement thermique en solution solide-étirage et tréfilage-traitement thermique de vieillissement-redressement et finalisation ;
    caractérisé en ce que, la température de coulée pour le traitement d'alliage et l'affinage couvert est de 1150 °C à 1350 °C ; la température pour l'extrusion à chaud est de 850 °C à 950 °C ; la température pour le traitement en solution solide est de 850 °C à 1000 °C ; le milieu de refroidissement est l'eau, et la vitesse de refroidissement est de 10 °C/min à 150 °C/s ; le taux d'usinage de l'étirage à froid et du tréfilage est de 20% à 60% ; la température pour le traitement thermique de vieillissement est de 420 °C à 520 °C ; et, l'alliage de cuivre est isolé pendant 2h à 4h.
  3. Utilisation de l'alliage de cuivre résistant au ramollissement selon la revendication 1 dans les lignes de contact et les matériaux de soudage.
EP17847871.5A 2016-09-09 2017-08-18 Alliage de cuivre résistant à l'adoucissement, procédé de préparation et application correspondante Active EP3511432B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201610813189.5A CN106350698B (zh) 2016-09-09 2016-09-09 抗软化铜合金、制备方法及其应用
PCT/CN2017/000536 WO2018045695A1 (fr) 2016-09-09 2017-08-18 Alliage de cuivre résistant à l'adoucissement, procédé de préparation et application correspondante

Publications (3)

Publication Number Publication Date
EP3511432A4 EP3511432A4 (fr) 2019-07-17
EP3511432A1 EP3511432A1 (fr) 2019-07-17
EP3511432B1 true EP3511432B1 (fr) 2021-07-21

Family

ID=57858375

Family Applications (1)

Application Number Title Priority Date Filing Date
EP17847871.5A Active EP3511432B1 (fr) 2016-09-09 2017-08-18 Alliage de cuivre résistant à l'adoucissement, procédé de préparation et application correspondante

Country Status (4)

Country Link
US (1) US20190161831A1 (fr)
EP (1) EP3511432B1 (fr)
CN (1) CN106350698B (fr)
WO (1) WO2018045695A1 (fr)

Families Citing this family (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106350698B (zh) * 2016-09-09 2018-03-27 宁波博威合金板带有限公司 抗软化铜合金、制备方法及其应用
JP6822889B2 (ja) * 2017-04-13 2021-01-27 株式会社Ｓｈカッパープロダクツ 銅合金材、銅合金材の製造方法およびかご型回転子
KR101810925B1 (ko) 2017-10-18 2017-12-20 주식회사 풍산 내열성 및 방열성이 우수한 구리 합금 판재
CN110512112B (zh) * 2018-05-21 2021-09-28 昆山微电子技术研究院 一种铜合金及其制备方法和天线材料
CN109913691A (zh) * 2019-04-22 2019-06-21 南通科誉德摩尔新材料有限公司 一种高强复合铬锆铜材料的制作工艺
CN110042273B (zh) * 2019-05-29 2020-11-06 南京达迈科技实业有限公司 一种高强高导铜合金管及其制备方法
CN111996411B (zh) * 2020-07-15 2021-11-30 宁波博威合金板带有限公司 一种高强高导铜合金材料及其制备方法和应用
CN113913642B (zh) * 2021-09-26 2022-07-05 宁波博威合金板带有限公司 一种铜合金带材及其制备方法
CN114807672B (zh) * 2022-03-23 2023-09-08 中南大学 Cu-Zn-Cr-Zr-Fe-Si系合金及其制备方法
CN114959350A (zh) * 2022-05-31 2022-08-30 西安理工大学 一种高性能Cu-Hf-RE合金及其制备方法
CN115418521B (zh) * 2022-07-11 2023-04-28 大连理工大学 一种耐高温铜合金及其制备方法
CN116005038B (zh) * 2022-12-08 2024-08-02 北京首钢吉泰安新材料有限公司 一种镍铬铁合金及其制备方法
CN116274955B (zh) * 2023-02-08 2025-07-04 陕西斯瑞新材料股份有限公司 一种火箭发动机燃烧室内衬用的高温铜合金
CN116083750A (zh) * 2023-03-10 2023-05-09 江西铜业集团有限公司 一种铜合金带材及制备方法、引线框架和连接器
CN116479283B (zh) * 2023-03-28 2025-02-18 宁波金田铜业(集团)股份有限公司 一种高性能铬青铜棒材及其制备方法

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5705125A (en) * 1992-05-08 1998-01-06 Mitsubishi Materials Corporation Wire for electric railways
JP4950584B2 (ja) * 2006-07-28 2012-06-13 株式会社神戸製鋼所 高強度および耐熱性を備えた銅合金
CN100587091C (zh) * 2008-09-12 2010-02-03 邢台鑫晖铜业特种线材有限公司 接触线用Cu-Cr-Zr合金制备工艺
JPWO2011036728A1 (ja) * 2009-09-25 2013-02-14 三菱マテリアル株式会社 銅合金トロリ線
CN102534291A (zh) * 2010-12-09 2012-07-04 北京有色金属研究总院 一种高强高导CuCrZr合金及其制备和加工方法
CN103382535B (zh) * 2013-07-10 2015-09-02 河南科技大学 一种高强、高导电、高延伸性铜合金及其制备方法
CN104342575B (zh) * 2014-10-11 2017-01-18 烟台万隆真空冶金股份有限公司 一种电气化铁路铬锆铜接触线及其加工工艺
JP6693092B2 (ja) * 2015-11-09 2020-05-13 三菱マテリアル株式会社 銅合金素材
CN106350698B (zh) * 2016-09-09 2018-03-27 宁波博威合金板带有限公司 抗软化铜合金、制备方法及其应用

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
CN106350698A (zh) 2017-01-25
EP3511432A4 (fr) 2019-07-17
WO2018045695A1 (fr) 2018-03-15
US20190161831A1 (en) 2019-05-30
CN106350698B (zh) 2018-03-27
EP3511432A1 (fr) 2019-07-17

Similar Documents

Publication Publication Date Title
EP3511432B1 (fr) Alliage de cuivre résistant à l&#39;adoucissement, procédé de préparation et application correspondante
KR101422382B1 (ko) 전자 재료용 Ｃｕ-Ｎｉ-Ｓｉ-Ｃｏ 계 구리 합금 및 그 제조 방법
JP5657311B2 (ja) 銅合金板材およびその製造方法
CN110923499B (zh) 一种含Ce和B的钛青铜合金带材及其制备方法
JP2022511276A (ja) 鍛造チタン合金による高強度のファスナ素材及びその製造方法
KR101802009B1 (ko) 전자 재료용 Cu-Si-Co 계 구리 합금 및 그 제조 방법
JP5520533B2 (ja) 銅合金材およびその製造方法
US4755235A (en) Electrically conductive precipitation hardened copper alloy and a method for manufacturing the same
JP6317966B2 (ja) Ｃｕ−Ｎｉ−Ｓｉ系銅合金板材およびその製造方法並びに通電部品
KR20220000900A (ko) 엔비(Nb) 및 에이엘(Al)을 함유하는 티타늄 구리 합금 스트립 및 그의 제조 방법
KR20130097665A (ko) 구리 합금
JP6730784B2 (ja) 電子部品用Ｃｕ−Ｎｉ−Ｃｏ−Ｓｉ合金
JP5607460B2 (ja) 切削加工性に優れた銅合金鋳塊と銅合金材料、およびこれを用いた銅合金部品
CN117265360A (zh) 一种复合析出强化型高熵合金及其制备方法
KR20080028754A (ko) 방전 가공용 전극선 및 그 제조방법
CN105018791A (zh) 一种钛铁铝碳合金
JP2016079472A (ja) 銅合金板材の製造方法並びにその板材および通電部品
JP5021873B2 (ja) 延性に優れたチタン板およびその製造方法
JP4130593B2 (ja) 疲労及び中間温度特性に優れた高力高導電性銅合金
JP2006097113A (ja) 析出硬化型銅合金の製造方法、析出硬化型銅合金及び伸銅品
CN116083749B (zh) 一种碲铜合金带材及其制备方法
JP2010106332A (ja) 抵抗溶接機の構造部材用銅合金材料
CN105112723A (zh) 一种低成本高强度钛铁碳合金
CN109763040A (zh) 一种铝合金材料及其制备的方法
CN113215439A (zh) 一种高强度铜合金板材及其生产工艺

Legal Events

Date Code Title Description
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE

PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20190326

A4 Supplementary search report drawn up and despatched

Effective date: 20190516

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAV Request for validation of the european patent (deleted)
DAX Request for extension of the european patent (deleted)
STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20200526

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

GRAJ Information related to disapproval of communication of intention to grant by the applicant or resumption of examination proceedings by the epo deleted

Free format text: ORIGINAL CODE: EPIDOSDIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

INTG Intention to grant announced

Effective date: 20201207

INTC Intention to grant announced (deleted)
GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

INTG Intention to grant announced

Effective date: 20210210

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602017042665

Country of ref document: DE

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1412681

Country of ref document: AT

Kind code of ref document: T

Effective date: 20210815

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG9D

REG Reference to a national code

Ref country code: NL

Ref legal event code: MP

Effective date: 20210721

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1412681

Country of ref document: AT

Kind code of ref document: T

Effective date: 20210721

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: SE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211122

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211021

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211021

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211022

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602017042665

Country of ref document: DE

Ref country code: BE

Ref legal event code: MM

Effective date: 20210831

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210818

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

26N No opposition filed

Effective date: 20220422

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210818

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20210831

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20170818

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20250820

Year of fee payment: 9

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20250821

Year of fee payment: 9

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20250828

Year of fee payment: 9

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: CH

Payment date: 20250901

Year of fee payment: 9

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20210721