EP1329528B1 - Hitzebeständige co-ni-basis-legierung und entsprechende herstellung - Google Patents

Hitzebeständige co-ni-basis-legierung und entsprechende herstellung Download PDF

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Publication number
EP1329528B1
EP1329528B1 EP01965698A EP01965698A EP1329528B1 EP 1329528 B1 EP1329528 B1 EP 1329528B1 EP 01965698 A EP01965698 A EP 01965698A EP 01965698 A EP01965698 A EP 01965698A EP 1329528 B1 EP1329528 B1 EP 1329528B1
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mass
resistant alloy
present
base heat
working
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French (fr)
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EP1329528A1 (de
EP1329528A4 (de
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Akihiko Chiba
Shirou Takeda
Shigemi c/o NHK SPRING CO. LTD. SATO
Shigeki Ueta
Toshiharu Noda
Michio Okabe
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NHK Spring Co Ltd
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NHK Spring Co Ltd
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    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • 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

Definitions

  • the present invention relates to a Co-Ni base heat-resistant alloy and to a preparation method therefor, and more particularly concerns a Co-Ni base heat-resistant alloy that is used for springs, bolts, etc., that are employed to portions, such as engines and exhaust systems and peripheral devices of gas turbines, which are exposed to high temperatures, and to a preparation method therefor.
  • heat-resistant parts that are employed in portions, such as engines and exhaust systems and peripheral devices of gas turbines, that are exposed to high temperatures, are manufactured by using Ni-base super heat-resistant alloy such as Inconel X-750 (Ni: 73.0 mass%, Cr: 15.0 mass%, Al: 0.8 mass%, Ti: 2.5 mass%, Fe: 6.8 mass%, Mn: 0.70 mass%, Si: 0.25 mass%, C: 0.04, Nb+Ta: 0.9 mass%) and Inconel 718 (Ni: 53.0 mass%, Cr: 18.6 mass%, Mo: 3.1 mass%, Al: 0.4 mass%, Ti: 0.9 mass%, Fe: 18.5 mass%, Mn: 0.20 mass%, Si: 0.18 mass%, C: 0.04 mass%, Nb+Ta: 5.0 mass%).
  • Ni-base super heat-resistant alloy such as Inconel X-750 (Ni: 73.0 mass%, Cr: 15.0 mass%, Al: 0.8 mass%, Ti: 2.5 mass%,
  • Ni-base super-heat-resistant alloys are reinforced by depositing ⁇ ' (Ni 3 (Al, Ti, Nb) and ⁇ " (Ni 3 Nb).
  • ⁇ ' and ⁇ " become coarse due to overaging, causing degradation in the strength.
  • parts such as springs and bolts on which stress is continuously imposed are subjected to great stress relaxation, failing to maintain performances originally required for the parts.
  • objects of the present invention are to provide a heat resistant alloy which exhibits higher strength than the above-mentioned Ni-base super-heat-resistant alloy, and is less susceptible to degradation in the strength even after a long-period of use under high temperatures, and to provide a preparation method therefor.
  • the inventors of the present invention have carried out various research and studies to find a heat-resistant alloy that has higher strength and is less susceptible to degradation in strength even after long-period of use under high temperatures in comparison with the Ni-base super-heat-resistant alloys, and have found that a Co-Ni-Cr based alloy is usable as the heat-resistant alloy, and that since this Co-Ni-Cr based alloy has a very low stacking fault energy so that when this is subjected to cold working or warm working, a solute element such as Mo, Fe and Nb is segregated in stacking faults of extended dislocation to block dislocation movements and consequently to achieve a high work hardening performance, and that when this is aged subsequently after the cold working or the warm working with working strain remaining therein, the strength is further improved.
  • EP 365716 discloses nickel-cobalt alloys for high temperature services.
  • Japanese Unexamined Patent Application Publication No. 10-140279 has disclosed such an alloy; however, since this is still not sufficient in strength under high temperatures, a ⁇ phase is deposited when this alloy is strengthened by increasing the amount of solute elements such as Mo, Fe, and Nb therein, resulting in degradation in workability and toughness.
  • the inventors of the present invention have found that in order to solve this problem, when Cr is set to be a minimum level that is required for use in a heat-resistant environment of not more than 750°C, it is possible to suppress the deposition of the ⁇ phase even when the amount of solute elements such as Mo, Fe, and Nb is increased, and that it is possible to further increase the strength by adding W thereto.
  • the Co-Ni base heat-resistant alloy of the present invention contains C: not more than 0.05%, Si: not more than 0.5%, Mn: not more than 1.0%, Ni: 25 to 45%, Cr: 13 to less than 18%, Mo + 1/2W of one kind or two kinds of Mo and W: 7 to 20%, Ti: 0.1 to 3.0%, Nb: 0.1 to 5.0% and Fe: 0.1 to 5.0%, with the rest being composed of Co and inevitable impurities.
  • the present invention preferably contains at least one selected from the group consisting of REM (at least one rare-earth elements such as Y, Ce, and misch metal): 0.007 to 0.10%, B: 0.001 to 0.010%, Mg: 0.0007 to 0.010% and Zr: 0.001 to 0.20%.
  • REM at least one rare-earth elements such as Y, Ce, and misch metal
  • the preparation method of the Co-Ni base heat-resistant alloy of the present invention is characterized by the steps in which: an alloy containing C: not more than 0.05%, Si: not more than 0.5%, Mn: not more than 1.0%, Ni: 25 to 45%, Cr: 13 to less than 18%, Mo + 1/2W of one kind or two kinds of Mo and W: 7 to 20%, Ti: 0.1 to 3.0%, Nb: 0.1 to 5.0% and Fe: 0.1 to 5.0%, and the rest being composed of Co and inevitable impurities, is subjected to a solid solution heat treatment at 1000 to 1200°C or a hot working at this temperature, and this is then subjected to a cold working or a warm working having a working ratio of not less than 40%, and this is then subjected to an aging heat treatment at 500 to 800°C for 0.1 to 50 hours.
  • the alloy is preferably allowed to contain at least one selected from the group consisting of REM (at least one rare-earth elements such as Y, Ce, and misch metal): 0.007 to 0.10%, B: 0.001 to 0.010%, Mg: 0.0007 to 0.010% and Zr: 0.001 to 0.20%.
  • REM at least one rare-earth elements such as Y, Ce, and misch metal
  • Carbon C is bound to Nb and Ti to form carbides to prevent crystal particles from becoming coarse at the time of a solid solution heat treatment, and also to strengthen the grain boundary; thus, this element is contained for these purposes.
  • the content must be set to be not less than 0.005%; however, since a content exceeding 0.05%, more specifically, 0.03%, would cause degradation in the toughness and corrosion resistance, and would also form a carbide with a dislocation anchoring element such as Mo, resulting in interference with the dislocation anchoring, the content is set to be not more than 0.05%.
  • the preferable range is set to be 0.005 to 0.03%.
  • Si is effectively used as a deoxidizer, this element is contained for this purpose; however, since a content exceeding 0.5%, more specifically, 0.3%, would cause degradation in the toughness, the content is set to be not more than 0.5%.
  • the preferable range is set to be not more than 0.3%.
  • the content must be set to be not less than 0.1%, more preferably, 0.25%; however, since a content exceeding 1.0%, more specifically, 0.7%, would cause degradation in the corrosion resistance, the content is set to be 0.1 to 1.0%.
  • the preferable range is set to be 0.25 to 0.7%.
  • Ni is an element that is used for stabilizing austenite serving as a matrix and improves heat resistance and corrosion resistance of the alloy, this element is contained for these purposes.
  • the content must be set to be not less than 25%, more preferably, 27%; however, since a content exceeding 45%, more specifically, 33%, would cause degradation in the work hardening performance, the content is set to be 25 to 45%.
  • the preferable range is set to be 27 to 33%.
  • the content must be set to be not less than 13%, more preferably, 14.5%; however, since a content exceeding 18%, more specifically, 17%, tends to cause deposition of a ⁇ phase, the content is set to be in a range of 13 to less than 18%.
  • the preferable range is set to be 14.5 to 17%.
  • the content must be set to be not less than 7%, more preferably, 9%; however, since the total amount of the content of Mo and 1/2 of the content of W exceeds 20%, more specifically, 16%, tends to cause deposition of a ⁇ phase, the content is set in a range of 7 to 20%.
  • the preferable range is set to be 9 to 16%.
  • the content must be set to be not less than 0.1%, more preferably, 0.5%; however, since a content exceeding 3.0%, more specifically, 1.8%, would cause deposition of an ⁇ phase (Ni 3 Ti) resulting in degradation in the workability and toughness, the content is set to be in a range of 0.1 to 3.0%. The preferable range is set to be 0.5 to 1.8%.
  • Nb is bound to C to form carbides to prevent crystal particles from becoming coarse at the time of a solid solution heat treatment and to strengthen the grain boundary, and also solid solution-treated in the matrix to strengthen the matrix, thereby improving the work hardening performance; thus, this element is contained for these purposes.
  • the content must be set to be not less than 0.1%, more preferably, 0.5%; however, since the content exceeding 5.0%, more specifically, 3.5%, would cause deposition of a ⁇ phase (Ni 3 Nb) resulting in degradation in the workability and toughness, the content is set to be in a range of 0.1 to 5.0%. The preferable range is set to be 0.5 to 3.5%.
  • the content must be set to be not less than 0.1%, more preferably, 0.5%; however, since a content exceeding 5.0%, more specifically, 3.3%, causes degradation in the oxidation resistance property, the content is set to be in a range of 0.1 to 5.0%. The preferable range is set to be 0.5 to 3.3%.
  • the application of Mo, Nb, and Fe in a combined manner makes it possible to greatly increase the solid solution strength and work hardening of the matrix, which greatly enhances the maximum tensile strength obtained at room temperature and at high temperatures, and exerts an effect of shifting the temperature having a maximum of the tensile strength at a high temperature to the high temperature side, in comparison with the application of Mo and Nb or Mo and Fe in a combined manner.
  • the content must be set to be not less than 0.007%, more preferably, 0.01%; however, since the content exceeding 0.10%, more specifically, 0.04%, causes degradation in the hot workability and oxidation resistance property in an inverse manner, the content is set to be in a range of 0.007 to 0.10%. The preferable range is set to be 0.01 to 0.04%.
  • B must be set to be 0.001%, more preferably, 0.002%
  • Mg must be set to be 0.0007%
  • Zr must be set to be 0.001%, more preferably, 0.01%
  • the ranges of the contents are respectively set to be in the above-mentioned ranges. More preferably, B is set to be in a range of 0.002 to 0.004%
  • Mg is set to be in a range of 0.001 to 0.003%
  • Zr is set to be in a range of 0.01 to 0.03%.
  • Co which has a close-packed hexagonal lattice structure, is allowed to contain Ni so as to have a face-centered cubic lattice structure, that is, austenite, thereby exerting a high work hardening performance.
  • solute atoms such as Mo are segregated at stacking faults between extended dislocations which have been introduced through cold or warm working so as to interfere with dislocation movements so that by suppressing the reoccurrence of dislocations, the Co-Ni base heat-resistant alloy having the above-mentioned component composition is strengthened.
  • the above-mentioned Co-Ni base heat-resistant alloy is subjected to a solid solution heat treatment at 1000 to 1200°C to make the organization homogenous, or a hot working at a temperature of not less than 1000°C to make the crystal grains finer, and this is then subject to cold working or warm working at a temperature of a working ratio of not less than 40% so that a great number of the dislocations are introduced to carry out work hardening.
  • the warm working may be carried out during a cooling process after the solid solution heat treatment or the hot working.
  • an aging heat treatment is carried out for 0.1 to 50 hours at 500 to 800°C so that solute atoms such as Mo and Fe are segregated in stacking faults formed between half-dislocations of extended dislocations; thus, the dislocation movements are blocked so that stress relaxation, that is, reoccurrence of dislocations, is suppressed.
  • the solid solution heat treatment or the hot working is carried out at 1000 to 1200°C is because a temperature lower than 1000°C fails to provide a sufficiently homogenous structure and also fails to lower the hardness, causing a difficulty in working. Moreover, this might cause deposition of a compound such as Mo that exerts an anchoring effect on dislocations, and the subsequent reduction in the age hardening property. Moreover, a temperature exceeding 1200°C makes crystal grains coarse, resulting in degradation in the toughness and strength.
  • the reason that the cold working or warm working having a working ratio of not less than 40% is carried out after the solid solution heat treatment or the hot working is because, as shown in Table 3 and Fig. 1, the working ratio of less than 40% fails to provide a high work hardening perfomance that is exerted by solute elements such as Mo and Fe to be segregated in the stacking faults in extended dislocations to interfere with the dislocation movements, and also causes greater creep elongation.
  • the reason that the aging heat treatment is carried out at 500 to 800°C for 0.1 to 50 hours after the cold or warm working of a working ratio of not less than 40% is because, as shown in Table 4 and Fig. 2, when the treatment is at less than 500°C or less than 0.1 hour, it fails to increase the strength sufficiently or, when the treatment exceeds 800°C or exceeds 50 hours, the dislocations reform to cause degradation in the hardness and strength, as well as the subsequent greater creep elongation.
  • the alloy is melted and prepared through a normal method by using a vacuum high-frequency induction furnace, etc., and is forged into an ingot through a normal forging method. Thereafter, this is subjected to a hot working and solid solution heat treatment at 1000 to 1200°C, and this is then subjected to a cold working or warm working having a working ratio of not less than 40%, and is then subjected to an aging heat treatment at 500 to 800°C for 0.1 to 50 hours.
  • Co-Ni base heat-resistant alloy of the present invention is applied to parts and devices such as exhaust-related parts such as engine exhaust manifolds, peripheral devices of gas turbines, furnace chamber materials, heat-resistant springs and heat-resistant bolts, in which Inconel X750 or Inconel X718 has been used. It is also applied to parts and devices used under higher temperature.
  • Alloys of an example and a comparative example of the present invention which have the component compositions shown in the following Table 1, were melted and prepared through a normal method by using a vacuum high-frequency induction furnace to obtain ingots of 30 kg. These ingots were formed into cylindrical bars each having a diameter of 35 mm through a hot forging process. Those bars except for that of comparative example 4 were subjected to a solution heat treatment at 1100°C, and then a cold working at a working ratio of 85% to form cylindrical bars each having a diameter of 13.6 mm, and these were then subjected to an aging of 720°C x 4 hours.
  • the bar of comparative example 4 was subjected to a solid solution heat treatment at 1050°C, and was then subjected to an aging treatment of 725°C x 16 hours at a working ratio of 30%.
  • Tensile test pieces having a diameter of 8 mm at parallel portions were obtained from these elements, and these were subjected to tensile tests at room temperature to measure the tensile strength.
  • creep test pieces having a diameter of 6 mm at parallel portions with a distance between scores of 30 mm were obtained, and these were subjected to creep test in which a stress of 330 MPa was applied thereto at 700°C to measure the elongation 1000 hours later. Table 2 shows the results of these tests.
  • Cylindrical bars having a diameter of 35 mm of No. 6 alloy of the present invention shown in Table 1 were subjected to a solid solution heat treatment at 1100°C, and were then subjected to cold workings at working ratios of 35%, 45% and 60% (comparative example 5, and examples 12 and 13 of the present invention), and these were then subjected to an aging of 720°C ⁇ 4 hours.
  • Tensile test pieces and creep test pieces were obtained from these elements in the same manner as in example 1, and tensile tests and creep tests were carried out on these under the same conditions as in example 1 to measure the tensile strength and creep.
  • Table 3 and Fig. 1 show the results of the tests.
  • Cylindrical bars having a diameter of 35 mm of No. 10 alloy of the present invention shown in Table 1 were subjected to a solid solution heat treatment at 1100°C and to cold working at working ratio of 85%, and were then subjected to an aging under conditions shown in Table 4 (comparative examples 6 and 7, examples 14 and 15 of the present invention).
  • Tensile test pieces and creep test pieces were obtained from these elements in the same manner as in example 1, and tensile tests and creep tests were carried out on these under the same conditions as in example 1 to measure the tensile strength and creep.
  • Table 4 and Fig. 2 show the results of the tests.
  • Table 1 and Table 2 show that, in the examples of the present invention, the tensile strength at room temperature was set in a range of 2148 to 2775 MPa, and the creep elongation was set to be 0.7 to 1.1%.
  • the tensile strength at room temperature was 1677 MPa which was lower than 78% of the examples of the present invention with the creep elongation being 1.7 times greater than that of the example of the present invention.
  • the tensile strength at room temperature was 1451 MPa which was lower than 68% of the examples of the present invention with the creep elongation being not less than 2 times greater than that of the example of the present invention.
  • the Co-Ni base heat-resistant alloy of the present invention has a higher strength at room temperature in comparison with Ni base super-heat-resistant alloys that have been conventionally used, and is less susceptible to degradation in strength even after long periods of use at high temperatures.
  • the preparation method of the present invention makes it possible to prepare a Co-Ni base heat-resistant alloy which has a higher strength at room temperature in comparison with Ni base super-heat-resistant alloys that have been conventionally used, and is less susceptible to degradation in strength even after long periods of use at high temperatures.

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Claims (8)

  1. Wärmebeständige Co-Ni-Basis-Legierung, umfassend: nicht mehr als 0,05 Gew.-% an C, nicht mehr als 0,05 Gew.-% an S, nicht mehr als 1,0 Gew.-% an Mn, 25 bis 45 Gew.-% an Ni, 13 bis weniger als 18 Gew.-% an Cr, 7 bis 20 Gew.-% an Mo plus 1/2 W von wenigstens Mo und/oder W, 0,1 bis 3,0 Gew.-% an Ti, 0,1 bis 5,0 Gew.-% an Nb, 0,1 bis 5,0 Gew.-% an Fe und optional 0,007 bis 0,10 an REM, 0,001 bis 0,010 an B, 0,0007 bis 0,010 an Mg und 0,001 bis 0,20 an Zr; und den Rest Co und unvermeidbare Verunreinigungen.
  2. Wärmebeständige Co-Ni-Basis-Legierung nach Anspruch 1, ferner umfassend: 0,007 bis 0,10 Gew.-% an REM.
  3. Wärmebeständige Co-Ni-Basis-Legierung nach Anspruch 1, ferner umfassend:
    wenigstens ein Element ausgewählt aus der Gruppe bestehend aus 0,001 bis 0,010 Gew.-% an B; 0,0007 bis 0,010 Gew.-% an Mg; 0,001 bis 0,20 Gew.-% an Zr.
  4. Wärmebeständige Co-Ni-Basis-Legierung nach Anspruch 1, ferner umfassend:
    0,007 bis 0,10 Gew.-% an REM; und wenigstens ein Element ausgewählt aus der Gruppe bestehend aus 0,001 bis 0,010 Gew.-% an B; 0,0007 bis 0,010 Gew.-% an Mb; und 0,001 bis 0,20 Gew.-% an Zr.
  5. Darstellungsverfahren einer wärmebeständigen Co-Ni-Basis-Legierung, wobei das Verfahren die Schritte umfasst:
    Unterwerfen einer Legierung, die nicht mehr als 0,05 Gew.-% an C, nicht mehr als 0,05 Gew.-% an S, nicht mehr als 1,0 Gew.-% an Mn, 25 bis 45 Gew.-% an Ni, 13 bis weniger als 18 Gew.-% an Cr, 7 bis 20 Gew.-% an Mo plus 1/2 W von wenigstens Mo und/oder W, 0,1 bis 3,0 Gew.-% an Ti, 0,1 bis 5,0 Gew.-% an Nb, 0,1 bis 5,0 Gew.-% an Fe und optional 0,007 bis 0,10 an REM, 0,001 bis 0,010 an B, 0,0007 bis 0,010 an Mg und 0,001 bis 0,20 an Zr; und den Rest Co und unvermeidbare Verunreinigungen enthält, einer Festlösungswärmbehandlung bei 1.000 bis 1.200 °C oder einer Heißbearbeitung bei dieser Temperatur;
    anschließendes Unterwerfen desselben einer Kaltbearbeitung oder einer Warmbearbeitung mit einem Bearbeitungsverhältnis von nicht weniger als 40 %; und
    anschließendes Unterwerfen derselben einer Alterungswärmebehandlung bei 500 bis 800 °C für 0,1 bis 50 Stunden.
  6. Darstellungsverfahren einer wärmebeständigen Co-Ni-Basis-Legierung nach Anspruch 5, wobei die Legierung ferner umfasst: 0,007 bis 0,10 Gew.-% an REM.
  7. Darstellungsverfahren einer wärmebeständigen Co-Ni-Basis-Legierung nach Anspruch 5, wobei die Legierung ferner umfasst:
    wenigstens ein Element ausgewählt aus der Gruppe bestehend aus 0,001 bis 0,010 Gew.-% an B; 0,0007 bis 0,010 Gew.-% an Mg; 0,001 bis 0,20 Gew.-% an Zr.
  8. Darstellungsverfahren einer wärmebeständigen Co-Ni-Basis-Legierung nach Anspruch 5, wobei die Legierung ferner umfasst:
    0,007 bis 0,10 Gew.-% an REM; und wenigstens ein Element ausgewählt aus der Gruppe bestehend aus 0,001 bis 0,010 Gew.-% an B; 0,0007 bis 0,010 Gew.-% an Mb; und 0,001 bis 0,20 Gew.-% an Zr.
EP01965698A 2000-09-19 2001-09-18 Hitzebeständige co-ni-basis-legierung und entsprechende herstellung Expired - Lifetime EP1329528B1 (de)

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JP2000282868 2000-09-19
JP2000282868A JP4315582B2 (ja) 2000-09-19 2000-09-19 Ｃｏ−Ｎｉ基耐熱合金およびその製造方法
PCT/JP2001/008104 WO2002024967A1 (fr) 2000-09-19 2001-09-18 Alliage thermoresistant a base de co-ni et son procede de fabrication

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EP1329528A1 EP1329528A1 (de) 2003-07-23
EP1329528A4 EP1329528A4 (de) 2005-09-07
EP1329528B1 true EP1329528B1 (de) 2007-03-14

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US (1) US20040025989A1 (de)
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JP (1) JP4315582B2 (de)
DE (1) DE60127286T2 (de)
ES (1) ES2283429T3 (de)
WO (1) WO2002024967A1 (de)

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JP5736140B2 (ja) * 2010-09-16 2015-06-17 セイコーインスツル株式会社 Ｃｏ−Ｎｉ基合金およびその製造方法
WO2015151318A1 (ja) * 2014-03-31 2015-10-08 日立金属株式会社 Ｆｅ－Ｎｉ基超耐熱合金の製造方法
CN104141066A (zh) * 2014-07-08 2014-11-12 株洲富力达硬质合金有限公司 一种钴基合金材料及其制造方法
JP7398415B2 (ja) * 2021-10-22 2023-12-14 トクセン工業株式会社 Ｃｏ－Ｎｉ－Ｃｒ－Ｍｏ系合金からなるばね用線
CN115011858B (zh) * 2022-06-23 2023-03-17 沈阳航空航天大学 高强度高塑性CoCrNiAlTi多主元合金及其制备方法
CN115323221B (zh) * 2022-08-19 2023-08-01 三峡大学 一种钴铬镍合金及其热处理工艺、及得到的热处理强化钴铬镍合金

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JP2002097537A (ja) 2002-04-02
EP1329528A1 (de) 2003-07-23
ES2283429T3 (es) 2007-11-01
WO2002024967A1 (fr) 2002-03-28
DE60127286D1 (de) 2007-04-26
US20040025989A1 (en) 2004-02-12
JP4315582B2 (ja) 2009-08-19
DE60127286T2 (de) 2007-12-20
EP1329528A4 (de) 2005-09-07

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