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WO2017006659A1 - Alliage de moulage à résistance élevée et dilatation thermique réduite destiné aux températures élevées, procédé pour le fabriquer et pièce moulée pour turbine - Google Patents

Alliage de moulage à résistance élevée et dilatation thermique réduite destiné aux températures élevées, procédé pour le fabriquer et pièce moulée pour turbine Download PDF

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Publication number
WO2017006659A1
WO2017006659A1 PCT/JP2016/066220 JP2016066220W WO2017006659A1 WO 2017006659 A1 WO2017006659 A1 WO 2017006659A1 JP 2016066220 W JP2016066220 W JP 2016066220W WO 2017006659 A1 WO2017006659 A1 WO 2017006659A1
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Prior art keywords
thermal expansion
strength
low
alloy
temperature
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Japanese (ja)
Inventor
半田　卓雄
志民 劉
直敏 来栖
新沼　透
竹田　真一
将弘 算用子
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Nippon Chuzo Co Ltd
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Nippon Chuzo Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention is applied to complicated shaped parts and large parts for precision instruments used at high temperatures such as turbines and pumps operating at high temperatures, and has high strength at low temperatures and high strength and low thermal expansion at high temperatures.
  • the present invention relates to a casting alloy, a manufacturing method thereof, and a casting for a turbine.
  • Non-Patent Document 1 As a typical low thermal expansion alloy applied for the purpose of maintaining and improving the accuracy of various devices operating at high temperatures, for example, the average thermal expansion coefficient between room temperature and 450 ° C. described in Non-Patent Document 1 is 5.3 ⁇ . There is an alloy of 29% Ni-17% Co-balance Fe (hereinafter referred to as Kovar) at 10 -6 / ° C. Rolled materials and forged materials (hereinafter referred to as steel materials) are commercialized and marketed. An example of its characteristics is shown.
  • Patent Document 1 by weight, C: 0.5 to 3.5%, Si: 2.0% or less, Mn: 1.0% or less, Mg: 0.1% or less, Ni: 25 There has been proposed a high-strength, low-thermal-expansion cast iron containing approximately 40% and Co: 0 to 15%, the balance being substantially composed of Fe, the main phase being the austenite phase and the interphase being the martensite phase.
  • Patent Document 2 by weight, C: 0.06 to 0.50%, Si: 1.0% or less, Mn: 2.0% or less, Ni: 22.8 to 29.2%, Co: 9.3 to 20%, the relationship between Ni and Co is 58- (5/3) Ni ⁇ Co ⁇ 86.25- (5/2) Ni, and the balance is composed of Fe except for impurities.
  • a high strength low thermal expansion alloy with a tensile strength comparable to that of piano wire and a low thermal expansion coefficient up to a temperature range of about 300 ° C, with a structure mainly composed of an austenite phase and a martensite phase generated by processing-induced transformation is proposed. Has been.
  • Kovar has a sufficiently small high-temperature thermal expansion coefficient compared with other heat-resistant alloys, but is inferior in tensile strength.
  • Kovar products are provided in simple shapes such as plates and bars, complex shaped products and large parts used in precision devices must be manufactured by cutting or welding assembly.
  • machinability and weldability are low, there is a problem that a great amount of man-hours and costs are required.
  • Patent Document 1 contains appropriate amounts of C and Si, has improved castability as compared to Kovar, and has excellent machinability and higher room temperature strength because graphite is distributed in the structure. .
  • Patent Document 1 does not disclose the coefficient of thermal expansion and strength at high temperatures, and it is unclear whether sufficient low thermal expansion and strength can be obtained at high temperatures.
  • Patent Document 1 in order to achieve high strength, it is necessary to immerse in liquid nitrogen or the like and cool to ⁇ 40 ° C. or lower, which limits the size of special manufacturing equipment and the size of the applied product. There are large restrictions on the scope of application.
  • the alloy of Patent Document 2 has a room temperature strength, it has a large tensile strength of 160 kgf / mm 2 or more, and a thermal expansion coefficient of 30 to 310 ° C. is 5.5, which is equivalent to Kovar shown in Non-Patent Document 2. ⁇ 10 ⁇ 6 / ° C. or less.
  • the alloy of Patent Document 2 requires work hardening that transforms a stable austenite phase into a work-induced martensite phase by cold working. Therefore, in order to obtain a complex shape product or a large part used in a precision device, it is necessary to manufacture by cutting or welding assembly, and there is a problem that much man-hour and cost are required as in the case of Kovar.
  • An object of the present invention is to provide a high-strength, low-thermal expansion cast alloy for high temperature, a method for producing the same, and a casting for turbine.
  • the present invention can manufacture complex shaped parts and large parts used in precision equipment without the need for special equipment and materials, and has high strength and low thermal expansion at temperatures up to 600 ° C.
  • the present invention has been made based on the above points, and provides the following (1) to (8).
  • a represented by the following formula (I) is in the range of 27.5 to 29.5, Furthermore, when the contents (mass%) of Mn and S are represented by [Mn] and [S], respectively, the relationship of [Mn] / [S] ⁇ 15 is satisfied, and the balance consists of Fe and inevitable impurities, A high-strength, low-thermal-expansion cast alloy for high temperature, characterized in that the area ratio of the martensite phase in the microstructure is 30 to 90%.
  • the average thermal expansion coefficient at 20 to 600 ° C. is 10 ⁇ 10 ⁇ 6 / ° C. or less, and the 0.2% proof stress at 600 ° C. is 100 MPa or more. Or a high-strength, low-thermal expansion cast alloy for high temperature.
  • the area ratio of the martensite phase in the microstructure is 50 to 90%, the average coefficient of thermal expansion at 20 to 600 ° C. is 10 ⁇ 10 ⁇ 6 / ° C. or less, and 0.2 at 600 ° C.
  • the high strength, low thermal expansion cast alloy for high temperature according to any one of (1) to (3), wherein the% yield strength is 150 MPa or more.
  • An average thermal expansion coefficient of 20 to 600 ° C. is 9 ⁇ 10 ⁇ 6 / ° C. or less, and a 0.2% proof stress at 600 ° C. is 100 MPa or more and less than 150 MPa (1)
  • a high-strength, low-temperature expansion cast alloy for high temperatures is 9 ⁇ 10 ⁇ 6 / ° C. or less, and a 0.2% proof stress at 600 ° C. is 100 MPa or more and less than 150 MPa
  • a high-temperature high-strength low-thermal-expansion cast alloy having high strength and low thermal expansion at temperature and having machinability superior to Kovar and a method for producing the same are provided.
  • the first embodiment is capable of obtaining a high-temperature high-strength low-thermal expansion cast alloy that can be dissolved in the atmosphere and casted in the atmosphere, exhibits low thermal expansion properties up to high temperatures, and has high high-temperature strength.
  • the percentage display in the component is mass%
  • the value of the thermal expansion coefficient is an average thermal expansion coefficient of 20 to 600 ° C.
  • ⁇ C 0.02 to 0.06% C has the effect of improving the castability and soundness of the low thermal expansion alloy casting.
  • the content exceeds 0.06%, it becomes difficult to make the thermal expansion coefficient 10 ⁇ 10 ⁇ 6 / ° C.
  • the C content is in the range of 0.02 to 0.06%.
  • Si 0.2-0.6%
  • Si is an element added for the purpose of deoxidation and improvement of hot water flow. Moreover, it has the effect of lowering the stability of the austenite phase and increasing the formation temperature of the martensite phase. However, if the content is less than 0.2%, the effect of improving deoxidation and hot water flow is insufficient, and if it exceeds 0.6%, the increase in the coefficient of thermal expansion at high temperatures cannot be ignored as with C. Therefore, the Si content is set to 0.2 to 0.6%.
  • Mn is an element effective for deoxidation. However, when the content is less than 0.3%, the effect is small, and when it exceeds 1.5%, the thermal expansion coefficient becomes larger than 10 ⁇ 10 ⁇ 6 / ° C. Therefore, the Mn content is in the range of 0.3 to 1.5%.
  • Ni is an important element that determines the thermal expansion coefficient together with Co described later, and the thermal expansion coefficient can be reduced to 10 ⁇ 10 ⁇ 6 / ° C. or less by adjusting it to the range described later according to the amount of Co.
  • Ni content is less than 24.0%, the desired low thermal expansion cannot be obtained, and if it exceeds 29.5%, the desired 0.2% yield strength cannot be obtained. Therefore, Ni is set in the range of 24.0 to 29.5%.
  • Co is an important element that determines the coefficient of thermal expansion together with Ni, and has an effect of expanding the temperature range where low thermal expansion property is developed to the high temperature side, and is an indispensable element in high temperature low thermal expansion alloys.
  • the Co content is less than 17.5% or more than 25.5%, the desired low thermal expansion cannot be obtained.
  • the Co content is in the range of 17.5 to 25.5%.
  • [Ni] +0.8 [Co] 40.5-44.5% Even if Ni and Co satisfy the above range, [Ni] +0.8 [Co] (where [Ni] and [Co] are the contents (mass%) of Ni and Co, respectively). When the Ni equivalent is less than 40.5% or more than 44.5%, the thermal expansion coefficient exceeds 10 ⁇ 10 ⁇ 6 / ° C. Therefore, [Ni] +0.8 [Co] is set in the range of 40.5 to 44.5%.
  • A 27.5-29.5
  • A is a value represented by the following formula (I), and is a parameter that represents a main factor affecting the stability of the austenite phase of the alloy, that is, the formation behavior of the martensite phase. Determine the site transformation end temperature. Also, the area ratio of the martensite phase is determined.
  • A 30 [C] ⁇ 1.5 ⁇ [Si] + 0.5 ⁇ ([Mn] ⁇ 55 ⁇ [S] / 32) + [Ni] + 0.05 ⁇ [Co] +0.1 (I)
  • [C], [Si], [Mn], [S], [Ni], and [Co] represent the content (% by mass) of each element.
  • A is set in the range of 27.5 to 29.5.
  • Cr 0.5 to 3.0% Cr is an element that improves oxidation resistance, and can be added as necessary. However, if the Cr content is less than 0.5%, the effect of improving the oxidation resistance is small. Conversely, if it exceeds 3%, an increase in the thermal expansion coefficient cannot be ignored. Therefore, when adding Cr, the content is made 0.5 to 3%.
  • the balance of C, Si, Mn, Ni, and Co is Fe and inevitable impurities.
  • S is contained as an impurity.
  • the microstructure of the alloy of this embodiment has an area ratio of 30 to 90% of martensite phase.
  • the area ratio of martensite can be roughly estimated from the ratio between the martensite generation temperature range (difference between martensite transformation start temperature and martensite transformation end temperature) and the temperature of the cooling medium. If the area ratio of the martensite phase is less than 30%, sufficient strength may not be obtained, and if it exceeds 90%, the thermal expansion coefficient up to 600 ° C. may increase. Conventionally, it has been said that when the amount of martensite is large, the thermal expansion coefficient becomes high, but with a relatively low C content as in this embodiment, even if the area ratio of the martensite phase increases to 30 to 90%. It has been found that both high strength and low thermal expansion coefficient can be achieved.
  • a preferred range for the area ratio of the martensite phase is 50 to 90%.
  • the remainder of the martensite phase is the austenite phase.
  • the first embodiment it has a composition that allows normal atmospheric dissolution and atmospheric casting, an appropriate amount of martensite area ratio is obtained without performing sub-zero treatment, and a thermal expansion coefficient up to a high temperature of 600 ° C. is 10
  • a high-strength, low-temperature-expansion alloy for high temperature is obtained, which is as low as ⁇ 10 ⁇ 6 / ° C. or less and has a high high-temperature strength with a 0.2% proof stress at 600 ° C. of 100 MPa or more.
  • the area ratio of the martensite phase is 50% or more, an extremely high high-temperature strength with a 0.2% proof stress of 150 MPa or more can be obtained.
  • the coefficient of thermal expansion varies depending on the strength level, and a lower coefficient of thermal expansion of 9 ⁇ 10 ⁇ 6 / ° C. is obtained when the 0.2% proof stress at 600 ° C. is 100 MPa or more and less than 150 MPa.
  • an appropriate amount of martensite in the above range is precipitated by rapidly cooling the alloy having the above composition after high-temperature heating.
  • the composition of the present embodiment is such that A, which determines the martensite phase generation temperature range, is in the range of 27.5 to 29.5. Therefore, the subzero treatment after high-temperature heating as in Patent Document 1 is performed.
  • the martensite phase can be obtained by quenching in water at room temperature. For this reason, there are no restrictions, such as installation of special manufacturing equipment like patent document 1, and the size of an applied product are restricted.
  • the coefficient of thermal expansion can be reduced by quenching after high-temperature heating in this way. This is presumably because the magnetization state changes due to the action of internal stress generated during rapid cooling, which affects the spontaneous magnetization strain.
  • the heating temperature is less than 700 ° C.
  • the low thermal expansion effect is insufficient, and if it exceeds 950 ° C., the effect is not improved and there is a risk of causing deformation or cracking.
  • the average cooling rate up to 450 ° C. is 5 ° C./sec. If the ratio is less than 1, the generation of internal stress is small, and the effect of reducing the thermal expansion coefficient is small. Therefore, after heating in the temperature range of 700 to 950 ° C., 5 ° C./sec. It cools to 450 degrees C or less with the above cooling rate.
  • the first embodiment has a composition that allows normal atmospheric dissolution and atmospheric casting, an appropriate amount of martensite area ratio is obtained without performing sub-zero treatment, and a thermal expansion coefficient up to a high temperature of 600 ° C. is 10 A high-strength, low-temperature-expansion alloy for high temperature is obtained, which is as low as ⁇ 10 ⁇ 6 / ° C. or less and has a high high-temperature strength with a 0.2% proof stress at 600 ° C. of 100 MPa or more. For this reason, it is possible to manufacture a complex-shaped product or a large-sized component that exhibits high strength and low thermal expansion at a high temperature without being assembled by welding.
  • the second embodiment is capable of normal atmospheric melting and casting, exhibits low thermal expansion to high temperatures, has high high-temperature strength, and further has high machinability superior to Kovar. A strength low thermal expansion cast alloy is obtained.
  • the thermal expansion coefficient, the high-temperature strength, and the production conditions are the same as in the first embodiment, but the point that defines the content of S and the like and the point that defines Mn / S are the first embodiment. Is different.
  • conditions unique to the second embodiment will be described. Note that, as in the first embodiment, unless otherwise specified, the% display in the component is mass%, and the value of the coefficient of thermal expansion is an average coefficient of thermal expansion of 20 to 600 ° C.
  • ⁇ S 0.02 to 0.05% S forms sulfides with Mn and contributes to improvement of machinability, but if it is contained in a large amount in the alloy, FeS having a low melting point is formed at the grain boundary and becomes brittle, causing ductility reduction and cracking. It becomes. If the content is less than 0.02%, the machinability improvement effect is small, and if it exceeds 0.05%, solidified cracks are likely to occur in complex shapes and large cast products. Therefore, the S content is in the range of 0.02 to 0.05%.
  • [Mn] / [S] ⁇ 15 [Mn] / [S] (where [Mn] and [S] are the contents (mass%) of Mn and S) are important parameters that influence the amount and composition of sulfides.
  • Mn 0 to 1.0% and S: 0.02 to 0.05%
  • [Mn] / [S] is less than 15
  • Mn is insufficient with respect to S
  • excess S is the above-mentioned FeS.
  • [Mn] / [S] is set to 15 or more.
  • the balance of C, Si, Mn, Ni, Co, and S is Fe and inevitable impurities.
  • the alloy of the first embodiment further contains S.
  • the S content is in the range of this embodiment, the thermal expansion coefficient is not affected.
  • the second embodiment has a composition capable of normal atmospheric dissolution and atmospheric casting, an appropriate amount of martensite area ratio can be obtained without applying sub-zero treatment, and a thermal expansion coefficient up to a high temperature of 600 ° C. is 10 ⁇ 10 ⁇ 6 / ° C or less, high strength at 0.2% proof stress at 600 ° C. of 100 MPa or more, high machinability without causing solidification cracks, high strength and low thermal expansion for high temperatures An alloy is obtained. For this reason, it is possible to manufacture a complex-shaped product or a large-sized component that exhibits high strength and low thermal expansion at high temperatures without welding and assembling with good cutting properties.
  • the first example corresponds to the first embodiment.
  • an alloy having each chemical composition shown in Table 1 was melted in the atmosphere in a high frequency induction furnace, and a specimen according to FIG. 1b) of JIS G0307 was cast. In either case, a CO 2 silica sand mold was used as a mold.
  • sample materials were heated to 800 ° C. and then cooled to 450 ° C. at an average cooling rate of 5 ° C./sec or more by water cooling. Thereafter, a thermal expansion test piece of ⁇ 8 mm ⁇ 100 mm was taken, and the thermal expansion coefficient between 20 and 600 ° C. was measured with a differential transformer type thermal dilatometer. In addition, a tensile test piece having a parallel part diameter of 10 mm and a distance between gauge points of 50 mm was sampled, and 0.2% yield strength at 600 ° C. was measured. In addition, an oxidation test piece having a diameter of 25 mm ⁇ 10 mm was collected and held at 800 ° C. for 100 hours in a heating furnace in the air atmosphere, and then the cross-sectional structure was observed with an optical microscope to measure the thickness of the oxide layer on the surface.
  • Table 1 shows the chemical composition, the value of Ni equivalent (Nieq), the value of A represented by the above formula (I), the martensite formation start temperature (Ms), the martensite area ratio (Ma), 20 to 600 ° C.
  • the average thermal expansion coefficient, 0.2% yield strength, casting defect, and oxide layer thickness are shown.
  • no. Nos. 1 to 7 are examples of the present invention, No. 1, which are within the scope of the first embodiment of the present invention.
  • 8 to 13 are comparative examples that deviate from the scope of the first embodiment.
  • No. 1 is an example of the present invention that satisfies the scope of the first embodiment.
  • Nos. 1 to 7 have a martensite area ratio of 30 to 90%, a thermal expansion coefficient of 20 to 600 ° C. of 10 ⁇ 10 ⁇ 6 / ° C. or less, and a 0.2% proof stress at 600 ° C. of 100 MPa or more. I met.
  • a comparative example No. 1 deviating from the scope of the first embodiment. 8-12 did not meet one or more of these.
  • No. 13 had a cast hole.
  • No. which is an example of the present invention.
  • Each of Nos. 5 to 7 has an oxide layer thickness of less than 60 ⁇ m, which is a value of 1/2 or less of Kovar shown as a reference, and was confirmed to have excellent oxidation resistance.
  • No. Cr contents other than 5 to 7 and 11 are impurity levels.
  • the martensite area ratio was 50% or more, and the high temperature strength was 0.2% proof stress at 600 ° C. of 150 MPa or more.
  • the thermal expansion coefficient in the examples of the present invention, the high-temperature strength is No. In 1, 2, 6, and 7, the thermal expansion coefficient at 20 to 600 ° C. showed a lower value of 9 ⁇ 10 ⁇ 6 / ° C. or less.
  • the second example corresponds to the second embodiment.
  • an alloy having each chemical composition shown in Table 2 was melted in the atmosphere with a high frequency induction furnace, and a specimen according to JIS G0307 (FIG. 1b) and a cylindrical casting having a diameter of 100 mm and a height of 200 mm were cast. In either case, a CO 2 silica sand mold was used as a mold.
  • the cutting force was measured by turning a ⁇ 100 mm outer diameter with a carbide tool P20 with a cutting depth of 2 mm and a feed of 0.2 mm / rotation, and measuring the main component force with a commercially available cutting resistance measuring device.
  • Table 2 shows the chemical composition, the value of [Mn] / [S] (indicated as Mn / S in Table 2 for convenience), the value of Ni equivalent (Nieq), the value of A, and the martensite formation start temperature. (Ms), martensite area ratio (Ma), average thermal expansion coefficient at 20 to 600 ° C., 0.2% yield strength, casting defect, cutting resistance, and oxide layer thickness.
  • Mn manganese
  • Mo martensite area ratio
  • Table 2 shows the chemical composition, the value of [Mn] / [S] (indicated as Mn / S in Table 2 for convenience), the value of Ni equivalent (Nieq), the value of A, and the martensite formation start temperature. (Ms), martensite area ratio (Ma), average thermal expansion coefficient at 20 to 600 ° C., 0.2% yield strength, casting defect, cutting resistance, and oxide layer thickness.
  • no. Nos. 21 to 27 are examples of the present invention, No. 1, which are within the scope of the second embodiment of the present invention
  • Martensite generation start temperature (Ms) and martensite area ratio were determined in the same manner as in the first example.
  • No. 1 is an example of the present invention that satisfies the scope of the second embodiment.
  • Nos. 21 to 27 have a martensite phase area ratio of 30 to 90%, an average thermal expansion coefficient of 20 to 600 ° C. of 10 ⁇ 10 ⁇ 6 / ° C. or less, and a 0.2% proof stress of 600 ° C. of 100 MPa. The above conditions were satisfied, the cutting resistance was less than 900 N, and no surface defects occurred on the test piece.
  • Nos. 28 to 33 have at least one of a martensite phase area ratio of 30 to 90%, a thermal expansion coefficient of 20 to 600 ° C.
  • No. which is an example of the present invention.
  • the martensite area ratio was 50% or more, and the high temperature strength was 0.2% proof stress at 600 ° C. of 150 MPa or more.
  • the thermal expansion coefficient in the examples of the present invention, the high-temperature strength is No. In 21, 22, 26 and 27, the thermal expansion coefficient at 20 to 600 ° C. showed a lower value of 9 ⁇ 10 ⁇ 6 / ° C. or less.
  • the third embodiment relates to manufacturing conditions.
  • Table 3 shows No. 1 in Table 1.
  • No. 4 composition alloy specimen was heated at a temperature of 650 to 1000 ° C. and an average cooling rate of 2.5 ° C./sec. And 5 to 7.5 ° C./sec. This shows the thermal expansion coefficient when heat treatment is performed under the heat treatment conditions.
  • Table 3 after heating in the temperature range of 700 to 950 ° C., 5 ° C./sec. It was confirmed that the coefficient of thermal expansion became 10 ⁇ 10 ⁇ 6 / ° C. or lower by cooling to 450 ° C. or lower at the above cooling rate.
  • Table 4 shows No. 2 in Table 2.
  • No. 23 composition alloy specimens were heated at a temperature of 650 to 1000 ° C. and an average cooling rate of 2.5 ° C./sec. And 5 to 7.5 ° C./sec. This shows the thermal expansion coefficient when heat treatment is performed under the heat treatment conditions.
  • no. No. 23 alloy is also No. 23. 4 and 5 ° C./sec. After heating in the temperature range of 700 to 950 ° C. It was confirmed that the coefficient of thermal expansion became 10 ⁇ 10 ⁇ 6 / ° C. or lower by cooling to 450 ° C. or lower at the above cooling rate.

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Abstract

La présente invention contient, en termes de % en masse, de 0,02 à 0,06 % de C, 0,2 à 0,6 % de Si, de 0,3 à 1,5 % de Mn, de 24,0 à 29,5 % de Ni et de 17,5 à 25,5 % de Co, l'équivalent en Ni étant dans la plage de 40,5 à 44,5 %, la valeur de A représentée par la formule (I) étant dans la plage de 27,5 à 29,5 et le reste étant constitué de Fe et des impuretés inévitables, et la surface d'une phase martensitique dans la microstructure représentant de 30 à 90 %. Formule (I) : A = 30 [C] – 1,5 × [Si] + 0,5 × ([Mn] – 55 × [S]/32) + [Ni] + 0,05 × [Co] + 0,1
PCT/JP2016/066220 2015-07-06 2016-06-01 Alliage de moulage à résistance élevée et dilatation thermique réduite destiné aux températures élevées, procédé pour le fabriquer et pièce moulée pour turbine Ceased WO2017006659A1 (fr)

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2022196775A1 (fr) * 2021-03-19 2022-09-22 新報国マテリアル株式会社 Alliage à dilatation thermique régulée
JP2022143790A (ja) * 2021-03-18 2022-10-03 日本鋳造株式会社 低熱膨張合金

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JP2016117924A (ja) * 2014-12-19 2016-06-30 日本鋳造株式会社 塑性加工用または鋳造用高ヤング率低熱膨張鋳造合金およびその製造方法

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JP2022143790A (ja) * 2021-03-18 2022-10-03 日本鋳造株式会社 低熱膨張合金
WO2022196775A1 (fr) * 2021-03-19 2022-09-22 新報国マテリアル株式会社 Alliage à dilatation thermique régulée
JPWO2022196775A1 (fr) * 2021-03-19 2022-09-22
EP4310212A4 (fr) * 2021-03-19 2025-04-02 Shinhokoku Material Corp. Alliage à dilatation thermique régulée

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