WO2012002208A1 - Acier inoxydable durci par précipitation et son procédé de production - Google Patents

Acier inoxydable durci par précipitation et son procédé de production Download PDF

Info

Publication number
WO2012002208A1
WO2012002208A1 PCT/JP2011/064229 JP2011064229W WO2012002208A1 WO 2012002208 A1 WO2012002208 A1 WO 2012002208A1 JP 2011064229 W JP2011064229 W JP 2011064229W WO 2012002208 A1 WO2012002208 A1 WO 2012002208A1
Authority
WO
WIPO (PCT)
Prior art keywords
stainless steel
precipitation
formula
strength
alloy
Prior art date
Application number
PCT/JP2011/064229
Other languages
English (en)
Japanese (ja)
Inventor
友典 上野
上原　利弘
真一 中務
Original Assignee
社団法人日本航空宇宙工業会
日立金属株式会社
住友精密工業株式会社
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 社団法人日本航空宇宙工業会, 日立金属株式会社, 住友精密工業株式会社 filed Critical 社団法人日本航空宇宙工業会
Priority to JP2011546519A priority Critical patent/JP4918632B2/ja
Publication of WO2012002208A1 publication Critical patent/WO2012002208A1/fr

Links

Images

Classifications

    • 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
    • C21D6/02—Hardening by precipitation
    • 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
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/04—Hardening by cooling below 0 degrees Celsius
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt

Definitions

  • the present invention relates to precipitation strengthened stainless steel and a method for producing the same.
  • Non-Patent Document 1 As a high strength material, low alloy type high strength steel represented by AISI 4340, 300M and the like is known. If these heat treatment conditions are selected, a tensile strength exceeding about 1800 MPa and an elongation of about 10% can be obtained (see Non-Patent Document 1). However, these are low-alloy steels, and their corrosion resistance is insufficient because Cr, which greatly contributes to corrosion resistance, is a little less than 1%.
  • martensitic precipitation strengthened stainless steels represented by PH13-8Mo (AISI XM-13), 17-4PH (AISI 630) and the like are known as high-strength stainless steels.
  • Patent Document 1 proposes a high-strength stainless steel and has excellent strength characteristics, but it cannot be said that the ductility is sufficient as compared with a low alloy high strength steel. Furthermore, the high-strength steel proposed in Patent Document 2 has a sufficiently high strength when Cr, which is an element for improving corrosion resistance, is not added. However, when Cr is added, it is compared with a low-alloy high-strength steel. Then the strength is slightly inferior.
  • the present applicant has proposed a high-strength stainless steel shown in Patent Document 3 as a high-strength material in which the corrosion resistance of the low alloy steel and the strength and ductility of the high-strength stainless steel are improved.
  • the high-strength stainless steel shown in Patent Document 3 is a material that can obtain a tensile strength exceeding 1800 MPa if heat treatment conditions are selected, and has excellent corrosion resistance.
  • the high-strength stainless steel shown in Patent Document 3 described above is an excellent material in terms of tensile strength and corrosion resistance, but 0.2% proof stress is lower than tensile strength.
  • the high-strength stainless steel shown in Patent Document 3 has a low yield strength ratio.
  • an object of the present invention is to provide a precipitation-strengthened stainless steel having excellent corrosion resistance while maintaining the tensile strength, 0.2% proof stress and ductility at the level of a low alloy high strength steel, and a method for producing the same. That is.
  • the present inventor has conducted a diligent study to achieve both the tensile strength, the 0.2% proof stress and the ductility of the low alloy high strength steel level, and the conventional high strength stainless steel. Mo is added based on a suppressed precipitation strengthened martensitic stainless steel, and the tensile strength and ductility are maintained without sacrificing corrosion resistance by balancing the proportion and amount of Al and Ti that form a compound with Ni.
  • the present inventors have found that the 0.2% proof stress can be greatly improved and reached the present invention. That is, in the present invention, in mass%, C: ⁇ 0.2%, 7% ⁇ Ni ⁇ 14%, 0% ⁇ Co ⁇ 3.5%, 9.5% ⁇ Cr ⁇ 14%, 0.5% ⁇ Mo.
  • Formula (1) 1260-65Ni-20Co-40Cr ⁇ 0 Formula (2) 670 + 75Ni + 40Co-100Cr ⁇ 0 Formula (3) 0.125 ⁇ (Al / Ti) ⁇ 1.25 Formula (4) 1.45 ⁇ (Al + Ti) ⁇ 2.95 (However, Ni, Co, Cr, Al, and Ti in the formula are calculated in terms of mass%)
  • this invention satisfies following formula (5).
  • Formula (5) 4.5 ⁇ Ni / (Al + Ti) (However, Ni, Al, and Ti in the formula are calculated in terms of mass%)
  • a more preferable range of the formula (4) in the present invention is 2.1 ⁇ (Al + Ti) ⁇ 2.55.
  • a more preferable range of the formula (3) is 0.35 ⁇ (Al / Ti) ⁇ 0.65.
  • Si, Mn, Cu, P, S, O, and N, which are impurity elements of the present invention are Si ⁇ 0.1%, Mn ⁇ 0.1%, Cu ⁇ 0.1%, and P ⁇ 0.03.
  • the precipitation strengthened stainless steel of the present invention has an elongation of 7.5% or more, a 0.2% proof stress and a tensile strength of 1600 MPa with a 0.2% proof stress, and a tensile strength of 1700 MPa in a tensile test at room temperature. As described above, this is a precipitation strengthened stainless steel satisfying any of fracture toughness of 40 MPa ⁇ m 1/2 or more.
  • the stainless steel having the above composition subjected to at least melting and hot plastic working is subjected to a solid solution treatment at 940 ° C. to 1050 ° C., and further from 480 ° C. to It is a manufacturing method of precipitation strengthening type stainless steel which performs an aging treatment at 550 ° C.
  • the sub-zero treatment is performed at ⁇ 50 ° C. to ⁇ 100 ° C. after the above-mentioned solid solution treatment, thereby producing a precipitation strengthened stainless steel.
  • it is a manufacturing method of precipitation strengthening type stainless steel whose processing ratio of said hot plastic working is 3 or more.
  • the precipitation strengthened stainless steel of the present invention has the tensile strength, 0.2% proof stress and ductility of the low alloy high strength steel level, and has the same corrosion resistance as conventional high strength stainless steel. In designing aircraft parts and the like that require corrosion resistance, it can be expected that the tensile strength can be effectively used as compared with a material having a small yield strength ratio.
  • Example 3 is an optical micrograph of a cross section of the alloy of the present invention. It is an optical microscope photograph of a comparative example alloy cross section. It is an optical microscope photograph of a comparative example alloy cross section. It is a graph which shows the fatigue test result of Example 4.
  • an important feature of the present invention is that Mo is added to improve tensile strength and 0.2% proof stress, based on the components of precipitation strengthened martensitic stainless steel with C kept low, This is because the proportion and amount of Al and Ti forming a compound with Ni were balanced.
  • the reason why each chemical composition and relational expression are defined in the present invention is as follows. Unless otherwise specified, the mass% is indicated.
  • C is an element to be regulated as an impurity in the present invention.
  • C is limited to 0.2% or less in order to lower the balance between strength and ductility by forming carbides with additive elements such as Ti and Cr, and to further deteriorate the corrosion resistance.
  • additive elements such as Ti and Cr
  • 7% ⁇ Ni ⁇ 14% Ni is an austenite-forming element and is effective for the disappearance of ⁇ -ferrite during the solution treatment, and it has the effect of strengthening precipitation by forming fine intermetallic compounds with Al and Ti during the aging treatment. It is an element to be added.
  • Ni is set in the range of 7% to 14%.
  • the lower limit of Ni is preferably 9%.
  • Co is an austenite forming element like Ni, and is effective in disappearance of ⁇ ferrite during solution treatment. Further, since the temperature drop at the Ms point is not larger than Ni, it is added in a range of 3.5% or less. It is effective to do. However, in the present invention, Ni is indispensably added in the range of 7 to 14%, so Co does not necessarily need to be added, and is an optional component that can be added at an additive level including 0%. In addition, unlike Ni, Co does not form intermetallic compounds with Al, Ti, etc., but indirectly promotes precipitation of intermetallic compounds, or refines intermetallic compounds to strengthen precipitation. Contribute.
  • Mo 0.5% ⁇ Mo ⁇ 3% Mo is essential to improve strength and corrosion resistance. However, if the Mo content is less than 0.5%, the ductility is remarkably reduced. On the other hand, if the Mo content exceeds 3%, the ⁇ ferrite becomes stable at the solution treatment temperature, and the form of the remaining ⁇ ferrite depends on the manufacturing process. Therefore, the directionality appears in the characteristics of the final product. In addition, the presence of ⁇ ferrite significantly impairs the balance between strength and ductility. Therefore, Mo is set in the range of 0.5% to 3%. Since Mo can be expected to improve corrosion resistance, particularly pitting corrosion resistance, due to combined addition with Cr, the lower limit of Mo is preferably 0.7%.
  • Al is an essential element because it is an element that forms an intermetallic compound with Ni during aging treatment and strengthens precipitation. In order to increase the strength by adding Al, 0.25% or more is necessary. On the other hand, addition of 1% or more causes a significant decrease in ductility. Therefore, Al was made into the range exceeding 0.25% and less than 1%.
  • Ti is an element that forms an intermetallic compound with Ni during the aging treatment and strengthens precipitation, it is essential to add Ti. In order to increase the strength by adding Ti, an addition amount exceeding 0.75% is required. On the other hand, when it exceeds 2.5%, the ductility is remarkably reduced. Therefore, Ti is set to a range of more than 0.75 and 2.5% or less. The preferable upper limit of Ti is 2.45%.
  • the elements other than those described above are Fe and impurities. Typical impurity elements include Si, Mn, Cu, P, S, O, N, and the like, and these elements are preferably regulated to the following ranges.
  • the following range is preferable. Si ⁇ 0.1%, Mn ⁇ 0.1%, Cu ⁇ 0.1%, P ⁇ 0.03%, S ⁇ 0.008%, O ⁇ 0.005%, N ⁇ 0.01%.
  • Formula (1) 1260-65Ni-20Co-40Cr ⁇ 0
  • Formula (1) is an index of ease of martensitic transformation during cooling after the solution treatment. In general, the temperature at which martensitic transformation occurs is known as the Ms point.
  • Formula (2) 670 + 75Ni + 40Co-100Cr ⁇ 0
  • Formula (2) is an indicator of whether or not a ⁇ ferrite phase exists at the solution treatment temperature. The presence of this ⁇ ferrite is determined by the balance between the addition amount of Cr, which is a ferrite forming element, and the addition amounts of austenite forming elements, Ni and Co.
  • this formula (2) If ⁇ is not satisfied, the ⁇ ferrite becomes stable at the solution treatment temperature, and the presence form of the remaining ⁇ ferrite has a direction depending on the manufacturing process, so that the directionality appears in the characteristics of the final product. In addition, the presence of ⁇ ferrite significantly impairs the balance between strength and ductility.
  • Formula (3) 0.125 ⁇ (Al / Ti) ⁇ 1.25
  • Formula (3) is an index for optimizing the precipitation phase responsible for precipitation strengthening.
  • L1 2 structure in which Ni 3 (Ti, Al) phase is liable to precipitate the balance between strength and ductility after aging treatment is most excellent.
  • (Al / Ti) is less than 0.125, a hexagonal Ni 3 Ti phase is likely to precipitate, resulting in a decrease in ductility.
  • (Al / Ti) exceeds 1.25, a Ni (Al, Ti) phase having a B2 structure is likely to be precipitated, the ductility is remarkably lowered, and the tensile strength is insufficient.
  • the range of the relational expression shown by the expression (3) is set to 0.125 to 1.25.
  • the range of the relational expression represented by the expression (3) is preferably 0.35 to 0.65.
  • Formula (4): 1.45 ⁇ (Al + Ti) ⁇ 2.95 Equation (4) is an index for optimizing the amount of precipitation of the precipitation phase responsible for precipitation strengthening.
  • (Al + Ti) represented by this formula (4) is less than 1.45, the amount of precipitation is small and the strength is insufficient, and when (Al + Ti) exceeds 2.95, the amount of precipitation is excessive and the ductility decreases. Is remarkable.
  • the range of the relational expression shown by the formula (4) is set to 1.45 to 2.95.
  • it is preferable that the relational expression represented by the formula (4) is 2.1 to 2.55.
  • Formula (5): 4.5 ⁇ Ni / (Al + Ti) Equation (5) is an index for optimizing fracture toughness.
  • Ni / (Al + Ti) represented by the formula (5) is less than 4.5, the fracture toughness tends to be lowered. Therefore, the relational formula represented by the formula (5) is preferably 4.5 or more.
  • precipitation strengthened stainless steel dissolves a precipitation strengthening element in an austenite phase in a solution treatment, and then transforms the austenite phase into martensite by cooling with water, oil, cooling gas, or the like. Thereafter, a high-strength material can be obtained by finely depositing an intermetallic compound phase or the like by aging treatment. Also in the present invention, the solid solution treatment is performed on the precipitation strengthened stainless steel adjusted to the above composition.
  • the solution treatment temperature of the present invention is less than 940 ° C.
  • the alloy element does not sufficiently dissolve, whereas when it exceeds 1050 ° C., austenite crystal grains are likely to be coarsened, and ⁇ ferrite is generated, resulting in mechanical properties. Therefore, the solution treatment temperature is set to 940 ° C to 1050 ° C.
  • As the solution treatment time for example, 0.5 to 3 hours is sufficient.
  • the precipitation strengthened stainless steel of the present invention has a relatively low martensite transformation start point (Ms point), a complete martensite structure cannot be obtained only by cooling at the time of solution treatment, a large amount of austenite structure remains, and the proof stress Therefore, after cooling to room temperature in the solution treatment, subzero treatment is further performed at ⁇ 50 ° C. to ⁇ 100 ° C. as necessary.
  • the processing time for the sub-zero processing can be set to 0.5 to 3 hours, for example.
  • an aging treatment (precipitation strengthening treatment) is performed at 480 ° C. to 550 ° C. in order to obtain a high strength and high toughness in a good balance. If the aging treatment temperature is less than 480 ° C., the strength is high but the ductility may be lowered. On the other hand, if it exceeds 550 ° C., the strength may be lowered. It is sufficient to keep the aging treatment time for 1 to 24 hours.
  • the precipitation-strengthened stainless steel of the present invention has the mechanical properties of an elongation of 7.5% or more, a 0.2% proof stress of 1600 MPa or more, and a tensile strength of 1700 MPa or more according to the above-described manufacturing method in a tensile test at room temperature. Obtainable. Further, since the above-described manufacturing method can have a fracture toughness of 40 MPa ⁇ m 1/2 or more, it can be stably used for aircraft parts and the like.
  • the precipitation-strengthening stainless steel of the present invention when the precipitation-strengthening stainless steel of the present invention is mass-produced to aircraft parts and power generation parts where inclusions and component segregation are problematic, as a melting method thereof It is preferred to apply vacuum melting. Subsequent to vacuum melting, a remelting method such as vacuum arc remelting or electroslag remelting may be appropriately combined. Moreover, in order to perform the above-mentioned heat processing, it heat-processes using the raw material which performed hot plastic working, such as a forge and a press, after the above-mentioned melt
  • the precipitation-strengthened stainless steel of the present invention when the precipitation-strengthened stainless steel of the present invention is heat-treated on an actual product, it is preferable to perform the aging treatment after performing machining to a shape close to the product shape before the aging treatment. Moreover, when performing hot plastic working, it is preferable that the working ratio is 3 or more. This is because if the processing ratio is less than 3, the 0.2% yield strength may be significantly reduced.
  • the processing ratio is obtained by the cross-sectional area of the workpiece before processing / the cross-sectional area after processing.
  • the workpiece before processing is a steel ingot, the steel ingot is often tapered. In that case, since the cross-sectional areas differ between the upper and lower ends of the steel ingot, the cross-sectional area is calculated as an average cross-sectional area.
  • Example 1 The following examples further illustrate the present invention.
  • a 10 kg steel ingot was produced by vacuum melting. Since the steel ingot was tapered, the upper and lower cross-sectional areas of the steel ingot were obtained, and the average cross-sectional area obtained by dividing the sum by 2 was 5625 mm 2 .
  • Table 1 shows the chemical composition of the steel ingot.
  • elements other than those shown in Table 1 are Fe and impurities. The contents of typical impurity elements Cu, P, S, O and N are 0.1% or less, 0.015% or less, 0.0025% or less, 0.005% or less, 0.005% or less, respectively. Met.
  • the conventional example No. shown in the following Table 1 and Table 2. 31 is a numerical value extracted from Patent Document 3, and No.
  • Non-Patent Document 1 is a numerical value extracted from Non-Patent Document 1 as AISI 4340, which is a low-alloy high-strength steel, and is a composition and mechanical property value of 1133K DOQT-steel 3R shown in Table III of Non-Patent Document 1.
  • the steel ingots of the present invention and comparative examples shown in Table 1 were heated to 1050 ° C., forged, and No. No. 14 alloy and no. Other than 15 alloys, 45 mm width ⁇ 20 mm thickness flat rectangular materials were used.
  • No. No. 14 alloy is a 38 mm ⁇ 38 mm square material.
  • 15 alloy produced 65 mm width x 30 mm thickness rectangular material.
  • the processing ratio of alloy No. 14 is 3.90.
  • the processing ratio of 15 alloy was 2.88.
  • each forged material produced was heat-treated.
  • the heat treatment was performed continuously with the solution treatment, sub-zero treatment, and aging treatment.
  • the solution treatment was carried out in an atmospheric furnace at a temperature of 950 ° C., 1000 ° C. or 1050 ° C. for 1 hour, and then cooled in oil.
  • the sub-zero treatment was maintained at ⁇ 75 ° C. for 2 hours using dry ice and ethanol.
  • the aging treatment was carried out in an atmospheric furnace at 500 ° C., 510 ° C., 520 ° C., and 530 ° C. for 16 hours and then cooled in the air.
  • the cross-sectional metal structure after the solution treatment was observed by etching with an aqueous solution of ferric chloride. As a result of the metal structure observation, No. No.
  • Example 2 No. 1 of the present invention used in Example 1.
  • a compact tension type test piece of 15 mm ⁇ 36 mm ⁇ 38.5 mm was produced from the heat-treated material of 13 alloy, and fracture toughness was measured based on ASTM E399.
  • Table 3 shows the measurement results.
  • Table 3 shows the temperature of the solution treatment and the aging treatment and the value of the formula (5).
  • Example 3 No. used in Example 1 No. 11 alloy and no.
  • the raw material after heat treatment of 13 alloy and AISI4340 equivalent material of low alloy type high strength steel were observed for rusting after 72 hours in a salt spray test at 35 ° C. and 5% sodium chloride solution.
  • the observation results are shown in Table 4. No. No. 11 alloy and no. In 13 alloys, the test was extended to 2000 hours and the rusting state was observed, but no rusting was confirmed.
  • Table 4 shows that the precipitation-strengthened stainless steel of the present invention is superior in corrosion resistance as compared with the conventional low alloy high strength steel.
  • a stress controlled axial force fatigue test was conducted.
  • Table 5 shows the number of cycles when the test piece was broken and the maximum number of cycles obtained in the test and the maximum stress applied to the test piece were summarized.
  • the fatigue curve of AISI 4340 described in Non-Patent Document 2 the fatigue curve of 15-5PH stainless steel, and 11, no.
  • FIG. 4 shows a summary of the 13 fatigue test results.
  • FIG. 4 shows that the precipitation-strengthened stainless steel of the present invention is superior in fatigue characteristics as compared with conventional low alloy high strength steel and stainless steel.
  • the present invention is a high-strength stainless steel having excellent 0.2% proof stress, tensile strength, and excellent corrosion resistance, aircraft legs and spacecraft primary structural members that require high strength, such as flap track rails. It is suitable for fastening members such as slat track rails and fasteners, various actuators, door hinges, engine parts and the like. As other applications, application to sports equipment such as turbine blade materials for power plants, shaft materials for engines, and heads of golf clubs, bicycle parts, automobile parts, ship parts, and the like can also be expected.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne un acier inoxydable de haute résistance qui conserve des niveaux de résistance à la traction et de ductilité qui peuvent être atteints par des aciers inoxydables de haute résistance classiques, et qui présente une résistance mécanique améliorée de 0,2 %. L'invention concerne spécifiquement un acier inoxydable durci par précipitation qui comprend, en pourcentage massique, 0,2 % ou moins de C, 7 à 14 % inclus de Ni, 0 à 3,5 % inclus de Co, 9,5 à 14 % inclus de Cr, 0,5 à 3 % inclus de Mo, 0,25 à 1 % exclus d'Al, et plus de 0,75 % et pas plus de 2,5 % de Ti, le solde étant du fer et des impuretés, et qui répond à toutes les exigences représentées par les formules (1) à (4). Formule (1) : 1260 - 65Ni - 20Co - 40Cr ≥ 0 Formule (2) : 670 + 75Ni + 40Co - 100Cr ≥ 0 Formule (3) : 0,125 ≤ (Al/Ti) ≤ 1,25 Formule (4) : 1,45 ≤ (Al+Ti) ≤ 2,95 Dans les formules, les teneurs en Ni, Co, Cr, Al et Ti sont des pourcentages massiques.
PCT/JP2011/064229 2010-06-28 2011-06-22 Acier inoxydable durci par précipitation et son procédé de production WO2012002208A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP2011546519A JP4918632B2 (ja) 2010-06-28 2011-06-22 析出強化型ステンレス鋼及びその製造方法

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP2010-146100 2010-06-28
JP2010146100 2010-06-28
JP2011055430 2011-03-14
JP2011-055430 2011-03-14

Publications (1)

Publication Number Publication Date
WO2012002208A1 true WO2012002208A1 (fr) 2012-01-05

Family

ID=45401928

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2011/064229 WO2012002208A1 (fr) 2010-06-28 2011-06-22 Acier inoxydable durci par précipitation et son procédé de production

Country Status (3)

Country Link
JP (1) JP4918632B2 (fr)
TW (1) TW201207127A (fr)
WO (1) WO2012002208A1 (fr)

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2012102638A (ja) * 2010-11-09 2012-05-31 Hitachi Ltd 析出硬化型マルテンサイト系ステンレス鋼およびそれを用いた蒸気タービン部材
CN103215521A (zh) * 2012-01-19 2013-07-24 株式会社日立制作所 析出硬化型马氏体不锈钢、使用其的蒸汽轮机长叶片、蒸汽轮机、发电设备
CN103290333A (zh) * 2012-02-27 2013-09-11 株式会社日立制作所 蒸气涡轮转子
JP2014201792A (ja) * 2013-04-05 2014-10-27 株式会社日立製作所 析出硬化系マルテンサイト系ステンレス鋼、蒸気タービン動翼および蒸気タービン
WO2015075262A1 (fr) * 2013-11-25 2015-05-28 Aubert & Duval Acier inoxydable martensitique, pièce réalisée en cet acier et son procédé de fabrication
JP2017066495A (ja) * 2015-10-01 2017-04-06 日立金属株式会社 析出強化型ステンレス鋼の製造方法
WO2020054540A1 (fr) * 2018-09-13 2020-03-19 大同特殊鋼株式会社 Acier inoxydable à base de martensite de type à durcissement par précipitation et élément de forage d'excavation souterrain
JP2020045560A (ja) * 2018-09-13 2020-03-26 大同特殊鋼株式会社 析出硬化型マルテンサイト系ステンレス鋼及び地下掘削用ドリル部品
WO2021173976A1 (fr) * 2020-02-26 2021-09-02 Crs Holdings, Inc. Acier inoxydable durcissable par précipitation à haute résistance, à ténacité élevée à la fracture
CN113981200A (zh) * 2021-10-20 2022-01-28 陕钢集团产业创新研究院有限公司 一种以水为介质的40Cr圆钢热处理方法
CN114645117A (zh) * 2022-03-21 2022-06-21 河南中原特钢装备制造有限公司 一种17-4ph材料控氮合金化锻后热处理工艺
CN115667570B (zh) * 2020-02-26 2024-06-07 Crs控股有限责任公司 高断裂韧性、高强度、沉淀硬化型不锈钢

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5409708B2 (ja) * 2011-06-16 2014-02-05 株式会社日立製作所 析出硬化型マルテンサイト系ステンレス鋼と、それを用いた蒸気タービン長翼

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05125490A (ja) * 1991-10-31 1993-05-21 Japan Steel Works Ltd:The 析出硬化型ステンレス鋼
JPH0610042A (ja) * 1992-06-24 1994-01-18 Daido Steel Co Ltd 析出硬化系ステンレス鋼の鍛造加工方法
JPH0892699A (ja) * 1994-09-21 1996-04-09 Daido Steel Co Ltd 析出硬化型ステンレス鋼
JP2008528797A (ja) * 2005-01-25 2008-07-31 ケステック イノベーションズ エルエルシー Ｎｉ３Ｔｉη相析出によって強化されたマルテンサイトステンレス鋼

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH05125490A (ja) * 1991-10-31 1993-05-21 Japan Steel Works Ltd:The 析出硬化型ステンレス鋼
JPH0610042A (ja) * 1992-06-24 1994-01-18 Daido Steel Co Ltd 析出硬化系ステンレス鋼の鍛造加工方法
JPH0892699A (ja) * 1994-09-21 1996-04-09 Daido Steel Co Ltd 析出硬化型ステンレス鋼
JP2008528797A (ja) * 2005-01-25 2008-07-31 ケステック イノベーションズ エルエルシー Ｎｉ３Ｔｉη相析出によって強化されたマルテンサイトステンレス鋼

Cited By (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2012102638A (ja) * 2010-11-09 2012-05-31 Hitachi Ltd 析出硬化型マルテンサイト系ステンレス鋼およびそれを用いた蒸気タービン部材
CN103215521A (zh) * 2012-01-19 2013-07-24 株式会社日立制作所 析出硬化型马氏体不锈钢、使用其的蒸汽轮机长叶片、蒸汽轮机、发电设备
JP2013147698A (ja) * 2012-01-19 2013-08-01 Hitachi Ltd 析出硬化型マルテンサイト系ステンレス鋼、それを用いた蒸気タービン長翼、蒸気タービン、発電プラント
US9388702B2 (en) 2012-01-19 2016-07-12 Mitsubishi Hitachi Power Systems, Ltd. Precipitation hardening martensitic stainless steel, and steam turbine long blade, steam turbine, and power plant using the same
US9200524B2 (en) 2012-02-27 2015-12-01 Mitsubishi Hitachi Power Systems, Ltd. Steam turbine rotor
CN103290333A (zh) * 2012-02-27 2013-09-11 株式会社日立制作所 蒸气涡轮转子
JP2013209742A (ja) * 2012-02-27 2013-10-10 Hitachi Ltd 蒸気タービンロータ
JP2014201792A (ja) * 2013-04-05 2014-10-27 株式会社日立製作所 析出硬化系マルテンサイト系ステンレス鋼、蒸気タービン動翼および蒸気タービン
US20160289805A1 (en) * 2013-11-25 2016-10-06 Aubert & Duval Martensitic stainless steel, part made in said steel and method for manufacturing same
FR3013738A1 (fr) * 2013-11-25 2015-05-29 Aubert & Duval Sa Acier inoxydable martensitique, piece realisee en cet acier et son procede de fabrication
WO2015075262A1 (fr) * 2013-11-25 2015-05-28 Aubert & Duval Acier inoxydable martensitique, pièce réalisée en cet acier et son procédé de fabrication
JP2017066495A (ja) * 2015-10-01 2017-04-06 日立金属株式会社 析出強化型ステンレス鋼の製造方法
WO2020054540A1 (fr) * 2018-09-13 2020-03-19 大同特殊鋼株式会社 Acier inoxydable à base de martensite de type à durcissement par précipitation et élément de forage d'excavation souterrain
JP2020045560A (ja) * 2018-09-13 2020-03-26 大同特殊鋼株式会社 析出硬化型マルテンサイト系ステンレス鋼及び地下掘削用ドリル部品
JP7298382B2 (ja) 2018-09-13 2023-06-27 大同特殊鋼株式会社 析出硬化型マルテンサイト系ステンレス鋼及び地下掘削用ドリル部品
WO2021173976A1 (fr) * 2020-02-26 2021-09-02 Crs Holdings, Inc. Acier inoxydable durcissable par précipitation à haute résistance, à ténacité élevée à la fracture
CN115667570A (zh) * 2020-02-26 2023-01-31 Crs控股有限责任公司 高断裂韧性、高强度、沉淀硬化型不锈钢
US11702714B2 (en) 2020-02-26 2023-07-18 Crs Holdings, Llc High fracture toughness, high strength, precipitation hardenable stainless steel
CN115667570B (zh) * 2020-02-26 2024-06-07 Crs控股有限责任公司 高断裂韧性、高强度、沉淀硬化型不锈钢
CN113981200A (zh) * 2021-10-20 2022-01-28 陕钢集团产业创新研究院有限公司 一种以水为介质的40Cr圆钢热处理方法
CN114645117A (zh) * 2022-03-21 2022-06-21 河南中原特钢装备制造有限公司 一种17-4ph材料控氮合金化锻后热处理工艺

Also Published As

Publication number Publication date
TW201207127A (en) 2012-02-16
JP4918632B2 (ja) 2012-04-18
JPWO2012002208A1 (ja) 2013-08-22

Similar Documents

Publication Publication Date Title
JP4918632B2 (ja) 析出強化型ステンレス鋼及びその製造方法
JP6111763B2 (ja) 強度及び靭性に優れた蒸気タービンブレード用鋼
TWI470095B (zh) 析出強化型麻田散鐵鋼及其製造方法
JP5076683B2 (ja) 高靭性高速度工具鋼
DE102010026808B4 (de) Korrosionsbeständiger austenithaltiger phosphorlegierter Stahlguss mit TRIP- bzw. TWIP-Eigenschaften und seine Verwendung
JP6223743B2 (ja) Ｎｉ基合金の製造方法
US20170088910A1 (en) Corrosion and cracking resistant high manganese austenitic steels containing passivating elements
KR20190046729A (ko) 지열 발전 터빈 로터용 저합금강 및 지열 발전 터빈 로터용 저합금 물질, 및 이들의 제조 방법
EP3134556A2 (fr) Aciers inoxydables durcissables en surface
US10000830B2 (en) Method for manufacturing martensite-based precipitation strengthening stainless steel
JP2009503257A (ja) 耐食性・冷間成形性・切削性高強度マルテンサイト系ステンレス鋼
JP5088455B2 (ja) 二相ステンレス鋼
CN106460100A (zh) 抗冲击或冲击负荷的钛合金以及由其制作零件的方法
WO2007123164A1 (fr) Matériau de segment de piston pour moteur à combustion interne
JP2006526711A (ja) ナノ析出強化超高強度耐腐食性構造用鋼
JP6582960B2 (ja) マルエージング鋼
US20160333432A1 (en) Case hardening steel and carburized component obtained therefrom
JP2014208869A (ja) 析出強化型マルテンサイト鋼
KR101301617B1 (ko) 고강도 고인성 소재 및 이를 이용한 타워 플랜지 제조방법
JP5512494B2 (ja) 高強度・高靭性非調質熱間鍛造部品およびその製造方法
JP6501652B2 (ja) 析出硬化能に優れたマルテンサイト系ステンレス鋼
JP7131225B2 (ja) 析出硬化型マルテンサイト系ステンレス鋼
CA2930153A1 (fr) Acier maraging
WO2014203302A1 (fr) Acier inoxydable à durcissement par précipitation et composant en acier inoxydable
WO2020054540A1 (fr) Acier inoxydable à base de martensite de type à durcissement par précipitation et élément de forage d'excavation souterrain

Legal Events

Date Code Title Description
WWE Wipo information: entry into national phase

Ref document number: 2011546519

Country of ref document: JP

121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 11800673

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 11800673

Country of ref document: EP

Kind code of ref document: A1